Smithells

S E m H EDITION

EDITED BY EA.. BRANDES & GOBo B

Smithells Metals Reference Book

Smithells Metals Reference Book Seventh Edition

Edited by

E. A. Brandes CEng, BSc(Lond), ARCS, FIM and

G. B. Brook

DMet(She$), FEng, FIM

U T T E R W O R T H E I N E M A N N

Butterw orth-Heinemann Linacre House, Jordan Hill, Oxford OX2 8DP 225 Wildwood Avenue, Woburn, MA 01801-2041 A division of Reed Educational and Professional Publishing Ltd

-@A

member of the Reed Elsevier plc group

OXFORD AUCKLAND BOSTON JOHANNESBURG MELBOURNE NEW DELHI

Fmt published 1949 Second edition 1955 Third edition 1962 Fourth edition 1967 Fifth edition 1976 Reprinted 1978 Sixth edition 1983 Seventh edition 1992 Paperback edition (with corrections) 1998, 1999 Q Reed Educational and Pmfessiond Publishing Ltd 1992 All rights reserved. No part of this publication may be reproduced in any material form (including photocopying or storing in any medium by electronic means and whether or not transiently or incidentally to some other use of this publication) without the written permission of the copyright holder except in accordance with the provisions of the Copyright, Designs and Patents Act 1988 or under the terms of a licence issued by the Copyright Licensing Agency Ltd. 90 Tottenham Court Road, London, England WlP 9HE. Applications for the copyright holder’s written permission to reproduce any part of this publication should be addressed to the publishers

British Library Cataloguing in Publication Data A catalogue record for tl& book is available from the British Library Library of Congress Cataloguing in Publication Data A catalogue record for this book is available from the Libmy of Congress ISBN 0 7506 3624 6

Printed and bound in Great Brihin by The Bath Press, Bath

Contents Preface to the Seventh Edition Acknowledgements List of contributors

xv xvi xvii

1 Related specifications

1-1

1.1 Related specifications Related specifications for steels Related specifications for aluminium alloys Related specifications for copper alloys Related specificationsfor magnesium alloys

2 Introductory tables

1-1 1-1 1-7 1-8 1-9

2- 1

2.1 Conversion factors SI units - Conversion to and from SI units - Temperature conversions, IPTS-49 to IPTS-68 - Corrosion conversion factors - Sieve Nos to aperture size - Temperature scale conversions

2-1

2.2 Mathematical formulae Algebra - Series and progressions - Trigonometry - Mensuration - Coordinate geometry - Calculus

2-12

3 General physical and chemical constants

3-1

Atomic weights and atomic numbers - General physical constants Moments of inertia - Periodic system 3.1 Radioactive isotopes and radiation sources Positron emitters - Beta energies and half-lives - Gamma energies and half-lives - Nuclides for alpha, beta, gamma and neutron sources

4 X-ray analysis of metallic materials 4.1 Introduction

4.2 Excitation of X-rays X-ray wavelengths 4.3 X-ray techniques X-ray diffraction - Specific applications - Crystal geometry 4.4 X-ray results Metal working - Crystal structure - Atomic and ionic radii V

3-5

4-1 4-1 4-1 4-1 1

4-36

vi

Contents 4.5 X-ray fluorescence 4.6 Radiation screening

442 444

Definitions - Concrete screening - Lead screening

5 Crystallography 5.1 The structure of crystals

Translation groups - Symmetry elements - The point group - The space group 5.2 The Schoenflies system of point- and space-groups notation 5.3 The Hermann-Mauguin system of point- and space-group notation Notes on the space-group tables

6 Crystal chemistry 6.1 Structures of metals, metalloids and their compounds 6.2 Structural details

7 Metallurgically important minerals 7.1 Ore grades and sources

5- 1 5-1 5-3 5-3

6-1 6-1 6-36

7-1 7-2

8 Thermochemical data

8-1

8.1 Symbols 8.2 Changes of phase

8-1 8-1

8.3 8.4 8.5

8.6

8.7

Elements - Intermetallic compounds - Metallurgically important compounds Heat, entropy and free energy of formation Elements - Intermetallic compounds - Selenides and tellurides Intermetallic phases Metallic systems of unlimited mutual solubility Liquid binary metallic systems Metallurgically important compounds Borides - Carbides - Nitrides - Silicides - Oxides - Sulphides - Halides Silicates and carbonates - Compound (double) oxides - Phosphides Phosphides dissociation pressures - Sulphides dissociation pressures Molar heat capacities and specific heats Elements - Alloy phases and intermetallic compounds - Borides Carbides - Nitrides - Silicides - Oxides - Sulphides, selenides and tellurides - Halides Vapour pressures Elements - Halides, oxides

9 Physical properties of molten salts 9.1 9.2 9.3 9.4 9.5

Density of pure molten salts Densities of molten salt systems Density of some solid inorganic compounds at room temperature Electrical conductivity of pure molten salts Electrical conductivity of molten salt systems

8-8 8-16 8-21

8-41

8-54

9-1 9-1 9-7 9-19 9-20 9-28

Contents

9.6 9.7 9.8 9.9

Surface tension of pure molten salts Surface tension of binary molten salt systems Viscosity of pure molten salts Viscosity of molten binary salt systems

10 Metallography 10.1 Macroscopic examination 10.2 Microscopic examination Etching reagents for macroscopic examination - Plastic for mounting Attack polishing - Electrolytic polishing solutions - Reagents for chemical polishing - Etching - Colour etching - Etching for dislocations 10.3 Metallographic methods for specific metals Aluminium - Antimony and bismuth - Beryllium - Cadmium Chromium - Cobalt - Copper - Gold - Indium - Iron and steel Cast iron - Lead - Magnesium - Molybdenum - Nickel - Niobium Platinum group metals - Silicon - Silver - Tantalum - Tin Titanium - Tungsten - Uranium - Zinc - Zirconium - Bearing metals Cemented carbides and other hard alloys - Powdered and sintered metals 10.4 Electron metallography Transmission electron microscopy - Extraction - Replica techniques for industrial alloys - Thin foil techniques for industrial alloys - Scanning electron microscopy - Electron spectroscopy 10.5 Quantitative image analysis 10.6 Scanning acoustic microscopy

11 Equilibrium diagrams 1 1.1 Index of binary diagrams 1 1.2 Equilibrium diagrams 11.3 Acknowledgements Binary systems 11.4 Ternary and higher systems

12 Gas-metal systems 12.1 The solution of gases in metals Dilute solutions of diatomic gases - Complex @-metal systems Solutions of hydrogen - Solutions of nitrogen - Solutions of oxygen Solutions of the noble gases - Theoretical and practical aspects of gasmetal equilibria

13 Diffusion in metals 13.1 Introduction 13.2 Methods of measuring D Steady-state methods - Non-steady-state methods - Indirect methods, not based on Fick’s laws 13.3 Mechanisms of diffusion Selfdiffusion in solid elements - Tracer impurity diffusion coefficients Diflusion in homogeneous alloys 13.4 Chemical diffusion coefficient measurements

vii

942 945 9-5 1 9-52

10-1 10-1 10-1

10-22

1M2

1M9 10-70

11-1 11-1 11-7 11486

11496

12-1 12-1

13-1 13-1 13-4

13-7 13-70

viii

Contents 13.5 Grain boundary self-dimusion 13.6 Self-diffusion in liquid metals

14 General physical properties 14.1 The physical properties of pure metals

Physical properties of pure metals at normal temperatures - Physical properties of pure metals at elevated temperatures 14.2 The physical properties of liquid metals Density - Surface tension - Viscosity - Specific heat, thermal conductivity and electrical resistivity 14.3 The physical properties of aluminium and aluminium alloys Aluminium alloys at normal temperatures 14.4 The physical properties of copper and copper alloys 14.5 The physical properties of magnesium and magnesium alloys 14.6 The physical properties of nickel and nickel alloys 14.7 The physical properties of titanium and titanium alloys 14.8 The physical properties of zinc and zinc alloys 14.9 The physical properties of zirconium alloys 14.10 The physical properties of pure tin 14.11 The physical properties of steels Normal and elevated temperatures - Low temperature properties of steels

15 Elastic properties, damping capacity and shape memory alloys

13-116 13-118

14-1 14-1 14-45 14-14 14-16 14-19 1422 14-25 14-26 1426 14-26 14-27

15-1

15.1 Elastic properties

15-1

Elastic constants of polycrystalline metals - Young's modulus Rigidity modulus - Bulk modulus - Poisson's ratio Elastic compliances and elastic stiffnesses of single crystals Room temperature - Cubic systems - Hexagonal systems - Trigonal systems - Tetragonal systems - Orthorhombic systems 15.2 Damping capacity Specific damping capacity of commercial alloys - Anelastic damping 15.3 Shape memory alloys Mechanical properties of shape memory alloys - Compositions and transformation temperatures - Titanium-nickel shape memory alloy properties

154

16 Temperature measurement and thermoelectric properties

15-36

161

16.1 Temperature measurement

161

Fixed points of ITS90 - Thermal electromotive force of elements and some binary alloys - Absolute thermoelectric power 16.2 Thermocoude reference tables

16-4

17 Radiating properties of metals Total and spectra emissivity - Temperature measurement and emissivity - Emissivity values, spectral and total - Emissivity of oxidized metals

17-1

Contents

18 Electron emission 18.1 Thermionic emission Elements - Adsorbed layers - Refractory metal compounds - Practical cathodes 18.2 Photoelectric emission Photoelectric work functions - Emitting surfaces 18.3 Secondary emission Emission coefficients - Oxidized alloys - Photocells - Insulating metal compounds 18.4 Auger emission 18.5 Electron emission under positive ion bombardment 18.6 Field emission

19 Electrical properties 19.1 Resistivity Pure metals - Alloys - Specific copper alloys - EC aluminium 19.2 Superconductivity Transition temperatures and critical fields of elements Superconducting compounds

20 Magnetic materials and their properties 20.1 Magnetic materials 20.2 Permanent magnetic materials Steels - cast irons - Alnico alloys - Ferrites - Rare earths and cobalt alloys - Neodymiun iron boron - Bonded materials 20.3 Magnetically soft materials Silicon iron alloys - Ferrites - Garnets - Nickel iron alloys Amorphous alloy materials 20.4 High saturation and constant permeability alloys 20.5 Magnetic powder core materials 20.6 Magnetic temperature compensating materials 20.7 Non magnetic steels and cast irons - Units and definitions

21 Mechanical testing 21.1 Hardness testing Brinell - Rockwell - Rockwell superficial hardness - Vickers - Microhardness - Hardness conversion tables 21.2 Tensile testing Test piece dimensions - standards 21.3 Impact testing of notched bars Izod - Charpy 21.4 Plane strain fracture toughness testing Test pieces - Calculation and interpretation of results - Plane stress COD - Recording test results

ix 18-1 18-1 18-4 18-5

18-7 18-8 18-9

19-1 19-1 19-7

20-1 20-1 2&2 20-9 20-1 7 20-17 20-17 20-18

21-1 21-1 21-8 21-10 21-10 21-12

x

Contents

22 Mechanical properties of metals and alloys 22.1 Aluminium and aluminium alloys Alloy and temper designation system - Mechanical properties at room, elevated and low temperatures - Creep and fatigue 22.2 Copper and copper alloys Standard specifications - Mechanical properties at room, elevated and low temperature - Fatigue - Impact - Creep - Tough pitch copper Silver alloys 22.3 Lead and lead alloys 22.4 Magnesium and magnesium alloys Mechanical properties at room and elevated temperatures - Creep Fatigue - Impact - Heat treatments 22.5 Nickel and nickel alloys Standard specifications - Mechanical properties at room, elevated and cryogenic temperatures - Fatigue - Creep 22.6 Titanium and titanium alloys Specifications - Mechanical properties at room, elevated and low temperatures - Creep - Fatigue - Impact 22.7 Zinc and zinc alloys Mechanical properties at room temperature 22.8 Zirconium and zirconium alloys Mechanical properties at room and elevated temperatures 22.9 Tin and its alloys 22.10 Steels Mechanical properties forged and rolled room temperature - Micro alloyed - Hot tensile - Fatigue - Creep - Sub zero - Tool steels 22.11 Other metals of industrial importance 22.12 Bearing metals

23 Sintered materials 23.1 23.2 23.3 23.4 23.5 23.6 23.7 23.8 23.10 23.11 23.12 23.13 23.14 23.15 23.16 22.17

The PM process The products Manufacture and properties of powders Properties of powder compacts Sintering Ferrous components Copper based components Aluminium components Mechanical properties of sintered components Heat treatment of sintered steels Case hardening of sintered steels Steam treatments Wrought PM materials Spray forming Injection moulding Hard metals

24 Lubricants 24.1 Introduction 24.2 Friction, wear and boundary lubrication 24.3 Characteristics of lubricating oils Viscosity - Boundary lubrication - Chemical stability - Physical properties 24.4 Mineral oils

22-1 22-1 22-26

2248 22-5 1 22-65 22-82 22-94 22-94 22-96 22-100 22-159 22-162

23-1 23-1 23-1 23-2 234 23-4 23-7 23-1 1 23-1 1 23-12 23-14 23-14 23-22 23-22 23-26 23-27 23-28

24-1 24-1 24-1 24-2 24-3

Contents

24.5 24.6 24.7 24.8 24.9

Emulsions Water-based lubricants Synthetic oils Greases Oil additives

25 Friction and wear 25.1 Friction Unlubricated - Static - Very hard solids - Sliding - Polymers Lubricated surfaces 25.2 Wear Definitions - Wear resistant materials - Materials for abrasion resistance - Wear rates - Hardfacings - Ceramics - Carbide composites Wear performance - Erosive wear - Cavitation erosion

26 Casting alloys and foundry data 26.1 Casting techniques 26.2 Patterns - Crucibles - Fluxing Contraction allowances - Materials - Dressings - Fluxing and inoculation 26.3 Aluminium alloys 26.4 Copper base alloys 26.5 Nickel base alloys 26.6 Magnesium alloys 26.7 Zinc base alloys 26.8 Steel castings Casting characteristics - Heat treatment - Typical properties Pressure purposes - Weldable tubes - Aerospace - Investment cast 26.9 Cast irons Classification - Typical analysis - Properties - Pig irons - Alloying elements - Microconstituents - Malleable iron - Nodular iron Compacted iron - Special purpose irons

27 Engineering ceramics and refractory materials 27.1 27.2 27.3 27.4 27.5 27.6 27.7 27.8

Physical and mechanical properties of engineering ceramics Prepared but unshaped refractory materials Aluminous cements Castable materials Mouldable materials Ramming materials Gunning materials Design of refractory linings

28 Fuels 28.1 Coal 28.2 Metallurgical cokes 28.3 Gaseous fuels, liquid fuels and energy requirements Liquid fuels - Gaseous fuels - Energy data

xi

24-6 24-6 24-6 24-8 24-10

25-1 25-1 25-9

261 26-1 26-10 26-20 26-32 26-44 2648 2660 26-62 26-74

27-1 27-1 27-6 27-7 27-12 27-12 27-12 27-12 27-12

28-1 28-1 28-9 28-15

xii

Contents

29 Heat treatment 29.1 29.2 29.3 29.4 29.5 29.6 29.7 29.8

Chemistry of controlled atmosphere processes Heat treatment equipment Steel - Normalizing - Hardening - Case hardening - Carburizing - Nitriding Cast iron - Malleabilizing- Nodular Aluminium alloys - Annealing - Stabilizing - Hardening Copper alloys - Environments - Annealing - Stress relief Magnesium alloys - Safety - Environment - Casting alloys Nickel and cobalt alloys

30 Laser metal working 30.1 30.2 30.3 30.4 30.5 30.6 30.7 30.8 30.9 30.10

Introduction Lasers - Basic principles Process considerations Cutting Drilling and engraving Welding Transformation hardening Surface cladding and alloying Safety Bibliography

29-1 29-1 29-5 29-7 29-17 29-17 29-20 29-21 29-23

30-1 30-1 30-1 304 30-7 3&9 30-10 30-12 30-13 30-13 3&14

-

31 Guide to corrosion control 31.1 Introduction Types - Environments - Accelerating factors 31.2 Bimetallic corrosion 31.3 Crevice corrosion 31.4 Corrosion/erosion resistant materials 31.5 Cavitation 31.6 Corrosion fatigue 31.7 Stress corrosion cracking 3 1.8 Hydrogen embrittlement 31.9 Fracture toughness under corrosive conditions 31.10 Atmospheric corrosion 31.11 High temperature oxidation resistance 31.12 Contact corrosion

32 Electroplating and metal finishing 32.1 32.2 32.3 32.4 32.5 32.6 32.7 32.8 32.9 32.10

Polishing compositions Cleaning and pickling processes Anodizing and plating processes Electroplating process Plating processes for magnesium alloys Electroplating process parameters Miscellaneous coating processes Plating formulae for non-conducting surfaces Methods of stripping electroplated coatings Conversion coating processes Phosphating - Chromating - Colouring 32.11 Glossary of trade names for coating processes

31-1 31-1 31-3 31-5 31-5 31-6 31-7 31-8 31-9 31-10 31-12 31-13 31-13

32-1 32-1 32-2 32-7 32-9 32-17 32-18 32-19 32-20 32-21 32-22 32-24

Contents

33 Welding 33.1 33.2 33.3 33.4 33.5 33.6

Introduction Glossary of welding terms Resistance welding Friction welding Fusion welding British standards relating to welding

34 Soldering and brazing 34.1 34.2 34.3 34.4 34.5

Introduction Quality assurance Soldering Brazing Bibliography

35 Vapoar deposited coatings 35.1 Physical vapour deposition Evaporation - Sputter plating - Ion cleaning 35.2 Chemical vapour deposition Elements - Oxides - Nitrides - Carbides

36 Superplasticity

xiii 33-1 33-1 33-1 33-5 33-10 33-13 33-40

34-1

341 34-1 34-2 34-9 34-14

35-1 35-1 35-2

36-1

Non-ferrous systems - Iron and steel systems - Powdered material systems

37 Metal-matrix composites

Index

37-1

I- 1

Preface to the Seventh Edition

This edition has been prepared with major assistance from co-editor G. B. Brook. The general presentation of previous editions has been retained and SI units have been used throughout. The values for formulations given are selected by the contributors as the most reliable but for a particular review the reader should consult the references. In the case of mechanical properties data the values are for general guidance only; for design purposes it is essential to consult the relevant specifications. To minimize bulk, the First Aid section has been omitted but a new chapter on related specifications has been added. Also added is a chapter on Metal-Matrix Composites. The Equilibrium Diagrams section has been considerably updated and extended and the Magnetic Materials, Sintered Materials, Heat Treatment, Engineering Ceramics, Soldering and Brazing, Shape Memory, X-ray Analysis of Metallic Materials and Lasers have been rewritten. Other chapters have been reviewed and updated as required.

E.A.B. Chalfont St Peter, Bucks

Acknowledgements Assistance given by the following organizations is gratefully acknowledged: British Ceramic Research Ltd Bureau International des Poi& et Mksures Copper Development Association Culham Labs UKAEA Fulmer Research Institute Ltd Imperial College of Science and Technology IMI Titanium Ltd International Tin Research Institute Lead and Zinc Development Association Magnesium Elektron Ltd Manganese Centre Amersham International University of Birmingham University of Dundee University of Manchester Institute of Science and Technology The Editors and Publishers thank all those who have authorized the reproduction of diagrams and tables and in particular the following: American Society for Metals, Cleveland, Ohio American Society for Testing Materials, Philadelphia, Pa. British Standards Institute, London Institute of Gas Engineers, London Genium Publications C o p , N.Y. International Atomic Energy, Vienna Maraw-Hill Book Co Inc., New York

Contributors Editors

E. A. Braodes, CEng, BSc(Lond), ARCS, FIM G. B. Brook, DMet(Sheff), FEng, FIM Contributors to this edition

Chapter

N.J. Archer, BA(Cantab), PhD L. C. Archibald, BSc(Nott), PhD B. J. Boden, CEng, BSc, PhD(Nott), MIM, FRIC, FICorrT

35 32 31 E. A. Braodes, CEng, BSc(Lond), ARCS, FIM 1, 2, 3, 11, 14.1, 22.10, 29.3-29.8 G. B. Brook, DMet(Sheff), FEng, FIM 6, 10, 14.3, 14.6, 15.2, 15.3, 22.1, 22.5, 22.11, 36, 37 V. A. Cahtt, CEng, FIM, MIQA 14.4, 22.2, 34 G. R. Campbell 22.12 J.Campbell, MA(Cantab), MMet(ShcE),PhD(Birm), DEng(Birm),FEng, FIM, 14.2, 26

FIBF W. C. Campbell-Heaelwood, CEng, BSc, FIMC, FIM, FInstP, FINDT S K. Cbatterjee, CEng, BSc(Calc), FIM A. R. Chivers, MA A. G. Clegg, MSc(Lond), PhD J. W. Cotton, BSc, FICeram M. Deighton, CEng, BSc(Dunelm), PhD, MIM A. G. Dowsoo, CEng, MA, PhD, FIM M. Fidao, BSc, MInstP I. Fitep.trick, CEng, BSc, PhD(Manc) P. J. Foster, CEng, BSc Tech, PhD, MIChE, MInstE T. I. Fowle, BSc(Eng), FIMechE R Freeman, BSc(Lond), MInstP T. G. Gooch, BSc(Lond), MSc(Eng), PhD, FWeldI A. M. Gothrie, CEng, BSc(Wales), MIM B. H. Haasoo, BSc(Lond) B. A. Hatt, MSc(Lond) D. Inman, CEng, BSc(Lond), PhD, DSc, DHonsCausa, MIMM, FRSC R. 0. J d m , ARCS, DIC, PhD, FInstP J. F. J&g, CEng, BSc, MIM A. D. Leclaire, BA(Cantab), FInstP J. H. Megaw, BSc(Qub), PhD, MInstP M. A. Moore, CEng, BSc(Met) (Wales), PhD A. Page, BSc, PhD(Lond), DIC T. J. Quino, BSc, DPhil, MInstP R A. Sbelton, CEng, BSc(Lond), PhD, AMIMM R. Smith, BSc(Birm), MINucE D. E. J. Talbot, CEng, MSc(Wales), MIM A. J. Wall, B$c, PhD N.A. Waterman, CEng, BSc(Wales), PhD, MIM, MInstP M. J. Wheeler, BTech, PhD, FInstP Xvii

14.11 22.9 14.8, 22.7 20 27 21 23 3.1, 4.7 15.1 28 24 19 33 29.2 14.7, 14.9, 22.6, 22.8 4.14.6 9 18 14.5, 22.4 13 30 25 7 16 8 22.3 12 14.8, 22.7 5 17

1 Related specifications Tables of related specifications are a guide to correspondence and should not be taken as exact equivalents. In all cases of doubt the national specification should be consulted. For more detail the references in some cases give more information. Unified number designations-UNS are five-digit numbers prefixed by a letter that characterizes the alloy system as shown below. UNS Letter Designation' Aluminium and aluminium alloys Copper and copper alloys u Specified mechanical properties steels E Rare earth and rare earth like metals and alloys F Cast irons and cast steels G AISI and SAE carbon and alloy steels H AISI H-steels J Cast steels (except tool steels) K Miscellaneous steels and ferrous alloys L Low melting metals and alloys NI Miscellaneous nonferrous metals and alloys N Nickel and nickel alloys P Precious metals and alloys R Reactive and refractory metals and alloys S Heat and corrosion resistant (stainless) steels T Tool steels W Welding filler metals

A C

gelated specifications for steels are given for seven countries in Table 1.1 with subsections for steels of different types. For cast aluminium alloys see Table 22.1 and for wrought aluminium alloys Table 1.2. Table 1.3 gives related copper alloy specifications subdivided into high-conductivity copper, brasses and nickel silvers. Magnesium cast and wrought are in Table 1.4, while for nickel alloys Table 22.26 and for titanium alloys Table 22.32 can be used. Table 1.1 RELATED SPECIFICATIONS FOR STEEL 1.1.1 Carbon steels UK Nominal BS970 composition (En) C < 0.06 Mn < 0.3 CS0.08 Mn0.2/0.4 c G 0.08 MnO. 110.4

CGO.08 Mn0.4J0.6 CO.OS/O.13 MnO.Sl0.7

015A03 030A04 MA04 (2A, 2B) 050A04 060A10

USA AISIISAE (UN9

1005 (G10050) 1006 (G10060) 1008 (G10080) M1008 (ClOOSO) 1011 (G10110)

W.Germany

Japan

France AFNOR

DIN (WkNo.)

JIS

Fd5

D6-2 (1.03 14) D7-1 (1.0313) UQ St36 (1.0204) U St14 (1.0336) U St36 (1.0203)

-

14 11 60

-

-

-

-

SPHTl

14 12 25

SBC

14 13 32

-

FdTu2 Fd3 XClO

Sweden

G405145 SIS

USSR GOST IOS&-M)

1-2

Related specijications

Table 1.1 RELATED SPECIFICATIONS OF STEEL-continued

UK Nominal BS970 composition (En)

C0.1/0.15 Mn0.3/0.5 CO.13/0.18 Mn0.7/0.9 C0.15/0.2 Mn0.3/0.6 CO.18/0.23 Mn0.4/0.6 C0.25/0.3 Mn0.7/0.9 C0.28/0.3 Mn0.7/0.9 CO.33/0.38 Mn0.7/0.9 C0.38/0.43 Mn0.7/0.9 C0.43/0.5 Mn0.6/1 .O C0.45/0.55 Mn0.6;l .O C0.6/0.65 Mn0.5/0.7 C0.7/0.75 Mn0.7/0.9 CO.7/0.9 Mn0.7/0.9 C0.95/1.05 Mn0.5/0.7

MOA12 080A15 080M15 040A17 050A20 (2C, 2D) 080A27 (5A) 080A30 (5B) 080A35 (8A) 080A40 (8C) 080M46 OXOM50 080A62 (43D) 080A72 080A83 060A99

USA AISIISAE (UNA')

1012 (G10120) 1016 (G10160) 1017 (G10170) 1020 (G10200) 1029 (G10290) 1030 (G10300) 1035 (G10350) 1040 (G10400) 1045 (G10450) 1050 (G10500) 1060 (G10600) 1070 (G10700) 1080 (G10800) 1095

W. Germany DIN (Wk No.)

Japan JIS

CklO (1.1121) Rst44.2 (1.0419/01) Ck15 (1.1141) C22 (1.0402)

-

-

-

SM58

13 50

-

-

-

-

-

14 50

20

-

-

S28C

-

-

-

cq35 (1.1172) Ck34 (1.1181) Ck40 (1.1186) Ck45 (1.1191) Ck50 (1.1206) Ck60 (1.1221) Ck67 (1.1231) Ck75 (1.1248) CklOl (1.1274)

s30c

-

30/m

s35c

15 12

35

s4oc

-

40

s45c

16 72

45

-

-

50

S58C

16 78

60,60G

-

17 70

-

17 74 17 78 18 70

-

France AFNOR

xc12 AF37C12 XC18 c20

XC32 XC42H1 XC4Wl xc45

xc60 XC68 xc75 XClOO

1.1.2 Carbon-higher manganese steels UK USA

20Mn6 (1.1169)

SMnC420 -

-

-

18G2S

-

GS-24Mn4 (1.1136) 20M6 (1.1170) 36Mn5 (1.1167)

-

CO.15/0.23 Mn1.0/1.4 CO.15/0.23 Mn1.35/1.7 C0.24/0.32 Mn1.0/1.4 C0.24/0.32 Mn1.3/1.7 C0.32/0.40 Mn1.0/1.4

1518 (G15180) 1524 (G15240) 1526 (G15260) 1527 1536 (G15360)

-

20M5

France AFNOR

150M28 (14A/14B) 120M36 (15B)

SUP4

105060

Japan JIS

AISIISAE (UNA')

150M19 (14Aj14B) 120M28

-

USSR GOST

W . Germany DIN ( Wk No.)

Nominal BS970 composition (En)

120M19

Sweden G4051-65 SIS

20M5 35M5

Sweden G4051-65 SIS

SCMnl

-

2120

3562 35GL

USSR GOST 105O-60

18G2

1.1.3 Carbon-free cutting steels UK Nominal BS970 composition (En)

USA AISIISAE (UNA')

France AFNOR

Ci0.15 Mn0.9/1.3 CO)

(x2 4 a c (roots m1 and m2), Ae"lX+ BemZX (b) If b2=4ac (two equal roots, m i ) , emlx(Ax+B) (c) If b2 I year

100 days-1 year

1311

3 7

'1'"7Te, OTm

'"Cel'"Pr,

94Nb,

137cs,

'"Eu, lS4Eu, 226Ra+D.P., 227Ac+D.P., 2 2 8 b 228 I Ac, 228Th+D.P. 36Cl,

'O-,

3-8

General physical and chemical constants

TI& 3.6 GAMMA ENERGIES AND HALF-LIVES

"'h,

Hnlf-ire P-enetgY

MeV

l0000.&)of inhomogeneous electron density distributions (e.g. vacancy clusters or Guinier-Preston zones) cause scattered radiation pattern near main beam

Determination of size, shape and composition (in terms d electron density) of Guinier-Preston zones,vacancy clusters, etc. in metallic transmission technique therefore limited to thin samples-typically IO-50pm

X-ray fluorescence

Electrons ejected from inner shells of atoms cause emission of X-rays (fluorescence)characteristic of atomic speciesexciting radiation may be photons ( y and X-rays), positive ions or electrons. Fluorescent X-rays analysed by wavelength or energy dispersive spectrometers.

Elemental analyses Na t o U routine. C, N, 0, F require specifically designed equipment. Hence used for routine analysis of composition of ores, semi-finished and finished metals and their alloys Quantitative analysis normally employs calibrated standards N.B. Results are obtained from surface layer of approx. 2um thickness

X-ray photo-electron spectroscopy (XPSI

Electrons from inner shells of atoms are ejected by Xradiation of specific wavelength. Energy of ejected electron measured by spectrometer givcs information on binding energy of electron shells

Qualitative and quantitative analysis of surfxe Iayers, XPS signals typically come from depths of less than 50 A. Elemental analysis He t o U including, C, N, 0, F. Information on the state of bonding of analysed elements

angles (e) by crystal planes of appropriate spacing (d) which satisfies the Bragg equation, i.e. til=2tlsinU

.____I.

__

I _ _ _ _ _ _

.r: 3

3

Q

G-

T a b 4.7

X-RAY DIFFRACITON TECHNIQUES

Experimental Techniuue

Descriotion

Metallurgical applications

Single-crystal camera Weissenberg camera Precession camera 4utomated single crystal iiffractometer

SmaU single crystal or metallic grains oriented on a two-axis goniometer with a prominent crystallographic axis along the goniometer axis. Crystal rotated in a monochromatic or filtered X-ray beam. Produces a spot diffraction pattern related to the symmetry of the crystal.

Crystal structure analysis (i.e. determination of atom positions and thermal vibrations) etc.

Back reflection or transmission Laue camera

Stationary sample, single crystal or polycrystalline irradiated with white, continuous wavelength radiation. The back scattered, (back reflection) and forward scattered transmission d i h c t i o n patterns are recorded on flat films perpendicular to the incident beam. The symmetry of the diffraction pattern is related to the symmetry of the crystal in the beam direction. The transmission pattern can be electronically recorded on recently introduced (1991) large-area detectors.

Texture studies on deformed (worked) metallic materials

Debye-Scherrer camera

Cylindrical compact of powder or wire sample (approx. 5mm long and 0.5-1mm in diameter) rotated (to avoid texture effects) in monochromatic X-ray beam. Diffraction cones intersect narrow cylindrical film (coaxial with sample) to give line spectrum

Phase identification Quantitative analysis of mixtures of chemical compounds usually with aid of calibrated standards Composition of alloy phases by correlation of lattice parameters with varying constituent elements

Glancing angle camera

Diffraction spectra obtained by irradiating surface or edge sample at glancing angle and recording one half of total diffraction spectra (other half absorbed by sample) on photographic film

Examination of bulk samples. simultaneous detection and analysis of surface film (e.g. oxides) and parent metal substrate

Gunier camera

Flat sample positioned on the circumference of the camera is irradiated by a monochromatic or filtered beam of X-rays diverging from a film around the circumference.

Improved resolution and inherently low background aids idcntifb cation and comparison of specimens with small differences of structure. Diffractions at low B r a g angles (high d values) can be studied

Diffractornetry

Flat sample irradiated by a diverging beam of monochromatic or filtered X-rays. Detector rotated at twice the angular speed of the specimen to maintain the Bragg-Brentano focusing conditions

Phase identification and quantification (usually with calibrated standards) Studies of crystal imperfections, e.g. stacking faults, microstrain, etc. by detailed measurement of spectra profiles With appropriate attachments the following are possible: Residual stress measurement Texture (preferred orientation) determination Thermal expansion parameter measurement Phase. transition monitoring

Determination of unit cell dimensions

Conknation of crystal symmetry Determination of crystal orientation

Y

3

k.

a

s 3. sa

2 P

I

Y

W

414

X-ray analysis of metallic materials

4.3.1.2

Accessory Attachments for Diflractometers

The range of applications of difiactometers is increased by accessory attachments for particular applications. These include: 0

0 0

0

0

Specimen holder with rotation and translation scanning for analysing coarse grained solid and powder samples. Specimen changers for the sequential analysis of up to 40 specimens. Chambers for high and low temperature measurement. Temperature control and data collection can be automated and with a CPSC, rapid data collection system, a 3 D display of 26 and intensity against temperature can be obtained in a few hours. Preferred orientation is measured with a Texture Attachment. Intensity data are automatically collected and results displayed as either a conventional pole figure or as orientation distribution functions (oDF).*' Attachments for quantitatively measuring residual stress. Diffraction patterns can be obtained from thin surfacefilms by irradiating the surface at a shallow angle to increase the effective thickness of the film.

43.2 Specific Applieations

4.3.2.1 Phase identiJcation and quantitative measurements

Phase identification and quantification depend on the accurate measurement of the interplanar (d) spacings and relative intensities of the diffractions in a diffraction pattern. For routine phase identification the observed d spacings and relative intensities are compared with standard X-ray data listed in the X-ray Powder Diffraction File (PDF) published by the Joint Committee on Powder Diffraction Standards (JCPDS).7-The file contains data for over NO00 materials and is regularly updated. It can be obtained on computer files for computer search and match procedures which have virtually replaced the previously used manual procedures. Interactive graphic search programmes are commonly employed. After entering any chemical information, the PDF files are automatically searched and possible matches listed. These are subsequently subtracted from the unknown pattern and the residual displayed for further analysis. With a mixture, the intensities of the file patterns can be varied to produce the best fit. In practice, the success in analysing a mixture often depends on the availability of additional information. For example chemical analysis of individual phases or particles carried out by EDAX in a SEM,or a manual separation of phases for separate XRD analysis. The patterns can then be subtracted from the unknown pattern. Quantitive determinations are carried out by comparing integrated intensities of selected diffractions. In order to allow for absorption, powders are usually analysed by adding a known fraction of standard calibrating powder and comparing the intensities of a diffraction from the component to be analysed with the intensity of a diffraction from the internal standard. Methods are thoroughly discussed in references 3,9,10 and 11. X-ray diffraction analysis is used for the identification of atmospheric pollutants. Examples include silica' and asbestos particles collected on multipore filters. The method requires the taking of an X-ray scan directly from the filter and determining the amount of pollutant by comparison with calibration curves prepared from similar filters containing known amounts of the pollutants. As little as 2 ~ g c m -of~silica can be detected by this method. Most metallurgical samples of interest, however, are solid and cannot be analysed by the above methods. In this case either a calibration curve is constructed from well characterized standards, showing, for precisely defined diffraction conditions, the variation in intensity of a particular diffraction with percentage of the phase to be analysed. Alternatively, theoretical intensities are calculated for diffractionsfrom each phase to be analysed and the ratios of their amounts determined from the observed intensity ratios. The method is illustrated below for the determination of retained austenite in steels but can be extended to other systems. X-ray data for calculating diffraction intensities are listed in Tables 4.8, 4.9, 4.10 and 4.11.

X-ray techniques

4-15

Table 4.8 ANGLES B E m E X CRYSTALLOGRAPHICPLANES IN CRYSTALS OF THE CUBIC SYSTEM Values of a, the angle between ( H a )and (bkk) (HKU (W 100

110

111

210

211

221

310

311

320

321

100

0"

110 111 210 211 221 310 311 320 321

45" 54"44' 26" 34' 35" 16' 48" 11' 18" 26' 25" 14' 33" 41' 36" 43'

110 111 210 211 221 310 31 1 320 321

00

35" 16 18" 26' 30" 19" 28' 26" 34' 310 30' 11" 19' 19' 6

111 210 211 221 310 311 320 321

39" 14' 19" 28' 15" 48' 439 5' 29" 30' 61" 17' 22" 12'

0"

90" 90" 63" 26' 65" 54' 70" 32' 71" 34' 72" 27' 56" 19' 57" 42'

90"

60" 90"

90"

H)" 46'

71" 34' 73" 13' 76" 22' 63" 26' 90" 66" 54' 55" 28

54" 44' 45" 47" 52' 64"46' 53" 58' 40" 54' 70" 32' 75" 2 61"'52 54" 44' 68" 35' 58" 31' 71" 19' 51" 53'

90"

90" 74" 3w

90' 90" 77" 5'

78" 41' 67"48'

79" 6'

90" 78" 54' 79" 58' 72" 1'

90"

210 211 221 310 311 320 321

0"

36" 52' 43" 5' 41" 49' 58' 3' 47" 36 29" 45' 33" 13'

53" 8' 56" 47' 53" 24, 45" 66" 8 41" 55' 53" 18'

66" 25' 79" 29' 63" 26' 64"54' 82' 15' 60" 15' 61" 26'

78" 28'

24" 6' 26" 34' 8" 8 19" 17' 7 ' 7' 17" 1'

211 221 310 31 1 320 321

0" 17" 43' 25" 21' 19' 8' 25" 9' 10" 54' 70' 54'

33" 33' 35" 16' 49O 48' 42" 24' 37' 31' 29" 12' 77' 24'

48" 11' 47" 7' 58" 55' 60" 30' 55" 33' 40" 12' 83" 44'

0" 32' 31' 25" 14' 22" 24' 11' 29' 79" 44'

27" 16 42" 27' 45" 17' 42" 18' 27" 1' 84" 53'

310 311 320 321

0" 17" 33' 15" 15' 21" 37' 65"

311 320 321 320 321

221 310 311 320 321

321

90"

90"

72" 3Y 73" 34'

90"

68" Y 70" 13'

75" 38' 83" 8'

60" 65" 54' 75" 2' 75' 45' 63' 5' 49" 6 90"

70" 32' 74" 12' 82" 35' 90" 83" 3W 56" 56'

80" 24'

38" 57' 58" 12' 59" Hy 49" w 36" 42'

63" 37' 65" 4' 72"'27' 68" 18' 57' 41'

83' 37' 83" 57' 84" 14' 79" 21' 63" 33'

90"

25" 51' 40" 17' 37" 52' 32" 19' 75" 19'

36" 52, 55" 6 52" 8' 40" 29' 85" 9'

53" 8' 67" 35' 74" 45' 41' 28' 90"

72" 33' 79" 1' 84' 58' 530 44'

0" 23" 6' 14" 46

35" 6' 41" 11' 36" 19'

50" 29' 54" 10 49" 52'

62" 58' 65" 17' 61" 5'

840 47' 75" 28' 71" 12'

85" 12' 82" 44'

0"

15" 30' 72" 45'

22" 37' 27" 11' 770 9'

46" 11' 35" 23' 85" 45'

62" 31' 48" 9' 90"

67" 23' 53" 37'

72" 5' 58O 45'

90" 63" 36'

0" 64" 37'

210 43 69" 4

31" 73" 24'

38" 13' 81' 47'

44"25' 85" 54'

50'

60"

82" 53' 90"

82" 12'

84" 42'

74" 3w 84" 16 90" 59" 32'

X-ray analysis of metallic materials

4-16

Table 4 9 SYMMETRY INTERPRETATIONS OF F,XTINCTIONS* Conditionfor Class of iwn-extinction reflection (n=m integer) hkl

h +k+ 1=2n h+k =2n h+l =2n k+l =2n

{iK;

I=;:}2n

Symbol of symmetry elemem

lnterpretation of extinction

Body centred lattice C-centred lattice 8-centred lattice A-centred lattice

Face centred lattice

== b, k, l, all even or ail odd

-h + k f l = 3 n

Rhombohedral lattice indexed on hexagonal rderence system

R

h+k+l=3n

Hexagonal lattice indexed on rhombohedral reference system

H

*From M. 1. Buager, 'X-ray Crystallography',John Wiky & Sons,New York, 1942

'Table4.10 MULTIPLICITY FACTORS FOR POWDER PHOTOGRAPHS h u e or point-group symmetry

hkl

hhl

33m, 43, m3m 23, m3

48 2x24

24 24

Cubic system Okl 24 2x12

Okk

hhh

001

12 12

8 8

6 6

Hexagonal and rhombohedral systems h e or point-pup symmetry

hkil

hhzhl

0k.B

hkiO

hhZh0

OkEO

OOOl

62m. 6mm, 62,6/mmm 6 . 6 6/m 3m, 32,3m 3,T

24 2x12 2x12 4x6

12 12 12 2x6

12 12 2x6 2x6

12 2x6 12 2x6

6 6 6 6

6 6 6 6

2 2 2 2

Tetragonut system Laue or point-group symmetry

hkl

hhl

Okl

hkO

hh0

OM)

001

42m, 4mm, 42,4/mmm 4, 4, Urn

16 2x8

8

8 8

8 2x4

4 4

4 4

2 2

hko

hoo

OM)

001

8

Orthorhombic system

Laue or point-group svmmetrv

hkl

Okl

hO1

Monoclinic system h e or point-group symmetry

hkl

h01

OM)

m, 2,2/m

4

2

2 Triclinic system

h e or point-group symmetry

hW

Where the multiplicity is given, for example, as 2 x 6, this indicates two sets of rei7ections at the same, an&

intensities.

but having diffemt

X-ray techniques

4-17

Table 4.11 ANGULAR FACTORS

0 1

O.ooO0

co

Q)

0.0003

I

O.ooo6 0.001 1

24 3 34 4 5 6 7 8 9

0.0019 0.0027 0.0037 0.0049 0.0061 0.0076 0.0109 0.0149 0.0193 0.0243

57.272 38.162 28.601 22.860 19.029 16.289 14.231 12.628 11.344 9.411 8.025 6.980 6.163

6563 2916 1639.1 1048 727.2 533.6 408.0 321.9 260.3 180.06 131.70 100.31 78.80

10

0.0302

5.506

12 14 16 18

0.0432 0.0581 0.0762 0.0955

20

45 47i

0.5436

1.Ooo 1.011

2.828 2.744

50

0.5868

1.046

2.731

524 55 574

0.6294 0.6710 0.7113

t.105 1.189 1.300

2.785 2.902 3.084

60

0.7500

1.443

3.333

624 65 674

0.7868 0.8214 0.8536

1.622 1.845 2.121

3.658 4.071 4.592

63.41

70

0.8830

2.469

5.255

4.510 3.791 3.244 2.815

43.39 31.34 23.54 18.22

72 74 76 78

0.9045 0.9240 0.9415 0.9568

2.815 3.244 3.791 4.510

5.920 6.749 7.814 9.221

0.1170

2.469

14.44

80

0.9698

5.506

11.182

2-24 25 274

0.1465 0.1786 0.2133

2.121 1.845 1.622

11.086 8.730 7.027

81 82 83

30

0.2500

1.443

5.174

324 35 374

0.2887 0.3290 0.3706

1.300 1.189 1.105

4.841 4.123 3.629

40

0.4131

1.046

3.255

424 45

0.4564 0.5000

1.011

6.163 6.980 8.025 9.411 11.344 12.628 14.231 16.289 19.029 22.860 28.601 38.162 57.272

12.480 14.097 16.17 18.93 22.78 25.34 28.53 32.64 38.11 45.76 57.24 76.35 114.56

1 .Ooo

2.994 2.828

85 8% 86 864 87 874 88 8% 89

0.9755 0.9806 0.9851 0.9891 0.9924 0.9938 0.9951 0.9963 0.9973 0.9981 0.9988 0.9993 0.9997

90

1.Ooo

W

co

1

84

4.3.2.2

0.500

Determination of retained austenite in steel

An important example of quantitative phase analysis by X-ray diffraction is the determination of retained austenite in steels. The method is based on the comparison of the integrated diffracted Xray intensities of selected (hkl) reflections of the martensite and austenite phases. The necessary formulae and reference data are given below; for more details of the experimental methods the definitive paper by Durnin and RidalX2should be consulted. The integrated intensity of a diffraction line is given by the equation:

I(uo=n2 Ym (LP)e-2m(Ff12

(4.1)

in which I,,,,=integrated intensity for a special (hkl) reflection; n=number of cells in cm3; V=volume exposed to the X-ray beam; (LP)= Lorentz-Polarization factor; m= multiplicity of (hkl); e-2m=Debye-.Waller temperature factor; F=structure factor; and f= atomic factor. For nZVwe may substitute V/v2,in which u is the volume of the unit cell. If the ratio between the integrated intensities of martensite and austenite i s denoted by P

4-18

X-ray analysis of metallic materials

Each factor is determined from the International Tabless and depends on the reflection used. A factor G is then determined for each combination of o! and p peaks used, hence:

If

o!

and y are the only phases present: 1

Vy=-

1+GP

(4.4)

Hence, measurement of the ratio (P)of two diffraction peaks and calculation of the factor G will give the volume fraction of austenite V, The factors involved in the calculation of G for two steels--l6.8%Ni-Fe(0.35%C) and N C MV (a Ni-Cf-Mo-V steel with composition wt % O.43C; 0.31Si; 0.57Mn; 0.009s; 0.005P; 1.69Ni; 1.36Cq 1.08Mo; 0.24V; O.llCu),Mo, Co and Cr radiation and a selection of hkl peaks have been extracted from the ‘International Tables for X-Ray Crystallography’s by Durnin and Ridallz and are presented in Table 4.12. These factors may be used to calculate G for different radiations and peaks. The results are presented in Table 4.13. When the alloy compositions are being investigated the factors which make up G must be determined from the International Tables.s Accuracy obtainable using a diffractometer is in the region of 0.5% for the range 1.5-38 volume percentage of austenite. X-ray diffraction determination accuracy thus compares favourably with other techniques such as metallography, dilatometry and saturation magnetization intensity methods which are all inaccurate below 10% austenite content. The main source of error in X-ray determination of retained austenite comes from overlapping carbide peaks. The carbides and their diffraction peaks most likely to cause problems are summarized in Table 4.14.

4.3.2.3 X-ray Residual Stress Measurements

Residual stresses can be divided into two general categories, macrostresses where the strain is uniform over relatively large distances and microstresses produced by non-uniform strain over short distances, typically a few hundred A. Both types of stress can be measured by X-ray diffraction techniques. The basis of stress measurement by X-ray diffraction is the accurate measurement of changes in interplaner d spacing caused by the residual stress. When macrostresses are present the lattice plane spacing in the crystals (grains) change from their stress-free values to new values corresponding with the residual stress and the elastic constants of the material. This produces a shift in the position of the corresponding diffraction, Le. a change in Bragg angle 13.Microstresses however give rise to non-uniform variations in interplanar spacing which broaden the diffractions rather than cause a shift in their position. Small crystal size also give rise to broadening. Measurement of kfacro-residical The working equation used in most X-ray stress analysis is

where o# is the surface stress lying in a direction common to the surface and the plane defined by the surface normal and the incident X-ray beam. E and v are Young’s modulus and Poisson’s ratio respectively, d, and d, are the interplanar spacings of planes with normals parallel to the surface normal and at an angle $ to the surface normal. These angles are related to the direction of the incident X-ray beam, as shown in Fig. 4.1. Thus u can be determined from two exposures, one with the incident beam inclined at 0 to the surface to measure d , and the other at an angle $ to the first to measure d$. This technique is known as the two-exposure technique. Alternatively equation (1) can be rewritten as

Table 4.12 INTENSITY FACTORS FOR DIFFERENT RADIATIONS AND PEAKS”

__

___ Muterial

Radiation

Factor

16.87;Ni-Pe NCMV 16.8:GNi -Fe 16.8%Ni-Fe Both compositions Both

Mo Mo

Brags angle, 8

16.8:~Ni-Fo NCMV 16.8XNi-Fe 16.8:;Ni-Fe 16.8”/;Ni-Fe NCMV 16.8”/Ni-Fe 16.8:LNi-Fe Both Both

CO Cr All Mo

co

Multiplicity, m Lorentz and polarimtion

Cr

(LP)

Mo Mo co

Debye- Wallcr temp. e- zm

Cr

Mo Mo co Cr AI1 All

Atomic scattering, fo

Peak a200 14.41 14.40 38.67 53.15 6 29.46 3.44 2.81 0.910 0.910 0.908 0.912 15.1 14.7

V200

y220

y311

17.73 17.70 49.89 78.05 24 18.84 273 9.26 0.869 0.869 0.869 0.869 13.4

11.49 11.49 29.99 39.74 6 41.56 5.79 3.29 0.943 0.943 0.941 0.943 17.0 16.6 12.69 15.09 4 4.68 x

16.32 16.32 44.92 64.65 12 22.55 283 4.01 0.889 0.889 0.889 0.889 14.0 13.7 9.84 12.24 4

19.2 I 19.21 55.85

13.1

9.14 11.54 13.19 2 2 1.79 x IO-) k x units 10.78

Structure lactor, F 1/VZ (Vis volume of unit cell)

a211

kx units

-

24 15.78 2.96

_-

0.847 0.848 0.852

--

12.8 12.5 8.60

4

Table 4.13 AUSTENITE DETERMINATION FACrOR G FOR DIFFERENT RADIATIONS AND PEAK

P 8

Material

Radiation

Peak combination a2003~2@4l

a200-7220

a2OCky311

a211-y200

a211-y220

a211-y311

16.8XNi-Fe NCMV 16.8XNi-Fe 16.8%Ni-Fe

Mo Mo Co Cr

2.22 2.23 2.52 1.66

1.36 1.38 1.40 2.50

1.50 1.51 2.15

1.16 1.15 1.09 0.17

0.71 0.72 0.61 0.26

0.78 0.78 0.93

-

-

eQ 3

%

%

E-

i%

F?

3

f?

2

E'

i ;

Table 4.14 INTERFERENCE OF ALLOY CARBIDE LINES WITH AUSTENITE AND MARTENSITE LINES'Z

-

-

Austenite and martensite 'd' spacings

Fe,C

M6C

V4C3

Mo,C or W,C

(200h, l.8OA (200)~1.43A (220)~1.27A (211b 1.17A (31 lb 1.08A

Clear Clear Weak overlap Strong overiap Weak overlap

Clear Strong overlap Strong overlap Clear Medium overlap

Clear Clear

Clear Clear Clear Weak overlap Strong overlap Weak overlap Weak overlap Weak overlap Weak overlap Clear

Weak overlap Clear Clear

WC

Cr,,C,

CrbCs

Strong overlap Weak overlap Medium overlap Medium overlap Strong overlap

Strong overlap Weak overlap Clear Medium overlap Clear

X-ray techniques

4-21

Fme 4.1

This shows that dq is a linear function of sin2$. The intercept on the d axis gives dl and the slope d,((l + v l / E ) c r ~A. positive slope correspondsto a tensile stress and a negative slope to compression. This technique takes advantage of measurements involving a number of d, values. The determination of interplanar spacings depends on the accurate measurement of the corresponding Bragg angle Q where

Back reflection diffractions are used as the highest sensitivity to changes in interplanar spacing are obtained as 0 tends to 90".In practice the specimen is rotated through $ between exposures (or the tube and detector together through the same angle on portable systems for measuring large samples). Due to the limited penetration of commonlyused X-ray wavelengths, typically 4 pM for chromium radiation to 11pm for molybdenum in steel, only surface stresses are measured. Stresses at lower depths in the sample are determined by repeating measurements after removing (electropolishing) layers of known thickness. The measured values are subsequently corrected for changes in stress resulting from the removal of upper layers. Residual stress in small components can be measured on a converted difiactometer by adding a specimen support table with three orthogonal adjustments to permit the surface of the component to be brought into the beam. Fully automated portable systems are avaikdble for determining residual stress in large components. Typical accuracy for steel is _+1.5-3.0x lO'NM (+l-Ztonin-'). MEASUREMENT OF MICROSTRESSES'8.19 A worked surface gives rise to broadened diffractions due to a combination of microstresses and small crystallite size. An approximate method to separate the two effects is to assume that the breadth is the sum of the separate broadening from each effect.

422

X-ray analysis of metallic materials

The relationshipsbetween diffractionbreadth P and averagecrystallitesizeE and mean stress 5 are: 1 Small crystallite alone

Ps,c.N

where k is a constant u 1and

2 Microstresses alone

fiM.s,N

klZ ~

€hk,

cos 8

is the linear dimensionperpendicular to the measured hkl plane. 48 tan 6 Ehkl

where E,

is the elastic constant perpendicular to hkl.

When both effects are present, then

P=

8S.C.

+Pt4.S.

I. - ___ +45tan6 EhkI cos @

&&I

which can be rewritten in the form: DcosO

-=-

A

1

+ 48sinO . . Ehkl 'E,,,

If only these defects are present, then a plot of PcosO/I against s i n 6 should be a straight line, with intercept on the P cos @/Iaxis giving l / and ~ the~slope ~ 45/E.Eh,,. ~ For non-cubic materials, for example tetragonal and hexagonal, separate plots should be made for the hkO and 001 results. In the above formula, diffraction breadth is measured as either the breadth in radians at half the peak height (HPHW) or as the integral breadth which is the integrated intensity of the diffraction divided by the peak height. It corresponds to the width of a rectangle having the same area and height as the diffraction. The latter is particukrly useful in analysing peaks with partially resolved a1at doublets. The measured breadths include the instrumental breadth which is independent of any crystal defects. This can be measured for subsequent subtraction from the measured breadths by running a scan from a defect-free specimen. 4.3.2.4 Preferred orientation Preferred orientation can be represented in two ways, either as a convential pole figure or as an inverse pole figure. A convential pole figure shows the distribution of a low-index pole-normal to a crystallographic plane, over the whole specimen. With a cubic metal, these are generally constructed for { loo), { 110) and { 11 1) planes while for hexagonal metals usually the basal (OOO1) plane is selected. A high density of poles shows the preferred direction of the pole with respect to the sample. An inverse pole figure on the other hand shows how the grains are distributed with respect to a particular direction in the sample.20Inverse pole figures are usually constructed for the principal directions of the sample, for example the extrusion, radial, and tangential directions in extruded material. The method is rapid, and data for a single direction can be determined from a conventional diffractometer scan taken from a surface which is perpendicular to the required direction. The method is based on the fact that all diffractions recorded on a convential scan come from planes which are parallel to the surface and their intensities are related to the number of grains (volume of material) which has this orientation. The diffraction intensities are compared to those from a sample having random orientation. These can be either theoretical calculated values or values measured directly from a correspondingscan taken from a sample with random orientation. These relative intensities are called texture codficients (TC) and arc expressed mathematically as

where I =measured integrated intensity of a given hkl diffraction IO=corresponding intensity for the same hkl diffraction from a random sample n =total number of diffractions measured.

X-ray techniques

4-23

The TChklvalues are proportional to the number of grains (volume of sample) which are oriented with an hkl plane parallel to the sample surface. The values can be plotted on a partial sterographic projection and contour lines drawn through the plotted points to produce an ‘Inverse Pole Figure’ for that particular specimen direction. High values show the preferred grain orientation in the specimen direction. 4.3.2.5 Specimen preparation

Methods for preparing standard diffractometerspecimens are discussed in references 14. The most common method is to pack loose powder into a flat cavity in an aluminium specimen holder, taking care not to introduce preferred orientation. Another method is to mix the powder into a slurry and smear some over a glass cover slip. Coarse powders which tend to slide out of the cavity during a scan can be mixed with petroleum jelly. The possibility of diffractions from the jelly or binder should always be considered when analysing the diffraction pattern. A problem when analysing a small amount of material, is diffractions and scatter from the specimen holder. These effects are reduced by using a single crystal holder of a low element material which has been polished so the surface is just off a B r a g plane. Most laboratories have developed procedures and specimen holders for non-standard applications. These have been surveyed by D. K. Smith and C. S. Barrett and the results published in ‘Advances in X-ray Analysis’.24 One application is the analysis of air-moisture reactive powders. A simple solution is to fill and seal the powder in thin walled glass quills inside a dry box. After removal from the glove box the quills are mounted in raft fashion across a recessed specimen holder. Sealed cells are also used to avoid handling delicate quills inside a glove box. One such method for lithium compounds was to load the powder inside a glove box into a recessed specimen holder and cover the powder with a flanged 0.001 in. thick aluminium foil dome. Petroleum jelly was lightly smeared round the flange to hold the dome on to the specimen holder and make a moisture seal. Metal samples submitted for XRD analysis are generally metallurgically mounted and polished samples. Due to the limited penetration of the X-ray beam into the sample it is always advisable to first electropolish the surface. Useful electropolishes are listed in Chapter 10, Table 10.4. An electropolish frequently used in preparing specimens for retained austenite determinations is 7 vol% perchloric acid 69 vol% ethanol

10 vol% glycerol 14 vol% water At a voltage of 23 V. Electrolyte maintained at temperature below 12°C.

EXTRACMON TECHNIQUES

Precipitates that are present at very low concentrations can be concentrated by dissolving away the matrix and collecting the residue. Typical solutions used for extraction are as follows.f5 (i) Carbides and certain intermetallic compounds (a) Immersion overnight in 5 or 10% bromine in methanol, or (b) Electrolyticallyin 10% hydrochloric acid in methanol at a current density 0€0.07Acm-~. .Extraction for 4h provides sufficient powder residue. The intermetallic phases which can be extracted using these solutions are sigma phase, certain of the Laves phases, Fe,Moz etc. (ii) Gamma prime, eta phase, M(CN) (a) Electrolyticallyin 10% phosphoric acid in water at a current density of lOAdm-’. Time of extraction 4 h. It is sometimes necessary to add a small amount of tartaric acid in order to prevent the formation of tantalum and tungsten hydroxides, or (b) Electrolyticallyin 1% citric acid plus 1% ammonium sulphate in water. Current density 2AdmsZ, duration 4 h. For quantitative work this solution is preferred to the phosphoric acid electrolyte. Certain of the Laves phases may also be extracted using either of these solutions. (iii) Precipitates and intermetallic compounds in chromium Immersion overnight in 10% hydrochloride acid. This has been used to extract carbides and borides. Precipitates can also be concentrated by heavily etching a surface to leave them proud of the surface as used to produce replicas in the early days of electron microscopy.26

Table 4.15 CRYSTAL GEOMETRY system

dclr=Iderplanar spacing

V=VoL of unit cell

Cubic

E --

1 d’

V=a3

Tetragonal

hZ+kZ+12 a2

I’ a2 c2

1 hz k’ -=-+-+d’

a’

V=abc

Orthorhombic

1

+

(h2 kZ +I2) sinza+Z(hk+ kl +hl)(cos’ a-cosa) a’(1 -3 COS’ ~ + ~ C Oa) S ~

Rhombohedral*

7=

Hexagonalt

1 4 ____ h2+hk+k2 1’ -=d2 3( a2 )+F

Monoclinic Triclinic

V=a2c

V=a3,/(l-3

cosz a + 2

COS,

a)

~

~~

&-angle between planes h,k,l, and hzkzlz

system

Cubic

Tetragonal

Orthorhombic

Rhombohedral*

Hexagonal+

Monoclinic

Triclinic

__

” Rhombohedral axes.

t Hexagonal axes, co-ordinates lrkil where i = -(k+R).

where s,,=bzez sin’ I s,,=ubc2 (cos a cos p-cos y ) s2z=azc2sinz /3 sz3=a2br (cos /3 cos y-cos a) s3,=a2b’ sinz y s,,=ah2c (cos y cos a-cos 8)

Y

3

k

? !

4-26

X-ray analysis of metallic materials

4.3.2.6 Formulae and crystallographic data

Formulae for calculating interplanar dbklspacings from lattice parameters and data for calculating intensities together with other useful information on crystal symmetry are given in Tables 4.8,4.9, 4.10, 4.11 and 4.15. INTENSITIES

The relative intensities of diffractions recorded on a diffractometer scan are given by the formula

where 1+cos' 28 )IF,' .T.p.A=Combined polarization Lorentz factor Fable 4.11) sin' e COS e F=structure factor involving the summation of scattering from all atoms in the unit cell

(.

T= temperature factor, ep =multiplicity factor, Tabie 4.10 A=an absorption factor.

For a diffractometer specimen of effectively infinite thickness, A=K/g where K is a constant and p the linear absorption coefficient of the sample. A is therefore independent of 8. A criterion for this condition is that the thickness of the specimens is >3.2/j~.

Table 4.16 MEAN ATOMIC SCAlTERING FACTORS Sin 0

0.2

-.&-I

0.0

0.1

H

1.000 2.000 2.000 3.ooo 2.000 4.000 4.00 3.000 2.000 5.000

0.811 0.481 0.251 0.130 0.071 1.064 0.519 0.255 0.130 0.070 1.832 1.452 1.058 0.742 0.515 2.215 1.741 1.512 1.269 1.032 1.935 1.760 1.521 1.265 1.025 2.176 1.743 1.514 1.269 1.033 3.067 2.067 1.705 1.531 1.367 2.583 2.017 1.721 1.535 1.362 1.966 1.869 1.724 1.550 1.363 4.066 2.711 1.993 1.692 1.534

4.000 3.000 2.000 6.000 4.000

3.471 2.757 1.979 5.126 3.686

1.

H-1 He

Li Li+'

Li-' Be Be+' Be'* B

B'1 B+2

B+3

c

C+2

c+3 c+4

N N+3 N+4 N-1 0 0" 0 + 2

0 + 3

0 - 1

F F-1 Ne Na

3.000 2.000 7.000 4.000 3.000 8.ooO 8.000 7.000 6.000 5.000 9.000 9.000 10.00 10.00 11.0

0.3

0.4

0.5

0.6

0.7

0.8

0.9

1.0

1.1

0.040 0.040 0.358 0.823 0.818

0.024 0.024 0.251 0.650 0.647

0.015 0.015 0.179 0.513 0.510

0.010 0.010 0.129 0.404 0.403

0.007 0.007 0.320 0.319

0.005 0.005 0.071 0.255 0.254

0.826 1.201 1.188 1.180 1.406

0.654 1.031 1.022 1.009 1.276

0.516 0.878 0.870 0.855 1.147

0.408 0.738 0.735 0.721 1.016

0.323 0.620 0.618 0.606 0.895

0.257 0.205 0.519 0.432 0.520 0.436 0.508 0.427 0.783 0.682

0.095

1.2

0.0035 0.0035 0.054 0.205 0.203

2.551 2.290 1.919 3.581 2.992

1.962 1.928 1.824 2.502 2.338

1.688 1.707 1.703 1.950 1.910

1.536 1.552 1.566 1.685 1.672

1.410 1.414 1.420 1.536 1.533

1.283 1.278 1.274 1.426 1.429

1.154 1.144 1.132 1.322 1.332

1.028 1.016 0.999 1.218 1.233

0.908 0.896 0.877 1.114 1.131

0.798 0.698 0.786 0.687 0.767 0.669 1.012 1.030

2.842 2.487 1.986 1.945 6.203 4.600 3.712 3.227 2.890 2.619

2.133 1.880 3.241 2.635 2.306

1.874 1.794 2.397 2.172 2.038

1.697 1.692 1.944 1.869 1.837

1.564 1.579 1.698 1.682 1.690

1.447 1.459 1.550 1.558 1.573

1.335 1.338 1.444 1.461 1.472

1.225 1.219 1.350 1.373 1.375

1.116 1.104 1.263 1.287 1.281

1.012 0.994 1.175 1.199 1.188

6.688 7.250 6.493 5.641 4.760 7.836 8.293 9.108 9.363 9.76

3.186 4.094 4.017 3.771 3.410 4.068

2.364 3.010 3.016 2.924 2.745 2.968 3.760 3.786 4.617 5.47

1.929 2.338 2.356 2.327 2.246

1.694 1.944 1.956 1.948 1.913

1.551 1.714 1.717 1.716 1.701

1.170 1.296 1.220 1.296 1.301 1.308

1.934 2.312 2.323 2.794 3.40

1.710 1.958 1.972 2.300 2.76

1.352 1.462 1.461 1.463 1.463 1.46 1.587 1.596 1.760 2.00

1.263 1.374 1.374 1.378 1.382

2.313 2.878 2.885 3.536 4.29

1.446 1.566 1.567 1.568 1.562 1.566 1.735 1.747 1.976 2.31

1.373 1.481 1.486 1.612 1.78

1.294 1.4% 1.399 1.322 1.504 1.419 1.63 1.52

4.631 5.634 5.298 4.776 4.151 5.756 6.691 7.126 7.824 8.34

5.044

5.188 6.987 6.89

*Condensed from 'International Tables for X-rayCrystallography', Kynoch Pms, E%i&&?.ni, England, 1962.

0.913 0.893 1.083 1.112 1.097

X-ray techniques

4-27

Table 416 MEAN ATOMIC SCAlTEIUNG FACTORS*-continued

si0 .---A-l 1

0.0

0.1

0.2

0.3

0.4

0.5

0.6

0.7

0.a

1.0

0.9

1.1

1.2

__

Na+ Mg Mg+z AI AI+'

10.00 12.00 10.00 13.00 12.00

9.551 10.50 9.66 11.23 10.94

8.390 8.75 8.75 9.16 9.22

6.925 7.46 7.51 7.88 7.90

5.510 6.20 6.20 6.77 6.77

4.328 5.01 4.99 5.69 5.70

3.424 4.06 4.03 4.71 4.71

2.771 3.30 3.28 3.88 3.88

2.314 2.72 2.71 3.21 3.22

2.001 2.30 2.30 2.71 2.70

1.785 2.01 2.01 2.32 2.32

1.634 1.81 1.81 2.05 2.04

1.524 1.65 1.65 1.83

A1+2

11.00 10.00 14.00 11.00 10.00

10.40 9.74 12.16 10.53 9.79

9.17 9.01 9.67 9.48 9.20

7.65 7.98 8.22 8.34 8.33

6.79 6.82 7.20 7.27 7.31

5.70 5.69 6.24 6.25 6.26

4.71 4.69 5.31 5.30 5.28

3.88 3.86 4.47 4.44 4.42

3.22 3.20 3.75 3.73 3.71

2.71 2.70 3.16 3.14 3.13

2.33 2.32 2.69 2.67 2.68

2.05 2.04 2.35 2.34 2.33

1.84 1.84 2.07

~ 1 + 3

Si Siw3 Si-*

P

S S-1 .-2

s

CI

15.00 13.17 10.34 16.00 14.33 11.21 17.00 15.00 11.36 18.00 (15.16) (10.74) 17.00 15.33 12.00

8.59 8.99 8.95 (8.66) 9.44

7.54 7.83 7.79 (7.89) 8.07

6.67 7.05 7.05 (7.22) 7.29

5.83 6.31 6.32 (6A7) 6.64

5.02 5.56 5.57 (5.69) 5.96

4.28 4.82 4.83 (4.93) 5.27

3.64 4.15 4.16 (4.23) 4.60

3.11 3.56 3.57 (3.62) 4.00

16.02 16.30 16.73 16.68 17.33

9.40 10.20 10.97 10.96 11.71

8.03 8.54 9.05 9.04 9.64

7.28 7.56 7.87 7.86 8.26

6.64 6.86 7.11 7.11 7.38

5.97 6.23

5.27 5.61

4.61 5.01

4.00 4.43

3.47 3.90

3.03 3.43

:5:

;:;%} 6.21

5.39 5.70

4.84 5.19

4.32

3.83

4.69

4.53 5.53 4.54 4.56 4.43

4.70

c1-1

18.00

A

18.00

K

i9.00 18.00 20.00

K+' Ca

Ca" Ca+a

sc SC+' SC'Z

sc+3

Ti Ti" Tic2 Tic3

V V+' V+Z v+3

Cr Cr+' Cr+Z CrC3 Mn Mn+'

MU+2 MnA3 &in+* Fe Fe+' Fe" Fe+3

Fe+4

co

CO+' co+z CO+)

Ni Ni+' Ni+' Ni+3

cu

CU+' CU'Z

cu+3

2.06

2.69 2.35 3.07 2.66 3.08 2.67 (3.13) (2.71) 3.47 3.02

12.22 12.93 13.73 13.76 14.32

6.75

4.21

19.00 18.00 21.00 20.00 19.00 18.W 22.00 21.00 20.00 19.00

17.21 16.93 18.72 18.50 17.88 17.11 19.96 19.61 18.99 18.24

14.35 14.40 15.38 15.43 15.27 14.92 16.41 16.55 16.52 16.27

11.70 11.70 12.39 12.43 12.44 12.38 13.68 13.64 13.75 13.82

9.63 9.61 10.12 10.13 10.18 10.22 11.53 11.53 11.50 11.58

8.26 8.25 8.60 8.61 8.64 8.68 9.88 9.98 9.86 9.84

7.38 7.38 7.64 7.64 7.65 7.76 8.57 8.56 8.58 8.55

6.75 6.75 6.98 6.98 6.98 6.98 7.52 7.52 7.52 7.53

6.21 6.22 6.45 6.45 6.45 6.44 6.65

5.70 5.70 5.96 5.96 5.96 5.96 5.95

5.19 5.18 5.48 5.48 5.48 5.49 5.36

4.68 4.68 5.00 5.00 5.01 5.02 4.86

23.00 22.00 21.00 20.00 24.00

20.90 20.56 19.94 19.19 21.84

17.23 17.37 17.35 17.11 18.05

14.39 14.36 14.46 14.54 15.11

12.15 12.15 12.12 12.19 12.78

10.43 10.44 10.41 10.38 10.98

9.05 9.05 9.07 9.04 9.55

7.95 7.95 7.96 7.97 8.39

7.05

6.31

5.69

5.15

7.44

6.67

6.01

5.45

4.97

23.00 22.00 21.00 25.00 24.00

21.50 20.89 20.15 22.77 22.44

18.20 18.18 17.96 18.88 19.02

15.07 15.18 15.26 15.84 15.79

12.78 12.75 12.82 13.41 13.42

10.99 10.97 10.94 11.54 11.55

9.54 9.56 9.53 10.04 10.04

8.40 8.40 8.41 8.84 8.84

7.85

7.03

6.34

5.75

5.25

23.00 2?.00 21.00 26.00 25.00

21.84 21.10 20.30 23.71 23.39

19.01 18.80 18.42 19.71 19.85

15.90 15.99 15.97 16.56 16.52

13.38 13.45 13.54 14.05 14.05

11.53 11.50 11.53 12.11 12.12

10.06 10.03 10.00 10.54 10.54

8.84 8.85 8.82 9.29 9.29

8.25

7.39

6.67

6.06

5.53

24.00 23.00 22.00 27.00 26.00

22.79 22.06 21.26 24.65 24.33

19.85 19.65 19.28 20.54 20.68

16.62 16.71 16.71 17.29 17.25

14.02 14.08 14.18 14.69 14.10

12.09 12.06 12.09 12.67 12.68

10.56 10.54 10.50 11.05 11.04

9.29 9.30 9.28 9.74 9.74

8.66

7.77

7.01

6.37

5.82

25.00 24.00 28.00 27.00 26.M1

23.74 23.01 25.60 25.28 24.69

20.69 20.50 21.37 21.52 21.53

17.35 17.44 18.03 17.98 18.08

14.66 14.72 15.34 15.34 15.30

12.66 12.63 13.25 13.25 13.24

11.07 11.04 11.56 11.55 11.58

9.74 9.76 10.20

9.08

8.14

7.35

6.68

6.11

25.00 29.00 28.00 27.00 26.00

23.97 26.54 26.22 25.64 24.93

21.35 22.21 22.35 22.37 22.20

18.18 18.76 18.71 18.81 18.91

15.36 15.98 15.99 15.95 16.00

13.20 13.82 13.83 13.81 13.77

11.56 12.07 12.07 12.09 12.07

10.21 10.66 10.66 10.65 10.68

9.46

8.52

7.70

7.00

6.40

10.20 10.19

*Condensed from 'InternationalTabks for X-ray Crystallography', Kynoch Press,Birmingham. England, 1962.

4-28

X-ray analysis of metallic materials

Table 4.16 Sin 0 i.

MEAN ATOMIC SCATTEFSNG FACTORS*+ontinued

---.&-'.

0.0

0.1

0.2

Zn Zn+*

30.00 28.00 31.00 30.00 28.00 32.00 30.00 28.00 33.00 32.00

27.48 26.59 28.43 28.12 26.84

23.05 23.32 23.89 24.03 23.90

Ga Ga+' Ga+=

Ge Ge+2

Ge+" As As+' AS+=

As+3

Se Br Kr

Rb Rb+' Sr

Y

zs zr+4 Nb Mo Mo+' Tc

Ru Rh Pd Ag Ag+'

cd In Sn Sb Te

I Xe

cs Ba

La Ce

Pr Nd

Pm Sm Eu Gd

Tb DY

Ho Er

Tm Yb Lu

Hf Ta W Re

os

Ir

29.37 28.50 27.02 30.32 30.02

29.45 28.75 31.26 32.21 33.16 37.00 34.11 36.00 33.82 38.00 35.06 39.00 36.01 40.00 36.96 36.00 34.72 41.00 37.91 42.00 38.86 41.00 38.59 43.00 39.81 44.00 40.76 45.00 41.72 46.00 42.67 47.00 43.63 46.00 43.37 48.00 44.58 49.00 45.53 50.00 46.49 51.00 47.45 52.00 48.40 31.00 30.00 34.00 35.00 36.00

53.00 54.00 55.00 56.00 57.00 58.00 59.00 60.00 61.00 62.00 63.00 64.00 65.00 66.00 67.00 68.00 69.00 70.00 71.00 72.00 73.00 74.00 75.00 76.00 77.00

0.3

0.4

0.5

0.6

14.40 14.40 14.98 14.99 14.93

12.59 12.61 13.11 13.10 13.11 13.63 13.65 13.60 14.16 14.16 14.18 14.17 14.69 15.22 15.76

0.7

31.39 27.25 32.40 27.81 33.25 28.57 33.39 28.51 34.12 29.34 34.98 30.12 35.84 30.89 36.70 31.67 37.57 32.44 37.71 32.38 38.44 33.22 39.31 34.00 40.17 34.78 41.05 35.57 41.92 36.35

16.64 16.60 17.29 17.30 17.30 17.95 17.92 18.05 18.61 18.63 18.58 18.61 19.28 19.95 20.62 21.29 21.31 21.96 22.64 23.32 23.39 24.01 24.69 24.72 25.38 26.07 26.76 27.46 28.16 28.18 28.85 29.56 30.26 30.96 31.67

11.12 11.12 11.59 11.60 11.61 15.57 12.06 15.57 12.06 15.53 12.07 16.16 12.54 16.16 12.54 16.16 12.53 16.11 12.53 16.75 13.02 17.35 13.50 17.95 13.98 18.55 16.30 14.47 18.55 16.30 14.48 19.15 16.84 14.96 19.76 17.39 15.46 20.37 17.94 15.95 20.31 17.92 15.97 20.98 18.49 16.45 21.60 19.04 16.95 21.59 19.04 16.96 22.21 19.60 17.46 22.83 20.16 17.96 23.46 20.72 18.47 24.08 21.28 18.98 24.71 21.85 19.50 24.70 21.85 19.50 25.34 22.42 20.02 25.97 22.99 20.53 26.60 23.56 21.05 22.74 24.14 21.58 27.87 24.71 22.10

37.14 37.93 38.72 39.51 40.30 41.09 41.89 42.69 43.48 44.28 45.08 45.88 46.68 47.49 48.29 49.10 49.90 50.71 51.52 52.33 53.14 53.95 54.76 55.58 56.39

32.38 33.09 33.80 34.51 35.23 35.94 36.66 37.38 38.10 38.82 39.55 40.27 41.00 41.73 42.46 43.19 43.92 44.66 45.39 46.13 46.86 47.60 48.34 49.08 49.83

28.51 29.16 29.80 30.44 31.09 31.74 32.39 33.04 33.69 34.35 35.01 35.66 36.33 36.99 37.65 38.31 38.98 39.65 40.32 40.99 41.66 42.33 43.01 43.68 44.36

19.50 19.55 20.35 20.19 20.39 24.73 20.99 24.91 21.03 24.45 21.18 25.58 21.74 25.72 21.68 25.76 21.77 25.62 21.88 26.42 22.49 27.27 23.24 28.12 24.00 28.97 24.75 29.11 24.70 29.83 25.51 30.68 26.28 31.54 27.04

49.36 50.32 51.27 52.23 53.19 54.15 55.11 56.07 57.02 57.98

42.79 43.66 44.54 45.41 46.29 47.16 48.04 48.92 49.80 50.68

58.94 59.91 60.87 61.83 62.79 63.75 64.71 65.67 66.64 67.60 68.56 ..... 69.52 70.49 71.45 72.42

51.56 52.45 53.33 54.21 55.10 55.98 56.87 57.75 58.64 59.53 60.42 ... .61.31 62.20 63.09 63.98

22.63 23.16 23.69 24.22 24.76 25.30 25.84 26.38 26.92 27.46 31.19 28.01 31.79 28.56 32.39 29.11 32.99 29.66 33.59 30.21 34.20 30.76 34.81 31.32 35.42 31.88 36.03 32.44 36.64 33.00 37.25 33.56 37.87 34.12 38.48 34.69 39.10 35.26 39.72 35.82

25.29 25.87 26.46 27.04 27.63 28.22 28.81 29.40 29.99 30.59

0.8

0.9

1.0

i.1

12

9.91

8.90

8.05

7.32

6.70

10.33

9.29

8.40

7.64

6.99

10.76

9.68

8.76

7.97

7.29

11.19

10.07

9.11

8.30

7.60

11.62 12.06 12.50 12.94

10.46 10.86 11.26 11.66

9.47 9.84 10.21 10.58

8.63 8.97 9.31 9.65

7.91 8.21 8.53

13.39 13.84 14.29

12.07 12.48 12.89

10.95 11.32 11.70

9.99 10.34 10.68

9.16 9.48 9.80

14.74 15.20

13.31 13.73

12.08 12.46

11.04 11.39

10.13 10.45

15.65 16.12 16.58 17.05 17.52

14.15 14.57 14.99 15.42 15.85

12.85

11.74

13.24 13.63 14.02 14.42

12.10 12.46 12.82 13.19

10.78 11.11

17.99 18.46 18.93 19.41 19.89

16.28 16.71 17.15 17.59 18.03

14.81 15.21 15.61 16.02 16.42

13.56 13.93 14.30 14.67 15.05

12.46 12.80 13.15 13.49 13.84

20.37 20.86 21.34 21.83 22.32 22.81 23.31 23.80 24.30 24.80 25.30 25.80 26.31 26.81 27.32 27.83 28.34 28.85 29.37 29.88 30.40 30.92 31.44 31.96 32.48

18.47 18.92 19.36 19.81 20.26 20.71 21.17 21.62 22.08 22.54 23.00 23.46 23.93 24.39 24.86 25.33 25.80 26.28 26.75 27.23 27.70 28.18 28.66 29.14 29.63

16.83 17.24 17.65 18.07 18.48 18.90 19.32 19.74 20.16 20.58

15.42 15.80 16.18 16.57 16.95

14.19 14.54 14.90 15.25 15.61 15.97 16.33 16.69 17.05 17.42 17.79 18.16 18.53 18.90 19.27 19.65 20.03 20.40 20.78 21.17 21.55 21.93 22.32 22.70 23.09

17.34 17.72 18.11 18.51 18.90 21.01 19.29 21.44 19.69 21.87 20.09 22.30 20.49 22.73 20.89 23.17 21.29 23.60 21.70 24.04 22.11 24.48 22.51 24.92 22.92 25.36 23.33 25.80 23.74 26.25 24.16 26.70 24.57 27.14 24.99

*Condensed from ?ntcrnatid Tables for X-ray Crystallography', Kynoch Press, Binningham, England, 1962.

8.84

11.45 11.78 12.12

X-ray techniques

4-29

Table 416 MEAN ATOMIC SCATTERING FACTORS*--eontinued ~~

Sin 0 --A-1 A pt

Au Au+' +2 ;;

T1

TI+' n+3

Pb Pb+3 Bi

Po At

Rn Fe Ra Ac

Tb Pa U

0.0

0.1

0.2

0.3

0.4

0.5

0.6

78.00 79.00 78.00 80.00 78.00 81.00 80.00 78.00 82.00 79.00

73.38 74.35 74.14 75.31 74.65 76.27 76.07 75.03 77.24 76.00

57.21 58.02 57.96 58.84 58.79 59.66 59.59 59.71

83.00 84.00 85.00 86.00 87.00

78.20 79.17 80.13 81.10 82.07

88.00 89.00 90.00 91.00 92.00

83.03 84.00 84.97 85.93 86.90

64.87 65.77 65.88 66.66 66.90 67.55 67.61 67.82 68.45 68.71 69.34 70.24 71.13 72.03 72.93 73.82 74.72 75.62 76.52 77.42

50.57 51.31 51.35 52.06 52.05 52.81 52.84 52.76 53.56 53.50 54.30 55.05 55.80 56.56 57.31 58.06 58.82 59.57 60.33 61.09

45.04 45.72 45.70 46.40 46.41 47.08 47.06 47.08 47.77 47.76 48.45 49.14 49.82 50.51 51.20 51.89 52.58 53.27 53.97 54.66

4034 36.39 40.96 36.96 40.97 36.97 41.59 37.54 41.59 37.53 42.22 38.12 42.23 38.12 42.24 38.10 42.85 36.69 42.87 38.68 43.47 39.27 44.10 39.85 44.73 40.43 45.36 41.01 45.99 41.59 46.63 42.17 47.26 42.75 47.90 43.34 48.53 43.93 49.17 44.51

60.48 60.53 61.30 62.12 62.94 63.76 64.58 65.41 66.23 67.06 67.88 68.71

0.7

0.8

0.9

1.0

1.1

1.2

33.01 33.53

30.11 30.60

27.59 28.04

25.41 25.83

23.48 23.87

34.06

31.08

28.50

26.25

24.27

34.60 31.59

28.68

26.68

24.67

35.13

32.08

29.42

27.11

25.07

35.66 36.19 36.73 37.26 37.80 38.34 38.88 39.42 39.96 40.50

32.57 29.81 33.06 30.33 33.55 30.79 34.05 31.25 34.55 31.71 35.04 32.17 35.54 32.64 36.05 33.10 36.55 33.57 37.05 34.04

27.53 27.96 28.38 28.81 29.24

* C o n d a d From 'International Tables of X-ray Crystallography', Kyn& Press, Birmingham, England, 1962. Note: For elements ofatomic number '22 or more Iactora are from Thomas-Fermi-Dirac Statistical Modcl.

25.46 25.86 26.26 26.66 27.06 29.67 27.46 30.10 27.87 30.54 28.27 30.97 26.68 31.41 29.09

6 LPZ 881C

OW1

L'EII t'6PI

W68 V8II

Z6OL IVP6

SL'9S L8SL

EL'SP ZVT9

P8LE 900s

ZL9P

8'061

L'861 6SSZ

L'911 L'ZSI

Z806 961 I

SE'IL LSP6

LS9S LE'SL

PZ'SP ES09

SS'9E

Pl'M

8681,

W6E

9ELE 8025

6191 0'602

09P6 I'PZT

OS'EL 10L6

SPLS SS9L

S9SP

LV9E 9881,

Sc'6Z 6V6E

9ZK SI'ZE

PZ0E ZOZP

LIZ1

S6PS

SLST

E8'OL LOE6

S9ZL

SOEP PZ'LS

OS'SP

61'LZ W9E

L81Z SV6Z

5081 96EZ

SLZ'Z LPI'E

Z8P6 0EZI

105s 6E'ZL

Z9ZP EP'9S

9E'EE IVPP

LE'9Z 9ZSf

€ 0IZ EZ8Z

96EI ES81

Z6L' I E9VZ

zL's9

ZO8E 0T 'OS

EV6Z 106E

ZO E t L9OE

61'81 PE'K

ISPI W61

1691 6L'ZZ L911 ZL'SI

6SV6 6L'Zl

L08C

9L'LZ T99E

8VIZ 8V8Z

0891 6E'ZZ

8ZEl 9L'LT

09'01

ES8

LVIE 9609

91'81 S6EZ ZOII

SOP1 E981

00'11

ZZPI OS69 lIE'6

EWS

8E'SX

zsz9

80'61 E8PZ PL96 85'21

ESP ET P19S BLE'L

P9Pl

2669

SOPS

869 8 Z911

8V11

PZSL

LSSP ZE1'9 S18Z t9L'E

OOLO 9160 S6VO sz90

WP'O

LZE'O E6E'O

OLZO

852'0

PZZO

OIE'S SLOL

0895

9PVE EWP

S9E'P LSL.5

8EVE

EIZZ LZ6Z

908 I 98E'Z

06V 1

SPSP

ZPL'Z 8Z9E

8892 9ZS'E

OEI'Z 96L'Z

IILI SPZZ

E6E'I EZ8' I

6P1'1 86V I

8560 spz'I E6V0 1190 90E'O 8PE'O

LSZP

EESZ 09TE

602'1 9SS'T

8L60 PSZ I

m8'0 520 I

E L90 OS80

ZLSO 91L'O

0101 19z' I

OZS 1 096 T 1990 f T80

PSSO EL90

PLVO 69SO

VIVO 06P'O

69E'O

PEE0 P8E'O

S6SO 859'0

905'0 SPS'O

6LP'O 605'0

8SVO

zwo

OEVO

8P8OZ 6062'2 '3

0860 EIE'I

L699 6688

6EV E PLVP

OEISZ 96PLZ L.!

L169 LE € 6

ZPS 8 IE'lI

P88'S 9E9L

--___.-

9LZI LEL'I

Z8OE ZIE'P PLP'Z OSP'E P10Z P6L'Z 8ZS'I 901'Z 8IZI Z991 E380 L81'1

Z8VO

zwo

LOZ9 1 zo6L.x 03

OEP'O 9WO

IZP'O PEVO

596 I

szs9

960 80E'I

06L'O 950 I

OIL'O EP60

6

9690 9160

8Z90 1280

OLSO OPL'O

8

SISO

ILVO L6S'O

EEVO

8590

E8E'O

9SE'O ZEVO

TSZO 581'0

181'0

LIZ0 W O

961'0 P61'0 661'0 OLE'O SLE'O

LOZO

SZVO

18E'O

ZZ6E'l 81PSI

ZS6Z I

WEVl

EZE90 LOIL'O

IN

nc)

UZ

om

El

Z80T TLVl

LOCO

9LE'O

PI

L161 IL9Z

OSE'I LS81

OOZO

VIVO

6Lc'Z

OEE'E

895'7 ILI'Z 861'1 t a gI

LSZO S6Z0 SIZO 6EZ'O

1659'1

1005'1

EOL'Z E8L'E PLI'Z OEOE PLL'I 8SVZ

PIC0

ZI 11

01

m.0

L

EEE'O W O SPZO

9

6LZ-0

S

805'0

6Zz'O

b

161'0

8L1'0 L81'0

E

Z61'0 L61'0

061'0 561'0

Z

89E'O ELE'O

99E'O

TLE'O

9SPSO

SOZSO

OL6VO=dX

LPT90

6985'0

fif)9S'O=Vf

1 JJqJWV

P

15

3.992 2.842

4.539 3.234

5.179 3.692

7.852 5.614

60.04 45.47

73.58 54.88

90.78 68.02

112.8 84.90

141.1 106.8

178.0 135.6

226.4 173.7

S

16

5.014 3.561

5.705 4.056

6.513 4.824

10.43 7.403

84.24 57.03

92.00 68.74

113.3 85.08

140.5 106.0

175.5 133.2

220.8 168.7

280.0 215.5

375.9 293.3 461.5 361.5

C1

17

5.796 4.109

6.599 4.684

7.536 5.356

11.44 8.172

86.38 65.68

105.6 79.03

129.8 97.70

160.6 121.5

251.1 192.5

317.4 245.2

518.5 408.1

A

18

6.486 4.592

7.385 5.238

8.435 5.992

12.81 9.148

116.9 87.75

143.5 108.3

177.2 134.4

275.3 211.8

346.7 268.9

560.9 443.7

K

19

8.238 5.830

9.382 6.651

10.72 7.611

16.26 11.62

95.83 73.06 120.4 92.09

200.1 152.3 220.2 168.1

146.6 110.3

221.3 168.3

274.0 210.0

341.5 263.8

428.1 333.6

684.6 545.0

ca

20

9.872 6.984

11.24 7.970

12.83 9.120

19.48 13.93

142.5 109.3

173.1 130.7

179.6 135.9 211.5 160.6

259.7 198.4

320.6 246.7

398.0 308.9

496.6 389.0

783.4 628.2

sc

21

10.66 7.543

12.14 8.608

13.86 9.851

21.00 15.03

151.7 116.7

183.8 139.2

223.9 170.7

274.1 210.3

337.1 260.6

416.5 325.0

516.8 407.3

802.4 649.0

Ti

22

12.08 8.548

13.75 9.754

15.70 11.16

23.65 17.02

169.0 130.6

204.3 155.3

248.0 189.9

302.5 233.2

370.5 288.0

455.3 357.4

561.2 445.5

V

23

13.54 9.585

15.41 10.94

26.56 19.06

185.8 144.2

224.0 171.0

271.0 m8.4

329.2 255.1

401.O 313.6

489.9 387.3

68.38 479.7(k)

116.2 89.57

Cr

24

15.67 11.11

17.83 12.67

17.58 12.51 20.34 14.49

30.67 22.03

210.7 164.3

253.1 194.2

305.0 235.9

446.7 351.8

55.67 431.9

70.08 53.30

118.8 91.70

MU

25

17.39 12.34

19.78 14.08

22.54 16.08

33.94 24.42

228.3 179.1

273.3 210.7

327.8 255.0

368.7 287.5 394.1

19.91 14.14

25.79 18.41

38.74 27.92

254.9 200.2

303.7 235.6

362.5 283.9

co 27

21.83 15.52

22.63 16.11 24.79 17.68

93.00 70.78 109.2 83.16

157.4 121.6

26

72.59 54.90 85.29 64.56

28.23 20.19

42.31 30.55

271.5 215.7

322.0 251.5

48.18 301.6(k)

60.17 45.02

Ni

28

25.18 17.93

28.59 20.42

32.53 23.30

48.62 35.19

303.5 243.0

45.99 281.7(k)

56.15 42.49

cu

29

26.55 18.93

30.12 21.54

34.24 24.58

37.03

40.41 30.53

49.61 36.91

45.73 34.57 49.49 37.44

56.10 41.77

Fc

51.05

Zn

30

29.30 20.92

33.22 23.80

37.74 27.13

56.09 40.78

Ga

31

31.04 22.20

35.16' 25.24

39.90 28.76

59.12 43.11

60.69 45.22

309.5

53.48 342.8(k)

57.20 376.6(k)

98.45 75.84

95.66 72.47

122.4 93.29

184.4 142.6 206.1 159.6

69.88 53.17

67.25 50.61 75.48 56.85 89.03 67.17

112.7 85.49

144.1 110.0

242.1 187.7

61.32 45.82

76.35 57.31

95.81 72.28

121.2 92.01

154.7 118.2

259.3 201.3

g.

69.30 51.83 74.92 56.08

86.23 64.78

108.1 81.65

136.7 103.9

174.2 133.3

291.1 226.4

f

93.15 70.05

116.7 88.22

147.3 112.1

187.6 143.8

312.5 243.5

%

@

Table 4.17 MASS ABSORPTlON COEFFICIENT #/p, CORRECTED FOR SCA'ITERING-continued _

~

~

_

P

W

i

N

Radiation

co

FC

Mn

1.7902 1.6207

1.9373 1.7565

2.1031 1.9102

Cr 2.2909 2.0848

Ti

2.7496 2.5138

Y 3 2

82.55 61.85

102.6 77.20

128.3 97.14

161.9 123.3

205.9 158.0

341.8 266.7

5.

74.03 55.26

91.25 68.44

113.3 85.36

141.6 107.3

178.4 136.1

226.6 174.1

374.8 293.0

%

65.14 49.52

79.72 49.57

98.19 73.73

121.8 91.88

152.1 115.4

191.3 146.2

242.6 186.8

399.8 313.3

77.97 57.61

72.75 55.26

88.97 66.55

109.5 82.31

135.7 102.5

212.7 162.7

269.2 207.6

441.8 346.9

56.19 41.05

81.49 60.46

78.20 59.47

95.57 71.56

145.4 110.0

227.4 174.3

287.4 222.0

469.4 369.5

53.47 39.01

60.26 44.18

83.32 64.78

85.88 65.39

104.9 78.61

117.5 88.44 128.8 97.1

169.2 128.6 181.2 137.9

159.2 120.6

198.2 151.0

248.2 190.6

313.2 242.4

509.2 401.8

50.74 36.95

57.03 41.74

64.18 47.22

92.04 68.92

93.51 71.30

114.1 85.63

140.0 105.6

172.9 131.2

214.8 164.0

268.7 206.7

338.3 262.4

541.3 433.0

39

54.50 39.83

61.16 44.93

97.92 73.72

102.5 78.24

188.8 143.5

234.3 179.2

292.5 225.5

367.6 285.8

591.3 469.2

57.66 42.29

64.61 47.66

14.94 77.63(k)

110.7 84.64

124.9 93.87 134.8 101.5

153.1 115.7

40

68.71 50.76 72.45 53.76

165.1 124.9

203.3 154.8

251.9 193.0

313.9 242.5

393.6 306.7

629.3 501.0

N b 41

61.23 45.09

68.49 50.73

76.65 57.14

16.23 82.02(k)

119.5 97.71

145.4 109.6

177.8 134.8

218.7 166.9

270.5 207.7

336.5 260.5

420.9 328.8

668.6 534.1

Mo 42

63.87 47.23

71.30 53.07

79.63 59.67

19.90 14.22

145.9 111.9

177.2 133.8

216.5 164.4

265.8 203.1

328.3 252.6

407.5 316.2

802.1 643.2

Tc

43

66.43 49.36

84.01 55.37

14.22 62.14(k)

21.57 15.42

157.0 120.7

190.6 144.1

232.5 176.9

285.1 218.2

351.3 271.0

435.1 338.5

508.4 398.3 541.5 425.4

R u 44

69.16 51.65

15.07 64.78(&)

22.85 16.35

165.2 127.2

200.2 151.7

243.9 185.9

298.6 229.1

367.2 283.9

453.7 354.0

563.0 443.7

874.3 707.0

Rh 45

72.82 54.68

76.88 57.83 14.34 61.10(k)

16.37 11.63

24.81 17.75

178.0 137.3

215.5 163.5

262.1 200.2

320.3 246.3

393.1 304.7

484.5 379.1

599.2 473.9

922.2 749.4

As Kar=0.5609 KB=0.4970

Pd 0.5869 0.5205

Rh

Mo

0.6147 0.5456

0.7107 0.6323

Ge 32

33.49 24.00

37.90 27.27

42.98 31.04

63.43 46.39

As

33

36.29 26.07

41.04 29.60

46.49 33.66

se34

38.31 27.59

43.28 31.29

Br

35

41.95 30.29

Kr

36

Rb

zn

cu

1.5418 1.3922

Ni 1.6591 1.5001

54.70 41.34

66.91 49.90

68.36 50.14

60.44 45.81

48.97 35.56

71.69 52.78

47.33 34.32

53.50 38.96

44.18 31.98

49.79 36.20

37

47.51 34.49

Sr

38

Y

zr

Absorber

-

1.4364 1.2952

847.8 682.6

J

f?.

-& n

3

$i;'

F

Pd

13.32 56.28(k)

15.17

A% 47

14.42 10.20

16.41 11.64

Cd

48

15.11 10.70

In

49

Sn Sb

Te

46

17.32 12.31

26.22 18.78

186.7 144.3

225.7 171.6

284.0 209.8

334.2 257.6

409.2 318.1

502.9 394.8

619.9 492.1

944.7 777.1

28.35 20.31

200.2 155.0

241.6 184.1

292.9 224.1

356.5 275.5

435.5 339.5

533.7 420.4

655.4 522.4

988.1 812.1

17.20 12.21

18.74 13.32 19.63 13.97

29.68 21.28

207.8 161.3

250.5 191.2

303.1 233.1

368.1 285.2

448.4 350.7

547.8 433.1

670.1 536.4

998.4 825.9

16.14 11.42

18.36 13.03

20.95 14.91

31.65 22.71

219.6 170.9

264.2 202.2

319.1 246.1

386.7 300.6

469.9 368.7

572.0 454.0

696.8 560.4

102.5 853.9

50

16.96 12.00

19.29 13.69

22.01 15.66

33.21 23.85

228.2 178.0

274.0 210.2

330.2 255.3

483.5 380.9

586.3 467.5

710.6 514.6

103.0 864.9

51

17.94 12.71

20.41 14.50

23.29 26.58

35.10 25.23

238.9 186.8

286.4 220.3

501.5 396.5

605.9 485.1

730.8

267.1

399.2 311.2 415.3 324.9

594.0

975.4 883.5(1,)

18.54 13.14

21.09 14.99

24.04 17.14

36.21 26.04

243.8 191.2

291.8 225.0

350.1 272.3

420.9 330.5

506.5

401 .2

730.6 597.6

513.1(1,) 727.3(1,)

448.3 353.4

537.4 428.7

609.2 490.3 643.4 520.6

766.8 631.5

458.0 362.5

546.8 438.3

651.2 530.2

642.2(1,) 639.6(L)

223.0(~ 447W11) 243.9 470.1(C)

567.0 456.9

671.3 550.1

669.7(1,) 659.8(L)

271.1 212.4

573.3 464.7

565.9(1,) 556.8(L)

417.0(1,) 555.w 197.7 576.6(1,)

293.3 230.0

218.0 374.9(1,)

52

10.75

344.5

I

53

20.15 14.29

22.91 16.29

26.12 18.63

39.30 28.29

261.7 205.9

312.5 241.7

Xe

54

21.03 14.93

23.91 17.01

27.24 19.44

40.94 29.50

269.5 212.7

321.2 249.1

374.0 2919 383.3 300.2

cs

55

43.54 31.39

283.1 224.2

336.6 261.9

400.6 314.9

56

25.46 18.13 26.48 18.87

29.00 20.71

Ba

22.40 15.90 23.31 16.56

30.16 21.56

45.21 33.64

344.3 268.9

408.5

322.5

476.9 379.1 484.6 387.1

359.2 281.6

424.8 336.8

501.8 402.9

590.7 481.8

359.0(1,) 574.2(L)

375.0 295.1

442.0 352.0

519.8 419.7

512.8(1,,) 499.6(L)

240.1 186.2

354.5 279.7 388.3 307.2

La

57

24.76 17.60

28.12 20.06

32.01 22.93

47.94 34.64

ce

58

26.34 18.74

29.91 21.35

50.89 36.82

Pr

59

28.04 19.96

31.82 22.73

34.03 24.37 36.21 25.95

290.2 230.7 303.7 242.2 317.9 254.5

54.07 39.16

332.7 267.5

391.1 309.1

459.3 367.6

537.5 436.4

333.4(1..) 517.3(l!)

383.1(l,,) 497.1(1,) 190.6 518.3(1,)

Nd

60

29.29 20.87

33.24 23.76

37.80 27.11

56.37 40.87

341.4 275.7

349.4(1,,) 442.4(1,)

205.7 337.4(i1,)

258.4 200.9

415.7 329.9

30.91 22.04

35.05 25.09

39.85 28.61

353.4 286.8

304.l(iI,) 458.0(L)

169.4 458.5(1,)

211.3 357.0(1,)

265.2 206.4

425.3 338.1

Sm 62

31.99 22.84

36.28 25.98

41.22 29.63

59.34 43.08 61.28 44.54

467.9 376.6 480.4 388.9

461A(1,) 445.5(L)

Pm 61

400.1 317.7 412.6 329.3 417.2 334.6

411.6(1,) 393.8(L)

314.9(1,,) 390.9(1,)

217.1 167.7

272.2 212.1

435.2 346.4

358.6 292.5

322.9 254.1

2 R

s

g. E

2

$

Table 417

MASS ABSORF'TION COEFFICIENT IJp, CORRECTED FOR SCAlTERlNG*-continued Radiation ~-

Rh

Mo

Ka=0.5609 Kfl=0.4970

Pd 0.5869 0.5205

0.6147 0.5456

0.7107 0.6323

Eu 63

33.72 24.09

38.22 27.41

43.41 31.24

a64

34.66 24.79

39.26 28.18

Tb

65

36.38 26.04

Zn 1.4364 1.2952

cu

Ni

1.5418 1.3922

1.6591 1.5001

64.43 46.90

370.1 303.6

326.5(iI) 345.9(L)

276.0(1,) 340.7(1,)

44.57 32.11

66.04 48.14

371.8 306.9

367.1 (i,) 348.1(L)

41.20 29.60

46.75 33.72

69.14 50.48

324.1 (1,) 316.6(L)

DY 66

37.83 27.11

42.82 30.80

48.56 35.06

71.69 52.41

217.7(1,,) 323.2(L)

249.3(1,) 357.6(L) 259.4(ill) 309.8(1,)

Ho 67

39.83 28.57 41.73 30.03

45.06 32.45

51.07 36.93

75.26 55.11

230.1(1,,) 333.8(L)

47.19 34.02

53.46 38.70

78.62 57.66

Tm 69

43.04 30.93

48.63 35.11

55.06 39.91

Yb

70

44.49 32.02

50.25 36.33

56.87 41.28

Lu

71

46.41 33.45

52.40 37.93

HI

72

53.58 38.66

Ta

73

w

Ag

co 1.7902 1.6207

Fe

Mn

1.9373 1.7565

2.1031 1.9102

189.4 317.7(in)

235.6 182.4

284.1(in) 345.1(1,)

153.1 4O4.WI) 162.3 268.1 (1,)

200.4 154.2

142.9 356.7(1,)

175.1 281.9(1,)

152.7 242.5(il,)

135.7 212.9(1,)

241.4(1,,) 292.2(1,)

80.81 59.37

117.6 198.6(in)

59.26 43.08

83.28 61.30 86.60 63.85

120.6 2ofj.2(4,) 123.5 215.4(4)

60.48 43.82

68.34 49.75

99.63 73.60

55.53 40.13

62.63 45.46

70.74 51.58

74

57.57 41.66

64.88 47.16

Re

75

59.37 43.03

Os

76

60.97 44.25

Absorber

Er

68

N

cr 2.2909 2.0848

Ti 2.7496 2.5138

e4

468.1 374.0

a 3.

248.7 193.0

294.7 230.2 310.3 243.1

489.6 392.6

%

215.8 166.5

267.3 208.0

332.6 261.3

520.7 518.1

186.9 143.4

229.9 177.8

284.1 221.7

352.5 277.8

547.4 442.6

165.0 256.0(fn)

201.7 155.1

247.5 191.9

305.0 238.7

377.3 298.4

580.7 471.9

139.0 223.6(1,,)

168.9 129.1

206.1 158.7

252.7 196.1

311.0 243.7

383.9 304.2

587.9 479.1

142.2 230W~) 145.6 110.8

172.7 132.2

210.6 162.3

257.8 200.4

316.9 248.7

390.6 310.1

595.2 486.3

176.6 135.4

215.2 166.1

263.2 204.9

323.0 254.0

397.3 316.1

602.2 493.5

149.0 113.5

180.6 138.6

219.8 169.9

268.5 209.4

329.1 259.2

404.1 322.1

609.2 500.7

124.9 302.4(1,)

151.0 114.8

183.3 140.3

223.6 172.4

273.8 212.8

336.5 264.1

414.7 329.2

632.0 516.3

102.9 76.16

133.3 103.3

160.9 122.6

195.1 149.7

237.4 183.5

290.0 226.1

355.4 279.9

436.4 347.9

658.0 540.7

73.24 53.49

106.3 78.81

142.1 110.3

171.3 130.8

207.3 159.4

251.7 195.1

306.7 239.9

374.6 296.2

458.3 366.9

682.9 564.8

66.87 48.69

75.42 55.19

109.1 81.12

151.4 117.7

182.0 139.3

219.8 169.5

266.3 207.0

323.6 253.9

394.0 312.7

479.9 385.7

706.0 588.1

68.63 50.05

77.36 56.69

111.6 83.17

158.5 123.6

190.5 146.1

229.6 177.5

277.7 216.4

336.5 264.9

408A

495.4 400.2

719.6 603.7

325.3

D

1

& g2. n

&

Ir

77

63.40 46.M

71.32 52.10

80.33 58.98

115.6 86.32

168.4 131.7

201.9 155.3

242.9 188.3

292.8 229.1

353.7 279.6

427.3 342.1

515.6 419.0

736.1 623.5

370.9 294.5

535.0 437.6

749.6 641.7

386.9 308.6

451.9 359.0 463.2 374.8

758.7 656.8 773.1 675.9

Pt

78

65.68 47.82

73.93 54.02

83.09 61.12

119.2 89.24

178.5 140.0

213.7 164.8

256.3 199.4

Au

79

67.84 49.48

76.t9 55.87

85.67 63.16

122.5 91.96

188.3 148.1

269.2 210.0

Hg

80

69.90 51.07

78.46 57.62

88.15 65.11

125.7 94.51

198.8 156.8

224.9 173.9 237.1 183.8

308.2 242.0 322.7 254.3

283.2 221.6

338.6 267.7

404.8 324.0

482.7 392.3

552.3 454.7 572.6 474.0

TI

81

71.77 52.52

80.49 59.23

90.37 66.87

128.4 96.90

206.7 163.6

245.7 191.2

292.5 229.9

348.2 276.8

414.0 333.6

490.3 401.I

576.1 481.9

Pb

82

73.74 54.07

82.63 60.93

92.67 68.75

131.2 99.31

215.4 171.1

255.6 199.6

303.1 239.2

359.5 287.2

500.5 413.0

583.1 492.2

Bi

83

76.60 56.26

85.78 63.37

96.13 71.44

135.7 103.0

268.3 210.3

317.4 251.5

375.0 301.0

516.2 4292

596.0 508.1

Po

84

79.42 58.44

88.86 65.77

99.50 74.1 1

139.9 106.5

226.8 180.0 237.7 190.3

425.6 344.7 441.5 359.9

280.3 220.6

330.3 263.1

454.6 373.4

527.3 442.5

602.0 519.5

At

85

81.40 60.05

90.97 67.53

101.7 76.00

122.1(1,) 108.8(L)

249.2 200.2

293.1 231.6

344.4 275.5

388.5 313.7 403.4 327.4

469.6 388.1

540.7 457.5

611.0 533.2

Rn

86

82.38 60.91

91.97 68.44

122.5(1,) 109.8(L)

249.0 201.1

291.9 231.7

341.5 274.7

397.8 325.1

459.8 383.4

Fr

87

92.98 69.35

91.18(In) 110.8(L)

258.8 210.1

302.2 241.1

351.8 284.8

407.2 335.5

466.7 393.1

524.3 448.6 526.0 4562

Ra

88

95.17 91.20

106.0 79.91

95.03(1,,) 113.1(L)

266.6 217.8

309.9 248.9

358.7 292.7

412.0 342.7

467.3 398.6

Ac

89

83.36 61.77 85.43 63.47 86.25 64.30

102.7 76.96 103.7 77.92

95.95 72.04

106.7 80.75

97.50(1,) 102.1(1,)

273.6 224.7

364.3 299.5

415.4 348.8

Th

90

88.04 65.81

97.82 73.66

97.75(i1) 82.48(L)

100.3(In) 75.07(l,,)

278.6 230.6

314.6 255.8 320.5 261.1

I03.2(1,,) 77.4(111) 105.9(i,,) 79.70(1,,)

290.1 240.2

332.8 272.2

366.1 304.0 378.6 316.0

294.9 246.7

336.7 275.2

380.7 320.3

Pa

U

91 92

90.63 67.91

88.60(i1) 75.95(L’)

72.19(i1,) 84.95(L)

93.18 69.94

89.92(1,) 78.17(L)

74.20(1,,) 87.38(L)

-

*Reproduced by permission from the International Tablesfor X-ray Crystallagrapby.

*4

9

E

25

5

e 1 W v,

4-36

X-ray analysis of metallic materids

4.4 X-ray results 4.4.1

Metal Working

Table 4.18

GLIDE ELEMENTS AND FRACTURE PLANES OF METAL CRYSTALS

Eleuared temperatures

LOW

temperatures Structure

Glide plone

Metal

Glide direction

Glide plane

Glide directian

Most closely packed Lattice plane

1

Approximately 450°C l(111) (100) [loll 2(100) 3(110)

ClOi]

-

[Ili] 11117

-

[lli]

c1m [iii] Ciii] [lli] &Cu-Zn

a-Fe-Si, 5% Si Hexagonal, Mg close zn packed Cd

(110) (112)(?) (110)

[lli] -

-

-

(110) (123) (110) (123)

-

-

-

-

z }

l(101) 2(100) 3(111)

-

[iii] [iii] [llfl

[111]

-

-

Lattice Fracture direction plane

-

-

-

l[lOIl 2[1Oo] 3[112]

-

--

-

l[lll] 2[100] 3[110]

(001)

-

I

-

I

-

1

Zn-Cd ZnSn

Tetragonal PSn (white)

Rhombohedral

As Sb Bi

-

Te

(ioio)

Hg

Hexagonal

4.4.2

(110) (100) (101) (121)

[Ool] [Ool]

Approximately 150°C 1(100) (110) [TI11 2(11O) 3(101)

-

-

-

1[001] 2[111] 3[100] 4[101]

~11~01-

-

(lOT1)

-

-

ClOi]

(111) (111) (100) and complex

-

(ioio)

Crystal Structure

Crystal structural data for free elements are given in Table 4.25. The coordination number, that is the number ofnearest neighbours in contrast with an atom, is listed in column 4 and the distances in column 5. In complex structures, such as a Mn where the coordination is not exact, no symbol is used and the range of distances between near neighbours is given.

X-ray results

4-37

TaMe 4.19 PRINCIPAL TWINNING ELEMENTS FOR METALS

-

Crystal structure

Twinning plane, Kl

Twinning direerion, VI

Second undisrorted K2

Direction v2

Shear

From C. S. Barrctt and T. B. Magplski, ‘Structurr of Metals’.’

A co-ordination symbol x in column 4 indicates that each atom has x equidistant nearest neighbours, at a distance from it (in kX-units) specified in column 5. The symbol x, y indicates that a given atom has x equidistant nearest neighbours, and y equidistant neighbours lying a small distance further away. These distances are given in column 5. In complex structures, such as z-Mn, where the co-ordination is not exact, no symbol is used, and the range of distances between near neighbours is given in column 5. The Goldschmidt atomic radii given in column 6 are the radii appropriate to 12-fold coordination In the case of the f.c.c. and c.p.h. metals the radius given is one-half of the measured interatomic distance, or of the mean c?f :he two distances for the hexagonal packing. In the case of the b.c.c. metals, where the measured interatomic distances are for 8-fold co-ordination, a numerical correction has been applied. In some cases, where the pure element crystallizes in a structure having a low degree of co-ordination, or where the co-ordination is not exact, it is possible to find some compound or solid solution in which the element exists in 12-fold coordination, and hence to calculate its appropriate radius. In a few cases no correction for coordination has been attempted, and here the figures, given in parentheses, are one-half of the smallest interatomic distances. It should be emphasized that the Goldschmidt radii must not be regarded as constants subject only to correction for co-ordination and applicable to all alloy systems: they may vary with the solvent or with the degree of ionization, and they depend to some extent on the filling of the Brillouin zones. Ionic radii vary largely with the valency, and to a smaller extent with co-ordination. The values given in column 8 are appropriate to &fold co-ordination, and have been derived either by direct measurement or by methods similar to those outlined for the atomic radii. All are based, ultimately, on the value of l.32A obtained for Oz+ ions by Wasastjerna,28 using refractivity measurements. Ionic radii are also dected by the charge on neighbouring ions: thus in CaF, the fluorine ion is 3% smaller than in KF, where the metal ion carries a smaller charge. It is not possible to give a simple correction factor, applicable to all ions: the effect is specific and is especially marked in structures of low co-ordination. Figures in arbitrary units indicating the power of one ion to bring about distortion in a neighbour (its ‘polarizing power’), and indicating the susceptibility of an ion to such distortion (its ‘polarizability’) are given in columns 9 and 10, respectively. The crystal structures of alloys and compounds are listed in Chapter 6, Table 6.1. Other sources of data are references 7 and PearsonZ3which is particularly valuable as the variation of lattice parameters with composition as well as structure is given. Structures are generally referred to standard types which are listed in Pearson and in Table 6 2 in Chapter 6. Further information on pure crystallography can be obtained from International Tables For X-ray Cry~tallography.~

Table 4.20 ROLLING TEXTURES IN METALS AND ALLOYS

2

-

Texture Metal or alloy

-

I

2

3

Facecentred cubic

CU' Cu 70Yo-21130% Cu 70Yo-Zn 30%* Cu+12 at. % AI Cufl.5 at. %AI Cu+3 at. % Au Cu +29.6 at. % Ni Cu+49 at. % Ni Ni Au Au+ 10 at. % Cu A1 AI A1+2 at. % Cu Al+ 1.25 at. % Si A1+0.7 at. % Mg Ag Pb+2 wt % Sb

Mo W V Fe+4.16 wt % Si

Metal or alloy

I

2

Y

3

Body-centred cubic (continued) Fe+35 wt YOCo Fe+35 wt % Ni ,&Brass

cu cu

Body-centred cubic a-Fe a-Fe

00

Texture

Hexagonal close-packed

Be, 5 = 1.5847 a

Ti, 5 = 1.5873 a

(OOOI) tilted approx. 2MO" round R D out of rolling plane; ; [IOiO] parallel RD

Zr, 5 = 1.5893 a

(0001)/[11m (OOO1) tilted 30-40' round R D out of rolling plane; [IOiO] parallel R D

Mg, 5 = 1.6235 a

(OOO1) parallel rolling plane

5a = 1.623

(OOOI) parallel rolling plane

/I-Co,

Zn, E= 1.8563 a

(112)K110]

(111)/C1121

6

2.

F n

(OOO1)tilted 2O"round transversedirection

Cd, 5 = 1.8859

out ofrollingplane

Mg+AI (76O*C)

UH3

A2 A15

UD3

A15

6.633

TiU, Zr-U

023 C32 cubic f.c.

10.26 4.828; 2.847 10.68 ( 180". 5.433; 8.561

1

1

Group VIE: Fe, Co,Ni; Ru, Rh, Pd; Os,Ir, Pt Fe (4 A2 2.8665 ( 4900" and > 1 400") (Y) AI 3.6467 (900-1400") k8Fe C14 421; 6.83 BeBe,Fe c15 5.88 (stable only z 1O O O O ) Be,Fe hex 4.14; 10.73 (A=18) D2b 7.253; 4.232 CeFe, c15 Gd,Fe, cubic 8.25 (M=6) GdFe, rhomb. 4.72; 39" 46 (M=6) 5.71; 6.78; 7.15 (M=2) Gd,Fe, orthorh. GdFe, hex. 5.15; 6.64 ( M = 2 ) GdFe, hex. 4.92; 4.11 ( M = l ) GdJe,7 hex. 8.39; 8.53 (M=2) GdFe, c15 7.391 Y Fez C15 7.357 ( M = 8 ) TiFe, C14 4.77; 7.75 TiFe E2 2.976 11.15 TiFe,O E93 11.28 Ti,Fe,O E93 Ti,Fe E92 11.31 (Duwez, Taylor)

28 29 30 221 222

31

223 224

-

225

22 1

32 33

66

Crystal chemistry

Table 6.1 STRUCTURES OF METALS. METALLOIDS AND THEIR COMPOUNDS- conrimed Elenrmt m

conrpolad

Struchue type

Luttice comtants, r-ks

MII: Fe,Co, Ni;Ru. Rh, W;Os. Ir, Pt- continued BFi, C15 7.04 C36 ZrFe, 4.95; 16.12 D2d ThFes D2C U,Fe 10.31; 5.24 C15 7.065 UFe, D8b VFe C14 4.82; 7.87 NbFe, TaFe, c14 4.80; 7.84 CrFe (u) 086 8.800; 4.544 D8b MoFe ( 0 ) 9.188; 4.812 Mo,Fe, 8.97; 30" 39' 0 83 WFe, C14 4.73; 1.70 9.02: 30" 31' 08, WPe7 MnFe, 2.53; 4.08 (not an equilibrium phase) A3 A3 2.5059; 4.0659 CQ (4 A1 3.5447 (>390°C) (8) BeCO n 2.61 1 A12 7.66(?) %CQ, D2b 7237; 4.249 J%CQ Cl5b 5.852 kco c15 YCO, 7.216 ( M = S ) La3CO 7.279; 10.088; 6.578 (M=4) Doll 7.449 023 C013~ D2d 5.09; 3.94 a l s h D2d cecos 4.96; 4.06 CosSm D2d 5.004; 3.971 D2d Co,Tb 4.947; 3.982 Co5Ho D2d 4.910; 3.996 Gd3Co 5.17; 6.72; 5.94 (M=2) DO11 Bf GdCO 3.90; 4.87; 422 (M=2) cubic 7.98 ( M =6) Gd2C03 Gdco, c15 7.256 rhomb. GdCo, 4.80; 41" 32' (M=6) Gdco, hex. 5.47; 6.02 (M=Z) GdCo, 026 4.91; 3.97 ( M =1) Ceco, CI 5 7.15 TiCo, C36 4.72; 15.39 (Co-rich) c15 6.73 B2 TiCo 2.99 Ti,Co,O 11.30 (Rostoke?') E93 Ti,Co 11.28 (Dewez, Taylor") E93 zrco, c15 6.89 D2d 4.95; 4.04 ThCo, uco, c15 7.005 UCQ Ba 6.36 U,Co D2c 10.36; 5.21 vco, 5.032; 12.27 (M56) DO21 D8b vco 8.84; 4.59 A15 4.68 v3CQ C36 4.73; 14.43 NbO.8C02.1 NbC% C15 6.75 0 6 4.72; 15.39 Tao.8Coz., Co3Ta (a) 3.647 (M=l) 4 hex. 9.411; 15.50 (M=32) (8) Co,Ta (a) c14 4.797; 7.827 C15 (8) 6.18 C36 (V 1 4.700; 15.42 ,.. CrCo 086 8.71; 4.54 D8b 8.81; 4.56 Cr17C013 tu) MoCo, 5.12; 4.11 DO19 Mo6Co, 8.98; 30" 48' 085 Mo,Co, D8b 9.229; 4.827 wco, 5.12; 4.12 Dol9

Rdz

Group

1

226

35 35

227

221 228

232 235

229

230

36 31

Structures ofmetuls, metalloidsand their compounds Ta& 6.1

6-7

STRUCTtXES OF METALS, METALLOIDS AND THEIR COMPOUNDS--continwd

~~

~~

Element or Ccmpound

Stmctwe type

Lattice constants, reinarks

Group Vm:Fe, Co, Ni;Ru, Rh, Pd; Os, Ir, Pt-continued W&O, D81 8.95; 30" 41' FeCO 82mnsf. temp. 7 3 0 ~ constents ; at room temp. A2 Ni A1 3.5240 BeNi Ln 2.60 7,s %IN'S D81.3 C36 4.81; 15.77 M8N1, M&Ni Ca 5.18; 13.19 CaNi, D2d 4.95; 3.44 YNi, c1s 7.181 (M=8) hex. YNi, 4.978; 24.45 YNi orthorh. 4.10; 5.51; 7.12 (M=4) D2d YNi, 4.883; 3.967 ( M =1) D2d 4.95; 4.00 LaNi, LaNi, c15 7.25 D2d 4.86; 4.00 GeNi, c15 1.19 or 7224 CeNi, 4.98; 16.54 CeNi, Do21 PrNi, 4.94; 3.97 D2d RNi, c15 7.19 Gd,Ni 5.15; 6.70; 6.23 (M=2) Dol 1 7.28; 8.61 (M=4) tetr. Gd,Ni, 827 5.43; 4.35; 6.93 GdNi 7.208 @dNip c15 4.937; 24.18 hex. Gd,Ni7 5.35; 5.83 (M=2) hex. GdNi, 4.90; 3.97 ( M =1) Md GdNi, 8.18; 8.47 (M=2) Gd,Ni,, Thh,Nil7 4.924; 3.974 Ni,Sm D2d 4.984; 3.966 Ni,Tb D2d 4.871; 3.966 Ni,Ho D2d 4.841; 3.965 Ni,Yb D2d 11.278 (A=%) Ti,Ni O:-Fd3m 5.10; 8.31 TiNi, W24 3.015 TiNi 82 11.29 Ti,Ni E93 11.30 Ti,Ni,O E93 ZrNi, 6.71 C156 6.417; 5.241 Ze2Ni C16 ZrNi, 6.925. C15 ZrNi, 5.309: 4.303 W,, 3.268; 9.937; 4.101 ZrWi 086 Hf,Ni 6.405; 5.252 C16 HfNi Bf 3.218; 9.788; 4.117 ThNi, D2d 4.92; 3.99 ThNi, 3.964; 3.852 C32 6.783 C15 UMi, 4.97; 8.25 C14 UNi, 10.37; 5.21 D2c U,Ni PUN& m o n d . 62Jm 4.87; 8.46; 10.27; 8- 1M)" (M=6) 6.22; 30" 44'(M=3) rhomb PuNi, 3.59; 10.21; 4.22 PuNi Bf 3.54; 7.22 mi3 Do21 2.61; 3.54; 2.57 orh. VNi, 8.91; 4.64 D8b V,,Nil, W 2 2 3.62; 7.41 NbNi, Wa 5.11; 4.25; 4.54 TaNi, A2(tetr. deformed) (cia = 1.09; metastable intermediate by quenching) Cr,Ni 8.82; 4.58 08b CrNi 5.72;3.56 Dla MoNL 5.064; 4.224; 4.448 WQ MoNi, 2.54; 4.18 A3 MoNi WNi, 5.73; 3.55 Dla

R4s

-

1

I

1

221 231

233 234

232 236

~~

38 238

239 240 241

242

6-8

Crystai chemistry

Table 6.1 STRUCTURES OF METALS, METALLOIDS AND THEIR COMPOUNDS-continued Ekmeitt or compound

Structure type

Lattice constants, remarks

Ref.

Grout, WI:Fe, Co, Ni;Ru, Rh, Pd; Os, Ir, Pt-continued MnNi, MnNi FeNi, Fe,Cr,Ni Ru Ru,Be, RuBe, Ru,Be,o Ru,Ce TiRu ZrRu, URu, RuU, Rh WRh, RhMg Rh,Ca RhBe Rh,Sr Rh,Ti Rh,Hf Rh,Nb Rh,Zr Rh,V Rh,Ta Pd BePd Be,Pd BePdl, Pd,Ca Pd,Sr Pd,Ba TiPd, Pd,Zr Pd,Hf Pd,Th PdTi, PdZr, PdHf, PdMg UP#; Pd,V Pd,V FePd, FePd

os

Be%,

TiOs ZrOsz

uos,

TaOs(u) cros

was, (d

Ir Ir,Ca Ir,Sr Ir,Ti Ir,Hf Ir3Nb Ir,Zr

LIZ Llo A2~

Li, cubic b.c. A3 hex. D53 C14 Do3

c15

B2 C14 c12 monocl. A1 A3 B2 C15 B2 C15 LIZ LIZ LIZ L12 LIZ LIZ A1

B2 ClSb ClSb Mb C15 C15 C15

Do,, DO,, Do24

L12

CllB CllB CllB 82 DO24 f.c. tetr.

DO,, LIZ L10 A3 monoclinic B2 C14 C15 A15 086 A1 c15 C15 LL L12 L12 L1,

3.59 ( ~ 5 1 0 ° C ) 3.74; 3.52 (< -700°C) 2.97 (range -7o(F-9oO0C; constant at 745") 3.54 ( c 586"Cl 8.88 (powder &gram similar All-type) 2.705 8; 4.281 6 2.7060; 4.253 7 11.42 5.90; 9.10 11.03 1.79 3.06 5.13; 8.49 3.980 13.106; 3.343; 5.202; 96O9.2' (M=4) 3.8032 2.73; 4.38 3.099 7.525 2.740

::q

3.911 3.865 3.921 3.195 3.86 3.8903 2.8 19 5.98 (ordered as &,Be, Pd) 5.98 [disordered as Be, [Be,Pd),] 7.27; 425 7.665 1.826 7.983 5.48; 8.96 5.612; 9.235 5.595; 9.192) 4.110 3.090; 10.084 3.306; 10,894 3.251; 11.061 3.12 5.757; 9.621 3.88; 3.72 3.84; 1.15 3.84 3.85; 3.12 2.734 1; 4.391 8 11.31; 10.63; 8.48 96" 32' 3.07 5.18; 8.51 7.4974 9.934; 5.189 4.677 9.686; 5.012 3.8392 7.545 7.700 3.822 3.911 3.865 3.943

1

243 252 244 40 39 245 246 241

248

247

248 249 342 342 342 341 39 250

40 39 41 42

41 247 250

Structures of metals, metalloids and their compounds

6-9

Table 6.1 STRUCTURES OF METALS. METALLOIDS AND TUHR COMPOUNDS-contimred Element or compound

Structure type

Lattice constants, remarks

Group VIE: Fe, Co, Ni; Ru, Rh, Pd; Os, Ir, Pt-cotrrinued Ir,V L12 3.812 k3Tc L12 3.889 TaIr (a) 086 9.938; 5.172 ZrIr, c15 7.346 UIr, c15 7.493 9 IrW B19 4.452; 2.760; 4.811 A1 3.923 6 Pt D8,, (deformed) Be,,Pts Pt2Ca c15 7.629 Pt2Sr c15 7.777 7.920 Pt,Ba a 5 4.86 PtMg B20 3.88; 3.72 h3Mg 7.73 CePt, 3.89 TiPt, Ti,R 5.033 5.63; 9.21 ZrPt, 5.636; 9.208 Pt,Hf 5.752; 4.889 Pt,U Pt,U 5.60; 9.68; 4.12 FePt, 3.88 (8w"C 3.90 4.0789 7.803 7.40; 5.51 4.67 6.097 3.266 4.63; 8.44 6.485; 4.002 2.79; 4.77 4.096 5.097 7.462; 5.989 4.88 5.21 3.256 3.363, 8.592 6.45; 4.03 3.926 1 3.98; 3.72 (c/u= 1.003) 3.7474 a (disordered)=3.752 8 2.665 0; 4.941 0 2.78; 4.39 4.36; 2.51 6.21 12.28 12.36 8.55 5.21; 8.54

342 48

43 48 49 49 259 260

Structures of metals, metalloids and their compounds

Task 6.1

6-1 1

STRUCTURES OF METALS, METALLOIDS AND THEIR COMPOUNDS--eontinued

Element or cornpolmd

Structure type

Group IIb: ZR Cd,Hg-continued CaZnlt 022 D2d orthorh. P m n 026 D23 orthorh. Amam D23 D2d 82 B2 82 LIZ C14 82 C16 C32 013 D2d D13 cybic f.c. f.c.c.Fd/3m orthorh. tetrP4,mm C36 hex. monocl. hex. 081-3

L1a A3 A2 A13 monocl. hex. D81-3 monocl. D81-3

A13 A20 "1-3

LlO 82 c15

Lattice constants, remarks 12.13 5.40; 4.22

5.32; 6.72; 13.15 (M=4) 5.549; 4.283 12.22 5.32; 8.44; 10.78 (M=4) 12.33 5.43; 4.23 3.15 3.70 3.67 3.932 2 5.064; 8.210 3.143 7.62; 5.64 4.491; 3,718 4.273; 10.59 5.24; 4.45 9.03; 13.20

50

5.68

52 262 262 263 264

14.11 17.8; 12.5; 8.68 7.633; 6.965 5.05; 16.32 12.9 30.5 13.7; 7.6; 5.1; 128' 44' 12.8; 57.6 9.14 3.85 ( ~ 3 2 0 ° C ) 275; 4.44 (>350°C) 3.05(high temp.) (lowtemp.) 13.65; 7.61; 5.1; 128" 44' (As28) 12.8; 57.6 (Az555) 8.98 13.46; 7.49; 5.06; 127" 05' 8.92 6.33 ( > 920 "C)

51 51 47,52 261 261 52 52

8.90

-

081-3

3.04 (> -600°C) 4.14; 3.50 3.05 (> -600°C) 18.08

5.35; 1.65; 4.14

341

mom similar to y-brass-str. than y'

similar to D81-3 4.10; 2.74 C32 4.03; 3.47 L10 3.89 (45O"C) 295 (< -450°C) 294 B2 3.678; 3.602 (intermediate state during precipitation a from tetr. f.c. 3, at 225°C)

2

50

273; 3.19 (high temp.) 2.91 6.96

D81-3

c371 type similar to A3 similar to D8,, similar to D8,, 82

Ref.

53

6-12

Crystal chemistry

T8bk 6.1

STRUCTURES OF METALS, METALLOIDS AND THEIR COMWUNDS-cOnthWd

Element or compound

Structure tppe

Lattice constants, remarks

teir. f.c

3.690: 3.650 (intermediate state during precipitation tl from fl at 250T)

CsCl (B2) type tetr. b.c.

A2 82 Bb

295 2.945; 3.007 (intermediate.state during precipitation a from p at 250°C) 2.81; 4.42 9.340 I 3.16 (high temp.) 3.16 (medium temp.) 1.64; 2.82 (42OoC; quenchable) 4.026; 4.107 (between2 7 0 4 5 ° C ; not quenchable) 3.948; 8.306 (7Oo0C) B2 3.001 82 2.977 B20 4.866 c1 5.91 5.41; 10.70; 3.95 (M=2) 0% B2 2.968 7.893; 7.854 0811 D8d 8.721; 6.428; 6.352; 94" 48' Au3Cu type 3.876 6.063; 4.872 (stable form) C16 82; 11.6 (metastable form, e.g. precipitated from supertetr. saturated solid solution) C1 (deformed into a-5.71; c/a=1.017 (metastable) tetr.) 6.88; 4.08; 9.87 (49-50 at. % Al; similar to -05'3 orthorh. monoct 7.06; 4.04; 1O.M); 90" 38' (4243 at. % Al; Similar to -D513) 8.69 (A=M.5 to 49.5; 38-41 at. % Ai) D81-3 -8.71 (A=51 for pscudo-cubic celk monocl) -081 -3

87 88 290

83 83 83 83 338

6-16

Crystal chemistry

Table 6.1 STRUCTURES OF METALS, METALLOIDS AND THEIR COMPOUNDS-cOnrimed Element or Structure type

compound

Lattice comants, remarks

Group IIIh AI, Ga,In, Tl-continued 8.685 to 8.704 (A=52.2 to 51.8; 31-35 at. % Al) C b A L (Y) 083 Cu,Al A3 2.60; 4.22 (Kurdjumow’s martensitic ?‘-phase) 4.51; 5.20; 4.22 A3, : D (B) A2 (>570 “C)2.94 (A) D4 (-300°C) 5.84 (unstable) -A1 (?) ( -440°C) 6.06 6.38; 625; 3.41 3.253; 4.9470 6.79 7.30 4.60 3.24; 4.38 (< -300°C)

337 83

293

(e-3OoOC) (> -300OC; ranging from -20-50 at. % In) (at -300"C, between B" and p; blase.1) 8.27; 3.42 (e300°C) 5.89; 4.76 9.44 4.461 4.695 9.18 4.39: 5.30 ---, ---3.09 (> 760°C) 4.54; 4.34 ( < 840°C; constant &er Hellner90; Makarowgl has a=5.20; c=4.34) 4.19; 5.15 5.32; 4.24 9.42 4.52; 5.49 3.25 4.06; 3.79 9.42 6.35 3.93; 3.87 4.53; 5.51 4.28; 5.25 9.24 (>61O'C) 8.97; 9.14 ( ~ 6 3 0 ° C fondants ; and symmetry derived by powder method Reynoldsg*;structure is said to be similar to D8,-,-type. Similarity to €38-typewas propond by Hellnerg3)

291 291 292

342

6-18

Crystal chemistry

Table 6.1 STRUCTURES OF METALS, METALLOIDS AND THEIR COMPOLiNDS-cmtimred

Element or compound

Structure type

Group IIIb; Al, Ga, In, "l-contimred CuJn A2 Cu,MnIn L2, C.C. pseudo orthorh. Lao hex. A3 A2 B2 832

B2 c22 D8g L12

B2

B2 A3 82

B2 L1, B2

Lattice constants, remarks

Refs.

3.046 6.181 4.29; 10.57; 3.55 (a90.54"; 890.00";~90.17')

80

5.872; 4.735; 5.150 3211 2; 2.992 8 3.4566; 5.5248 (~230°C) 3.879 (2230°C) 3.42 7.41 3.63 8.11; 1.34 15.17; 7.30; 6.16 4.79 3.85 4.02 3.45; 5.52 3.91 3.89 4.748 3.86

88

-

L60 B35 A2 AI B2 A2

4.12; 3.84 5.61; 4.64 3.82 4.66 (perhaps with superstructure) 3.35 3.81

Group IWx Si, Ge, Sn, Pb Si A4 NaSi, tetr. Mg,Si c1 casi, c12 CaSi B. Ca,Si C23 mi, C32 LaSi2 cc CeSi, cc PrSi, cc NdSi, cc SmSi, cc YSi Bf YSi, C42 TiSi 827 TiSi, c49 Ti& D8, Zr,Si C16 Zr,Si, C16 ZrSi, c49 HfSi, a 9 ThSi, cc USi, (a) cc C32 USi ()' 827 U3Si2 DSa U,Si Doc NpSi, Cc PuSi, C32 VSi, C40 V,Si A15 V,Si, D8s NbSi, C40

5.430 6 4.98; 16.1 6.34 10.4; 20" 30' 3.91; 4.59; 10.80 7.661; 4.799; 9.002 4.38; 4.82 4.27; 13.72 4.14; 13.81 4.14; 13.64 4.10; 13.53 4.04; 13.33 4.25; 10.52; 3.82 (M=4) 4.05; 3.95; 13.22 6.544; 3.638; 4.997 3.6; 13.76; 3.60 7.47; 5.16 6.56; 5.36 1.87; 5.54 3.72; 14.69; 3.66 3.69; 14.46; 3.64 3.85; 4.06 5.65; 7.65; 3.90 7.33; 3.90 6.02; 8.68 3.96; 13.67 3.884; 4.082 4.56; 6.36 4.71 7.12; 4.832 4.79; 6.58

64

292 342

IO2

294

295 296 94

95,96 95 94 94

99 100

Structures of metals, metalloids and their compounds

6-19

Table 61 STRUCTURES OF METALS, MJZTALLOIDS AND THEIR COMPOUNDS--cwUinued ~~

Elor compound

Structure type

~

Lattice constants, remarks ~

Group 1% Si, Ge, Sn, Pb-continued Nb,Si, 088 TaSi, C40 CrSi, C40 820 CrSi Cr,Si A15 c11 MoSi, A15 Mo,Si Mo& 088 c11 WSi, tetr. Mn,Si, MnSi BZO Mn,Si, 088 A2 Ma,Si c11 Re& FeSi, tetr. FeSi Brn Fe,Si, 088 fe,Si CoSi, c1 CoSi B20 Co,Si c37 Nisi, c1 Nisi 820 Bd Nisi 88 Ni,Si (0) C23 (6) (Bll L12 tetr. Ru,Si, B2 RuSi (1) B20 (2) B20 Ru~l.o-0.1 RhSi B20 C23 Rh,Si orthorh. Rh,Si, 88 Rh& 831 RhSi 831 PdSi c22 Pd,Si tetr. 0s,Si2 B2 Ossi BC tetr. IrSkI.3 Ir,Si Do, C23 Ir,Si Ir& IrSi, Ptsi

R,Si Pt,Si BeZrSi Pd4A1,Si cU15Si4 (8) Cu,Si

-

Cu,Si Cu,,MgbSi, Cu,SiMg,

AlNaSi AI,,Cr,Si, Al,Mn,Si, Al,Mn,Si AlFeSi ( a ) Al,,Fe,Si, A1,FeSi

B8, 4

8

831 L'2, c22 B8* B20 0% A13 A3 D8a C14 C36 C38 cubic cubic Al,,Mn,, E9c AI,,MnJ hex. cubic monocl.

-

Rafs. 100

7.52; 5238 4.771 6.55 4.42; 6.35 4.62 4.56 3.19; 7.83 4.89 7.27; 4.992 3.20; 7.81 5.51; 11.42 4.55 6.90; 4.80 2.85 3.12; 7.66 269; 5.13 4.49 6.73; 4.70 5.64 5.36 4.44 7.10; 4.91; 3.13 5.40

101 100 101

4.446

5.62; 5.18; 3.34 3.81; 4.89 (>12oo"C) 7.03; 4.99; 3.72 (e12GO'C) 3.50 (< 1040°C) 5.52; 4.46 2.909 4.703 4.703 4.672 7.418; 5.279; 4.005 10.07; 5.30; 3.88 3.94; 5.047 6.36; 5.53; 3.06 6.12; 5.59; 3.31 6.48; 3.42 5.57; 4.41 2.960

1

5.22; 7.95 7.615; 5.28; 3.98

I

3.96; 5.12 4.31; 6.61 5.92; 5.58; 3.60 3.93; 5.91 6.16; 3.45 3.71; 7.19 4.830 9.69 6.21 2.57; 4.18 11.67 (A=116) 5.00, 7.87 5.0; 16.0 (>870"C) 4.13; 7.40 10.917 12.63 7.51; 7.74 12.3; 26.2 12.52 6.11; 6.11; 41.4; 90" @&o-tett.)

106 106 106

297

107 293 108 297 297 293

109

I10 8 83

111

112 113

6-20

Crystal chemistry

Table 6.1 STRUCTURES OF METALS, M E T A U I D S AND THEIR COMPObWDS--eontimed

Element or Compound

Structure type

Lattice constants, remarks

Re$.

Grouo Ivb: Si. Ge. Sn, Pb-continued

Al,deSi, AINi,Si A1,FeMg3Si A1,Cu,MgsSi, Ge Mg,Ge GaGe CaGe, Ca,Ge Y5Ge3 CeGe,

tetr. Ga,Pd 820 E9b tetr. A4 c1 BC

c12 C23 088

M e 2

cc cc 827 c54

=*

c49

TiGe Tie, Ti,Ge, Zr,Ge3 Hf,Ge, aThGe, ThGe, Th3Ge ThGe, V,Ge

NbGe,

TaGe, Ta,Ge, Cr3Ge CrGe Cr,Ge, Mo,Ge

088

088

D8s cc BI D5a cubic A15 C40 C40 08,

A15 820 D8m

A15

Mn5-3

088

IWn3.2SGe

DO19

Fa2 FezGe CoGe CosGe8 C f i 2

NiGe Ni,Ge Ni,Ge GeRu Ge,Ru, PdGe Pd,Ge OsGe,

w% IrGe,

Ir,Ge, IrGe PtGe PtzGe Pt,Ge Pt3Ge2

Pt,Ge3 PtGe, PtGe Cu,Ge(l) (2) (3) a s Co,GaGe,

A3 C16 88

D7a D2b Ce 83I 88 L12 820 tetr. 831 c22 cg

tetr.

hex. D8f 831 B31 CU

L1,monocl. B31 831 c35 A1 DO8

DOa A2 A3 B20

6.13; 9.46 4.55 6.62; 1.92 10.30; 4.04 5.6514 6.31 4.001; 4.575; 10.845 10.49; 21" 42' 8.47; 6.35 4.202; 14.153 4.25; 13.94 3.80; 5.22; 6.82 8.58: 5.02: 8.85 7.54; 5 2 2 3.80; 1501; 3.76 1.99; 5.59 7.88; 5.53 4.106; 14.193 6.033 7.911; 4.170 11.72 4.76 4.96; 6.77 4.95; 6.74 7.58; 5.23 4.645 4.18 9.41; 4.78 4.93 5.053; 7.184 5.35; 4.37 (at low temp.) (at high temp.) 5.90; 4.94 4.03; 5.02 (FeFe,,,Ge) 11.64; 3.80; 4.94 @=lOl.lW; M=8) 7.64; 5.814 (A=26) 5.65; 5.65; 10.8 5.80; 5.31; 3.42 3.95; 5.04 ( N i & e ) 3.56 4.546 5.709; 4650 6.25; 5.71; 3.47 6.67; 3.52 8.995; 3.094; 7.685 (8=110" 10'; M=4) 5.62; 18.31 6211; 7.77 8.74 6.27; 5.60; 3.48 6.08; 5.12; 3.69 667; 3.52 7.931; 7.767; 1.767 @=W.OS) 7.544; 3.423; 12236 3 x 5.48; 3.37; 6.22 6.18; 5.76; 2.908 3.91 4.16; 7.50 (> - 6 W C ) 2.64; 5.45; 4.19 (< -600°C) (27-28 at. % Ge;between620-700"C; superstructurewith holes and ar=3u). 4.168 2.65; 428 4.63

83

114 102 298 299

300

115

298

301

115

337 115

293

302 108

293

108

293

83

Structures ofmetals, metalloids and their compounds Table 6.1

6-21

STRUCTURES OF METALS. METALLOIDS AND THEIR COMPOUNDS--continued

Ekment or

Strucnae type

compound

Ivb: Si, Ge, Sn, Pb-eonrinued E20 Ni50Ga4,Ge, Pd,ALGe B20 RhiGaCe, 820 A4 Sn grey A5 metallic -DS,, orthorh. Na,,Sn, C1 Mg& CaSn Be CaSn, LIZ LaSn, LL CeSn, LL PrSa, L1a Ti&, D88 Ti& DO19 Hf,Sn, 088 ThSn, =I2 USn, LIZ MnSn, C16 Mn,Sn, 88 88 Mn,Sn -Mn,,Sn, DO19 C16 FeSn2 B35 FeSn monocl. Fe,Snz Fe,,Sn*, 882 Fe3Sn Do,, C16 CoSn, 835 CoSn 88 Co,Sn, D510 Co,MnSn Do3 D7a Ni,Sn, 88 Ni,Sn, tetr. A3 Ni,Sn

Lattice constants, remarks

Refs.

4.64 4.86 4.822 6.4892 (113.2"C) 5.831 8; 3.181 8 (> 13.2"C) 9.79; 22.78; 5.65 (A = 30 to 40) 6.75 4.349; 4.821; 11.52 4.73 4.77 4.71 4.70 8.05; 5.45 5.92; 4.76 8.39; 5.82 4.718 4.62 6.65; 5.43 4.37; 5.48 (at low temp. superstructure) 4.39; 5.46 5.67; 4.53 (< 1000°C) 6.5% 5.31 5.29; 4.44 13.53; 5.34; 9.20, 103" ( M = 8 ) 4.23; 5.21 5.46; 4.36 (760-900°C) 6.35; 5.44 5.27; 4.25 (high temp.) 4.12; S.18 (c55o"C), 8.18; 7.08; 5.20

83 83 83

5.991

116

&OUp

Ni4Sn NiZMgSn Ni,MnSn Ru3Sn, RhSn -Rh3Snz RhSn, (1) (2) (1)

(2) PdSn Pd,Sn, Pd,Sn Ir3Sn, IrSn, IrSn PtSn, PtSn, h2Sn3 hSn Pt,Sn Cu&,

L 21 DO3

D8f 820 E8 C16 ce

CJ

PdSn,

PdSn,

tetr. (?)

D4

ce

c, -B31

(monocl. deformed) 331 88

L1,

2 B8 D1, c1

2 W 1 9

(d

-Cu3Sn

(E)

B8 A3 -A3 (orthorh. deformed)

114

304 292

-

12.20; 4.06; 5.22; 105" 3' 4.08; 5.18 (at low temp. superstructure 9.20; 8.58 (A=.%) (>9oO'C) ( > 900°C) ( 50OoC) 6.32; 11.97 ( ~ 5 0 0 ° C ) 6.38; 17.88 6.38; 6.41; 11.47 6.48; 12.15 6.55; 24.57 (lowtemp. mod.) 6.18; 3.93; 6.38; 88.5" (quenched from high temp.) 6.13; 3.87; 6.32 4.39: 5.70 3.97 9.36 6.34 3.99; 5.57 6.38; 6.41; 11.33 6.43 4.33; 12.96 4.10; 5.43 4.00 4.19; 5.09 276; 4.32 5.51; 38.18; 4.32

I16

117 118 117 118

I19 119 120

6-22

Crystal chemistry

Table 61 STRUCTURES OF METALS, METALLOIDS AND THEIR COMWUNDS--continwd E h t or compound

Structure type

~ O U1% P Si, Ge, So,Pb-continued -A3 (orthorh -Cu,Sn (E') deformed) orthorh. yCu3Sn -08, Cu;,Sn; -D8, "Cu41Sn11 A2 Cu17Sn3(8) orthorh. (8") Cu,MnSn L21 (Cu,Ni)& 4 Ag$n A, A3 -Ag,Sn Ag&fg3Sn L21 Dlc AuSn, C46 AuSn, AuSn B8 A3 Au,Sn ZnSn, c54 CdSn (B) hex. CdSn, hex. A3 *HgSn15(1) orthorh. (2) -InSn, A5 hex. InSn, In,Sn L1, (deformed into tetr.) Pb A1 LiPb B2 Li,Pb Do, Li7Pb2 hex. Li,Pb, monocl. C2/m Li,,Pb3 0 83 f.c.c. J-izzPbs Na2Pb, L12 NaPb tetr. Naid'b4 D8, C14 KPb, c1 ~. MgzPb CaPb, LIZ SrPb, LIZ (deformed into tetr.) LaPb, LIZ CePb, LIZ PrPb, L12 Ti,Pb MI9 Zr,Pb, 08, UPb, LIZ

-

ThPb, RhPb, PdPb, PdPb Pd,Pb, Pd,Pb IrPb PtPb4 PtPb Pt,Pb A&Pb AuPb, Au,Pb -In,Pb n3Pb Tl,Pb

LIZ C16 C16 monocl. B8

LIZ

88 D1d

B8

A3 C16 C15 A6 A1

A1

Lmtice constants, rematks

Ref.

9.993; 5.5% 8.46

121

4.772; 5.514; 4.335 (700'C) 7.32; 1.85 D'& (A=26) 17.92 2.97 (stable >6 W C ) 4.55; 5.36; 4.31 (A=8; at low temp.) 6.15 5.59 2.99; 5.14; 4.71 2.94; 4.77 6.60 [structural formula: Ag,Mg(Mg, As, Sn)] 6.43; 6.47; 11.58 6.845; 6.990; 11.760 4.31; 5.51 2.92; 4.77 9.55; 5.63; 9.90 3.226 3; 29% 3 3.21; 2.99 3.20; 298 orthorh d d o d on the Sn-poor end 3.20; 5.55; 2.98) 3.181; 5.827 3.21; 2.99 4.94; 4.40

I22

4.9502 3.52 6.687 4.751; 8.589 8.240; 4.757; 11.03; 8=104" 25' (Mn2) 10.08 20.8 (A4=16) 4.87 10.580; 17.746 13.29 6.66; 10.76 6.80 4.89 4.96; 5.03 4.89 4.86 4.86 5.962; 4.814 8.51; 5.85 4.79 (because U and Pb scatter similarly no decision between LIZ and Al-type was possible) 4.856 6.65; 5.85 6.84; 5.82 7.08; 8.43; 5.56; 71" 4.447; 5.71 4.01 3.99; 5.56 6.65; 5.97 4.25; 5.46 4.05 2.92; 4.16 7.31; 5.64 7.91 4.85; 4.50 4.88 strong indications that ordered structures PbTI, and 4.86) Pbll, exist

80 123 64 63

63

124 124 125 305 126 127

128 123 292

129

Structures of metals, metalloids and their compounds

6-23

Table 6.1 STRUCTURES OF METALS, METALLOIDS AND THEIR COMPOUNDS--continued Element or compound

Stmture type

Group Vb: As, Sb, Bi As A7 Li,As Do,, monocl.P:, LiAs Na,As Dol, K,As DO*, WAsz D53 c1 MgLiAs B1 LaAs CeAs 81 PrAs B1 B1 NdAs Bi ZrAs ZrAs, C,, B8i TiAs Bi 831 CrAs C38 Cr,As B8 -MnAs (1) 8 31 (2) C38 Mn,As Mld Mn,As FeAs, C18 FeAs B3 1 Fe,As C38 CoAs, Do2 COAS, C18 CoAs B31 NiAs, Do, C18 MAS, C46 B8 NiAs tetr. Nil,& hex. Ni,As2 c2 PdAs, c2 PtAS, cubic Cu,As Do2I

Cu,As CuMgAs Ag,As AgMgAs ZnAs, Zn3As2 ZnLiAs ZnNaAs ZnCuAs ZnAgAs Cd,As, AlAs AiLi3Asz GeAs, GaAs InAs SnAs Sn,As, Sb Li,Sb (u)

-

-

(B)

NaSb Na3Sb

A3 C38 A3 c1 orthorh. 059

c1

c1 c1 Cl D59 83 -c1 orthorh. Pbam B3 B3 B1 cubic, deformed A7

Do,, Do, LiAs

DO1 8

Latrice constants, remarks 4.1359; u=54" 7' 4.39: 7.81 5.79; 5.24; 10.70 (8=117.4"; M=8) 5.09: 8.98 5.78; 10.22 12.33 6.21 6.13 6.06 6.00 5.96 3.80; 12.87 6.80; 9.02; 3.68 3.63; 6.14 3.64; 12.3 6.21; 5.73; 3.48 3.61; 6.33 3.72; 5.70

Refs.

306

307 130 130

131 132

3.76; 6.27 3.78; 3.78; 16.26 2.86; 5.20; 5.92 6.02; 5.43; 3.37 3.63; 5.97 8.195

-

5.96; 5.15; 3.51 8.26 3.53; 4.78; 5.78 (Rammelsbergite) 5.74; 5.81; 11.41 ( M m 8 ) (para-Rammelsbergite) 3.61; 5.03 6.84; 21.83 (Mmll) 6.80; 12.48 5.97 5.96 9.59 ( M = 16) (Domeykite) 7.09: 7.23 (synthetic) 2.58; 4.22 (part of Algodonite and Whitneyite) 3.95; 6.23 2.89; 4.72 6.24 1.72; 7.99; 36.28 (M=32) 11.78; 23.65 5.91 5.90 5.87 5.90 8.95; 12.68 5.62 11.87; 11.98; 12.11 [orthorh, deformed (D;;) superstructure] 14.76; 10.16; 3.728 (M=8) 5.6534 6.050 84 5.72 2.91; 88-54' (A=l) 4.54067; a=57"7' 4.70; 8.31 6.56 6.80; 6.34; 12.48 (8=117.6') 5.36; 9.50

133 134 134

308 309 309

306

6-24

Crystal chemistry

Table 6.1 Element m compound

STRUCTURES OF METALS,METALLOIDS AND THEIR COMPOUNDS-continued

Structure type

Lattice constants, remarks

Group Vb: As. Sb, Bi-continued K3Sb 6.03; 10.69 Do18 Cs3Sb 9.147-9.1 88 832 4.57; 7.23 Mg3Sb2 D52 MgLiSb 6.61 C1 LsSb B1 6.48 CeSb B1 6.40 PrSb B1 6.35 BI NdSb 6.31 TiSb, C16 6.65; 5.80 B8 TiSb 4.06, 6.29 Ti,Sb A15 5.218 6 D8m 10.465;5.2639 (M=32) Ti,Sb 5.95; 4.80 w,9 ThSb B1 6.305 9.353 Th3Sb.3 073 ThSb, C38 4.344; 9.154 VSb, C16 6.54; 5.62 V3Sb A15 4.932 (M=2) Nb$b A15 5.262 ( M = 2 ) CrSb, C18 3.27; 6.02; 6.86 CrSb B8 4.11; 5.47 MnSb B8 4.12; 5.78 Mn,Sb C38 4.078; 6.557 FeSb, C18 3.19; 5.82; 6.52 FeSb to Fe,Sb, B8 4.064.12; 5.13-5.17 CoSb, C18 3.21; 5.78 CoSb B8 3.87: 5.18 CoMnSb c1 5.89 NiSb, C18 3.21; 5.63; 6.23 NiSb B8 3.91; 5.13 Ni,Sb tetr. 5.79; 6.00 (A%15) (Ni,Sb,?) Ni3Sb M)n 5.96 NiMgSb 6.04 c1 NizMgSb 6.05 NiMnSb c1 5.90 NizMnSb 6.00 u 1 RhSb B31 6.32; 5.94; 3.87 PdSb, c2 6.44 PdSb B8 4.07; 5.58 B8 PdsSb3 4.44; 5.77 IrSb, 6.6; 6.5; 6.7; B=115" El, c2 PtSb, 6.43 PtSb B8 4.13; 5.47 Cu2Sb orthorh. 278; 4.77; 4.38 C38 3.97: 6.07 C u S b b) tetr. (?) (>440"cx9.01; a57 C~SS'JZ 0 DO3 (tetr. deformed) ( -SOOT) 3.08; 327 3.29; 14.0; 3.13 3.28; 0.867; 3.16 5.78; 4.86 2.97; 3.07 2.98; 13.02; 2.95 2.986; 13.02; 2.952 2.96; 7.81; 2.94 5.46; 10.64 5.18; 4.31 4.26; 7.38; 14.71 3.01; 20.93 3.05; 3.1 1 3.11; 16.97 5.54; 4.74 2.98; 13.87 3.02; 3.05 3.19; 8.40; 3.07 (>1850°C) 3.12; 16.93 5.56; 4.74 3.03: 12.86: 2.96 4.15; 5.56; 2.98 5.15; 4.21

B1 C32 Dle

% 07, 2 2 07b

4

cubic C32 07b

2 6 C32 D7b 07b

Bf tetr. C16

Bf

D8i C32 Bg C16 D8h C32 Bf

BB

C16

D 7b Mn,B

827 C16

Refi.

220

315 316

.147 149 (149, 150) 147 151 151 148 (149, 150)

317

152

318 153 153 153

Structures qfmetals, metalloids and their compounds

6-27

Table 6.1 STRUCTURES OF METALS,METALLOIDS AND THEIR COMPOUNDS-continued Element or compound

Structure type

Lattice constants, remarks

Metalloids, etc.: B, C, P, N, Po, Te. Se, S-conrinued Mn,B D1f 14.53; 7.29; 4.21 ReB, hex. 2.900; 7.478 (M=2) 4.05; 5.50; 2.95 827 FeB5.10; 4.24 Fe,B C16 3.95: 5.34: 3.04 827 COB 5.01; 4.21 Co,B C16 4.41; 5.23; 6.63 Co,B WII 4.98; 4.24 C16 N1,B 4.389; 5.211; 6619 Ni3B Dol 1 b.c.c. 7.02 RUB orthorh. 2.865; 4.045; 4.645 RUB, 5.42; 3.98; 7.44: (M=4) orthorh. Rh,B 6.48; 3.42 hex. PdP2 12.786; 4.955; 5.472 (8=97"2'; M=4) monocl. C2/a Pd,B, 5.463; 7.567; 4.852 Pd,B 41 2.871; 2.876 OsB Bh 7.03 cubic OSB 2.77; 2.95 %B 3.00; 3.25 c32 AIB, 8.881; 9.100; 5.690 (M-2) orthorh. Ah0 8.51; 10.98; 9.40; llO"54' ( M = 8 ) monocl. t. AIR,, (Mod.1) 10.28; 14.30 (A= 196) (Mod. 11) Mr. &Mo,B, 6.319; 12.713 hex. R3m B,Si 3.5609 (diamond) A4 C 2.461 2; 6.709 A9 4.97; 21.35 -A9 4.94; 17.45 -A9 4.926; 22.78 hex. 4.95; 17.99 hex. 4.945: 17.76 hex. ,

c1 ietr.

hex. c11 c11 c11 c11 b.c.c. c11 c11 c11 B1 B1 B1 c11 cg

B1

c11 c11 c11 DSc B1 D5c B1 B1 L'3 B1 A2 hex. B1 hex.

Reb.

319

I

4.33 5.55; 5.03 ( M = + similar to ThC,?) 7.45; 10.61 ( M = 8 ) 5.48; 6.37 5.81; 6.68 6.22; 7.06 3.94; 6.572 8.803-8.819 5.48: 6.48 5.44: 6.38 5.41; 623 4.32 (TiCp.ahas a=4.26) 4.67 4.46 5.85; 5.28 6.53; 4.24; 6.56; 104" 5.34 (complete solid solution with ThC, at -2300°C Wilh~lm'~8) 3.51; 5.97 3.54; 5.97 3.55; 6.00 8.09 4.95 7.13 4.91 4.17 2.86; 4.54 4.424-4.457 3.301 2 3.12C2138; 4.957-4.974 4.430 M.4690 3.12; 4.95

154

154 320 155 321

339

322

323

156 157 159 160 161 162

163 324 163

6-28

Crystal chemistry

Table 6.1

STRUCTURES OF METALS, Mi3ALU)IDS AND THEIR COMPOUND.S-muinued

Element or compound

Structure type

Lattice constants, remarh

Metalloids, etc.: B, C, P, N, Po, Te,Se, %ontitrued Nb3cto LA -4.40, depending on composition Nb4C E1 TaC 4.45 Ta2C JY3 3.09; 4.93 Ta to Taco,,, A2 3.306 flac0.38to C6 3.101; 4.937 TaC0.5 yTaC0.,, to B1 4.420 TaC0.5 6TaC0.,, to hex. 246; 6.69 TaC0.s D10, 4.526; 7.01; 12.14 Cr,C, hex. 13.98; 4.52 (Am80) (isom.with Mn,C3) Cr7C3 1l.W 5.52; 2.82 cr3cz D510 10.64 cr23c6 084 2.90; 2.81 MoC (Y) Ex 293; 10.97 (Y') 4 61 MoC, _= 4.27 (perhaps only as substructure) E3 3.01; 4.74 Mo,C Bh wc 290; 283 299; 4.71 c3 wzc D8, ordered w7.cr2 I c6 hex. 13.87; 4.53 (Am 6 z)(isom. with Cr,C3) Mn7C3 10.59 Mn23C6 D84 ortborh. 9.06; 15.69; 1.93 (M=4); or hex. with a'=% c'=e, M'=8 Fe20C9 2.76; 4.35 hex Fe,C Fe,C 4.52: 5.09; 6.75 (Cementite) DO,1 hex. ('E') 4.767: 4.354 hex. SFeC Fe (+0.25% C) L2 (deformed tetr.) 2842; 3.008) at low temp. (+0.75% C) L2 (deformed tetr.) 2.850: 2939 A1 Fe ( + C ) 3.6 (Austenite at high temp.) el, Fe6A12C 3.7E-3.78 Fe3Mo,C 11.1 E93 08, ordered 10.63 Fez,MozC, Fe3W3C 11.087 E93 D8,ordered 10.54 Fe21w2c6 hex. 7.85 (isom.Co, Ni-compounds) -7.85; Fe3w 1OC4 cubic -11.25 (isom.Co, Ni-wmpounds) Fe3w6c2 cubic f.c. (Cr,Fe),C 3.62> 1O O O T (below 1OOO"C Cr7C3-type) C18 C0,C 2.910; 4.469: 4.426 C0,C 4.483; 5.033; 6.731 *I 1 co3w,c 11.01 E93 hex. 1.286; 1.286 co3w,c4 hex. 7.85; 7.85 (isom.Fe,Ni-compounds) c03w, Oc4 11.25 c02w6cZ E93 Ni,C hex. 2.628; 4.306 11.217 Ni3W3 (8) E93 10.873 Ni$W6C E93 Ni3W,C2 cubic f.c. -11.25 hex. -7.85; -7.85 Ni3W10C4 hex. 7.818 3; 7.818 0 Ni3W16C6 3.33; 24.94 AIL3 07, A1Mn3C El, 3.83 -AlFe3C El, 3.7M.78 63 Sic 4.35 there are several other modifications described B5 3.08; 10.08 with the ES-type 5.60; 1212 Dlg DE 12.5s; 10.18 (Ms4.31) (diamond-type boron) monocl. 17-a4;25.0; 10.26; =90" (?) (graphite-type boron) cubic 11.31 ( A = 6 6 ) p (red) (white) I432 18.51 (A =224; other possible space groups: lm3m and I43m) 4.26: 7.58 Li,P

efi

164 164 164 164

165 1.66 167 325

-

-

-

}

326 168 169 170 170 170

Structures of metals, metalloids and their compounds

629

Table 6.1 STRUCTURES OF METALS, MEZALLOIDS AND THEIR COMPOUNDS-continued ~~

Element or compound

Structure type

Lattice

consumts, remarks

Refs.

Metalloids, mc.: B, C, P, N, Po, Te. Se, Scontinued Na,P 4.998; 8.80 Dol, 053 D53

m3p2

c1

MgLiP AIP GaF InP LaP CeP PrP NdP Th8'

B3 B2

B3 B1 B1 B1 B1 073 B1 073 Bl 073

n4p3

u3p4

UP Np3P4 v3p CrP Cr,P WP

s:

B31

s:

B8 (orthorh.

10.15 12.01 6.023 5.42 5.4505 5.868 75 6.01 5.90 5.86 5.83 8.60 5.82 8.20 5.59

309 309

-

(similar to Cr,P) 5.93; 5.36; 3.12 9.13; 4.56 [isom. with (V, Mn, Ni, Fe),P] (?)

deformed) MnP Mn,P Mn3P

B31 C22

00,

FeP, FeP Fe,P Fe3P COP Ni,P Ni,P3 Ni3P Rh2P Ir,P PtF, CUSP ZnP, Zn3P2 ZnLiP CdP, Cd3PZ AIP AlLi3P, GaP InP Li,N Mg3N2 MgLiN

Ca3N,(4 ScN LaN

CeN PrN NdN EuN GdN SmN

YbN TiN TiLi,N,

(B)

C18 8 31 c22 DO* 831 C23 c22

cubic b.c. (?) DO, c1

c1 c2 0011 tetr. D59 c1

tetr. D59 83

orthorh. B3

B3 C32 D53 D53 C1 D53

pseudo-hex.

B1 B1 B1 B1

E1 B1 B1 B1 B1 B1 E9d

5.91; 5.25; 3.17 6.07; 3.45 9.16; 4.59 (isom.Cr,P) 2.13; 4.98; 5.66 5.78; 5.18; 3.09 5.93; 3.45 9.10; 4.45 (isom. Cr3P) 5.59; 5.07; 3.27 6.66; 5.71; 3.53 5.85; 3.37 8.63 (M=6) 8.92; 4.39 (isom. Cr,P) 5.51 5.54 5.68 6.9% 7.14 5.07: 18.65 (isom. with CdP,) 8.10:-11.45 5.77 5.28; 19.70 (isom.,with ZnP,) 8.75; 12.28 5.42 11.47; 11.61; 11.73 (orthorh. deformed, with superstructure) 5.44 .. . 5.86 3.66: 3.88 8.13 9.95 4.91 11.40 (high temp. mod.) 3.55; 4.11 at 300°C (low temp. mod.) 4.44 5.28 5.01 5.16 5.14 5.007 4.99 5.048 1 4.785 2 4.24 9.73

172 172 172 173

6-30

Crystal chemistry

TaMe 6.1

STRUCTURES OF METALS. MMALLOIDS AND THE4R COMPOUNDS-continued

Element or compound

Structure type

Lartice com&mts, remarks

Metalloids etc.: B,C, P. N. Po. TI%Se. S-cmtinrced B . . . . 4.63 3.88; 6.18 DS2 5.32 c1 10.70 D53 B1 4.89 B1 4.89 4.90 B1 4.13 E1 4.07 B1 2.84; 4.55 [superstructure d = 43; e3 similar to (Fe,Ni, Co),N] CoIzN 81 4.38 2.93; 5.45 88, 2.95; 11.25 4.38; 8.68 4 L'3 3.05; 4.96 5.181; 2902 hex. E3 3.06; 4.96 4.14 B1 2.76; 4.46 L'3 2.86; 2.80 Bh 4.18; 4.02 E6 4.17 E1 4.12 E1 B1 4.12 (4 W in simple cubic all; perhaps a'=4 x4.12) 4.19; 4.03 E6 3.85 El 3.92 E1 5.52; 4.83; 4.43 (deformed A3-type with superstructure; orthorh. detailed description see Ja~k"'~~'') hoc. L'3 2.76; 4.43 2.72; 4.39 complex superstructures; see Jack"' hex. 2.66; 4.34 hex. 3.80 L'1 5.72; 6.29 D2g 2.84; 4.63; 433 E3 (orthorh. deformed) C1.8 E3 266; 4.35 (a* =2a) C32 3.74; 3.62 E3 267; 4.31 (isom. c-Fe,N) C32 3.77; 3.52 3.81 W 9 C32 3.68; 3.77 9.74 D53 4.89 (ordered) c1 10.79 D53 3.10; 4.97 B4 E9d 9.48 3.18; 5.17 B4 9.61 E9d 3.53; 5.69 84 7.758; 5.623 hex. DgP3lc 7.603; 2909 hex. C&P6/3rn 5.498; 8.877; 4.853 orthorh hex. 4.534; 4.556 orthorh. 13.38; 860;7.74 9.43 E9d 13.84; 9.06; 8.18 orthorh. E9d 9.66 Bk 2 5 9 6.66 3.28; 21.55 E94 Ah 3.35 3.37; 98" 13' Ai

174

1

---

327

173 173

Structures of metals, metalloids and their compounds

6-31

Table 6.1 STRUCTURES OF METALS, METALLOIDS AND THEIR COMPOUNDS-continued ~~

Element or compound Metalloids. etc.: B. PbPo Te Li,Te Na2Te K,Te K2.67(Sb, Te) K d T e , Sb) Kz.zs(Te,Sb) BeTe MgTe CaTe SrTe BaTe EuTe YbTe TiTe, TiTe Ti,Te, UTe U3Te4

me,

-

VTe CrTe MoTe, me, MnTe, MnTe FeTe, FeTe CoTe, CoTe NiTe, NiTe RuTe, PdTe, PdTe QsTe, PtTe, CuzTe Cu,Te CuTe Cu,-=Te AgzTe (Au, Ag)Te,

AuAgTe, ZnTe CdTe HgTe Ga,Te3 Te,AI, InTe In,Te3 TeTl Te3T1, y-Te3T1, SnTe PbTe As,Te3 Sb,Te3 Te,SbTl

Structure rype

Lnttice constants, remarks

Ref.

C P. N. Po. Te, Se. bcontimred Bl' ' A8 c1 c1 c1 c1 -c1 c1 83 84 B1 B1 B1 B1 B1 C6 B8 tetr. 14/mcg5 B1 D73 C38 88 B8 c7 orthorh.

5

c2

88 C18 B8 C6 C18 88 C6 B8 c2 C6 B8 c2 C6 Ch cubic Lc. orthorh. C38 c1 orthorh. monocL c34

--

C46 Elb B3 83 83 B3

-

B4

-

B37 83 b.c.tetr. monocl. b.c. tetr.

B1 B1 monocl. hex

-

4.456 6; 5.926 4 175 6.50 7.32 8.15 a continuous series of unit crystals between K,Te and K3Sb appears probable at high temp. 8.2 5.61 4.53; 7.38 6.34. 6.65 6.99 6.57 6.34 3.77; 6.54 3.83; 6.39 328 lO.lW, 3.7720 6.151 176 176 9.378 4.243; 8.946 3.81; 6.12 3.89-3.98; 5.91-6.21 329 3.519; 13.964 177 3.490; 6.282; 14.073 6.94 4.12; 6.70 3.85; 5.34; 6.26 3.80; 5.65 3.78; 5.40 3.88; 5.30; 6.30 3.88; 5.37 3.86; 5.30 3.96; 5.35 6.36 4.03; 5.12 4.13; 5.66 6.37 4.01; 5.20 4.24; 7.27 6.10 (A = 12) 80 80 3.10; 4.02; 6.86 3.98; 6.12 (> 150°C) 6.57 (high temp. mod) 13.0; 127; 12.2 (lowtemp. mod.) 5.98; 6.31; 5.56; 75" 24' (Hessite) 7.18; 4.40, 5.07; -90" (Calaverite) 16.51; 8.80; 4.45 (Krennerite) 8.94; 4.48, 14.59; 145" 24' 6.09 6.46 6.429 (Coloradoire) 175 5.89 4.07; 6.93 330 63,80 8.42; 7.12 6.16 12.950; 6.175 331 13.5; 6.5; 7.9 (8=73") 8.92; 12.63 6.28 6.44 (Altaite) 178 14.% 4.05; 9.92 B=97" 179 4.24; 29.90 8.177 (a=31" 24') 332

:$}

6-32

Crystal chemistry

Table 6.1 Element or compound

STRUCTURES OF METALS, METALLOIDS AND THEIR COMPOUNDS--eOntinued

Structure type

Lattice constants, remarks

Metalloids, e t c B, C, P, N, Po, Te,Sc,S-continued 8.137 (r=32" 18') Te,BiTI F~I 10.45; 24" 8' (Tellurobismuthite) Bi,Te, c33 4.365 9; 4.953 7 A8 9.05; 9.07; 11.61; 90" 46' Ak A1 1285; 8.07; 9.31; 93" 8' c1 6.01 6.80 c1 K,Se 7.68 c1 5.13 B3 BeSe 5.45 B1 MgSe 5.91 81 CaSe B1 6.23 SrSe 6.59 BaSe B1 8.40; 6.30 Y&3 D8 6.17 EuSe B1 5.87 B1 YbSe 3.54; 5.99 TiSe, C6 3.56; 6.22 TiSe B8 monocl. ZrSe, 5.41; 3.77; 9.45 (8=97.59 C6 3.79; 6.18 ZrSe, 8.804 U3se.i 073 11.33; 10.941; 4.06 U,% D58 4.98; 7.50; 9.38 ThSe, c23 11.56; 4.35 D8k Th,Se,, Th,Se, 11.32; 11.55; 4.26 D58 ThSe 5.86 B1 5.68, 4.06, 19.26: (d=7.25) monocl. use3 3.35; 6.12 C6 VSe,,, to VSe, VSe 3.58; 5.98 B8 3.60; 5.77 Cr,Se, B8 -B8 (monocl.) CrSe 55-58 at. % Se: 6.30; 3.60; 5.85; 90" 30' B8 50-54 at. % Se: 3.68; 6.02 CrNaSe, 3.71; 2029 F51 -F5, 3.44; 24.2 CrK0.& CrRbSe, 3.43; 26.9 F51 c7 3.29; 1297 WSe, MnSe, c2 6.42 5.45 B1 MnSe (a) .. . 5.82 B3 (B) 4.12; 6.72 B4 (Y) C18 FeSe, 3.58: 4.79: 5.72 FeSe 88 to B8 monocl. 3.64; 5.96 6.25; 3.58; 5.81; 91') 50-56 at. % deformed B10 44 at. % Se: 3.77; 5.52 Cose, c2 5.85 CoSe B8 3.61; 5.28 NiSe, c2 6.02 NiSe B8 3.66; 5.33 B13 9.84; 3.18 RuSe, e2 5.92 RhSe, c2 6.015 (63.6%): 5.985 (71.4yJ c2 5.93 OsSe, C6 3.72 5.06 PtSe, CuSe -818 3.94; 17.25 (superstructure a'= 124 (Klockmannite) Cu,Se c1 5.84 (Berzelianite) c1 (>133"C), 4.98 (at 170°C) (Naumannite) Ag*Se ZnSe B3 5.66 ZnCr,Se HI1 10.44 ('normal' Hl,-type) CdSe B3 6.04 B4 4.30; 7.01 CdCr,Se, HI, 10.72 ('normal' Hl,-type) HgSe 83 6.074 (Tiemannite)

Ref.

333

340

334 334

180

181

--

182 182 175

Structures of metals, metalloids and their compounds

6-33

Table 6.1 STRUCTURES OF METALS, METALLOIDS AND THEIR COMF'OUNDS-continued ~

Element or compound

Structure type

Lattice constants, remarks

Metalloids, efc.: B, C, P, N, Po,Te, Se, S-continued GaSe hex. 3.73: 15.89

~~

Refs.

63. 184,

Ga2S3

In,Se3

TlSe GeSe,

G& SnSe PbSe Sb,Se, Bi,Se3 S (orthorh.) (monocl.) (rhomb.) (fibre) Li,S Na,S KZS Rb,S

BeS MgS CaS SrS BaS ta;S3 Ce2S3 CeA CeS DYS AcA Tisz

ns2 ThAz ThZS3

ThS ZrS, u2s3

us

NP2S3 PU83

PUS Am2S3 vs to VO.88 TaS, CrS

CA

CrNaS, CrKS, CrRbS, MoS,

ws,

MnS, MUS

MnCr2S4

-

hex. 3.74; 23.86 83 5.43 h.c.p. (room temp.) 4.01: 19.24 837 8.02; 7.00 orthorh. 7.003; 12.221; 23.04 B16 4.38; 3.83; 10.79 (M=4) B16 4.46; 4.19; 11.57 B1 6.14; (Clausthalite) 11.58; 11.68; 3.98 D58 c33 4.14; 28.59 (A= 15) A16 10.464; 12.866; 24.486 C:h 10.9; 10.9; 11.0; 83" 16' (A=48) 10.9; 4.26 (A= 18) C19 monocl. 26.4; 9.3; 12.3; 79" IS' (C=9.3=fibre axis; A=112) 5.71 c1 . . 6.53 c1 7.39 c1 7.65 c1 B3 4.86 B1 5.19 81 5.69 (Oldhamite) 6.0 1 B1 6.37 B1 8.71 073 8.617 D73 8.608 D73 5.77 B1 B1 5.96 8.97 073 3.40; 5.69 C6 4.26; 7.25; 8.60 C23 11.04, 3.98 D8k 10.97; 10.83; 3.95 D58 B1 5.67 C6 3.68; 5.85 10.39; 10.63; 3.88 D58 B1 5.47 10.3; 10.6; 3.85 D58 8.44 073 B1 5.53 8.43 D73 B8 3.36; 5.81 C6 3.40; 5.90 -a 50.0-52.4 at. % S: 12.00; 11.52 BS 52.4-54.2 at. % S; 3.45; 5.75 B8 with monocl. 55-59 at. % S: 5.95; 3.42; 5.63;91" 44' deformed 8 8 with ordered -60 at. % S vacant sites 3.51; 19.57 F51 3.62; 21.16 F5 L 3.59; 16.20 or 5.74; 34"21' F51 Cl 3.15; 12.30 (Molybdenite) c7 3.15; 12.3 (Tungstenite) c2 6.10 B1 5.21 (Alabandite) B3 5.60 84 3.98; 6.43 Ill,

10.06

185 63, 184 186 336 187 80

6-34

Crystal chemistry

Table 6.1

STRUCTURES OF METALS. METALLOIDS AND THEIR COMPOUNDS-continued

Element or compound

Structure type

Lattice constants, remarks

R&

Metalloids, etc.: B. C,P. N, Po, Te,Se, S-concinued FeS, c2 5.40 (Pyrites) C18 4.44; 5.41; 3.83 (Marcasite) FeS 88 183,189 3.447; 5.761 Room temp. modifications: (4 88 50.0-51.0 at. % S: 5.96-5.97; 11.74-11.58 51.0-52.3 at. % S: 3.44; 5.79-5.74 (0 B8 (8) 88 52.3-53.5 at. % S: 3.44-3.43; 5.74-5.69 High temp. modifications: B8 -100°C to -320"C, 50.0-54.0 at. % S (8) Ea > -32OoC, lattice parameters different from p-modification (8) (-0.5%) with different temp. coeff. B9 FeS 3.444; 5.876 8 8 (monocl. 190 5.94; 3.43; 5.69; W 38' (natural material) Fe1.78s2 deformed) -88 3.44; 5.82 (superstructure with a'=3 x 3.44 and c'=2x 5.82; Fe*,S,

-

Graham'91)

Fe,Ss

-88

FeKS2 FeCr2S4

F5a HI1 D~z c2 07, E8

cos, co3s4 cos C09S8

CoCr2S4 NiS, Ni,S3 Ni& NiS NiS Ni6S5 Ni3Sz (Ni, Fe)& Ni,FeS, RuS,

RhS, PdS

oss, PtS,

PtS (Pi, Pd, Ni)S

cus

CUl.,S cu2s

(r)

(i3 CU~VS4

CuFeS2 CuFezS, CusFeS4

cuco,s, AgFeS, ZnS

ZnA1,S4

089

HI1

c2 monocl. 07, B8 813 D S orthorh. D5e D89 07, c2 c2 834 c2 C6 B17 834 B18 C1b orthorh. 06; H24 El1 E9e 83 orthorh.

-

HI1 c1, monocl. El1 B3 B4 BS cf: Sic cf: Sic HI1 B4

6.86; 11.9; 22.7; 89"33' (detailed superstructure proposed by Bertantl92) 7.05; 11.28; 5.40; 112"30' 9.989 (ordered veision of D7,) 9.97 5.52 9.38 (Linnaeite) 51-53 at. % S: 3.37-3.36; 5.18-5.16 (Jaipurite) 9.91 9.91 5.68 b =3.2 (Parkerite) 9.46 3.43; 5.33 (high temp. mod) 9.59; 3.15 (low temp. mod.)(Millerite) 11.22; 16.56; 3.27 (M=4) 4.04; 90" 18' 10.1 (Pentlandite) 9.45 5.59 5.51 6.43; 6.63 5.64 3.54; 5.02

4.91; 6.10 (Cooperite) 6.37; 6.58 (Braggite) 3.75; 16.2 (Covellite) 5.56 11.90; 27.28; 13.41 (C::AbZm; Sahex. cl. pack&, 105°C) 3.89; 6.68 (M=2; structures proposed by 3 e l 0 v ' ~and ~ Uedatg6 differ cJLg7) 5.38 (Sulvanite) 5.24; iau, (chalcopyrite) 6.23; 11.12; 6.46 (Cubanite) 2 x 5.49 > 220°C 21.94; 21.94; 10.97 (M=32: superstructure of orthorh. deformed B-type)(Bornite) 9.46 (Carrollite) 4.88 (z 180°C) (Acanthite) ( 550°C 816 3.93; 4.43; 10.62: ( A = 8 ) B1 5.37 30O0C HI, 10.77 HI1 10.77 HI1 10.69 HI1 10.69 Hi1 10.60 HI1 10.56 HI1 10.46 H1i 10.81 HI1 837 7.79; 6.80 C6 12.20; 18.17 n2s SiS, C42 5.60; 5.53; 9.55 GeS, C44 11.66; 22.34; 6.86 GeS 816 4.29; 10.42; 3.64 8 3 (FeyGe)Cu3S4 5.29 (Germanite) SnS, C6 3.M; 5.87 SnS B29 3.98; 4.33; 11.18 (Henenberate) SnCu,FeS, 5.46; 10.28 (Stannite) H26 PbS B1 5.92 (Galena) PbSnS, 829 4.04; 4.28; 11.33 (Teallite) ASS B1 9.27; 13.50; 6.56; 106" 37' (Realgar) 11.46 9.56; 4.21; W k l " (Orpiment) As& 05. FeAsS 9.6; 5.7; 6.4; -90" (Arsenopyrite) EO7 CoAsS c2 5.61 (Cobaltite) NiAsS c2 5.66 (Gersdorffite) CuAsS -83 (orthorh.) 3.78; 5.47; 11.47 (Hautite) (Cu, Fe),AsS, 83 10.2 (Tetrahedrite, Fahletz) 11.3; 11.5; 3.9 (Stibnite) Sb2S3 D58 FeSbS 10.00, 5.93; 6.73; -90" (Gudmundite) Eo7 NiSbS 5.90 (Ullmannite) m1 CuSbS, 6.01; 3.78; 14.46 (Wolfsbergite) F56

0.W,,

(Sb, AsF3 Bi,S3 NaBiS, KBiS, CuBiS, AgBiS, Bi,Te,S

B3

D5.3 B1 81

F56

B1 B1 (orthorh. deformed) c33

10.2-10.3 (Tetrahedrite, Fahlen) 11.13; 11.27; 3.97 (Bismuthite) 5.76 6.01 6.13; 3.89; 14.51 (Emplectite) (>210°C). 5.648 (

A7 (As type) -

Rhombohedral: D : , - R b Co-ordinates: Rhombohedral (I), 2As (C3"): f(xxx) Rhombohedral (11), 8As(C3,): (000; 9; 2 )f(xxx) Hexagonal (III), 6As(C3,): (OOO; $-$$;#)t(OOx) Rhomb. I A=2

Hexagonal IIi A=6

Rhomb. I1 A=8

cia a

As Sb

Bi Simple cub.

4.t2 4.50 4.74

-

K

54"lO' 57"W 51"14' 60"

a

5.57 6.20 6.57

-

U

84"38' 87"24' 87"32' 90"

a

3.75 4.30 4.54

-

AS (Se type)

Hexagonal: D$P3,21 (and D$P3,21) Co-ordinates: 3Se(C2): x00; ?E*; Ox$ (and x00; 523; 0x4)

se Te Simple cub.

a

c

eja

x

4.36 4.45

4.95 5.92

1.14 1.33 1.23

0.22 0.27 0.33

-

-

e

10.50 11.24 11.84

X

0.226 0.233 0.237

-

2.80 2.62 2.61 2.45

Structures of metals, metalloids and their compounds

6-37

Table 6.2 STRUCTURAL DETAILS-continued

A9 (Graphite type) __ (a) Hexagonal: D&-P6,/mmc (if z=O); or C& -P6,/mc (if z # 0); a =2.46, c = 6.7; A =4 Co-ordinates: 2C(D3, or Cas): 000;W 2C(D3, or C3J: $4~; &+z); zaO (or very probably z=O) (fi) Rhombohedral: D:,-R%n; a=2.46, c = 10.1; A=6 Co-ordinates: 6C(C3,): (000; -#; (OOx), with x c i (or very probably x = $

g)?

A10 (Hg type) Rhombohedral: D&-RJm Co-ordinates: Rhombohedral (I) 1Hg (D3d): Rhombohedral (11): 2Hg (D3d): Rhombohedral (111): 4Hg (D3& Hexagonal (IV): 3Hg(D33: Rhombohedral

3.46

f ~ 2

FJ~

98"15'

-

-

-

2

4

6.71 3 1.94

IV

a

3.00

4.90

4.38

a

70"32'

41"25'

A

1 I

Ideal cubic

I1

Ill

cJa

OOO,% #

I

I1

I

OOO; # >

Hexagonal

1

C

OOo 000;

-

-

2

111

Hex.

a

3 2

60" -

2 33"33'

90"

-

-

1

2

4

-

-

-

2

aJ3 3 2.45

A l l (Ga type) Ortkorhombic Dti-Abma; a=4.52, b=4.51, c=7.64; A=8 Co-ordinates: 8Ga(C& (000;O#+(xOz; s + x , f .f) with x=O.O79; 250.153 A12 (a-Mn type) Cubic: T,,3-143m; a = 8.89; A = 58 Co-ordinates: (OOO; &)+ 2Mn(T,): OOO +8Mn(C3,): xxx; Z x ; ; with x=0.32 +24Mn(C,): xxz; ; Ez; 1; Txjca 2 : x2g 1; with x=O.36; 2-0.04 + 24Mn(C,) with similar co-ordinates but with x =0.09; z ~ 0 . 2 8

>

>

A13 (P-Mn type) Cubic: 06-P4,3 and 07-P4,3; 0 ~ 6 . 3 0 ;A=20 Co-ordinates: 8Mn(C3): xxx; (i+x)(+-x)g 2 ; ($-x)(z-x)(s-x); ($-x)@+x)($+x); 1; with x-0.061 12Mn(C2): &$+x); 2 ; g($+x)(&x); 2 ; &&+x); 1 ; $(i-x)($-x); 2 ; with x=0.206 An alternative structure has been proposed (Wilson') with space group OETFm3c; a=12.58; A = 160 A15 (p-W or Cr,Si type) Cubic: 02-Pm3n; a=5.04 or 4.56; A=8 Co-ordinates: 2W or 2si(G): OOo; #+ 6W or 6Cr(D,,): fi;1 ; fi;2 A16 (orh. S type) Orthorhombic: Df:-Fdd&a=10.48, b=1292, c=24.55; A=128 Co-ordinates: 4 times 32S(C1)in (OOO; #I; > ) + x y z ; Z y Z ; ( $ - x ) ( ~ - y ) ( ~ - z ) ; ( $ + x ) ( i - y ) ( i + z ) ; xyg Pp; (* -x)($ +y)(% +z); ( +i x)($+y)(* -2)

6-38

Crystal chemistry

Table 6.2 STRUCTURAL DETAILS-continued

SI SIl

s 111 s IV

X

Y

z

-0.017 -0.094 -0.167 -0.094

0.083 0.161 0.105 0.028

0.072 0.200 0.125 0.250

A20 (a-u type)

Orthorhombic: DiZ-Crncrn; a=2.85, b=5.87, c=4.95; A=4 Co-ordinates: 4U(C2,): (OOO; $)+Oh;OJ$ y=O, 10.5 A, (Pa type) Tetragonal: D~~-l*/mrnm;a =3.93, c =3.24; A -2 Co-ordinates: 2Pa(D4,): 000;4% Ab

(8-’

The structure of pure /?-U is not yet known. It is very similar to B-U with 1.4 at. % Cr contamination. The structure of such a product has been determined by Tucker”. Tetragonal: Ct,-P4nm; a = 10.52, c = 5.57; A = 30 Co-ordinates: 2U(C2,): 002; #($+z); z =0.66 552; I~+X)($-X)(~+Z); (~-x)(++x)(~+z);~=0.11; ~ = 0 . 2 3 4U(C,): XXZ; 4U(C3 in similar position with x=0.32; z=O.00 4U(C,) in similar position with x=0.68; z=0.50 8U(C,): XYZ; f j ~(++x)($-~)(++z); ; (+-x)()+J+(++z~ X ~ Z ;~ Z Z(++y) ; c$-x)($+z); (i-y)($+x)($+z); with x=O.56; y=0.24; z=0.25 8U(C,) in similar position with x=0.38; y=O.o4; 2=0.20 Thewlis’* compared the lattice constants at 720°C of pure B-U and Cr containing &U.

Pure B-U at 720°C 1.4 at % Cr-Ualloy at 720°C 1.4 at 5; Cr-Uallov at 20°C

a

C

10.759 10.763 10.590

5.656 5.652 5.634

Orthorhombic: D:,6-Prncn; a=4.72, b=4.89, c=3.66; A = 8 Co-ordinates: 4Np(Cs): feyz); f (4-y, i, ++z); y=0.208; z=0.036 4Np(C,) in similar positions with y=0.842; z=0.319 Ad (/?-NP)

Tetragonal: Di-P42,; a=4.90,6=3.39; A = 4 Co-ordinates: 2Np(D2): OOO, #O 2Np(C4): 402; ~~0.38 A, (8’-TiCu, type) Orthorhombic: D:Z-Cmcm; a=2.59, b=4.53, c=4.35; A=4 Co-ordinates: 4Ti or Cu(C,,): (000; f@)+O& 03; y=0.345

Hexagonat DQk-P6/mmm; a = 3.20, c =2.98; A = 1 Co-ordinates: 1Hg or Sn(DBk): OOO

Structures ofmetals, metalloids and their compounds Table 6.2 STRUCTURAL DETAILS-continued A, (B type) Tetragonal: D&-PZn2, a-8.73, c=5.03; A=50 Co-ordinates: 2B(S,): OU#; $9 6 times 8B(C,): xyz; (&x)($+y)($+z) fJz; (4+x) (i-y)($ 2 ) P$(+ +y,(i x) (4-2) YfZ (ii-Y)(t -X I (+ -2 )

+

x Y x

+

BI

B I1

BIII

BIV

BV

BM

0.328 0.095 0.395

0.095 0.328 0.395

0.223 0.078 0.105

0.078 0.223 0.105

0.127 0.127 0.395

0.250 0.250 -0.078

4 (z-po type) Cubic: Oi-Pm3m; a=3.35; A = l Co-ordinates: lPo(0,): OOO A , (P-po)

Rhombohedral D : , - R h ; aa3.37; a=98" 13'; A = l Co-ordinates: 1Po (D&): OOO At

(E-%)

Monoclinic C:,-P2,/n; a=9.05, b=9.07, c=11.61; B=W 46'; A=32 Co-ordinates: 8 times 4Se(C,): f(xyz)f($+x, &y, ) + z )

x Y z

MI

Sei

Sell

SeIIl

SeIV

SeV

SeM

Se

0.321 0.486 0.237

0.427 0.664 0.357

0.317 0.637 0.535

0.134 0.820 0.556

-0.081 0.686 0.521

-0.156 0.733 0.328

-0.084 0.520 0.229

Sen11 0.131 0.597 0.134

A , GB-Se)

Monoclinic c:h-P2,/a; a= 12.85, b=8.07, c=9.31; p=93" 08'; A=32 Co-ordinates: 8 times 4Se(C,) k(xyz)*(++x, 4-y, 2)

x Y Z

M

Sel

Sell

Sell1

SelV

SeV

Se

0.334 0.182 0.436

0.227 0.221 0.245

0.080 0.397 0.238

0.102 0.578 0.050

0.159 0.832 0.157

0.340 0.832 0.141

B1 (NaCI type) Cubic: 0:- Fm3m; a = 5.63; A = 8 Co-ordinates: (OOo,1.80,>)+4Na(oh): OO0 +4C1(Oh): B2 (CsCl type)

Cubic: Ot-Pm3m; a=4.11; A = 2 Co-ordinates: Cs(0,): OOO, Cl(0,):

444

Se

MI

0.409 0.763 0.366

Se Vlll

0.459 0.476 0.336

6-39

&IO Table 6.2

Crystal chemistry STRUCTURAL DETAIJ-S-Continued

B3 [Sphalerite (ZnS) type] Cubic: T," - F43m; a = 5.42; A = 8 Co-ordinates: (OOO;&O; 2 )+4Zn(T,): OOO +4S(T,): tal

8 4 [Wurtzite (ZnS) type] Hexagonal: C&, - P6,nse; a = 3.81, c = 6.23; A = 4 Co-ordinates: 2Zn(C3,): $@; 41-4 2S(C3J: #z; ff(f+z); 2s;

B8 (a-NiAs tyue; B-NiJn type) Between the main types (a) and (p) there exist a number of intermediate arrangements due to the variation of the stoichiometric formulae. The axial ratio c/a may change from the value 1.75 (in type a) to 1.22 (in type /I) Similarly, . there is virtually a continuous change from the 8 8 type to the C6 type. a-NiAs type Hexagonal: D:,,-P6,/mmc; a = 3.61, c = 5.03,c/a = 1.39; A =4 Co-ordinates: 2Ni(D,&: OOO,

2As(D3d: +$:;

gf9

p-Ni,In type Hexagonal: D&-PL,fmmc; a=4.19, c=5.15, cfa=l.23; A=6 2Ni(D3,,): OOO; 2Ni(D3,J $$$ 21n(~,,,): f H f i ; $4:

w,

;:5$

B9 [Cinnabar (HgS) type] Hexagonal: D:-P3121 and D2-P3221; a=4.14, c=9.49; A = 6 Co-ordinates: 3Hg(CJ: XOO; i%& 0x5; x=0.33 3s(c2): @; 233; OX& x=0.21

B10 (LiOH type) Tetragonal: Dih-P4/nmm; a=3.55, c=4.33; A=4 Co-ordinates: 2Li(DZd): OOO; 20H(C4J: O+z; 9%2=0.20 For FeSc z=0.26

B11 (PbO type) .. ~Tetragonal: D:, -P4/nmm; a = 3.98, c =5.01; A = 4 Co-ordinates: 2Pb(C4J: $02; z =0.24 20(C4,): the same with z=O.74 For y-TiCu: z(Ti)=0.65; z(Cu)=O.lO

ez;

813 [Millerite (NiS) type] __--__ Rhombohedral: C ; , - R3m; a = 5.64; a = 116" 35'; A = 6 Co-ordinates: 3Ni(Cs): xxz; ; x=O; zt0.264 3S(Cs): the same with x=0.714; z=0.361

>

Structures of metals, metalloids and their compounds

Table 6.2

MI

STRUCWRAL DETAILS--contintted

-816 (GeS _ type) _ ~ Orthorhombic: 0: -Pbnm; a= 4.29, b = 10.42, c = 3.64, A =8 Co-ordinates: 4Ge(Cs): *(xy&); +[(*-x)(i+x)$l; x=0.167; y=0.375 4S(CJ the same with x=O.111; y=0.139 B17 [Cooperite (PtS) type] Tetragonal: D&-P4/mmc; az3.47, c-6.12; A=4 %; 2S(D23: @ Co-ordinates: 2Pt(D2J:

w;

w,

818 [Covellite (CuS) type]

-

Hexagonal: D:,, P6,/mmc; a= 3.80, c = 16.4; A- 12 ($&) Co-ordinates: 2Cu(D3& 4 c U ( c d *($$z); +($, 4, 4-2); 2=0.107

B19 (AuCd type) Orthorhombic: D&,-Pmcm; a=3.14, b=4.85, c=4.75; A=4 Co-ordinates: 2Au(C2& f (Ofi); y =0.805 2Cd(CzJ: *($A); y=0.315 For MgCd: y(Mg)=0.818; y(Cd)=0.323 820 (FeSi type) Cubic: T4-P&$ a=4.48; A=8 Co-ordinates: 4Fe(C,): xxx; &+x)($-x)jt; 2 ; x=0.137 4Si(C3): the same with X = -0.158 x(Be)= -0.156; x(Au)=O.l5O For Be&: For RhSn: x(Rh)=0.14&x(Sn)=O.159 B27 (FeB type) Orthorhombic: D:,b--Pbnm; a=4.05, b-5.50, c=2.95; A s 8 Co-ordinates: 4Fe(C,): *(x& f($-x, i + y , ik x=O.125; y=0.180 4B(CJ: the same with x=0.61; ysO.036 For M n B x(Mn)= 0.125; y(Mn)= 0.180; x(B)=0.614; y(B)=0.031 For USE x(U)=O.125; y(U)=0.180; x(Si)=0.611; y(Si)=0.028 For TiB: x(Ti) =I 0.123; y(Ti) = 0.177; x(B) = 0.60% y(B) = 0.029

B29 (SnS type) Orthorhombic: D::-Pmcn; a=3.98, b=4.33, c=11.18; A-8 Co-ordinates: 4Sn(C,): * ( b z ) ; *j$, i-y, t4-z); y=O.115; z=0.118 4S(C,): the same wth y=0.478; zd.850 If this description, given in Strukturbericht vol. 3, p. 14, is transformed to the following, it is virtually identical with the B16 (GeStype). , 11.18, ~ ~ 3 . 9A 8 t; 8 Orthorhombic: D i t -Pbnm; a ~ 4 . 3 3bCo-ordinates: 4Sn(CJ: &(xA); +_(i-x, f+y, & x=O.115; y=0.382 4S(C,): the same with x=O.O22; ~50.150 B31 (MnP type) Orthorhombic Di,"-Pemn; a-5.91, b33.17, c=5.25; A=8 34-2); x=0.20; z=0.005 Co-ordinates: 4Mn(CJ: &(x$z); +_(i-x, i, 4P(CJ: the same with x-0.57; z=o.19 For AuGa: x(Au)=O.184; z(Au)=O.O10; x(Ga)=0.590, z(Ga)=O.195

6-42 Tabk 6 2

Crystal chemistry STRUCTURAL DETAILS-conrimred

For PdSi: x(Pd)=0.190; z(Pd)=0.070; x(Si)=O.570; z(Si)=0.190 For PtSi: x(Pt) =0.195 z(Pt)=0.010; x(Si) =0.5% z(Si)=0.195 For NiGe: x(Ni)=O.190; z(Ni)=O.OO$ x(Ge)=0.583; z(Ge)=O.188 For PdGe: x(Pd)=O.188; z(Pd)=0.005; x(Ge)=0.595; z(Ge)=.O.190 For IrGe: x(lr)=0.192; z(Ir)=0.010; x(Ge)=0.5% z(Ge)=0.185 For PtGe: x(Pt)=0.195; z(Pt)=0.010; x(Ge)=0.590; z(Ge)=0.195 For PdSn: x(Pd)=O.182; z(Pd)=0.007: x(Sn)=0.590; z(Sn)=0.182 For RhSb x(Rh)=0.192; z(Rh)=0.010; x(Sb)=O.590; z(Sb)=0.195 For NiSi: x(Ni)=O.184; z(Ni)=0.006; x(Si)=O.580; z(Si)=0.170

B32 (NaTI type) Cubic 0:-Fd3m; a =1.47; A= 16

834 (PdS type) Tetragonal: c&,-P4& a=6.43, c=6.63; A=16 2Pd(C2,): O$O;fi Co-ordinates: 2Pd(S4): 4Pd(C,): f (xy0); f (%&); x=0.475; y-0.250 E, 8S(C,): ~ ( x Y z ) ;f(xy.7); &(y, 5, $+z); ~(JJ, 2 =0.22

w;w,

4-2)

with ~ ~ 0 . 2 y=O.32; 0;

B35 (CoSn type) Hexagonal: 02, -P6/mmm; a =5.21, c =4.25; A =6 Co-ordinates: lSn(D& OOO,2Sn(D3&: 3)h $45 3CO(D,dc 30

w;v;

B37 (TISe type)

-

Tetragonal: Dij I4/mm; a =8.02, c =7.00; A = 16 Co-ordinates: (OOO; 444)+4TI(D4): +4TI(D& #;# +8Se(CzV): k(x, $+x, 0); &($+x, E, 0); x=0.179

w;w;

B o (UCO type)

Cubic: T5-12,$ a=6.36; A=16 Co-ordinates: (OOO; f#)+SU(C,): xxx; (&+x)($-x&; 1;x.50.035 +8Co(C3) the same with x-0.294

-

Hexagonal: Ci, Ps; a = 7.64, E = 282; A = 9 Co-ordinates: ~ z n ( c , ~ ) :OOO; +2zn(c,) $52; f j z , z = 4 (1.5Zn+4.5Ag) (Cl): f(xyz); f(j, x - y , z); f(y-x, y =0.032 z =0.750

Z, z) with x=0.350;

B, (CaSi tvuel

Orthorhombic: D::-Cmmc; a=3.91, 4.59, 10.80; A = 8 Co-ordinates: (OOO;44) +4Ca(C,,): f ($2); z 50.36 +4Si(C,J: the same with z=O.07 By choosing dilferent axes and origin from those given in the original paper, this type becomes virtualiy identical with the Bf(CrB type): Di:-Cmcm; a=4.59, 6=10.80, c=3.91; y(Ca)=O.l+ y(Si)=O.43

Structures ofmetals. metalloids and their compounds

6-43

Table 6.2 STRUCTURAL DETAILS-continued

B, +Nisi) Orthorhombic: DiZ-Pbnm; 4=5.62, b=5.18, c=3.34; A=8 Co-ordinates: 4Ni(C,): xy0; %pi; (4-x) (t+y)0; ($+x) ($-y)$; x=0.184; y=O.006 4Si(C,): the same with x=0.080; y=0.330 By choosing different axes and origin from those given in the original paper, this type becomes identical with the B31(MnP type): Dif-Pcmn; u=5.62, b=3.34, c=5.18; x(Ni)=0.184; z(Ni)=O.OO6; x(Si)= 0.580; z(Si)=O.170

Orthorhombic: Dii-Pbca; a=6.47, b=8.25, c=8.53; A=16 Co-ordinates: 8Sb(C,): +(xyz); &(f+x, f-y, 9; &(% f+y, 8Cd(CI): the same

Cd or Zn

Sb

CdSb

ZnSb

4-2);

X

Y

2

X

Y

2

0.136 0.142

0.072 0.081

0.108 0.111

0.456

0.119 0.103

-0.128 -0.122

0.461

.__

Orthorhombic: 0:: -Cmcm; a =2.97, b =7.86, c =2.93; A = 8 Co-ordinates: (OOD; #O)0)+4Cr(C2,): y=O.146 +4B(C2,): the same with y=0.440 For NbB y(Nb)=0.146, y(B)=0.444 For CaSi: y(Ca)=0.14; y(Si)=0.43 (cf. Bc type)

&@A);

B,

(MOBtype)

Tetragonal: D:f-I4/amd; a-3.11, c=16.97; A=16 Co-ordinates (OOO, ff$)+8Mo(C2,): +(OOz); &(O,$, $+z); 2=0.197 +8B(C2,): the same with z=o.35 Bh (WCtype) Hexagonal: Dkh- P6Jmmm; a=2.91, c=2.84; A=2 Co-ordinates: 1W(D6J: OOO; lC(D3,J: 9,# Bi

(y'-MoC type)

Hexagonal: D:,-P6,/mmc; a=2.93, c=10.97; A - 8 Co-ordinates: 4Mo(C3&): %z; g ( 4 - z ) ; %($+z); @; z*+ 4C: in holes

~BI, (BN type) Hexagonal: D& -P6,Jmmc; a =2.50, c =6.66; A =4 Co-ordinates: 2B(D3& %I; @; 2N(D3,): %& &

+(3-x, Y; f+z)

644 Crystal chemistry Table 6.2

STRUCTURAL DETAIIS-cmtinued

B1 [Realgar (ASS)type]

Monoclinic: C;,-PZ,n; a=9.27, b=13.50, c=6.56; j?=106" 37'; A=32 Co-ordinates: 4 times 4As(C,) and 4 times 4S(C,)in: +(xyz); +(i+X, +-x, i + z )

As I X

Y z

0.118 0.024 -0.241

As11

Aslll

AsN

0.425 -0.140 -0.142

0.318 -0.127 0.181

0.038 -0.161 -0.290

SI

SI1

0.346 0.008 -0.295

0.213 0,024 0.120

SI11 0.245 -0225 -0.363

SIV 0.115 -a215 0.048

B,,, (TiB type) Orthorhombic: 0:t-Pnrnn; a=6.12, b=3.06, c=4.56; A = 8 Co-ordinates: 4Ti(Cs): *(x$z); +(+-x, f , *+z); x=0.177; z=0.123 4B(C,): the same with x=0.029; z=0.603 If the axes are changed from those of the original paper, this type becomes identical with the B27 (FeB) type: D j f -Pbnm; a =4.56, b =6.12, c= 3.06, x(Ti)=O.123; y(Ti)=0.177 x(B)=0.603; y(B)=O.O29 C1 (CaF, type-MgAgAs type) (e) Cubic:

0Z-Fm3m; a=5.45; A = 1 2 Co-ordinates: (000; #; 2) + 4Ca(0,,): OOO +8F(&): k ( 9 In those cases in which the I.'-position is occupied by two components in an ordered fashion-for example in As(MgAg)-the space group is changed to (8)Cubic: q2-F43m; a=6.24; A=12 2 )+4As(&): 000 Co-ordinates: (OOO; 9; +4Ag(T,): & +4Mg(T,): $$ %Pyrites (FeS,) type1 Cubic: T6-Pu3; a=5.40, A=12 Co-ordinates: 4Fe(S3,): 000; $9; 2 8S(C3): ~ ( x x x )2 ; (.$+x, ;-x, P; 2 1; ~ ~ 0 . 3 8 6 For MnS,, x=0.401; for CoAsS and NiAsS (random distribution of As and S ) x=0.385; for PtBi,: x =0.38.

C6 ( ( 3 1 2

type) Hexagonal: D : , , - P h l ; a=4.24; c=6.84; A=3 Co-ordinates: ICd(D,,): OOO,21(C3") & $2 z-; There is virtually a continuous change from this type to the 88 type. C7 (MoS, type) Hexagonal: D&, - P6,Immc; a = 3.15, c = 12.30; A = 6 Co-ordinates: 2Mo(D3,): 424; & 4S(C3J 352; %,%

08fClr,Sn, type) Cubic: 0z-Im3m; a=9.36; A=40 Co-ordinates: (000; + 12Tr(C4,): _+ (xm, ) ); x=0.342 +12Sn(D,,): k($O+h>1 +16Sn(C,,): (xxx; xxx; 3 );x=0.156

if+)

Structures of metals, metalloids and their compounds Table 6.2

STRUCTURALDETAILS-continued

08, (Mg5Ga2 tYW) Orthorhombic: D:E-lbam; a=13.72, b=7.00, c=6.02; A=28 Co-ordinates: (oOa,s) +8Ga(Cs): +(xyO); f(xj+); x=O.122; y=0.262 +8Mg(CJ: the same with x=0.080; y=0.660 8Mg(Cz): f(XOL) + (XC& x =0.242 +4Mg(D2): *IC&)’ -

+

[Unpublished work b y E, Hellner;for Mg,TI,: x(Tl)%i;y(Tl)si]

~

Hexagonal: Dih-P6,/mmc; a = 2.98. c = 13.87; A = 14 Co-ordinates: 4W(C3,): f(‘j$zx *($$ f-2); z=0.139 2B(D,& & (w&+2B(D3,): f ($$$ 2B(D,,,): OOo; 00) 4B(C3J +(%z); *(i,f f - 2 ) ; Z= -0.028 0 8 , (MozB, ~ Y W ) Rhombohedral: D&-R3m; a=7.19; c(=24“ lo’; A=7 (Hexagonal setting: a=3.01, c=20.93; A=21) Co-ordinates (for hex. setting): (OOO, is$;)ff)+ 6Mo(C3,): f.(002);z =0.075 +6B(C3& the same with z = i +6B(C33: the same with z=0.186 +3B(D3d): @% 0%cT”n7Si2 f ~ p ” l Hexagonal: C&-W,/m; a = 11.04, c = 3.98; A = 19 Co-ordinates 1Th(S6): &(@) 6Th(Cs): f(xd); f@,~-y,$); +(Y-x, R,~~x=O.153;y= -0.283 6S(CJ: the same with x=O.514; y=0.375 6S(C3: the same with x=0235; y=O+O.OlO

EO, (FeAsS type) Monoclinic: C:h-B2,/d; a-9.51, b=5.65, c=6.42; 85~90”;A=24 Co-ordinates: (000,fO))+8Fe(C1): &(xyz); fe+x,f-y,f+z); x=O;y=O; z=0.275 +8As(Ci): the same with x=0.147; y=0.128; 0-0 +8S(Ci): the same with x=0.167; y=0.132; z=0.500 El, (CuFeS2 type)

Tetragonal: Dii-Iq2d; a=5.24, c = 10.30; A=16 Co-ordinates (000;#)+4Cu(S4): OOO; @$ +4Fe(S4): OO+; $O$ +8S(C,): id;+&,&;

x;y =0.27

E l , (MgCuAlz type) Orthorhombic: Dil-Cmcm; a=4.00, b=928, c=7.14; A=16 Co-ordinates: (OOO; +4Mg(C2J: +(Ohhy =0.072 +4CU(C,”): +(Oh); y= -0.222 +8A1(Cs): +(Oy+, +(O, y, 3-z); y=0.356; 2=0.056

w)

6-59

6-60

Crystal chemistry

Table 62 STRUCTURAL DETAILS-continued

El, [AuAgTe, (Sylvanite) type] _l__l___. --

Monoclinic: Cg,, -P2/c; a = 8.96, b =4.49, e= 14.62; = 145" 26'; A = 12 Co-ordinates: 2Au(Cj): 000, 2Ag(C2): +(Oh); y=0.433 4Te(C,): +(xyz); f(x, p, $+z); x=O.298; y=O.O31; z=0.999 4Te(C,): the same with x=0.277; y=0.425; z=O.235

E94 (AI,C,N type) Hexagonal: C&-P6,mc3; u=3.28, c=21.55; A=18 Co-ordinates: 2A1(C3,): Ooz; OO(f+z);z-0.150 2A1(C3,): the same with z=O.345 2Al(C3,): $32; $+(i+z);z=0.045 2A1(C3,): the same with z==O.456 2AI(C3,): the same with ztO.240 2C(C3,) the same with z=O.133 2C(C3,): the same with 210.369 2C(C3,): 002; 00($+z); z=O.OOl 2N(C3,): the same with z=0.250 E9, ( F a 4 7 type) Tetragonal: 02,-P4mnc; a =6.32, c = 14.78; A =40 Co-ordinates: 4Fe(C4): f(Ooz); f ($ i,f+z); z=o.300 8Cu(C,): k(xy0); +(;+x,f-y,$); ~(JxO);*(f+y,f+x,$); ~=0.278;~=0.092 4AI(C4): (002); k (t,$, f+z);2=0.122 8AI(CJ: f (x, 4 +x, $; P, 4-X, $; $-X, X, x ~ 0 . 1 6 7 16Al(C,): ~ ( X Y Z ;i j ~~ ;X Zy ;i ~ !+x, ; i-y, f+z; f-X, f+u, )+z; )+y, f + x , i + z ; 4-y, i-x, $+z); x=0.203; ~ 1 0 . 4 1 4z=O.lOo ;

4);

E9, (FeMg3A1,Si6 type) Hexagonal D;,, -P62m; a =6.62, c =7.92; A = 18 Co-ordinates: lFe(D,,,): OOO ; x=O.445 3Mg(C2,): ~ 0 %0x4; lAl(D3b): 004 3Al(C,,): XOO; OXO; %a, ~=0.403 4AI(C3): +(f.f~); f (if.?);~eO.231 6Si(C,): xOz; xOZ; 0x2; Ox% Zlz; 5%~ ~ 0 . 7 5 20~; 0 . 2 2 3

ie,

E9, (Mn,A19Si type) Hexagonal: D$,,-P6,jmmc; u=7.51, c=7.74; A=26 Co-ordinates: 6Mn(C,,): +(x, 2x, &); &(2x, x, 3); *(xi*); x=O.l20 6A1(Cz,): the same with xe0.458 12Al(C,): k(x, 2x, Z; 2x, X, x ~X, ,2x, 4-2; &, X, )+z; Z= -0.067 2Si(DJd): OOO;

X,

E, 4-Zk ~==0.201;

Structures ojmetals, metalloids and their compounds Table 6.2 m d

6-61

STRUCTURAL DETAILS-contimed

(A1Li3N2type)

Cubic: T,' -Ia3; a =9.48; A =96 x=O.115 Co-ordinates: (OOO; &$)+16A1(C3): ~ ( x x x ) ;k(f+x, t-x, % +48fi(C,): _+(xYz; 3 k _+(x, jj, +-G 3 ); _+(+-x, y, 2; f-y, Z; 3 ); ~=0.160,y=0.382; ~=0.110 8N(C,i): OOO; 3 +24N(C2): +(x%; 2 ); _+(Q*f; 2 k xt0.205 For GaLi,N1 : x(Ga) =0.117; x(Li)-0.152; y(Li)=O.381; z(Li) =0.114; x(N)=0.215

>

3 X *(E,

+

E9, [CuFe2S, (Cubanite) type] Orthorhombic: D i t - P n m a ; a=6.23, b=11.12, c=6.46; A=24 Co-ordinates: 4Cu(Cs) _+(x+z); _+(+-x, $, ++z); x = k z=& 8Fe(C,): ~ ( X Y fZ+;x , * - y , 4-2; 2, f+y, 2; $ - x , 8S(C,): the same with x = & y=&, z=& 4S(CS): +(x$zX -1(3-x, 2, &+E); x=fi; z = s

3, $+z); x = k

y=&

z=&

FO, WiSbS (Ullmannite) type] Cubic: T4-P2,3; a=5.60; A=12 Co-ordinates: 4Ni(C3): xxx; (f+x)(f-x)R 3 ; XEVO 4Sb(C,): the same with ~ ~ 0 . 3 8 5 4S(C3): the same with x%0.615 F51 WaHF, type) Rhombohedral: D:,-R3m; a=5.05; a=40° 2'; A=4 (Hexagonal setting: a = 3.45, c = 13.90, c/a =4.03; A = 12) Co-ordinates: lNa(D,,): OOO; lH(D,,) =H 2F(C3,): ~(xxx);x ~ 0 . 4 1 0 For CaCN,: u=43" So'; clu~3.63;x=0.37 For NaCrS, : u =29" 48'; c/a = 5.59; x =0.236 For NaCrSe, : a =30" 18'; c/a = 5.49; x =0.235 For RbCrSe,: a=21" 33'; cla17.85 F56

(CuSbS2 type)

Orthorhombic: Dii-Pnma; a=6.01, b=3.78, c=14.46; A=16 Co-ordinates: 4Cu(Cs): _+(x;tzk_+t$+x,4, $-& x-0.25; z=0.83 4Sb(C,): the same with x=0.23; z=O.O6 4S(Cs): the same with x=0.63; z.=O.lO 4S(Cs): the same with x=0.88; z=0.83 F5a W e S 2 tYP) Monoclinic: C;,,-CZ/c; a=7.05, bi11.28, c=5.40; 8=112" 30'; A=16 Co-ordinates: (000;)fO)+4K(C2): f (O& y=0.355 +Fe(C2): the same with y= -0.008 +8S(C,): ~ ( x Y z )f(x,f,~+z);x=0.195;y-0.111;~=0.10 ;

Hll [Spinel (A12Mg04)type] Cubic: O:-Fd3m;a=8.06, A t 5 6 Co-ordinates: (OoO,$$@ 2 )+8Mg(Id): OOO,&g + 16Al(D3,,): 368; 3% 2 +320(C3,,): XXX;xfR; 2 ; ($-X)($-X)($-X);

(i-x, i + x , $+X);

2;x=-+

In some compounds, better agreement with observed intensities is obtained by assuming that the metal atoms are distributed at random among the 24 available sites, or %hatthe trivalent element occupies all the 8-equivalent sites and half of the 16-equivalent ones. In some cases lattice sites may be vacant, e.g., y-A120, or In,S,.

Crystal chemistry

6-62 Table 6.2

STRUCTURAL DE?~Ls---eontimted

iY2,[Cu3VS4 (Sulvanite)type]

Cubic: Tj -P83m; a=5.37; A = 8 Co-ordinates: 3Cu(D2,): @ lV(T,): OOO 4S(C3,): xxx; xEi; 2 ;x=0.235

w,O@;

H2, [Stannite (FeCu,SnS,) type] -~

~

-

Tetragonal: D::-I(nm; a=5.46; ~910.72;A=16 Co-ordinates (OOO;$$$)+2Fe(D,): OOO +2Sn(Dz,): W +4cu(S,): Oft;303 +8S(C,): XXZ; ZRz; xZZ; XXXZ; x-0.245; z=0.132

L1o ( ~ A type) U

-

Tetragonal: Di,, C4/mmm; a =3.98m c =3.72; A =4 Co-ordinates: (OOO;B0)+2Cu(D,): OOO +2Au(D,): Superstructure of the A1 (Cu) type

L1 (CURtype) Rhombohedral: D:,-RTm; a=7.56; u=9W 54'; A=32 Co-ordinates: (OOO, f f Q 2 )+ 16Cu(D3,): W, $44; 2 +16Pt(D,,): g$;8 0 2 Superstructure of A1 (Cu) type

LIZ (CU,AU type) Cubic: Oi-Pm3m; a=3.75; A=4 Co-ordinates: 3Cu(D4,): $40; 3 IAU(O~): OOO Superstructure of AI (Cu) type

L1, (Pt,Cu type)

-

Cubic: O3 Fm3c; a s 5.6; A =32 Co-ordinates: (OOO;$40; 2 )+4Pt(O): OOO +4Cu(O): $+f +WPt, Cu)(Dz):

ofit; 3 A& 2

This structure was suggested by Tang?05 An alternative has been proposed by Schneider and Esch.206 (CulMnAl type)

-

Cubic: 0: Fm3m; a- 5.90; A = 16 Co-ordinates: (OOO;$40; 2 +4A1(Ok): OOO +8Cu(Id): &H +4Mn(Ok): $34 Superstructure of the A2 (W) type; this type is virtually identical with the Do, (BiF, or BiLi,) type L2z U W z type) Cubic: O ~ - I m 3 r n ; a = l l . S 9 ; A = 5 4 Co-ordinates: (W,$44) +2T1(Ok): OOO + 16Tl(C3,): f (xxx, xZZ; ); x = 0 . 1 7 ~ 4 +24TI(Cz,): ~ ( x x Q2 ;xZQ ;x=0.35sf +12Sb(C4,): k((X0D; 1; x=0.29s+

>

>

>

Structures of metals, metalloids and their compounds Table 6.2

6-63

STRUCTURAL DETAILS-continued

L2, (6-TiCu type)

-

Tetragonal: D:,-P4/rnmm; a=3.14, c=2.86; A=2 Co-ordinates: 1Ti(D4,,jC OOO

3ff Cubic 0:-Pm3m or 0:-Fm3m (depending on the distribution of the N atoms); a =3.79; A = 5 Co-ordinates: 4Fe at OOO; 3 f Q 2 1N at $ti;or at probably the latter; or at random at 444;423; 1 ;and (or) at 2%; $$& 2 ; and (or) at f$$;YOa; 2

it),

L'1, j-AlFe,C type)

-

Cubic: Oi-Pm3m; a=3.76; Are5 Co-ordinates: lAl(O,,): OOO 3Fe(D.& *%> 0.6 to O.9C(Oh)at ffi

L'2 (Martensite type) Tetragonal D~~-I4/mmm;a=2.84,~ ~ 2 . 9A=2Fe+(up 7; to) 0.12 C Co-ordinates: 2Fe(D,) at OOO,# The C atoms at random: $#O and (or) 004 L'3 (Interstitial A3 type) ~-

-

Hexagonal: D f -P6, /mmc or D;,, P6/mmm Co-ordinates: 2 metal atoms (DJh): $fa; - 21 C or N(C,,): &;f+(++z); &;&-z);

iy

zre& or OO+; 00:

L6, (Ti,Cu type) Tetragonal D:,-P4fmmm; a=4.16, c=3.59; A=4 Co-ordinates: lCu(D,): O00 1Ti(D4,): ff0 2Ti(D,,): 033;$04 Tetragonal deformed Ll, (Cu,Au) type; superstructure of A6 (In) type L'6 (Interstitial A6 type)

-

-

Tetragonal: 0:; F4/mmm (or Dih P4/rnmm, depending on the distribution of the N atoms) Co-ordinates: 4 metal atoms (D4,,): OOO,f& 2 N atoms in the holes: 2 ;;::4 $it;2 ;or fOQ 2

is;e:;

Table 63

COMPARISON op s m m ~ m r u c m AND PBARSON NOMBNCLATURE

StnJcturbericht structural type A1 A2 A3 A4 A5 A6 A7 A8 A9

+If;

Typical compound or element

cu

W Mg

C (Diamond) Sn (Beta)

In As Gamma-% C (Graphite)

Pearson symbol

cF4 c12

hP2 cF8 t14 t12

hR2 hP3 hP4

6-64 Table 6.3

Crystal chemistry aJMPARlsoN OF SraUgTuRBERlCHT AND PBUISON NOMENCLATURE-contiIIWd

Struktwbericht structurd type

A10 A1 1 A12 A13 A15 A16 A20

A, Ab

A, Ad

A, A,

A, AI Ai At Al

B1

82 E3 84 88, B8,

B9

B10 B13 816 817 818 B19 820 827 829 831 832 B34 €335 B37 B. Be 8, BJ BB Bi

Bt B" c1 c2 C6

CI c11, c11, c12 C14 C15 Cl5, C16 C18 a 2

Typical compound

or element Hg Ga Alpha-Mn

Beta-Mn Cr,Si Alpha-S Alpha-U Pa Beta-U Alpha-Np Beta-Np Beta-TiCu,

Pearson s ~ o l

hR1 0c8 c158

CPM cP8 0f128 0C4 t12 tP30 0p8

B Alpha-Po Beta-Po Alpha-Se Beta-Se NaCl CSCl ZnS (Sphalerite) ZnS (Wiirtzik) NiAs Ni,In HgS LiOH; PbO NiS

tP4 0f4 hP1 tP50 cP1 hR 1 mP32 mP32 cF8 cP2 cP2 hP4 hP4 hP6 hP6 tP4 hR6

GeS

0p8

HgSnXo

m

cus AuCd FeSi FeB

SnS MnP NaTl PdS CoSn

Tlse

uco AgZn CaSi Nisi CdSb CrB MOB

wc

MoC BN ASS TiB CaF, FeS, CdI, MOS, CaC, MoSi, CaSi, MgZn, MgCu, AuBe, CuAI, FeS, (Marcasite.) FezP

tP4 hP12 0p4

CP8 0p8 0p8 0p8

cF16 tP16 hP6 t116 e116 hP9 0p16 0p8

0p16

0c8

t116 hP2 hP8 hP4 mP32 0p8

cF12 cP12 hP3 hP6 t16 t16

hR6 hP12 cF24 cF24 t112 0p6

hF9

Structures of metals, metalloids and their compounds Table 63

COMPARISON OF STRUR1zIRBERICHTA N D PEARSON N O M E N C L A T U R P e O n t ~ d

Strukturbericht structuraI type c23 C32 c33 c34 C36 c37 C38

C40 C42

C44 C46 c49 c54

6-65

Typical compound

Pearson

or eIement

symbol

pm2 AlB, Bi,Te,S AuTe, (Calavente) MgNi, Co,Si Cu,Sb CrSi,

oP12 hP3 hR5 mC6 hP24 OP12 t P6 hP9 0112 oF72 oP24 oc12 oF24 hP18

SiS, GeS, AuTe, (Krennerite) ZrSi, TiSi, MgzNi M g p ThSi, COGe, ThC, CuTe, LiZn, CoAs, BiF, Re03/Cu3N Fe,C Na3As Mg3Cd NiA1, CU3P TiAl, ZrAl, TiNi, TiCu, U,Si Mn3As BaAl, MoNi, UA1, PtSn, PtPb, UB4 MnB, B4C CaB6 NaZn,, TiBe,, ThMn12 U6Mn CaCu, BaHg11 UBe12 Fe,N La203 Mn203 Sb2S3 Zn3P2

CrG

Ni,Al, U,Si, W n , pu2c3

Ni,S, As,% AI4C3

oF48 tI12 oC24 mC12 hP6 hP3 c132 cF16 cF4 0Pl6 hP8 hP8 oP16 hP24 oPl6 tI16 hP16 oP8 hP9 tI16 0P16 tIlO tIlO 0120 OC20 tPlO tP20 OF40 hR15 CP7 cF112 hP13 tl26 tI26 hP6 cP36 cF52 tI18 hP5 cI80 oP20 tP40 OP20 hP5 tPlO hPlO cI40

hR5 mP20 hW

6-66 Table 63

Crystal chemistry C o M P A R w l N OF STRUKTURF3ERICHT AND PEARSON

Strukturbmicht structural type

NoBiENmTLm-continUed

Typical compound or element a 3 s 4

n3p4

Ni3Sn4 Ta3B4 Fe3Zn10 Cu,Zn8 Cu,A14 Cr&, Fe7w6

Cu, ,Si4 Mn5Si3 a 9 s s

Cr5A1, Co,A15 Th6Mn23

Sigma ( F a r ) Mg2Cu6A15(MgZznll) Co,Al, Mg3zX49 Ir,Sn, Mg,Ga, WZB, Mo2B5

Th,S,Z FeAsS CuFeS, MgCuAl, AuAgTe, Fe,W3C A15C3N FeCu,Al, FeMg3AlsSi, Mn3A1,Si AlLi,N, CuFe,S, NiSbS NaHF, CuSbS, KFeS, MgAlzO4 CU3VS4 FeCuZSnS4 CuAu CUR Cu,Au Pt,Cu CUzMnAl 'Wbz TiCu Fe4N AlFe3C Fe-C (Martensite) FezN CuTi,

Pearson symbol cF56 ci28 mC14 0114

c152 c152 cP52 cF116 hR13 c176 hP16 cF68 hR26 hP28 cF116 tP30 cP39 mP22 c1162 c140 0128 hP14 hR7 hP19 mP24 t116 0c16 mP12 cF112 hP18 tP40 hP18 hP26 c196 0p24

cP12 hR4 0p16

mC16 cF56 cP8 tP16 tP2 hR32 cP4 c132 cF16 c154

t12 cF5 cP5 t12

hP3 tP4

REFERENCES 1 E. A. Owen and G. I. Williams, Proc. phys. SOC., 1954 (A), 67, 895. 2 T. W. Baker and J. Williams, Acta Cryst., 1955, 8, 519. 3. C. S. Barrett, 3. chem Physics, 1956, 29, 1123. 4. F. H.Spedding, A. H.Daane and K. W. Herrmann, Trans. Amm. lnst. min. (metaN.)Engrs., 1957 209,895. 5. F. H. Ellinger, US Atonic Energy C o r n Publn, LADC-1460.

Structures of metals, metalloids and their compounds

6-67

6. J. D. Farr, A. L. Gore, and M. G. Bowman, U S Atomic Energy Comm.Publn, LA-1545, 1953. 7. K. Gordon, B. Skinner and H. L. Johnston, U S Atomic Energy Comm.Publn, NP-4737, 1953. 8. I. W. Nielsen and N. C. Baenziger, Acta Cryst., 1954, 7, 132. 9. P. Duwez, J. appl. Physics, 1951,22, 1174. 10. J. D. Fast,J. appl. Physics, 1952, 23, 350. 11. D. M.Poole, G. K. Williamson and J. A. C. Marpks, J . Inst. Metals, 1957-58, 80, 172. 12. D. T. Peterson, P. F. Djilak and C. L. Vold, Acta Cryst., 1956, 9, 1936. 13. P. A. Sellers, S. Fried, R. E. Elson and W.H.Zachariasen, J. Amer. chem Soc., 1954, 76, 5935. 14. J. Thewlis, Acta Cryst., 1952, 5, 790. 15. C. W.Tucker, Acta Cryst., 1951, 4, 425; 1952, 5, 395. 16. A. 6.Knapton, Acta Cryst., 1954,7,457. 17. A. M. Holden and W. E. Seymour, Trans. Amer. Inst. mtn. (metall.) Engrs, 1956, 206, 1312. 18. W. H. Zachariasen, Acta Cryst., 1952, 5, 664. 19. 0. J. C. Runnalls, Acta Cryst., 1954, 7, 222: 20. W. H. Zachariasen and F. Ellinger, J. Chem. Physics, 1957, 27, 811. 21. F. H. Ellinger, Trans. A m . Inst. mln. (metall.) Engrs, 1956, 206, 1256. 22. M. A. Gurevich and B. F. Ormont, Fizika Metall., 1957, 4, 112. 23. A. E. Austin and J. R. Doig, Pans.Amer. Inst. min. (metall.) Engrs, 1957, 209, 27. 24. R. F. Domogala and D. J. McPherson, U S Atomic Energy Comm. Publn, COO-100, 1952. 25. R. F. Raeuchle and F. W. von Batchelor, Acta Cryst., 1955, 8, 691. 26. P. Duwez and C. B. Jordan, J . Am. chem. SOC.,1951,73, 5509. 27. E. K. Halteman, Acta Cryst., 1957, 10, 166. 28. E. Oehman, Metdlwirtschaft, 1930, 9, 825. 29. A. I. C. Wilson, Bull. Am. phys. Soc., 1934, 9, No. 16. 30. 2. S. Basinski and J. W. Christian, J. Inst. Metals, 1952, 80, 659. 31. H. Margolin and Elmars Ence, Trans. Amer. Inst. min. (metall.)Engrs, 1954,200,1267. 32. W. Rostoker, J. Metals, 1952, 4, 209. 33. P. Duwez and J. L. Taylor, J. Metals, 1950, 2, 1173. 34. E. T. Hayes, A. H.Robertson and W. L. O'Brien, Trans. Am. Soc. Metals, 1951, 43, 888. 35. D. Bergman and D. P. Shoemaker, Acta Cryst., 1954,7, 857. 36. G. J. Dickins, Abs. Dissert. Univ. Cambridge, 1954-55, 1957, 244. 37. G. I. Dickins, Audrey M. 8. Douglas and W. H. Taylor, Acta Cryst., 1956, 9, 297. 38. Emma Smith and R. W. Guard,Trans. Amer. Inst. ntin. (metall.) Engrs., 1957, 209, 1189. 39. T. J. Heal and G. I. Williams, Acta Cryst., 1955, 8, 494. 40. C, B. Jordan, Trans. Amer. Insr. min. (metall.) Engrs, 1955,203,832. 41. M. V. Nevitt and J. W. Downey, 7tans. Amer. lmt. min. (metall.), Engrs, 1957, 209, 1072. 42. R. M. Waterstrat and J. S. Kasper, Trans. Amer. Imt. min. (metall.) Engrs, 1957, 209, 872. 43. P. Duwez and C. B. Jordan, Acta Cryst., 1952,s. 213. 44. L. Misch, Z . physikal Chem, 1935, (B), 29,42. 45. G. F. Kossolapow and A. K. Trapesnikow, Metallwirtschqft, 1935,14,45. 46. A, Brystrom, P. Kierkegaard and 0. Knop, Acta Chem. Scand., 1956,6709. 47. N, C. Baenziger, R. E. Rundle and A. I. Snow,Acta Cryst., 1956, 9, 93. 48. J. R. Murray, J . Inst. Metals, 1955-56, 84, 91. 49. E. k Wood and B. T. Mattheas, Acta Cryst., 1956, 9, 534. 50. N. C. Baenziger and J. W. Conant, Acta Cryst., 1956, 9, 361. 51. P. Pietrokowsky, Trans. Amer. Inst. min. (metall.)Engrs, 1954, 200, 219. 52. E. S. Makarov and L. S. Gudhov, Krystallografiya, 1956, 1, 650. 53. H. Nowotny, E. Bauer and A. Stempfl, Monntsh., 1950,81, 1164. 54. R. E. Marsh, Acta Cryst., 1954,7,379. 55. R. Ferro, Acta Cryst., 1954, 7, 781. 56. M. J. Sanderson and N. C. Baenziger, Acta Cryst., 1953, 6, 627. 57. E. A. Owen and E. A. O'D. Roberts, J . Inst. Metals, 1940,66, 389. 58. A. Bystrom and K. E. Almin, Acra Chem. Scand., 1948,1, 76. 59. t.S. Barrett, Acta Cryst., 1957, 10, 58. 60 J. W. Nielsen and N. C. Baenziger, Acta Cryst., 1954, 7, 277. 61. E. J. Duwell and N. C. Baenziger, Acta Cryst., 1955, 8, 705. 62. N. C. Baenziger, E. J. Duwell and J. W. Conant, US Atomic Energy C o r n Publn, COO-127, 1954. 63. K. Schubert, U. Rosler, W. Mahler, E. Done and W. Schutt, Z . Metallk, 1954, 45, 643. 64. G. V. Raynor and J. A. Lee, Acta Met., 1954, 2, 616. 65. E. S. Makarov, Dokl. Akad. Nauk. USSR, 1950,74, 935. 66. D. K. Das and D. T. Pitman, Trans. Amer. Inst. win. (metall.) Engrs, 1957, 209, 1175. 67. J. H. N. van Vucht, Z. Metallk., 1957, 48, 253. 68. E. Ence and H. Margoli Trans. Amer. Inst. min. (metall.) Engrs, 1957,209,484. 69. W.Koster and A. Sampaio, Z . Metallk., 1957, 48, 331. 70. 0. J. C. Runnals, J. Metals, 1953, 5, 1460. 71. J. F. Smith and E. A. Ray, Acta Cryst., 1957, 10, 169. 72. A. J. Bradley and S. S. Lu, Z . Krist., 1937, 96,20. 73. W. Hofmann and H. Wiehr, Z . Metallk., 1941, 33, 369. 74. K. Little, I. N. Pratt and G. V. Raynor, J. Inst. Metals, 1951, 80,456. 75. K.Little,, J . Inst, Metals, 1953-54, 82, 463.

6-68

Crystal chemistry

76. S. Samson, Nature, 1954, 173, 1185. 77. J. Adam and J. B. Rich, Acta Cryst., 1954, 7, 813. 78. idem. Acta Cryst, 1955, 8, 349. 79. A. D.I. Nicol, Acta Crysf., 1953, 6, 285. 80. K.Schubert, U. Rosler, M. Kluge, K. Anderko and L. Harle, Natunviss., 1953,40,269,437. 81. A. C. Larsen, D. T. Cromer and C. N. Stambaugh, Acta Cryst., 1957, 10,443. 82. J. H.Keeler, US Atomic Energy Comm. Publn, SO-2515, 1954. 83. P. Esslinger and K. Schuhert, Z. Metalk, 1957,48, 126. 84. M. G.Bown, Acta Cryst., 1956,9,70. 85. K. Anderko and U. Zwick, Naturwiss., 1957,44, 510. 86. K.Anderko, Natwwiss., 1957,44,88. 87. M.B. Waldron, J. Inst. Metals, 1951,79, 103. 88. K. Robinson, Acta Cryst., 1952,5,401. 89. G.Phragmen, J. Inst. Metals, 1950, 77, 489. 90. E. Hellner, Z.Metallk., 1950, 41, 401. 91. E. S. Makarov, Izvest. Akad. Nauk S.S.S.R., 1943, (Khim), 264. 92. J. Reynolds, W. A. Wiseman and W. Hume-Rothery, J . Inst. Metals, 1952,80, 637. 93. E. Hellner and F. Laves, Z . Naturforsch., 1947 (A), 2, 180. 94. P. G. Cotter, J. A. Kohn and R. A. Potter, J . Amer. Ceram Soc., 1956,39, 11. 95. H. Schachner, H. Nowotny and R Machenschalk, Monatsh, 1953,84,677. 96. P. Pietrokowsky, Acta Crysta., 1954,7, 435. 97. W. H. Zachariasen, Acta Cryst., 1949, 2, 94. 98. G.Brauer and H. Haag, Z . anorg. Chem., 1949,259, 197. 99. 0.J. C. Runnals and R. R. Boucher, Acta Cryst., 1955,8, 592 100. H. Schachner, E. Cerwenka and H. Nowotny, Mmatsh., 1954, 85, 245. 101. H. Nowotny, R. Kieffer and H. Schachner, Monatsh., 1952,83, 1243. 102. P. Eckerlin and E. Wolfel, Z . Anorg. Chem., 1955, 280, 321. 103. K. Schubert and H.Pfisterer, Z . Metallk., 1950,41,438. 104. A. Osawa and M. Okamoto, Sci. Rep. Tohoku Imp. Uniu., 1939,(i), 27, 326. 105. B. Boren, Arkiu. Kemi MheraJ. Geol, 1933,11A, (lo), 1. 1%. K. Toman, Acta Cryst., 1951, 4,462. 107. S. Geller and E. A. Wood, Acta Cryst., 1954, 7, 441. 108. K. Anderko and K. Schubext, 2.Metallk., 1953, 44, 307. 109. J. H. Buddery and A. J. E. Welch, Nature, 1951,167,362. 110. K. Schubert, Natwwiss., 1952,39,351. 111. G.Bergman and J. L. T. Waugh, Acta Cryst., 1953,6,93. 112. K. Robinson, Acta Cryst., 1953, 6, 854. 113. K.Robinson and P. J. Black, PhiL Mag., 1953, 44, 1392. 114. P. Eckerlin, H. J. Meyer and E. Wolfel, 2. anorg. Chem, 1955, 281, 322. 115. E.ParthC and J. T. Norton, Acta Cryst., 1958,11,14. 116. P. I. Kripyakevich, E. I. Gladyshevskv and 0. S. Zarechnyuk, Dokl. Akad. Nnuk., S.S.S.R., 1954, 95,525. 117. K. Schubert and H. msterer, 2. MetaNk., 1951,41, 433. 118. E. Hellner, Fortschr. Mineral, Krist. Petrogr., 1951, 29-30, 59. 119. A. Westgren and G. Phragmen, Z . anorg. Chem., 1928, 175,80. 120. 0.Carlssohn and G. Hagg, Z . Krist., 1932, 83, 308. 121. S. T. Knobejewski and W. P. Tarassova, Zh.fiz. Khim. (J. phys. Chem.), 1937,9, 681. 122. H. Knodler, Acta Cryst., 1957,10, 86. 123. H.Nowotny and H. Schachner, Monatsh., 1953, 84, 169. 124. A. Zalkin and W. J. Ramsey, J . phys. C h a , 1956, 60,234. 125. idem, J. phys. Chem., 1956,60, 1275. 126. R E. Marsh and D. P. Shoemaker, Acta Cryst., 1953, 6, 197. 127. D.Gilde, Z. anorg. Chem., 1956,ZS4,142 128. P. Farrar and H. Margolin, Trans. A m . I@. mia (metall.) Engrs, 1955,203,101. 129. R D.Heidenreich, Acta Met., 1955, 3, 79. 130. K Bachmayer, H.Nowotny and A. Kohl, Monntsh., 1955,86,39. 131. H. Nowotny, R. Funk and J. Ped, Monatsh, 1951,82,513. 132. K. E. Fylking, Arkiv. Kem. Min. Geol., 1935, (B), 111 (48), 1. 133. H. Cole, F. W. Chambers and H. M. Dum, Acta Cryst., 1956, 9, 685. 134. H.Nowotny and B. Glatzl, Monatsh., 1951,82,720. 135. K. H.Jack and M. M. Wachtel, Proc. Roy. SOC.,1957, A, 239,46. 136. R. Ferro, Acta Cryst., 1956,9, 817. 137. Le Roy Heaton and N. S. Gingrich, Acta Cryst., 1955, 8, 207. 138. R. N. Kuzmin, G. S. Khdanov and N. N.Zhuravlev, KristaNografya, 1957,2, 48. 139. A. Osawa and N. Shibata, Sci. Rep. Tohoku Imp. Uniu., 1939, (i), 28, 1, 197. 140. W. Hofmann, 2.Metallk., 1941,33, 61. 141. R. Ferro, Acta Cryst., 1957, 10, 476. 142. W. P. Binnie, Acta Cryst., 1956, 9,686. 143. J. L. Hoard,S. Geller and R. E. Hughes, J . Am c h m Sm., 1951, 73, 1892. 144. A. W. Laubengayer, D.T. Hurd, A. E. Newkirk and J. L. Hoard, J. Am chem Soc., 1943,65, 1924. 145. St. v. N. Szabo and C. W.Tobias, 1. Am chem SOC.,1949, 71, 1882.

Structures of metals, metalloids and their compounds

M 9

146. V. Russell, R. Hirst, F. A. Kanda and A. J. King, Acta Cryst., 1953, 6, 870. 147. B. Post and F. W, Glaser, J. chem Phys., 1952, 20, 1050. 148. B. F. Decker and J. S. Kosher, Acta Cryst., 1954,7, 77. 149. P. Ehrlich, Z. anorg. Chem, 1949, 259, 1. 150. R. Kiessling, Acta Chem Scand., 1950, 4, 164. 151. F. W. Glaser and B. Post, J. Metals, 1953, 5, 1117. 152. D. Moscowitz, Trans. A m . Inst. min (metall.) Engrs, 1956,206, 1325. 153. F. Bertant and P. Blum, Compt. Rend., 1953, 236, 1055. 154. Stig Rundqviet, Nature, 1958, 181, 259. 5 5 . R. W. Mooney and A. J. E. Welch. Acta Cryst., 1954, 7, 49. 156. M. von Stackelberg, Z.physical Chem, 1930,4 9,437. 157. E. B. Hunt and R. E. Rundle, J. Am. chem. Soc., 1951, 73, 4717. 158. H. A. Wilhelm and P. Chiotti, Trans, Amer. Soc. Metals, 1950, 42, 1295. 159. R. E. Rundle, N. C. Baenziger, A. S. Wilson and R. A. McDonald, J. Am. chem. SOC.,1948, 70, 99. 160. U. Esch and A. Schnieder, 2. anorg. Chem, 1948, 257, 254. 161. L. M. Litz, A. B. Garrett and F. C. Croxton, 1.Am. chem. Soc., 1948, 70, 1718. 162 M. W. Mallett, A. F. Gerds and D. A. Vaughan, J . electrochem. Soc., 1951.98, 505. 163. G. Brauer, H. Renner and J. Wernef Z. anorg. Chem., 1954,277, 249. 164. V. I. Smirnova and B. F. Ormont, Dokf. Akud. Nuuk. SSSR, 1954.96, 557. 165. K. H. Jack, Proc. Roy. Soc., 1948, 195, 56. 166. L. J. E. Hofer, E. M. Cohen and W.C. Peebles J . Am chem Soc., 1949, 71, 189. 167. K. H. Jack, Acta Cryst,, 1950, 3, 392. 168. N. Schonberg, Acta Met., 1954, 2, 837. 169. S . Nagakura, J. phys. SOC.Japan, 1957, 12,482 170. K. Whitehead and L. D. Brownlee, Planseebur, Puluermet, 1956, 4, 62. 171. K. H. Jack, Acta Cryst., 1952, 5, 404. 172. H. A. Eick, N. C. Baenziger and L. Eyring, J . Am chem Soc., 1956, 78, 5987. 173. R. Jusa, H. H. Weber and C. Meyer-Simon, 2 . unorg. Chem., 1953, 273, 48. 174. G.Brauer and K. H. Zapp, Naturwiss, 1953, 40,604. 175. U. Zorll, Z. Physik, 1954, 138, 167. 176. R. Ferro, Z . anorg. Chem., 1954, 275, 320. 177. 0. Knop and H. Haraldsen, Canad. J . Chem., 1956, 34, 1142. 178. J. Singer and C. W. Spencer, Trans. Amer. Inst. min. (metall.) Engrs, 1955, 203, 144. 179. S.A. Semiletov, Kristallografiya, 1956, 1,403. 180. P.Khodadad and J. Flahaut, Compte rendu., 1957,244,462. 181. S . Geller and B. B. Cetlin, Acta Cryst., 1955, 8, 272. 182. H. Hahn and K. F. Schroder, 2. anorg. Chem.,1952,269, 135. 183. H. Haraldsen, Z. anorg. Chem, 1941, 246, 169. 184. K. Schubert, E. Dorre and M. Kluge, 2 . Metallk., 1955,46,216. 185. L. I. Tatarinova, Yu K. Auleitner and Z. G.Pinsker, Kristaflografiya, 1956, 1, 537. 186. H. Miyazawa and S. Sugaike, J. phys. Soc. Japan, 1957, 12, 312 187. A. Okazaki and I. Ueda, 1.phys. Soc. Japan, 1956, 11,470. 188. K. Schubert and H. Frieke, 2. Metalfk., 1953, 44, 457. 189. Structure Reports, 1951, 11, 246. 190. A. Brystrom, Arkiu Ked. Mineral. Geol., 1945, 1 9 4 No. 8. 191. A. R. Graham,Amer. Mineralogist, 1949, 34,462. 192. F. Bertaut, Compt. rend., 1952, 234, 1295. 193. H. Hahn, Z. anorg. Chem, 1951,264, 184. 194. D. Lundqvist, Arkiv Kern’. Mineral.Geol., 1943, 17B, No. 12. 195. N. V. Belov and V. P. Butuzov, Dokl. Akud. Nauk. SSSR, 1946,54, 717. 196. R. Ueda, J. Phys. Soc. Japan, 1949,4, 287. 197. Structure Reports, 1952, 12, 156. 198. K. Schubert, E. Dorre and E. Giiml, Naturwiss., 1954, 41,448. 199. K. Toman, Acta Cryst., 1952, 5, 329. 200. H. Haraldsen, Z.anorg. Chem, 1939, 240, 337. 201. R. F. Raeuchle and R. E. Rundle, Acta Cryst., 1952, 5, 85. 202. B. G.Bergman and D. P. Shoemaker, J . chem. Physics, 1951, 19. 515. 203. J. S . Kasper. B. F.Decker and J. R. Belanger, J . appl. Physcs, 1951,22,361. 204. W. B. Pearson and J. W. Christian, Acta Crysr., 1952, 5. 157. 205. Y.-C. Tang, Acta Cryst., 1951, 4, 377. 206. A. Schneider and U. Esch. Z.Elektrochem., 1944,50, 290. 207. F. H. Spedding, A. H. Deane, G. Wakefield and B. H. Dennison, Trans. metall. SOC. A.I.M.E., 1960, 218, 608. 208. F. H. Spedding, A. H. Deane and J. J. Hanah, Trans. metall. Soc., A.I.M.E., 1959, 212, 179. 209. E. M. Savitsky, V. F. Terekhova and I. V. Burov, Tswt. Metally, 1960, 33, 59. 210. E. M. Savitsky, V. F. Terekhova and 0. P. Naumking, Tstiet. Metally, 1960,33,43. 211. D. V. Keller, F. A. Kanda and A. J. King, J . phys. Chem., 1958,62, 732. 212 A. Zalkin, R. G. Bedford and D. E. Sands, Acta Cryst., 1959, 12, 701. 213. R. M. Paine and I. A. Carrabine, Acta Cryst., 1960, 13, 680. 214. E. F. Sturken and B. Post, Acta Cryst., 1960, 13, 852.

670 215. 216. 217. 218. 219. 220. 221. 222. 223. 224. 225. 226. 227. 228. 229. 230. 231. 232. 233. 234. 235. 236. 237. 238. 239. 240. 241. 242. 243. 244. 245. 246. 247. 248. 249. 250. 251. 252. 253. 254. 255. 256. 257. 258. 259. 260. 261. 262. 263. 264. 265. 266. 267. 268. 269. 270. 271. 272. 273. 274. 275. 276. 277. 278. 279. 280. 281. 282. 283. 284.

Crystal chemistry

W. H. Zadareisen and F. H.Ellinger, Acta Cryst., 1959, 12, 175. D. B. McWhan, US Atom’c Energy Comm. Publn, UCRL 9695, 1964. A. Zalkin, D. E. Sands and A. H. Krikorian, Acta Cryst., 1960, 13, 160. idem, Acra Cryst., 1960, 13, 713. S. A. Spakner, Trans. metall. SOC.A.I.M.E., 1958, 212, 57. R. M.Paine and J. A. Carrabine, Acta Cryst., 1960, 13, 680. B. J. Baudry, J. F. Haufling and A. H. Daane, Acta Cryst., 1960, 13, 743. R. I. Myklebist and A. H. Deane, Trans. metall. SOC.A.I.M.E., 1962, 224, 354. N. H. Krikorian, W. G. Witteman and M. S. Cowme, J . phys. Chem, 1960, 64, 1517. B. A. Hatt, Acta Cryst., 1961, 14, 119. V. F. Novy, R. C. Vickery and E. V. Kleben, Trans. metall. Soc. A.I.M.E., 1961, 221, 585. G. Katz and A. J. Jacobs, J. nucl. Mater., 1962, 5, 338. F. R. Morral, J. Metals., N X , 1958, 10.662. D. J. Cromer and A. C. Larsen, Acta Cryst., 1961, 14, 1226. S. Saito, Acta Cryst., 1959, 12, 500. M.Korchynsky and R. W. Fountain, Trans. metall. Soc. A.I.M.E., 1959,215, 1053. B. J. Baudry and A. H.Daane, Trans. metall. Soc. A.I.M.E., 1960,218, 854. S. E. Haszko, Trans. metall. Soc. A.I.M.E., 1960, 218, 763. D. T. Cromer and G. E. Olsen, Acta Cryst., 1959, 12, 689. V. F. Novy, R. C. Vickery and E. V. Kleben, Trans. metall. Soc. A.I.M.E., 1961, 221, 585. idem. Trans. metall. SOC.A.I.M.E., 1961, 221, 588. G.A. Yurks, J. W. Barton and J. S. Parr, Acta Crysr., 1959, 12, 909. D. Kramer, Trans. metall. Soc. A.I.M.E., 1959, 215, 256. J. F. Smith and W. L. Laram, Acta. Cryst., 1962, 15, 252. D. T. Cromer and A. C. Larsen, Acta Cryst., 1950, 13,909. D. T. Cromer and C. E. Olsen, Acta Cryst., 1959, 12,689. D. T. Cromer and R. B. Roof, Acta Cryst., 1959, 12,942. S. Saito and P. A. Beck, Trans. metall. Soc. A.I.M.E., 1959, 215, 938. E. Rudy, B. Kieffer and H.Frohlich, Z. Merallk., 1962, 53, 90. W. Obrowski, Z. Metallk., 1962, 53, 715. A. F. Bemdt, Acta Cryst., 1961, 14, 1301. V. B. Crompton, Acta Cryst., 1958, 11, 446. E. A. Wood and V. B. Compton, Acta Cryst., 1958, 11, 429. A. E. Dwight and P. A. Beck, Trans. metall. SOC.ALM.E., 1959, 215, 976. J. R. Thomson, Proc. 11th Amer. Coqf on X-Ray, 1963. W. Koster and W. D. Hackl, Z. Metallk., 1958-59, 12, 647. E. A. Hatt and G. I. Williams, Acta Cryst., 1959, 12, 685. W. Obrowski, Metall., 1963, 17, 108. A. C. Larsen and D. T. Cromer, Acta Cryst., 1961, 14, 514. idem, Acta Cryst., 1961, 14, 73. D. T. Cromer, k C. Larsen and R B. Roof, Acta Cryst., 1960, 13, 913. S. C. Haszko, Trans. metall. Soc. A.I.M.E., 1960, 218, 4, 763. E. Ence and M. Mayoln, Trans. metall. SOC.A.I.M.E., 1961, 221, 370. R. P. Rand and L. D. Calvert, Canad. J. Chem, 1962,40, 705. E. 0. Hall and J. Royan, Acta Cryst., 1959, 12, 607. D. Watanabe, J. Phys. SOC. Japan, 1960, 15, 1251. P. Chiotti and K. J. Gill, Trans. metall. SOC.A.I.M.E., 1961, 221, 573. idem. Trans. metall. SOC.A.I.M.E., 1959, 215, 892 D. R. Petersen and H. W. Rim, Acta Cryst., 1961, 14, 328. C. L. Vold, Acta Cryst., 1961, 14, 1289. W.Heine and U. Zwicker, 2.Metallk., 1962, 53, 386. E. Giinzcl and K. Schubert, 2.Metallik., 1958,49,234. R. V. Schablaski, B. S. Tani and M. G. Chesaaov, Trans. metall. Soc. A.I.M.E., 1962, 224, 867. S. Samson, Nature, Lond., 1962, 195, 259. D. V. Masson and C. S. Barrett, Trans. metall. Soc. A.Z.M.E., 1958, 212,260. E. I. Duwcll and N. C. B a d g e r , Acta Cryst., 1964 13, 476. W. Rostowker, Trans. metall. SOC.A.I.M.E., 1958, 212, 393. R. F. Domagala, R. P. Elliott and W. Rostotier, Trans. metall. SOC.A.I.M.E., 1958, 212, 393. S. Sansom, Acta Cryst., 1958, 11, 857. T. Dagenham, Acta Chem. Scand., 1963, 17, 267. L. M. d’Alte da Veigeq Phil. Mag., 1962, 7, 1247. A. J. Goldat and J. G. Pair, Trans. metall. Soc. A.Z.M.E., 1961, 221, 639. C. J. Wilson and D.Sand, Acta Cryst., 1961, 14, 72. T. J. Rensuf and C. A. Beevers, Acta Cryst., 1961, 14,469. C. G. Wilson, D. K. Thomas and F. J. Spooner, Acta Cryst., 1960, 13, 56. C. G. Wilson and F. J. Spooner, Acta Cryst., 1960, 13, 4, 358. L. E. Edshammer, Acta Chem Scand., 1961, 15,403. idem, Acta Chem. Scand., 1960, 14, 2248. C. R. McKinsey and G. M.Faubring, Acta Cryst., 1959, 12,701. J. W. H. Clare, J. Inst. Mab., 196041,89,232.

Structures of metals, metalloids and their compounds

6-71

285. J. A. Bland and D. Clarke, Acta Cryst., 1958,11,231. 286. J. H. Bland, Acta Cryst, 1958, 11, 236. 287. M. A. Taylor, Acta Cryst., 1959,12, 393. 288. idem, Acta Cryst., 1961, 14, 84. 289. L.M.d‘Alte de Veiges and L. K. Walford, Phil. Mag., 1963, 8, 349. 290. W. Obrowski, Metall., 1963, 17, 108. 291. K. Andutro, Z.Metallk., 1958,49, 165. 292. R. Ferro, Acta Cryst., 1958,11, 731. 293. S. Bhan and K. Schubert, Z . Metallk., 1960,51, 327. 294. E. I. Gladishevsky, Dopov., Akad. Nauk ukr. R.S.R., 1959, 3,294. 295. E. Panhb, Acta Cryst., 1959,12, 559. 296. B. J. Baudry and A. H. Daane, M.A., 1962,443. 297. L. M.Finme, J . less common Metals, 1962,4, 24. 298. E.Parthb, Acta Cryst., 1960,13,968. 299. E. I. Gladishevsky, Dopov. Akad. Nauk ukr. R.S.R., 1959, 3, 294. 300. N. Ageev and V. Samsonov, Dokfady Akud. Nauk S.S.S.R., 1957, 112, 853. 301. A. G. Tharp, A. W. Searcy and H. Novofkny, J. Electrochem Soc., 1958, 105,473. 302. E.Raub and W.Fuzsche, Z.Merallk, 1962,1962,53779. 303. E. Weitz, L. Born and E. HelIness, Z . Metallk., 1960, 51, 228. 304. D. M.Bailey and J. F. Smith, Acta Cryst., 1961,14, 57. 305. A. Zalkin and W. J. Ramsey, J . Phys. Chen, 1958,62,689. 306. D.T.Cromer, Acta Cryst., 1959, 12, 36. 307. W. Trzebratowski, S. Weglowski and K. Lukasgewag, Roczniki Chem., 1958,32,189. 308. J. H. Bryden, Acta Cryst., 1962,15, 167. 309. C. Giesecki and H. Pfister, Acta Cryst., 1958,11, 369. 310. A. Kockus, F. Gronvolde and J. Thorbioin, Acta Chem. Scand., 1962,16, 1493. 311. V. N. Bykoff and V. V. Kazarnikov, Kristallografya, 1959, 4,924. 312, I. Obinata, Y. Takechi and S. Saikewa, Trans. Amer. SOC.Metals, 1959,52, 156. 313. J. L. Hoard, R. E. Hughes and D. E. Sands, J . Am. chem Soc., 1958,80,4507. 314. D. E. Sands, C. F. Cline, A. Zalkin and C. L. Hoenig, Acta Cryst., 1961,14, 309. 315. G. V. Samonov, V. P. Dzeganovsky and I. A. Simashko, Kristallografya, 1959,4, 119. 316. Y. B. Paderno, T. I. Serebaykova and G. V. Samsonov, Dokl. Akad. Nauk S.S.S.R., 1959, 125, 317. 317. B. 3. MacDonald and W. I. Stuart, Acta Cryst., 1960, 13,447. 318. M.Elfstrom, Acta Chem Scand., 1961, 15, 1178. 319. S. Laplace and B. Poste, Acta Cryst., 1962, 15, 97. 320. W. Obrowski, Metafl., 1963,17, 108. 321. E. Steinberg, Acta Chem Scund., 1961, 15, 861. 322. B. Magnussen and C. Brossit, Acta Chem Scund., 1962,16, 449. 323. M.Atoji, K. G. Schneider, A. H. Waane, R. E. Rundle and F. H. Spedding, J . Am. chem. SOC., 1958,SO, 1804. 324. G. Brauer and K. Lesser, Z. Metallk., 1959, SO, 8. 325. S. Naeakura. J. =vhvs. Soc. Javan. 1959. 14. 186. I 326. idem, y. phys. SOC.Japan, 1981,i6, 12i3. 327. W. D.Forgang and B. F. Decker, Trans. metall. SOC.A.I.M.E., 1958,212, 343. 328. F. Gronwold, A. Kietshus and F. Raun, A n a Cryst., 1961, 14, 93. 329. D. Pustiner and R.-E. Newnham, Acta Cryst., 1961,14, 691. 330. M.S. Mirgalowskaya and E. V. Skudnova, Izu. Akud. Nauk S.S.S.R., 1959,4, 148. 331. A. Stechen and P. Eckerlin, Z . Metallk., 1960, 51, 295. 332 E. F. Hockiup and J. C. White, A n a Cryst., 1961, 14, 328. 333. E. Parthi, Acta Cryst., 1960, 13, 865. 334. P. Khodad, C. R. Akud. Sci., P m k , 1960,250,3998. 335. idem, C.R . Akud. Sci, Puris, 1959,249, 694. 336. A. Okasaki, J . phys. SOC.J a p q 1958, 13, 1151. 337. E. A. Wood, V. B. Compton, B. T. Matthias and E. Carengurt, Acta Cryst., 1958, 11, 604. 338. W. Klemm, F. Dam and R. Huck, Naturwiss, 1958,45,490. 339. J. A. John, G. K a u and A. A. Giardini, 2.Krisr., 1958, 111, 52. 340. W. Kronert and K. Plieth, Nufurwiss., 1958,45, 416. 341. H. H. Stadelmeier and W. K. Hardy, Z . Metallk., 1961, 52, 391. 342. M.V. Nevitt and J. W. Downey, Trans. metall. SOC.A.I.M.E., 1962, 224, 195. I

See also: ‘Pearson’s Handbook of Crystallographic Data for Intermetallic Phases’ (3 volumes) by P. Villars and L. D. Calvert, published by ASM, 1985 (new edition pending).

7 Metallurgically important minerals Table 7.1 gives data on the minerals from which the more important metals are. extracted. Those minerals of major importance are shown in bold type in column 2. Parentheses indicate that the element is recovered as a by-product in the extraction of another metal. The chemical formulae assigned in column 3 are given only to indicate the nature of the minerals since they are not stoichiometric chemical compounds. The mineral-producingcountries are listed in order of decreasing production in column 6, and the major metal producers in column 8. The figure for abundance given in column 1 is the amount of the metal in parts per million of the igneous rocks of the lithosphere. The figure for metal production in column 9 refers to refined primary metal production, except where indicated as contained metal in produced ores or concentrates, or as including secondary refined production. The figure for reserves given in column 10 is the recoverable material in the reserve base that can be economically extracted or produced at the time of determination.

BEiLIOGRAPHY Mineralogicai data

P. Crowson, ‘Minerals Handbook 7-1, 1986-87, MacMillan, Basingstoke, 1986. C. Palache, H.Berman and C. Frondel, ‘Dana’s System of Mineralogy’, 7th edn, Chapman and Hall, London: Vol. I, 1944, Voi. 11, 1951. W. E. Ford, Textbook of Mineralogy’, 4th edn, Wiley, New York, 1957. H. H. Read, ‘Rutley’s Elements of Mineralogy’, 25th edn, George Allen and Unwin, London, 1962. M. P. Jones and M. G. Fleming, ‘Identification of Mineral Grains’, Elsevier, London, 1965. ‘Mineral Facts and Problems Bulletin 630’, Bureau of Mines, US Department of the Interior, Washington, 1965. S. J. and M. G. Johnstone, ‘Minerals for the Chemical and Allied Industries’, 2nd edn, Chapman and Hall, London, 1961. V. M. Goldschmidt, ’Geochemistry’ (Ed. A. Muir), Oxford University Press, 1954. D’Arcy George, ‘Mineralogy of Uranium and Thorinm Bearing Minerals’, US Atomic Energy Commission, RMO 563, 1949. G. Frondel ‘SystematicMineralogy of Uranium and Thorium’, Geological Survey Bulletin 1064, US Department of the Interior, 1958. K. A. Vlasov, ‘Geochemistry and Mineralogy of Rare Elements and Genetic Types of Their Deposits’, Israel Programme for Scientific Translations, Jerusalem, 1968. W. Uytenbogaart and E. A. J. Buske, ‘Tables for Microscopic Identification of Ore Minerals’, 2nd edn, Elsevier, Amsterdam, 1971.

Economicfactors W. Ryan, ‘Non-ferrous Metallurgy in the UK’, Institution of Mining and Metallurgy, London, 1968. J. D. Gilchrist, ‘Extraction Metallurgy’, Pergamon Press,Oxford, 1967. Kirk-Othmer, ‘Encyclopedia of Chemical Technology’, 2nd edn, Interscience, New York, 1970. ‘Mineral Commodity Summaries 1988’, US Bureau of Mines, 1988. ‘Mineral Commodity Summaries 1989’, US Bureau of Mines, 1989. ‘Mining Annual Review, 1979’, Mining Journal, London, 1979. ‘Mining Journal’, London. ‘Metal Bulletin’, London. ‘World Mineral Statistics, 1972-76‘, Institute of Oeological Sciences, HMSO,London, 1979. ‘World Metal Statistics’, World Bureau of Metal Statistics, London.

7-1

Table 7.1 ORE GRADES AND SOURCES

4 I"

EIement abundance D.0.m.

Minerals

1

Aluminium 81 300

Formulae

Mefal content %

Spc@ gravity Majar mineral ~ c m - ~ sources

2

3

4

5

Bamite

Hydrous aluminium and iron oxides

25-39

2.55

WorId reserves 1983J84 ('W World tonnes production metal (tonnes) of contained metal)

Normal ore grade

Major metal sources

4

7

8

Australia, Guinea, Jamaica, Brazil, USSR, Yugoslavia

25-39% AI

USA, USSR, 15.1~10~ 20954000 Canada, W. Germany, Narway

% .-. B m

'9. $'

I

1

Senarmotite Valentinite Kennesite Stibnite

Arsenic

(A-wWe)

Antimony

2

China, Bolivia, S. Africa, USSR, Mexico, Thailand

%25%

71.7

40-49.9 60.9 70

5.9-6.3 3.49 3.48-3.56

chile, USA, Canada, France, Mexico, Philippines

2-I5% AS

(Orpiment) (Realgar) and Arsenides of Cu, Pb, Au, Sn)

15-23 (in flue dusts)

Bwtnndite

15.1 5

2.59-2.66 2.7

Brazil, India, USSR, Argentina, USA, S. Africa

0.1-0.6% Be

USA, USSR, Brazil, Zimbabwe, Portugal, Argentina

341

0.381

9.7-9.8

Australia, Japan, Mexico, Peru, China

0.0548% Bi

Australia, USA, Peru, Japan

4.3~103

92

Beryl

2 Bismuth

(Native bismuth)

Bi

100

BismDthinite

BizS3

81.2

6.4-6.5

Traceto

-

(0.2)

Cadmium

(in Sphalerite)

1.66 (0.15)

49.6 x lo3

IO

5.3 5.60 4.60 4.5-4.6

84 84 15.3

(s& .-

Beryllium

China, Turkey, Peru, Bolivia

9

Canada, USSR, Australia, Peru, USA, Mexico

Sb

4170

=z

w

5.. B

3 -. a 2 a i;

in Pb,Cu, Sn ores

0.1-0.3% Cd (in sphalerite)

USSR, USA, Sweden, France, Mexico. Chile

39403

loo0

(as trioxide containing 76% As)

(metal+ in ores and concentrates)

18.4~103 USSR, Japan, (includes USA, Canada, Belgium, W. Germany secondary)

555

Calcium

Limiom Brines

Chiefly CaCO,

36 300

Cerium

40 3.6

2.71

Worldwide

Pure

Bastnaesite Monazite

(Ce, La, Di)(C03)F (Ce, La, Y,Th) PO.,

4.9-5.2 4.6-5.4

Australia, India, Brazil, S. Africa, USA, Malaysia

0.1-3'% Ce

46

Chromite

FeCr,O,

38.246.5

4.5-4.8

S. Africa, USSR, Zimbabwe, Finland, Philippines, India

2 0 4 5 % Cr

13-28 11-21.7 13.8-24 54 18.8-26.6 13

6.9-7.3 6.5-6.9 5.7-6.8 4.1 3.06 2.8-4.4

Zaire, Cuba, 0.1-1% Zambia, New Caledonia, Indonesia, USSR

Variable

3.44 6.0-6.3 4.8 4.8-5.0

50

200

Cobalt 25

copper 70

-

Vast

37 x 103

-

(Variable)

(25)

Chromium

USA, Franm, W. Germany

(satnoritc) (Skattdte) (Smaltite) (Sphaerocobaftite) (Erythrite) (Asbolite) (Heterogenite) (Cobaltite) (CarroUite) (Linnaeite)

28.5-35.5 35-36 58

Native copper Aacrite Malachite Cuprite Chrysoeoll. Brochantite Chalcanthite Atacamite Chhite Bornite Chalcopyrite Covellite Enargite Tennantite Tetrahedrite

100 55 58 88.8 36.2 56 25 59.4 79.9

63.5 34.6 66.7 45.7-49.0 57.5 var. 25.e45.7

8.95 3.77 4.05 5.9-6.2 2.0-2.2 3.97 2.1-2.3 3.76 5.5-5.8 4.9-5.4 4.1-4.3 4.6-4.76 4.45 4.4-4.5 4.6-5.1

Chile, USA, Zambia, Zaire, USSR, Mexico, Canada, Peru

(rare earth oxides)

co

0.3-5% CU

USSR, USA, Japan, UK USSR, Australia, Canada, W.Germany (estimated order)

3 x lo6 (metal + alloys)

1056 x lo3

19789

3 595

(excl. USSR)

USA, USSR, 9.6~10~ Japan, Chile, Zambia, Canada, Belgium, W. Germany

337x lo6

5

-,

e T

4

*China unknown. Probably large.

I?

Table 7.1 ORE GRADES AND SOURCES-continued

Element abundance p.p.m.

Metal content Minerals

Formulae

Spec@c

gravity

%

Major mineral sources

Normal ore grade

Major metal sources

World reserves 1983184 (TKOs World tonnes production of contained metal (tonnes) metal)

2 -5

3a a,

Q

Gallium 15

(Gallite) (in Bauxite) (in Coal ash) (in Germanite) (in Sphalerite)

CUGaS,

35.5

4.2

-0.3210-* ( t - ICCJ)~. Betwan 315°C and 505°C d~=2.6224.26810-3( t - 1oO)-0.3~10-a (1-100)'+8.8.10-'*(t-1CCJ~-3.~10-'~

(~-~ccJ)S.

REFERENCES TO TABLE 9.1

1. I. Pierre, Ann. Ckim. (Php.), 1845, IS,325. 2€ Kopp, I. Ann. Chem., 1855,%, 307. 3. H. Kopp, ibid, 1855,9!5,350. 4. Roscoe, Phil. Tram. R. Soc., 1868, 158, 1. 5. Hannay, J . chem SOC, 1873, 26, 815. 6. R. W. E. MacIvor, Chem. News, 1874, 29, 179. 7. Ditte, Compz. rend., 1877, 85, 1069. 8. Nat. Res. Council, USA, 'International Critical Tabks', voL 3, p. 23, 1928. 9. Lecoq de Boisbaudran, Chem. News,1881,44, 166; Compt. rend., 1881,93,294, 329, 815. 10. Rodwell, Phil. Trans. R. SOC.,1882, 173, 1125. 11. L'HGte, Compt. rend, 1885, 101, 1151. 12 H. Moissan, ibid., 1891, 112, 718. 13. Mond and Nasini, Z.phys. Chem., 1891,8, 150. 14. J. W. Retgers, ibid, 1893, 11, 328. 15. Ghira, ibid., 1893, 1% 765. 16. E. Brunner, 2.anorg. Chem., 1904,38, 350.

Physical properties of molten salts

9-5

17. 0.Ruff and W.Plato, Ber. dt. chem. Ges., 1904, 37, 679. 18. H. M. Goodwin and R D. Mailey, Phys. Rev., 1907, 2S, 469. 19. K. Amdt and A. Gessler, Z . Elekrrochem., 1908 14,665. 20. Z. Klemensiewicz, Bull. int. Acad., Cracovie, 1908, 487. 21. R. Lorenz, H.Frei and A. Jabs, 2. phys., Chem, 1908,61,468. 22. K. Arndt and W. Lowenstein, Z. Elekrrochem, 1909,lS, 789. 23. A. H.W. Aten, 2. phys. Chem., 1909,66,641. 24. A. H. W.Aten, ibid., 1910,73, 578. 25. Prandtl and Bleyer, 2.anorg. Chem., 1910,66,152. 26. E. B. R. Prideaux, J. chem. Soc., 1910,97,2032. 27. lzbekov and Plotnikov, 2.anorg. Chem., 1911,71, 328. 28. K.Arndt and Kunze, 2. Elektrochem., 1912, 18, 994. 29. Kbrber, Ann. Physik., 1912,37, 1014 30. Sackur, 2. phys. Chem, 1913.,1913,83,297. 31. N. S. Knmakov, Krotkov and Oksmann, J. Russ. Php-Chem. Soc., 1915,47,558. 32. E. Moles, Z.phys. Chem., 1915,90, 74. 33. R. Lorenz and A. HGchberg. Z. anorg. Chem., 1916,94,288. 34. F. M. Jaeger, ibid, 1917,101, 16. 35. F. M. Jaeger and B. Kapma, ibid., 1920,113,27. 36. V. M e r , J. Am. ckem. Soc, 1922,44, 1668. 37. Meyer and Heck, 2. phys. Chem., 1922, 100, 316. 38. W. Blitz and A. Voigt, 2. m r g . Chem, f923,126, 39. 39. Timmermans, Bull. SOC. Chim. Be&., 1923, 32,299. 40. A. Voigt and W. Blitz, Z . anorg. Chem., 1924,133,277. 41. N.S. Kurnakov, ibid, 1924, 135, 86. 42. Pascal and Allendorfi, ibid., 1924, 135, 327. 43. C.W.Muehlberger and V. Lenher, J . Am. chem SOC.,1925,47, 1843. 44. Samsocn, Compr. rend., 1925,181, 354. 45. K. Arndt, Z.phys. Chem, 1926, 121,448. 46. H.V. A. Briscoe, P. L. Robinson and Stephenson, J. chem. Soc., 1926,39. 47. W. Klemm, 2. anorg. Chem., 1926,192,235. 48. W.Klemm, ibid., 1926, 152,252. 49. W. Blitz and W . Klemm,ibid., 1926, 152, 267. 50. Friedrich, quoted by W. Blitz and W. Klemm, &id., 1926,152,267. 51. V. Lenher and C. H. KBO, J . A m ehem. Soc, 192648, 1550. 52. H.V. A. Briscoe, P. L. Robinson and H.C. Smith, J. chem. Soc., 1927,282. 53. Dortmann and Hildebrand, J. Am chem Soc., 1927,49, 737. 54. S. Sugden and A. Freiman, J . chem SOC. 1927, 1185. 55. Dantuma, 2. anorg. Chem, 1928, 175, 33. 56. E. B. R. Prideaux and C. B. Cox, J. chem Soc, 1928, 740, 1606. 57. W. J. R. Henley and S. Sugden, ibid., 1929, 1064. 58, F. B. Garner and S. Sugden, ibid., 1929,1298. 59. J. H.Simons, d . Am. chem SOC.,1930,S2, 3491. 60. E. Salstrom, ibid., 1930, 52, 4647. 61. A. Wachter and J. Hildebrand, ibid., 1930,S2, 4656. 62. E. Ogawa, Bull. Chem. SOC. Japan, 1931, 6, 315. 63. T. W. Parker and P. L. Robinson, J. chem. Soc., 1931, 1316. 64. 0.Ruff and A. Ascher, Z. anorg. Chem., 1931,196,417. 65. J. H.Simons and G. Jemop, J . Am. chem. Soc., 1931,S3, 1265. 66. E. van Aubef, Bull. Acad. Belg., 1932(5), 18, 692. 67. H.V. A. B r i m , P.L. Robinson and A. J. Rudge, J. chem Soc., 1932,2675. 68. 0.Ruff, A. Brader, 0. Bretshneider, W. Menzel and H. Plaut, Z . anorg. Chem., 1932,206,59. 69. W. Klemm and P. Heakel, ibid., 1932, 207, 73. 70. W. Klemm and W. Tilk, ibid., 1932,287,161. 71. H.Ulich, E Hertel and W . Nespital, 2. phys. Chem., 1932, B17,369. 72. E Salstrom, J. Am. chem. SOC.,1933,55, 1031. 73. T. Sugawa, Sci. Rep. TBhoku Univ., 1933, 22, 959. 74. British Aluminium Co. Ltd., 1934,private commun. 75. S. Karpachev, A. Stromberg and 0. Poltoratzkaya, J. phys. Chem. (USSR),1934,5,793. 76. W. Kwasnik, Diss, Breslau, T. H. 1934,p. 13. 77. K. Laybourne and W. Madgin, J . chem SOC.,1934, 1. 78. M. G.Malone and A. L. Ferguson, J . chem PhysSs, 1934,2, 99. 79. 0.Ruff and W. Kwasnik, 2. anorg. Chem., 1934,219, 65. 80, P. Drossbach, ‘Electrochemistry of Fused Salts’, Berlin, 1938. 81. N. S. Kurnakov, N. K. Voskresenskaja and G. D. Gurovic, Bull Acad. Sei., U.R.S.S.,ser chim, 1938, 396. 82. Lundina, quoted by V. P. Mashowts, ‘The Electro-Metallurgy of Aluminium’, Russia, 1938. 83. W. Treadwell et aL, Helu. Chim. Acta, 1939, 22, 445. 84. D.I. Zuravlev, J . Phys. Chem (USSR),1939,13, 684. 85. Y. P. Barzakovskii, Bull. Acad. Sei., U.R.S.S. (Cl. Sci chira), 1940, 825. 86. Y. P. Barzakovskii, J. appl. Chem. (USSR),1940, 13, 1117.

9-6

Physical properties of molten salts

87. S. T.Bowden and A, R. Morgan, Phil. Mag., 1940,29,367. 88. E. Ya Gorenbein, J. Gen. Chem (USSR), 1947, 17, 873. 89. E. Ya. Gorenbein, ibid., 1948, 18, 1427. 90. R. de Malleman and F.Suhner, Compt. rend., 1948,227,546. 91. N.K. Boardman, F. H. Dorman and E. Heymann, J. phys. Chem, 1949,53, 375. 92. G. Fuseya and K. Ouchi, J . Electrochem SOC.Japan, 1949, 17,254. 93. I. M. Bokhovkin, J. Gen. Chem (USSR), 1950, 20, 397. 94. S. E. Rogers and A. R. Ubbelohde, Trans. Faraday SOC., 1950,46,1051. 95. A. Vayna, AIluminio, 1950, 19, 541. 96. E. Y a Gorenbein and E. E. Kriss, J. phys. Chem. (USSR), 1951,25, 791. 97. R. C. Spooner and F. E. W. Wetmore, Canad. J . Chem., 1951,29, 171 98. J. D. Edwards, C. S. Taylor, A. S. Russell and L. F. Maranville, J. Electrochem Soc., 1952,99,527. 99. R. W. Huber, E. V. Potter and H. W.St. Clair, Rep. inuest. U S Bur. Mines No. 4-78,1952. 100. J. Byme, H.Fleming and F. E. W. Wetmore, Canad. J. Chem.,1952,30,922 101. E. F. Riebling J . Am. Ceram. Soc., 1964,47,478. 102. H. Bloom. I. W. Knaggs, J. J. Molloy and D. Welch, Trans. Faraday Soc., 1953.49,1458. 103. I. P. Vereshchetina and N. P. Luzhnaya, izuest. Sekt. Fiziko-Khfm. Anal., 1954, 25, 188. 104. J. S.Peake and M. R. Bothwell, J. Am. chem. Soc., 1954,76,2653. 105. V. D.Polyakov, Izvest, Sekt. Fiziko-Khim Anal., 1955,26,147. 106. V. D. Polyakov and S. I. Berul, ibid., 1955,26, 164. 107. V. D.Polyakov, ibid., 1955,26 191. 108. N.P. Popovskaya and P. I. Protsenko, Zh.fiz. Khim., 1955,29,225. 109. K. B. Moms, M. I. Cook, C. Z. Sykes and M. B. Templeman, J. Am. chem. SOC.,1955,77,851. 110. E. R. van Artsdalen and I. S. Yaffe, J. phys. Chem., 1955,59,118. 111. T. Baak, Acta. Chem. Scad., 1955, 9, 1406. 112. N.P. Luzhnaya, N. N. Evseeva and I. P. Vereshchetina; Zh. neorg. Khim., 1956, 1, 1490. 113. I. S. YaiTe and E. R. van Artsdalen, J. phys. Chem., 1956.60, 1125. 114. J. D. Mackenzie, Trans. Faraday Soc., 1956.52, 1564. 115. J. M. Blocher, R. F. Rolsten and I. E. Campbell, J. electrochem Sac., 1957,104,553. 116. N.N.Greenwood and K. Wade, J. Inorg. nuclear Chem., 1957,3,349. 117. F. R. Duke and R. A. Fleming, J. electrochem. SOC.,1957, 104,251. 118. S. Toshiaki and T. Ishibashi, Sci. Papers Coli. Gen. Educ., Uniu. Tokyo, 1957, 7, 53. 119. M. Bourgon, G. Derge and C. M. Pound, Trans. Amer. Inst. M i n Met. Eng., 1958,212,338. 120. F.J. Keneshea and D. Cubicciotti, J . phys. Chem., 1958,62,843. 121. A. D. Kirshenbaum and J. A. Cahill, J. inorg. nucl Chem., 1960,14,283. 122. I. S. Yaffe and E. R. van Artsdalen, Chem. Semi-Ann. Progr. Rep. No. 2159, Oak Ridge Natl Lab., 1956 p. 77. 123. A. D.Kirshenbaum, J. A. M i l l and C. S. Stokes, J. inotg. nucl. Chem., 1960,15,297. 124. P. I. Protsenko and A. Ya. Malakhova, Zh. neorg. Khim., 1961,6, 1662 125. K.B. Morris, M. McNair and G. K o o p , J. chem Engng Data, 1962,7, 224. 126 N.V. Smith and E. R. van Artsdalen, Chem. Semi-ann. Progr. Rep. No. 2159, Oak Ridge Natl Lab., 1956, p. 80. 127. N.N. Greenwood and I. J. Worrall, J. chem Soc., 1958,1680. 128. E. F. Riebling and C. E. Erickson, J. phys. Chem, 1963,67,307. 129. L. A. Nisel’son, Zh. neorg. Khim., 1961,6, 1242. 130. G.J. Janz and J. D. E. McIntyre, J. electrochem.Soc., 1962,109,842. 131. E. R. Buckle, P. E. Tsaoussoglou and A. R. Ubbelohde, Trans. Faraday SOC.,1964,60,684. 132. A. D.Kirshenbaurn, J. A. Cahill, P. J. McGonigal and A. V. Grosse, J. inorg. nucl. Chem., 1962,24,1287. 133. J. N.Reding, J. chem. Engng Data, 1965, 10,1. 134. K. B. Morris and P.L. Robinson, J. phys. Chem., 1964,68,1194. 135. K. B. Morns and P. L. Robinson, J. chem. Engng Data, 1964,9,444. 136. J. Padova and J. Soriano, ibid., 1964,9, 510 137. I. G. Murgulescu and S. Zuca, Acad. rep. pop. Romaine, Studii Cerc. Chim., 1959, 7, 325. 138. T.Kuroda and T. Suzuki, J. electrochem SOC.Japan, 1961,29,E215. 139. B. M.Lepinskikh, 0. A. b i n and G. A. Teterin,Zh. neorg. Khim, 1960,5,642 140. H.Schinke and F. Saverwald, 2. anorg. allgem. Chem., 1956,207,313. 141. G. J. Janz and M. R. Lorenz, J. electrochem Soc., 1961,108, 1052 142. J. P. Frame, E. Rhodes and A. R. Ubbelohde, Trans, Faraday Soc., 1959,s 2039. 143. A. Kvist and A. Lunden, 2.N w f o r s c h , 1965,uk,235. 144. J. O’M. Bockris, A. Pilla and J. L. Barton, Rev. Chim. Acad. Rep. Populaire. Romaine, 1962,7,59. 145. V. D.Polyakov, Izv. Sektova. Fiz. Khim Analiza Inst. Obshch.Neorgan, Khirn.Acad. Nauk SSSR,1955,26,173, 191. 146. E. Vogel, H.Schinke and F. Saverwald, Z. m g . allgem. Chem., 1956,284, 131. 147. J. O’M. Bockris, A. Pilla and J. L. Barton, J. phys. Ckem., 1960,64,507.

Physical properties of molten salts

9-7

Table 9.2 DENSITIES OF MOLTEN BINARY SALT SYSTEMS AND OTHER MIXED IONIC MELTS The density (gcm-') at temperature t("Q and composition p(wt.%)of the first-named constituent is given as d,, or theconstantsaandbintheequationd,=a-lO-' btorA,BandCintheequationd,=106At *-103Btr1+Care given together with the temperature range r("C).Principal references are in bold type. AgBr-AgC1 Ref. 25

AgBr-KBr Ref. 64 25, 7

AgBr-LiBr Ref. 65

AgBr-NaBr Ref. 66

b r

0 5262 0.94 480-630

27.8 5.523 1.08 440-580

46.9 5.678 1.12 420-590

71.6 5.832 1.07 420-580

100 6.025 1.04 440-600

P

0

U

b r

2.706 0.80 750-800

50.8 3.686 0.98 593-700

70.4 4.376 1.03 380-600

85.7 5.156 1.12 380-600

100 6.023 1.05 440-600

64.6 4.077 1.03 546-629

P a b r

68.5 4.504 0.877 517-555

P

64.6 4.311 0.9 607-619

0 4.167 1.00

9.00 4.242 1 .00

125 4.279 1 .00

15.5 4.297 1.00 310-330

20.0 4.338 1 .00

30.0 4.431 1 .00

40.0 4.497 0.90

0 1.988 0.60 785-880

63.8 3.286 0.88 560-745

80.3 4.001 0.96 385440

88.9 4.463 0.95 433-670

5.263 0.94 480-630

0 5.702 1.50 5 16-7 10

11.0 5.660 1.45 520-700

19.4 5.634 1.42 470-680

24.7 5.582 1.34 445-670

31.0 5.543 1.28 444-680

41.0 5.520 1.26 380-700

66.9 5.387 1.08 478- 660

20 4.53 1.2

30 4.97 2.2

40

50 5.12 5.31 2.1 2.1 about 1'50-300

60 5.44 1.8

70 5.53 1.5

324 1.721 1.01 210-290

37.0 1.762 1.05 160-290

46.8 1.843 1.10 160-290

51.2 1.930 1.15 190-290

68.4 2.003 1.15 190-290

14.2 2.032 1.14 210-290

13.8 5.826 1.58 160-240

19.9 5.732 1.46 160-240

27.2 5.584 1.46 100-240

35.9 5.364 1.46 120-240

46.6 5.188 1.40 100-240

52.8 5.074 1.34 109-240

67.9 4.930 1.28 120-240

15.7 2.284 0.76 350400

29.6 2.534 0.97 300-400

41.9

52.8

2.654 0.84 250-400

2.856 0.89 250-400

62.7 2.986 0.76 250-400

79.7 3.516 1.08 170-350

93.8 3.765 0.85 200400

0 2.124 0.70

10 2.226 0.71

20 2.357 0.77

30 2.486 0.79

60 2.974 0.70

80 3.439 0.90

P U

U

b r AgBr-RbBr Ref. 67

P U

b

r AgCI-AgNO, Ref. 33

P U

b r

AgCI-KCI Ref. 25, I

P a b r

AgCI-PbClz Ref. 25

P U

b r

AgI-AgNO, Ref. 54. 30

P a b r

P a b r AgNO,-HgI, Ref. 49

P a b

r AgNOs-KNOS Ref. 57,46

P U

b

r AgN03-NaN03 Ref, 37

P a

b r

53.2 4.470 1.23 514-624

100

40 2.616 0.79 about 290-370

9-8

Physical properties of molten salts

Table 9.2 DENSITIES OF MOLTEN BINARY SALT SYSTEMS AND OTHER MIXED IONIC MELTS-contimced

P d170 dirt0

AgN03-TINOS Ref. 26

P dl00 dl so dzoo

dzzs

AIBr,-HgBr2 Ref. 21, 4

P

AIBr,-KBr Ref. 28,4

P

2AIBr3-KCl Ref. 23

a

dl10 dido dim dl40

b

r AIBr,-NaBr Ref. 28

P

2AIBr3.NaBr Ref. 23

a

AIBr,-NH,Br Ref. 21

P

dl20 dl40

b r

0 1.432 1.426

5 1.479 1.474

10 1.529 1.523

25

50 4.630 4.526 4.410 4.351

60 4.554 4.435 4.319 4.261

-

90 -

-

-

4.638 4.579

45 4.671 4.575 4.452 4.406

4.183 4.132

4.074 4.024

3.922

59.7 3.577 3.504

65.4 3.415 3.359

71.2 3.276 3.202

74.9 3.173 3.097

80.5 3.030 2.961

89.6 2.827 2.755

100 2624 2555

81.8 2818 2775

83.2 2.815 2771

84.7 2810 2764

86.2 2.804 2.755

87.5 2.798 2.749

88.0 2.790 2.741

84.7 2.820 2.792

85.6 2.817 2.787

86.8 2.809 (2777)

87.9 2.798 2.767

88.9 2.786 2.756

87.9 2.865 1.40

89.0 2.877 1.45

89.4 2.881 1.50

90.8 2889 1.60

100 2.877 2.30

-

83.8 2.827 2.797 3.005 1.5 110-170

a

84.5 2.842

b

1.30

a

b

r AIBr,-SbBr, Ref. ZO, 4

P dioo d140

100

2.846 1.445 80-170

r 2AIBr, .NH4Br Ref. 23

75

110-150

2848 1.36 110-160 0 3.697 3.594

34.1 3.402 3.311

42.5 3.318 3.224

67.4 3.034 2941

71.9 2.971 2.881

91.3 2737 2.641

100 2.644 2556

AIBr3.SbBr, Ref. 32, 23

a

b r

3.541 2.3 80-170

AIBr, .SbBr3AsBr3 Ref. 32

P

0

d85 dl00

3.232 3.193

16.3 3.231 3.191

59.9 3.286 3.247

67.9 3.304 3.263

77.3 3.310 3.274

86.8 3.330 3.295

100 3.346 3.313

AlBr,-ZnBr, Ref. 20

P

70.5 3.014 2.915

74.5 (2.957) 2850

77.7 2914 2811

82.5 2.849 2.740

85.0 2.811 2.704

88.4 2.768 2.657

2.644

dl00

d1so

2A1Br3ZnBr, Ref. 23

t

100

d

3.01

140 2.93

180 2.81

AICIj-KCI** Refs. 63, 45, 29, 19

P

50.4 1.787 0.590 600-800

53.7 1.785 0.605 600-800

62.5 1.755 0.600 600-800

64.2 1.931 0.935 260-350

71.2 1.859 0.902 240-280

76.1 1.819 0.789 190-270

75.9 1.735 0.77 180-330

79.3 1.737 0.68 175-225

82.5 1.757 0.80 175-225

85.4 1.759 0.84 175-225

87.9 1.768 0.90 175-225

90.4 1.741 0.80 17.5-225

AlCI,-LiCI** Ref. 63, 19

a

b r

P a

b

r

100 2.534

84.2 1.820 0.850 175225

Physicul properties of molten salts Table 9.2

9-9

DENSITIES OF MOLTEN BINARY SALT SYSTEMS A N D OTHER MIXED IONIC MELTS4ontimced

AICI,-NaBr Ref. 53

P a

b r AlC1,-NaCI** Ref. 63,45, 16, 19

P U

b r AlC13.NH4C1 Ref. 19 AlCI,-RbCI Ref. 63

t

d P U

b

r AlF,-Na3A1F6* Ref. 62, 38, 31, 24, 22, 1.5, 14, 13, 10, 9, 6

P

Al,03-Na,A1Fs Ref. 62, 38, 14, 31, 6

P dl LOO

B,O,-BaO Ref. 44

U

d,ooo dl100

dl000

P b r

B,O,-CaO Ref. 44

P U

b r BZOS-KZO Ref. 40

79.3 1.944 1.12 200-275

69.5 1.848 0.812 220-280

71.9 1.858 0.910 160-210

73.5 1.839 0.849 150-210

75.8 1.829 0.844 150-210

79.5 1.792 0.715 150-210

84.1 1.787 0.840 175-225

284 1.475

293 1.470

311 1.445

315 1.440

324 1.425

354 1.420

71.9 1.992 0.96 175-225

76.7 1.975 1.00

0 2.096 2.002

5 2.078 1.987

10 2.048 1.965

15 2.015 1.935

20 1.977 1.894

25 1.930 1.839

30 1.873 1.775

0 2096 2002

2.5 2.076 1.985

5 2.060 1.974

7.5 2.048 1.966

10 2.039 1.960

12.5 2.033 1.957

2.028 1.954

20.7 4.038

30.0 5.006 1.32 1000-1200

39.8 4.780 1.40 1000-1100

49.2 4.422 1.34 850-1 100

59.7 3.704 0.96 850-1 000

67.9 3.392 0.96 850-1 100

-

1120

89.4 85.2 2.281 2.400 0.402 0.467 800-1000 700-1000

93.5 2.103 0.335 600-1000

97.2 100.0 1.901 1.662 0.260 0.153 600-1ooO 600-1200

b

64.0 2540 0.57

r

900-1 000

69.2 2.778 0.86 700-800

P

44.9 3.472 0.43 1150-1 200

49.6 56.8 3.513 3.402 0.56 0.61 1120-1 220 960-1 100

39.2 3.318 0.937 660-850

45.1 3.324 0.849 640-850

0 3.870 0.84 582-725

18.99 3.996 0.93 597-700

a

P U

U

P a

b r

P a b

r

90.1 1.810 1.04 175225

15

55.3 59.8 62.8 67.9 70.2 73.3 2901 2.876 2.871 2.932 2.844 2.926 0.46 0.51 0.59 0.56 0.45 0.44 1 160-1 200 1110-1 210 1 140-1 190 1 100-1 200 1060-1 100 90-1 200

71.3 2.340 0.467 800-1 000

P

b r

BaCI,-CdCI, Ref. 25, 1

74.8 1.979 1.02

84.9 2.057 0.295 700-1000

r

BaBr,-KBr Ref. 46

70.3 2.017 0.96

75.3 2.185 0.310 800-1000

b

B,O,-SrO Ref. 44

65.7 2.064 0.92

55.7 65.6 2.412 2.534 0.687 0.500 800-1000 700-1000

U

r

B,O,-Na,O Ref. 40

61.0 2.119 0.86 175-225

51.5 2690 0.905 900-1 OOO

P b

B,O,-Li,O Ref. 40

58.6 2.158 0.92

94.8 1.855 0.255 600-lo00

94.4 1.898 0.235 600-1100

99.1 1.759 0.222 600-1000

61.6 3.230 0.57 950-1 100

65.2 3.124 0.57 950-1 100

70.0 2.948 0.51 920-1 120

55.5 3.558 0.896 630-850

62.5 3.720 0.930 630-850

73.0 3.932 0.906 630-850

82.2 4.117 0.875 690-850

39.00 4,018 0.93 580-700

57.35 4.069 0.96 600-690

100 3.672 0.52 above 1000

85.8 77.6 2.137 2.413 0.278 0.435 700-1000 700--1000

98.5 1.737 0.217 500-1000

100.0 1.662 0.153 6001200

882 4.425 1.02 750-850

9-10

Physical properties of molten salts

Table 9.2

DENSITIES OF MOLTEN BINARY SALT SYSTEMS AND OTHER MIXED IONIC MELTS-continued

BaCI, -KCI Ref. 43

P a

b r

BaC12-MgC12 Ref. 69, 35, 70

P a

b

20.4 2.199 0.64 790-900

29.6 2.237 0.59 790-890

47.4 2.554 0.63 790-890

58.2 2.744 0.70 800-890

70.1 3.035 0.77 790-880

9.95 2.073 0.36

25.0 2.333 0.47

50.2 2.835 0.64 800-900

75.1 3.400 0.75

90.0 (3.642) 0.71

44.0 1.992 1.986

54.4 2.204 2.192 2.180 2.169

62.7 2.350 2.334 2.318 2.302

69.7 2.491 2.471 2.452 2.432

75.3 2620 2590 2.560 2.531

0 1.426

1.5 1.436

0 5.702 1.50 516-710

5.430 1.35 565-700

15.57 5.356 1.36 575-690

24.83 5.156 1.27 660-710

100 3.662 0.52

0 3.069 0.96 1020-1 130

33.1 3.429 0.838 920-1 175

55.4 3.978 0.996 960-1 155

71.5 3.804 0.447 910-1 120

0 2590 0.628 1010-1 120

45.2 3.291 0.626 955-1 160

67.5 3.739

5.7 3.240 3.226 3.212

13.4 3.243 3312 3216

59.0 2.274 2.245 2.132 2.218

73.7 2.492 2.458 2.440 2.422

9.54 1.914 1.884 1.885

r

BaC1,-NaCI Ref. 71, 17

P d725

d750 d775 d800 BaCI2-NH4NO, Ref. 58 BaC12-PbC12 Ref. 25, 1

P d180

P a

b r

BaF,-Na3AIF, Ref. 15, 10

Y a

b r BaF,-.NaF Ref. 15

P a

b r Ba(N0J2Ba(N03)2 Ref. 72

P d300 d320

d340 Ba(N02)2-KN02 Ref. 72

P d280 d320 d340 d360

Ba(N03)2-KN03 Ref. 72, 36, 73

P d340 4 8 0 d420 d460

Ba(NO3),NH4N03 Ref. 58 BaO-Si02 Ref. 74

P dl70 dl80

P a

b

-

P a

-

-

2.615 2.577 2577

2.780 2.750 2.750

2.950 2.921 2.921

25.8 2.014 1.984 1.953

-

33.1 2.068 2.036 2.004 1.974

39.7 2.118 2.088 2.056 2.026

0 1.432 1.426

2.5 1.453 1.447

5.0 1.474 1.466

22.1 2.580 O.Oo0

39.0 3.016 0.048

52.3 63.0 3.401 3.748 0.068 0.075 1600-1 950

b r Bi-BiBr, Ref. 68

P

51.5 2.09 0.27 500-800 52.1 6.69

80.1

-

-

84.4

-

-

2.650 2.616

2.760 2.730

80.7 4.195 0.600 0.624 970-1 165 955-1 180

80.0

-

91.4 3.456 0.68 880-940

above 1Oo0

-

r BeFrLiF Ref. 75

10.71

82.8 3.268 0.65 820-910

86.8

92.5

45.9

97.6 3.154 3.126 3.099 3.099

51.5

-

-

2.143 2.111 2.080

2.201 2.168 2.136

72.0 4.044 0.080

57.0

-

2.228 2.196

Physical properties of molten salts

9-11

Table 9.2 DENSITIES OF MOLTEN BINARY SALT SYSTEMS AND OTHER MIXED IONIC MELTS-eontinued Bi-BiCl, Ref. 61

P

O

a

4.42 2.20 240-330

7.5 4.61 2.06 290400

14.7 4.87 2.08 270420

19.7 5.07 2.13 290450

23.8 5.24 2.15 310-440

97.9 10.39 1.29 330440

100 10.39 1.29 310-440

O 1.495 1.434

20 1.573 1.517

40 1.671 1.613

50 1.725 1.667

60

d,,, d,,,

80 1.896 1.850

100 2.057 2.009

p a b r

22.6 2.16 0.47 123-895

27.7 2.115

42.6 2217 0.44 728-886

59.4 2.319 0.48 730-902

76.6 2.365 0.45 746-898

44.9

74.0 1.944 1.912 1.879 1.846

88.5

94.5

b r

CaCi,-KCI Ref. 8 CaCl,-MgCI, Ref. 35

CaC12-NaCI** Ref. 71, 27, 18, 8

P

p d625

17.5

-

0.40

753-907 32.3

-

-

65.5 1.899 1.855 1.830 1.798

-

1.780 1.734

-

d700

--

d77, dsso

1.612 1.575

1.679 1.646

1.767 1.730 1.693

CaF,-CaO Ref. 53

p 454s

929 2.63

94.6 2.50

95.3 253

97.1 2.59

98.6 268

100 2.75

CaF,-Na,AlF, Ref. 38, 31, 15

P

O

10 2.162 2.070

20 2.223 2.135

30 2.283 2.200

40 2.334 2.256

50 2.366 2.294

CaF,-NaF Ref. 15

P

O

48.0 2.804 0.57 870-1 165

65.0 2.929 0.54 1050- 170

CaWO,),NH4H0, Ref. 58

P

O

d170

1.432 1.426

1.460 1.453

CaO-SiO, Ref. 74

p

28.6 2.578 0.066

38.4 2.651 0.064

O

38.55 4.138 0.90 580-680

55.46 4.255 0.91 590-710

73.64 4.390 0.93 606-705

100 4.687 1.08 580-720

D

O

a

r

4.828 1.12 380-700

14.2 4.638 1.06 360-700

33.2 4.361 0.88 440-700

59.9 4.187 0.87 520-700

100 3.839 0.80 560-700

P

O

b r

1.988 0.60 above 750

44.77 2.495 0.72 604-750

62.10 2.791 0.82 460480

78.10 3.176 0.95 464-680

92.36 3.625 0.96 534-700

P

O

59.1 2.572 0.577 560-750

81.2 3.245 0.845 510-750

92.9 3.593 0.825 520-750

100 3.839 0.800 560-750

O 2.053 0.63 above 800

62.08 2.896

71.38 3.090 0.86 500-690

79.64 3.315 0.92 570-680

85.23 3.543 1.04 540-680

dlooo 2.096 diioo 2002

a b r

dlso a

b r CdBr,CdCI, Ref. 25

CdCI,-CdI, Ref. 41

P a b r

b

CdC1,KCI Ref. 25, 7

CdC1,-LiCI Ref. 41

a

a

b r

CdCl,-NaCl Ref. 25, 7

P a

b r

26.9 2.692 2.602 0.58 0.64 1010- 120 930-1185

3.870 0.84 582-725

1.731 0.382 600-750

2.005 1.974 1,944

I

2.013 1.985

10

5

1.480 48.4 2.758 0.084 1600-1 950

0.83

580-690

58.5 2.840 0.103

100 3.870 0.84 582-725

91.66 3.678 0.95 580-700

100

3.870 0.84 582-725

9-12

Physical properties of molten salts

Table 9.2 DENSITIES OF MOLTEN BINARY SALT SYSTEMS AND OTHER MIXED IONIC MELlS-cominaed CdCIZ-PbCl, Ref. 25

0 3.870 0.84 582-725

27.62 4.305 1.02 540480

5214 4.726 1.18 515-700

75.66 5.222 1.39 480-680

85.40 5.402 1.43 545-680

100 5.702 1.50 510-710

r

680-800

28.0 3.469 1.09 540-800

525 3.769 1.12 400-800

68.8 4.120 1.22 190-700

81.6 4.43 1 1.29 300-700

92.6 4.645

b

0 3.108 0.96

P

50.0 2.436 0.92 260-xw)

55.7 2.475 0.89 220-300

65.7 2.583 0.93 200-300

74.1 2.689 0.93 180-300

81.2 2.820 0.95 200-300

0.57 3.1695 3.1327 3.0932

1.14 3.1800 3.1440 3.1040

2.31 3.2055 3.1700 3.1333

3.50 3239 0 3.204 1 3.1740

4.70 3.287 5 3.249 0 3.228 8

11.49 1.62

P a

b

r CdIZ-KI Ref. 41

Cd(NO3)Z-KNOS Ref. 50

P a

a

b

r

&so

0.28 3.165 5 3.1275 3.087 7

CU,CI~-KCI Ref. 5

P dsoo

0 1.51

Cu,S-FeS Ref. 60

P

0 3.85

CeCeC1, Ref. 76

P dsso

dgoo

a

b r

FeO-SiO, Ref. 55

P

KBr-KN03 Ref. 41

P

d1300

a

b

r KBr-NaCI Ref. 41

P a

b r

KBr-T1Br Ref. 77

P a

b

KBRnSO, Ref. 4 2 34

73.7 3.67

78.3 3.81

82.8 4.00

88.1 4.16

91.5 4.32

95.7 4.61

0 2.116 0.729 330-600

17.2 2.186 0.714 330600

37.0 2.285 0.727 340-600

54.1 2.415 0.779

70.2 2.476 0.730 530-800

86.9 2635 0.801 650-800

100 2.725 0.794 740800

67.2 2.447 0.723 750-800

100 2.725 0.794 740-800

5.7 6.493s 1.934,

15.2 6.9084 3,421,

57.6

-

60.5

74.6 3.978, 1.8936

37.0

-

-

B C r

-

-

490-628

584-732

1.7816 3.8789 4.1928 707-759

P

34.1 3.090 0.46

41.0 3.003 0.40

426 2985 0.42

0

3.098 0.956 680-900

2.8 3.030 0.930 680-900

7.8 2.914 0.864 710-900

6.4 2.101 0.728 349-540

15.3 2.090 0.721 429-580

23.5 2.069 0.680 485-633

a

b

r KCI-KI Ref. 52

P a

b

r KCI-KNO, Ref. 78

P a

b r

360-700

1.828 1.12 380-700

50 I00 5.10 6.76 0.62 0.75 1250-1 450 1 100-1 500 1 150-1 400

-

A

1.17

100

440600

41.4 5.7328 3.084,

-

-

750-799

552 3.105 0.80 500-550 13.3 2.873 0.890 640-910

-

-

I

100 4.90

-

3.218, 6.6319 6.087, 721-798

6.425, 14.160, 10.347, 747-857

59.6 2939 0.52

63.9 2.940 0.60

68.9 2.965 0.74

26.8 2.684 0.826 620-900

41.2 2.498 0.755 680-920

64.4 2.274 0.690 710-900

758797

Physical properties of molten salts Table 9.2

S13

DENSITIES OF MOLTEN BINARY SALT SYSTEMS A N D OTHER MEED IONIC MELTs-continued

KC1-LiCl** Ref. 5&12

KCl-MgCI, Ref. 35, 69, 11

KCl-MnCl, Ref. 79

0 1.766 0.433 620-780

28.2 1.835 0.489 530-750

42.6 1.856 0.507

a b r

10.7 1.896 0.31 706-886

P

-

126

P a b r

P

4 0 0

d600 d700 d800

460400

55.8 1.885 0.528 390-590

72.2 1.923 0.561 590-750

20.4 1.993 0.41 695-890

31.2 1.990 0.48 756901

41.5 1.924 0.44 734-894

49.7 1.946 707-880

59.0 1.944 0.52 707-881

2.337 2.214 2.212

23.2 2.210 2.157 2.104 2.051

321 2.111 2.051 1.998 1.941

36.6 2.063 2007 1.958 1.898

41.3 2.009 1.955 1.900 1.845

51.0 1.943 1.881 1.818 1.755

0.50

87.6 1.968 0.509

690-850

100

1.977 0.583 780940 80 1.946 0.54

704876 63.5

-

1.795 1.727 1.668

KCl-NaBr Ref. 41

P

41.8 2449 0.728 750-800

100 1.986 0.582 770-800

KCI-NaCl** Ref. 52, 17, 8

P

a b r

0 1.991 0.543 800-1 030

18.7 1.989 0.554 780-920

31.1 1.985 0.560 710-920

40.6 1.982 0.557 710-930

54.8 1.976 0.568 670-910

64.8 1.977 0.575 680-910

82.9 1.979 0.581 720930

KCl-NaI Ref. 41

P

0

a b

3.412 670-800

19.8 2.971 0.900 520-800

33.0 2.724 0.815

r

8.0 3.118 0.824 600-800

49.1 2.482 0.727 570-800

73.6 2.195 0.625 690-800

100 1.986 0.582 770800

P

0

r

5.702 1.50 516-700

5.51 5.145 1.42 565-700

13.21 4.513 1.28 580-680

22.94 3.960 1.13 490-680

1.988 0.60 above 750

5.4 2.653 0.55 460-670

9.3 2.588 0.50 450660

20.0 2.542 0.62 450660

31.1 2.448 0.66 450-640

49.2 2.272 0.60 440-660

55.9 2.217 0.60 450-650

70.1 2.080 0.57 690-720

23.2 3.024 0.68

29.0 2.884 0.64

31.4 2.821 0.58

38.2 2.681 0.56 475-550

47.0 2.619 0.72

54.3 2.511 0.70

56.1 2.491 0.70

r

33.6 2.253 0.632 720-800

55.0 2.484 0.706 680-800

74.1 2.727 0.819 560-800

86.9 2.893 0.858 580-800

94.2 3.034 0.965 640-800

100 3.108 0.960 680-800

P a b r

17.5 3.997 4 1.133 7 761-869

27.5 3.937 1 1.099 7 614-750

43.0 3.781 3 1.1189 631-792

52.2 3.653 4 1.052 9 632-779

60.0 3.428 2 0.995 1 574-766

79.4 3.163 7 0.7146 783-933

KCl-PbCl, Re.f. 25. 7

KCI-ZnCl, Ref. 59

a b r

a b

P a

b r

KC1-ZnSO, Ref. 42,M

P a

b

1.00

r

KF-LiF-NaF eutectic

Ref. 80

PKF PLiF

a b r

KI-NaC1 Ref. 41

K,MoO,-MoOj Ref.81

P a b

540-800

100

59.0 29.2 2.47 0.68 600-800

91.0 3.0360 0.6340 882-978

9-14

Physical properties of molten salts

Table 9.2 DENSITl€?S OF MOLTEN BINARY SALT SYSTEMS AND OTHER MlXED IONlC MELTS-eontinued KNOZ-KNO 3 Ref. 48,72

P

O

a b r

2.116 0.73 340-500

26.5 2.068 0.69 340-500

35.9 2.062 0.70 340-500

50.7 2.052 0.70 380-500

100 2005 0.70 440-500

KNO,-NaNOz Ref. 48

P

O

17.8 1.959 0.59 260-500

29.1 1.951 0.58 260-500

45.1 1.961 0.59 260-500

55.2 1.951 0.58 350-500

74.2 1.963 0.61 350-500

100 2.005 0.70

KNOZ-NaN03

Ref. 48

b r

2.004 0.69 380-500

P

O

a

2121 0.68 350-500

15 2117 0.70 300-500

35 2073 0.66 200-500

50 2.057 0.68 200-500

65 2028 0.66 240-500

85 1.993 0.63 350-500

100 2005 0.70 440-500

b r

16.7 1.954 0.599 257-403

26.7 1.974 0.623 264-350

40.9 1.997 0.638 219-445

59.5 2.033 0.683 328-476

71.0 2055 0.696 306-454

81.9 2083 0.729 294425

92.2 2.102 0.735 318-452

P

O

20.5 1.991 0.61 300-500

44.0

59.4 2.048 0.67 200-500

73.1 2.061 0.67 200-500

89.3

2028 0.66 200-500

100 2.116 0.73 340-500

20 2.127 0.71 290-500

40 2.127 0.72 250-500

60 2.126 0.73 240-500

80 2.126 0.72 290-500

2.5 1.441 1.429

5.0 1.451 1.439

7.5 1.462 1.450

10.0 1.473 1.460

50 2.881 1.00 230-365

60

3.080 1.00 275-345

2679 0.908 275-380

70 2.483 0.750 300-390

80 2362 0.787 320-405

529 2.403 0.721 421-452

60 2.360 0.760 365-445

70 2285 0.748 300-420

80 2.226 0.752 305-465

90 2.167 0.753 325-475

100 2.113 0.730 350-460

23.9 2.353 0.14

26.7 2.320 0.11

29.9 2.377 0.16

32.9 2.380 0.16

38.7 2464 0.23

43.6 2,504 027

a

b r

KN03-LiNO,

p

Ref. 7 8 82

a

KN03-NaNOz Ref. 48

a

b r

2004 0.69 380-500

KN03-NaN03** Ref. 48,47, 36,

P

O

a

82, 8, 3

b r

2.121 0.68 350-500

KNO,-NH,NO, Ref. 58

P

O

d,,, dXgo

1.432 1.420

KNO,-Pb(NO3)2 Ref. 36

P a

b r

KNO~-SC(NO& Ref. 73, 36

p a

b r

K,O-SiO, Ref. 56, 39

K,S0,-ZnS04 Ref. 34

p

a b r p

d,,,

d,,, Kz WO4-WO3 ~ e fa3 .

p a

b r

LiCI-LiNO, Ref. 78

p a

b r

N

0.72 240-500 100 2.116 0.73 350-500

90 2218 0.709 330-420

100 2113 0.730 350-460

IOOO-1400 26.59 (2.841) 2.812

32.66 2.751 2727

35.15 2731 2.708

36.77 2.728 2.692

41.41 2.680 2.641

49.92 2.592 2.556

58.86 2.509 2485

37.4 5.8898 1.5538 897-999

50.5 5.486 5 1.519 6 772-943

58.3 5,3326 1.5620 655-783

67,4 4.955 3 1.334 1 682-851

76.6 4.532 2 1.0157 803-910

85.0 4.244 4 0.907 4 860-987

92.2 4.077 1 0.845 2 9041029

6.4 1.911 0.537 278-446

13.3 1.903 0.538 340-497

20.8 1.899 0.524 378497

10 2.1275 0.723 2 230-400

15 2.1394 0.744 1

LiCIO, in KN03-NaN03

PLicIo, 5 a 2.1201

eutectic

b

(57.3% KNO,)

r

Ref. 84

2.100

440-500

0.7110 I

Physical properties of molten salts

9-15

Table 9.2 DENSITIES OF MOLTEN BINARY SALT SYSTEMS AND O'THER MIXED IONIC MELTS-continued 34.0 2.014 0.610 240-357

57.3 2.088 0.629 198-341

82.3 2.134 0.629 225-336

19.5 3.9932 0.9502 766-921

33.9 3.895 1 0.8451 755-924

51.5 3.7359 0.7723 760-934

p dl80

0

5

1.426

1.430

p u

16.1 2.311 0.13

21.8 25.9 2.355 2359 0.19 0.20 1100-1 400

31.9 42.8 2.344 1.980 0.22 1250-1 400

-

54.6 5.9718 1.1628 809-939

59.7 6.0776 1.341 1 764-968

69.0 5.7696 1.1903 755-978

77.5 5.5275 1.1124 736-930

92.3 5.0160 0.851 1 733-959

b r

20.0 1.961 0.49 750-888

45.7 1.963 0.47 732-890

60.6 2.002 0.48 722-896

15.8 2.000 0.43 712-893

p d950 dg8o

2.12

3

2.13

p a b r

328 2541 0.049

35.5 2579 0.056

38.3 41.1 2597 2.655 0.052 0.071 1600-1 950

44.0 2670 0.070

p a b

r

21.4 2.79 700-830

26.4 3.63 1.0 690-790

512 3.92 1.2 660-760

62.2 4.02 1.2 650-810

71.2 3.88 1.o 650-750

p

0

d1,o

1.432 1.420

2.5 1.426 1.414

5 1.419 1.407

7.5 1.412 1.403

10 1.403

95.0 1.435 1.421

97.5 1.430 1.417

100

100 1.432 1.426

LiC10,-LiN03

p

Ret. 13

a

b

r Li,Mo04-Mo03 Ref. 81

p a

b r LiN0,-NH4N03 Ref. 58

*

Li,0-Si02

Ref.

39

Li,W04-W03

Ref. 83

b r p a

b r MgC1,-NaCl

p

Ref. 35

a

MgF2-Na3AIF6

Ref. 62 MgO-SO2

Ref. 74

Mo03-Na2Mo04

Ref. 51

NH,CI-NH,NOB Ref. SS

dlso

NH4NO3-

p

(NH4)2S04

PISO

92.5

-

6

Ref. 58

dzo0

NH4NO3-

p

Pb(N03)z

d170

-

Ref. 58

d18,

1.527

95.0 1.481 1.475

NH4NO3Sr(N03)2 Ref. 58

P dl70

95 1.466 1.453

100 1.432 1.420

NaCI-NH4N03 Ref. 58

p dlso

0

1.426

1.5 1.432

NaCI-NaNO,

p

Ref. 71

d350

1.4 1.879 1.842 1.806

28 1.878 1.841 1.804

d,,,

d400 d450

1.425

89.9

60.5 3.564 1 0.6448 802-962

71.3 2.9856 0.0317 799-950

85.2 5.2819 0.9913 714-923

85.2 3.4559 0.5930 781-905

91.0 3.3520 0.5317 825-924

48.1 1.955 1400

9 2.14

-

4.2 1.879 1.843 1.806

83.7 3.74 0.8 730-840

86.2 3.81

0.9 780880

-

1.427 1.416

5.7 1.875 1.839 1.802

7.1 1.875 1.839 1.803

8.6

-

1.840 1.803

10.1

1.836 1.800

9-16

Physical properties of molten salts

Table 9.2 DENSITIES OF MOLTEN BINARY SALT SYSTEMS A N D OTHER MIXED IONIC MELTS- 4ontinued NaQ-PbCI, Ref. 17

P

O

dsoo

4-96 4.82

dsoo NaF-Na,AlF,t Ref. 38,31,24,22, 15, 14 13, 10, 9, 6 NaF-UF,-ZrF, Ref. 85

p

dloo0 dlloo

PNaF PUF4

a

b

r NaF-ZrF, Ref. $6

P a b r

NaNO,NaNO, Ref. 4 4 1

p a

b

r NaN03-NH,N03 Ref. SS

p

da,o d180

NaN03-Pb(N0,), Ref. 36

p a b

r Na,O-P,O, Ref. 87

P a b r

Na,W0.,-W03 Ref. 83

p

a b r

Nd(NO,), in KNO,-NaNOI eutectic (57.3”/.KNO,) Ref. 84 Nd(NO,), in KN0,-LiCI0,NaNO,(45%-

WL-%l

5.85 4.34 4.22

9.42 4.21 4.08

13.32 3.96 3.77

20 2.108 2019

40 2.085 2.002

60 2.042 1.970

17.05 3.83 0.91

22.0 3.71 0.89

27.3 3.61 0.87 300-800

31.8 3.52 0.86

51.1 3.23 0.81

0 2.121 0.68 310-500

21.3 2094 0.68 250-500

44.8 2.066 0.68 220-500

65.4 2.043 0.68 270-500

82.1 2.028 0.70 270-500

100 2.004 0.69 280-500

0 1.432 1.426

2.5 1.443 1.436

5.0 1.452 1.446 70 2.498 0.726 295-

80 2.373 0.746 305-420

2.238 0.695 310430

40 3.171 1.12 340-365

50 2867 0.806

305-375

60 2.703 0.856 285-390

50.0 2.516 0.26 1050-1 400

45.9 5.963 6 1.4244 782-926

50.9 5.711 3 1.2289 775498

55.9 5.8825 1.5570 758-899

74.2 5.2325 1.2262 688480

83.0 4.9976 1.1167 654-815

6.4 21587 0.7254

12.0 2.2186 0.757 1

29.1 2.3371 0.708 7

35.3 2.4183 0.753 3

24.46 5.840 1.52 492620

57.19 6.025 1.55 465-640

0.707 1 230-400

P

0 5.702 1.50 516-570

P

91.6 3.9344 4.0510 685-880

33.6 36.9 2436 2.456 0.18 0.20 900-1 400

b r

dslo dssa

100 2.117 0.670 3201460

t

65.1 4.4159 4.0312 737-882 21.4 2.2741 0.686 7 230-400

PNd(?fO,h 35.3 a 2.412 8

PbCl2-ZnC1,

90

20.0 30.8 2.312 2.380 0.10 0.14 1100-1 400

PELIBIO,),1.3 2128 5 b 0.73 1 7 r

Ref. 89

100

1.957 1.895

30.4-48.5 liquidus-1 070

a

a b r

80 1.998 1.933

19.0 11.4 3.93 0.93 600-800

Ref. 84 PbBr,-PbCI, Ref. 8 2

17.5 3.66 3.50

10 2.110 2.017

dp.,=2372+0.2O4p/(100 -p) -0.338 x ‘P

4

NatO-SiOz Ref. 56, 39

0 2.096 2002

269 4.72 4.57

67.1 3.733 3,703

87.88 5.264 1.71 410-600

100 6.338 1.65 505-600

Physical properties of molten salts

e17

Table 9.2 DENSITIES OF MOLTEN BINARY SALT SYSTEMS AND OTHER MIXED IONIC M E L T W o n t i d PbO-BZO3 Ref. 88

P

diose

57.9 28

68.1 3.5

76.3 4.0

82.9 4.6

882 5.3

92.9 6.0

96.6 6.6

Pbo-SiO, Ref. 88

P dioso

61.4 4.2

712 4.9

78.8 5.7

84.8 6.0

89.7 6.7

93.7 7.0

97.1 7.4

PbO-V,Os Ref. ?XI

P diooo

15.3 3.1

39.6 4.0

528 5.0

65.4 5.0

79.0

6.2

85.1 6.8

92.1 7.8

PPM)

28.5 10.3 3.8

38.6 10.4 3.8

58.4 10.4 4.0

60.0 10.1 4.0

68.5 10.6 4.0

80.0 10.0 5.2

48.1 3.129 0.058

53.4 3.247 0.059

63.3 58.5 3.493 3.384 0.079 0.074 1600-1 950

67.8 3.612 0.072

55.23 (4.116) 4.076

57.99 4.146 4.094

59.86 4.1% 4.155

63.55 4.277 4.227

PbOSi0,-V,O, Ref. 90 SrOSiO, Ref. 74

Psiq 4ooo P a

b T

TICI-ZnSO, Ref. 34

P d450 dsoo

61.04 4.223 4.177

59.24 4.421 4.376

74.82 (4.573) 4.512

* See ako NaF-Na,AIF,.

t See also AIF,-Na,AIF,

** See also ‘Physical Properties Data Compilations Rekvant to Energy Storags 11 Molten Salts-Data on Single and MultiComponent Salt Systems’, Jam et nl., NSRDS-NBS 61. REFERENCES TO TABLE 9.2 1. K. Arndt and A. Gesslor, Z.Ekctrochem., 1908, 14,665. 2. R Lorenz, H. Frei, and A. Jabs, Z. phys. Chem., 1908,61,468. 3. Smith and Menzies, P r w R. Soc., Edinburgh, 1910,30,432. 4. Izbekov and Plotnikov, J. Russ. Phys.-Chem. SOC,1911, 43, 18. 5. Sackur, Z.phys. C h e w 1913,83,297. 6. Pascal and Jouniaux, Bull. SOC.chim., France, 1914,15,312; Z.Elektrochem, 1916,22,71. 7. F. M. Jaeger, Z.anorg. Chem, 1917, 101, 175. 8. C. Sandonnini, Gazz. Chim. Ital., 1920, 51, 289. 9. J. D. Edwards, F. C. Frary and Z. Jeffries, ‘The Aluminium Industry’, New York, 1930, p. 308. 10. N. Kameyama and A. Naka,J. Soc.Chem. I d . , Japan, 1931, 34, 140. 11. S. V. Karpachev, k G.Stromberg and 0. Poltoratzkaya, J. Phys. Chem (USSR), 1934, 5, 793. 12. S. V. Karpachev, A. G. Stromberg and V. N. Podchainova, J. Gen Chem (USSR), 1935,5, 1517. 13. G. A. Abramov, Legkie Metally, 1936, 11, 27. 14. Z. F. Lundina, Trans. All Union Aluminium and Magnesium Inst., 1936, 13, 5. 15. G. A. Abramov and P. A. Kaunov, Trans. Leningrad Indusr. Inst., 1939, No. I , 60. 16. A. I. Kryagova, J. Gen Che?n.(USSR), 1939, 9,2061. 17. V. P. Barzakovskii, Bull. Acad. Sci., U.R.S.S. (Class sci chim), 1940, 825. 18. V. P. Barzakovskii, J. appl. Chem (USSR),1940, 13, 1117. 19. Y. Yamaguti and S. Sisido, J. chem Soc. Japan, 1941, 62, 304. 20. E. Ya Gorenbein, J. Gen. Chem (USSR), 1945, 15, 729. 21. E. Ya.Gorenbein, ibid, 1947, 17, 873. 22. T. G. Pearson and J. Waddington, Disc. Faraday Soc., 1947, No. 1, 307. 23. E. Y a Gorenbein, J. Gen. Chem. (USSR), 1948, 1% 1427. 24. V. P. Mashovets, ‘The Electrometallurgy of Aluminium,’ 1948. 25. N. K. Boardman, F. H.Donnan and E. Heymann, J. phys. Chem., 1949,53, 375. 1949, 19, 805. 26. I. M. Bokhovkin, J. Gen Chem. (USSR), 27. G. Fuseya and K. Ouchi, J. electrochem. SOC.Japan, 1949, 17, 254. 28. E. Ya.Gorenbein and E. E. Kris, J . Gen. Chem (USSR), 1949, 19, 1978. 29. H. Grothe, Z.Elektrochem, 1949, 53, 362. 30. I. M. Bokhovkin, J. Gen Chem (USSR), 1950,20, 397. 31. A. Vayna, Aliuminio, 1950, 19, 541. 3 2 E. Ya. Gorenbein and E. E. Kriss, J . phys. C h . (USSR), 1951, 25, 791. 33. R. C. Spooner and F. E. W. Wetmore, Canad. J. Chem, 1951, 29, 777. 34. I. P. Vereshchetina and N. P. Luzhnaya, J. appl. Chem. (USSR), 1951, 24,148. 35. R. W. Huber, E. V. Potter and H. W.St. Clair, U.S.Bur. Mines, Rep. Invest. 4858,1952. 36. K. Laybourne and W. M. Madgin, J. chem Sac, 1934, 1. 37. J. Byrne, H.Fleming and F. E. W. Wetmore, Canad. J. Chem., 195530, 922.

9-18

Physical properties

of molten salts

38. J. D. Edwards,C. S. Taylor, L. A. Cosgrove and A. S. Russell, Trans. eleetroehem Soc., 1953, 100,508. 39. L. Shartsis, S. Spinner and W. Capps, J. A m ceram Soc.,1952,3S, 155. 40. L. Shartsis. W. Capps and S. Spinner, J. Am. ceram Soc., 1953.36,35. 41. H. Bloom, I. W. Knaggs, J. J. Molloy and D. Welch, 7hm. Faraday Soc., 1953, 49, 1458. 42 N. P. Luzhnaya and I. P. Vereshchetina, Izuest. Sekt. FLiko-Khim Anal., 19% 24,192 43. J. S. Peake and M. R. Bothwell, J . Am. chem Soc., 1954, 76, 2653. 44. L. Shartsis and H. F. Shermer, J. Am. ceram SOC, 1954, 37, 544. 45. R. Midorikawa, J. electrochem. SOC.Japan, 1954, 23, 310. 46. V. D. Polyakov, Izuest. Sekt. Fkiko-Khim Anal, 1955, 26, 147. 47. A. G. Bergman, I. S. Rassonskaya and N. E. Schmidt, ibid., 1955, 26, 156. 48. V. D. Polyakov and S. I. Berul, ibid., 1935,26, 164. 49. V. P. Polyakov, ibid., 1955, 26, 191. 50. N. P. Popovskaya and P. I. Protsenko, Z b f i z . Khim.,1955, 29,225. 51. K. B. Morris, M. I. Cook, C. 2. Sykes and M. B. Templeman, J. Am chem. SOC., 1955, 77, 851. 5 2 E. R. van Artsdalen and I. S. Yafe. J. phys. Chem., 1955,59, 118. 53. T. Baak, Acta. Chem. Scand., 1955,9, 1406. 54. N. P. Luzhnaya, N. N. Evseeva and I. P. Vereihchetina, Zh. neorg. Khim., 1956, 1, 1490. 55. S. I. Pope1 and 0. A. &in, Zhur. Pri&lad. Khim, 1956,29, 651. 56. J. O'M. Bcckris, J. W. Tomlinson and J. L. White, Trans. Faraday Soc., 1956, 52, 299. 57. H. Bloom and D. C. Rhodes, J . phys. Chem, 1956,60, 791. 58. S. Toshiaki and T. Ishibashi, Sci. Papers Coll. Gen. fiduc., Uniu. Tokyo, 1957, 7, 53. 59. F. R. Duke and R. A. Fleming, J. elecrrochem. Soc., 1957, 104, 251. 60. M. Bourgon, G. Derge and C. M. Pound, T r m . Amer, Inst. Min. Mer. Eng., 1958,212, 338. 61. F. J. Keneshea and D. Cubicciotti, J . phys. Chem., 1958,62, 843. 6 2 E. Vatslavik and A. 1. Belyaev, Zh. neorg. Khim., 1958, 3, 1044. 63. R. H.Moss, Uniu. MicrojXms (Ann Arbor. Mich.), 1955, No. 12, 730. 64. E. J. Salstrom J. Am chem SOC.,1931, 53, 3385. 65. E. I. Salstrom and J. H. Hildebrand, ibid., 1930, 52, 4650. 66. E. J. Salstrom and J. H. Hildebrand, ibid., 1931, 53, 1794. 67. E. J. Salstrom and J. H. Hildebrand, ibid., 1932, 54,,4252. 68. L. E. Topol and F. Y. Lieu, J. phys. Chem, 1964, 68, 851. 69. J. N. Reding, J . chem Engng Data, 1965, 10, 1. 70. N. V. Bondarenko and K.L. Strelets, Zh. prikl. Khim, 1962, 35, 1271. 71. I. P. Vereshchetina and N. P. Luzhnaya, Ino. Sekt.jz.-&him Analiza, 1954, 25, 188. 7 2 P. I. Protsenko and A. Ya. Malakhova, Zh. neorg. Khim, 1961, 6, 1662 73. G. F. Petersen, W. M. Ewing and G. P. Smith, J. chem Engng Data, 1961,6, 540. 74. J. W. Tomlinson, M. S. R. Heynes and J. O'M. Bockris, Trans. Faraday SOC.,1958,54, 1822. 75. B. C. Blanke, E. N. Bouquet, M. L. Curtis and E. L. Murphy, Mound Lab., Miamisburg, Ohio. Memo, 1086 (1956) 76. G. W. Mellors and S. Sender&, J . phys. Chem, 1960, 64,294. 77. E. R. Buckle, P. E. Tsaoussoglou and A. R. Ubbelohde, Trans Faraday Soc., 1964, 60,684. 78. G. P. Smith and G. F. Petersen, J . chem Engng Data, 1961,6,493. 79. I. G. Murgulescu and S. Zuca, Studii, Cerc. Chim, 1959, 7 , 325. 80. M. Blander, W. R. Grimes, N. V. Smith and G. M. Watson, J. phys. Chem., 1959, 63, 1164. 81. K. B. Morris and P. L. Robinson, ibid., 1964, 68, 1194. 82 P. C. Papaioannou and G. W . Harrington, ibid., 1964, 68,2424. 83. K. B. Morris and P. L. Robinson, J . chem. Engng Data, 1964, 9, 444. 84. J. Padova and J. Soriano, ibid., 1964, 9, 510. 85. W. R. Grimes, N. V. Smith and G. M. Watson, J. phys. Chem., 1958, 62, 862. 86. J. H.Shaffer, W. R. Grimes and G. M. Watson, ibid., 1959,63,1999. 87. C. F. Callis, J. R. Van Wazer and J. S. Metcalf, J. A m chem Soc.,1955, 77, 1468. 88. J. O'M Bockris and G.W. Mellors, J . phys. Chem, 1956, 60, 1321. 89. A. Wachter and J. H.Hildebrand, J. A m chem. Soc., 1930, 52,4655. 90. B. M. Lepinskikh, 0.A. Esin and G. A. Teterin, Zh. neorg. Khim,1960,5,642.

Physical properties of molten salts T9bh 9 3

DENSlTy OF SOME SOLID INORGANIC COMPOUNDS AT ROOM TEMPERATURE ~

Compound

Density g ~ m - ~Compound

Density gm-’

AgBr AgCi AgC103 At&) AgNOa

6.47 5.56 4.43 5.683 4.35

4.51 3.69 4.24

AIBr, AICI, AN, AsBr, BI3

2.64 244 3.98 3.54 3.35

BaF,

1.84 4.78 3.856 4.43 4.89

BdZ BaO BaO, BaSO, BeBr,

5.15 5.68 4.96 4.50 3.47

BeF, Be0 BiBs, BiC1,

1.90 1.99 3.00 4.72 4.75

cza,

2.09

B2°3

BaBr, BaCI,

Baco,

CaBrz CaCl, CaC03 CaF,

3.353 2.15 271* 3.18

CaO CdBr, CdCl, CsBr

3.2513.38 2.96 5.19 4.05 4.43

cscl CsF

3.99 4.12

cas04

* Calcite.

9-19

4.14 6.0 3.69 247 4.15 1.44 6.11 7.31 5.44 7.15 8.95 6.36 7.7 4.74 4.19 3.66 3.46 4.69 2.55 275 1.98 1.52 2.43 2.68 2.48 2.31 3.13 291 211 2.04

Density

Density

Compound

gcm-’

Compound

LaCl, LiBr

3.84 3.46

Rb,SO, ReF,

LiCl Li,co, LiF LiNO,

2.07 2.11 2.64 2.38 222

MgCIz

MgF2 MgO MnO, Na,AIF,

232 3.0 3.58 4.9 290

NazB407 NaBr NaCl Na,C03 NaF

2.37 3.20 2.17 253 256

Nal NaNO, NaOH Na,P20i Na,SO,

3.67 2.26 2.13 253 2.70

Na,WO, NH,CI Ni(COLt NiO

4.18 1.53 1.32 6.67 4.91

Re201

Li,so,

ReOF, SbBr,

Sbclj SnC1, Snl, SrBr, SrCl,

SrF, SrI,

PBr, PbBr,

pm,

PbCht PbI, RbBr

RbCl 2.56 3.08 (hex) RbF 2.67 (cub) RbI RbNO, 2.66

285 6.66 5.85 3.18 6.16 3.35 280 3.56 3.55 3.11

3.14 3.95 4.47 4.22 3.05

TeC1, ThC14

4.24 4.55 4.7 3.26 4.59

TiBr, TiF, TiI, TiO,

2.6 280 4.3 4.26

SrO

eo4

3.61 4.25 6.10 4.03 4.15

rutile 3.84

anatase TlBr

7.56

TIC1

7.00 7.1 5.8 3.88 3.52

TI1 TlNO, WCI, WCld

wo3

ZnBr, ZnClz

72 4.87 2.8 4.20 2.9 1

ZnIz

4.74

UCl,

ya3

t Liquid.

REFERENCES TO TABLE 9.3 ‘Handbook of Chemistry and Physics’, 58th edn, Cleveland, Ohio, 1977-78 Gmelin, ‘Handb. anorg Chem.’, 8th edn, Berlin. J. W. Mellor, ‘A Comprehensive Treatise on Inorganic Chemistry’, London, 1922-1937.

~~

\o

Table 9.4 ELECTRICAL CONDUCTIVITY OF PURE MOLTEN SALTS The conductivity in a-' cm-' is given at the melting point e,, and at 50" intervals beginning at 0, or as an equation in the temperature t, or at the temperatures given in brackets. All temperatures are in "C. Extrapolated conductivitiesare also bracketed. Principal references are in bold type. Conductivity Q-' cn-'

e

!%

Substance

"C

4ll

e

8+50

8i-loo

e+im

8+rn

AgBr AgCl

430 455

450 500

2.8561 3.817

2.903 3.972

3.016 4.131

3.119 4276

3.214 4.407

3.3 4.523

AS103 AgI

231 557 210

0.417 2.3 0.67

0.474 2.35 0.84

AIBr, AICI, AII, AsBr,

97 193 191 31

ASCI,

- 16

AsF,

- 13 142 - 107 -128.7 570

AsI, Ba3 BF, bo3

150 200 200 35

0

BaI, BaRJO,), BeCI,

711

750 280 450

405

I

2.40 1.05

(0.02x10-6) 5.5 10-7 1.852 x 2.6 x 10- '

2.45 1.24

0.10 x ii.iX1o-7 5.645 x IOb6

-

-

1.56 x

1.84 x

2.92~10-5

-

850 975

-

1.0x10-'

-

-

847 960

-

(99.92%

58

1 523-2 493 1261-2893

IVa(i), TalS', p.c. IVa(i), Tals2, S.C.

59 99

Group VA

V

Nb

Ta

Group V I A Cr 1280 Mo A, =OS26 A, = 139 W A, =0.04 A,=46

1073-2 OW

IVa(i), s.c., Cr", 99.986%

60 and 100

1 363-2 723

IVa(i), s.c., M O ~ ~

61

1 703-3 413

Wa(i), s.c.. WlS7,99.999%

62

I

I

I

I

9

10

11

72

lfl(1WK-J)-

1

F

v 13.1

13-12 Table 13.1 Element

D$usion in metals SELF-DIFFUSION M SOLID EL.EMENTs--contirtued

Q

A

em's-'

Wmol-’

Group VI11 a-Fe See Figure 13.2*) 118 281.52 2.76 250.58 12s 281.6 y-Fe 0.49 284.12 4.085 311.1 &Fe 2.01 240.7 6.8 258.3 co 0.55 288.5 2.54‘b’ 304 Ir 0.36 438.3 Ni A, =0.85 A,-1350 Q2=400.3 Pd 0.205 266.2 Pt A, =0.034 A, = 88.6 Q, = 390.6

Transuranic elements a-Th 395 in’-s .. .x 103 104-10: P-Th 1-U 2x1011110 lIO10 99.97% 973-1 173 (a) IVb, P.c., SJ5,99.996% 1223-1 523 (Y) Ib, D.c., S35 1073-1 773 (;andp)IVb,p.c., (a-stabilized-1 wt% Be)99.9% 1373-1 23 (7) IVb, P.c., Be', 99.9% 1 371-1 626 ( y ) IVb, P.c.. Hf'", 99.98% 1438-1 593 ( y ) IVb, P.c., Hf'', 99.95% 1058-1 172 (I-P) mati), p.c., ~ 4 * , 9 9 . 9 8 % 21&1 607

Sb Sn

S

Be Hf

V

Nb

Cr Mn

co

Ni

Pd Pt

u

4.3 0.58 80 440 5.4 2.4 6.1 x 104 0.845 34.6 1.7 5.34 0.1 3.6 x 103 9.0 x 104 124 0.62

0.75 264.2 D=1.0x10-12 D = 5 . 4 ~lo-'' 50.2 252 0.83 266.5 8.52 250.8 10.80 291.8 90 27 1 1.49 233.6 0.35 219.8

Method

'}

)

309 153 159 208 310 311 312 150 148 149 151 313 314

IVb. D.c.. V48. 99.98%

151

1059-1 162 (a-p) 121C-1604 (y) 107C-1150 ( a ) 1233-1 669 (y) 1043-1 150 (0l-p) 973-1033 (a-f) 1073-1 173 (a-p) &%&&5)3 (Y)

IVa(i), P.c., Nb. 99.98%

315

IVb, P.c., Cr", 99.98% IVa(i), P.c., Cr51

151 316

IVb. s.c., Cos', 99.95% IVb, S.C. and P.c., Cos', 99.95% IVa(i). P.c., Cos', 99.95% IVb. D.c.. Co60. 99.999% 40 IVa(ik), iIa(i) (EMPA), P.c., 99.999% 34and42 IVb, P.c., Co6', 99.9% 318 319 IVa(i), s.c., co60,99.997% and 320 IVa(i), p s . , Cos' 316 IVb and c, s.c., NP3, 99.97% 1 IVb, S.C. and P.c., NiS3, 99.97% IVb. s.c.. Ni". 99.97%

1393-1 653 (Y)

I

1

8%

3!M

7.19 6.38 6.38 118 1.o 2.9 x See Figure

260.4 257.1 257.1 285.9 301.9 247.4 13.5

956-1 OOO (a-f) 1081-1 157 ( a p ) 1702-1 794 (6) 1044-1 177 la-u) 1409-1 633 (yf ' 1233-1 493 (7)

See Figure

1.4 1.3 0.77 See Figure 9.9 3.O

13.5 245.8 234.5 280.5 13.6 259.2 314

a-f and a-p 873-953 (a-0 1083-1 173 (a-p) 1203-1 323 (Y)

See Figure

13.6

9.7 0.41 2.7 7x

261.5 280.9 2% 133.2

:~~!~~$o}

IVb, P.c., Mn54, 99.97% 152 Combined data 317 aIa(ii) (EMPA), p.c.,317 1719/1767 (&)Iand 152

,

I

~

~ ~ ~ ! & $ $ p ) } IVb, P.c., NiS3, 99.999% 90 1 409-1 673 6 ) IIa(ii) and IVa(ui) (EMPA), P.c., 99.999% 34 and 364 ~ & ~ ! & $ ~ p ) } IVa(i), P.c., NiS3 321 1748-1 767 (6) IIa(ii) (EMPA), P.c., 99.96% 361 1373-1 573 h) Ib, D.c., Pd'". 99.97% 419 1233-1 533 (jj P.c., pt193m 222 1223-1 348 IVa(iii) (fission fragment radiog), p.c. 160

-

e))

(a) a-f=a-phase. ferromagnetic; a-p =a-phase, paramagnetic. I n Hf

A1

170

357

C

74 0.8 5.3~ 0.14

312.3. 21 1A 95.46 213.9

Co Cr

IIa(ii) (ion impl. and NRA). 97% Hf+3% Zr 1393-2033 (a) IVb, P.c., Ct4, Hf+l.Swt% Zr 2073-2373 (p) IIa(ii), P.c., Hf+3 wt% Zr 1 1 6 1 798 (a) IVb, P.c., Cob', 99.99% 1183-2 173 (aandB)IVb, D.c., Cr5I, 99.99% 1023-1 173 (a)

323 402 403 235 235

Mechanisms of d&%ision Table 13.2

TRACER IMPURITY DIPPUSION c

Q

A Element cmzs-'

13-21

oemmmontinued

Temp. range

klmol-'

K

Method

2.8 x lo-'

125.6

873-1 430

Ivb, P.C.,

IIc 0.11

48.1 53.6 28.1 64.9 25.1

298423 298-423 323429 383-423

IVa(i), s.c., Ag"'", 99.99% IVa(i), s.cP', Ai1",99.99% IVa(i). pc., TIZo4,99.9% IVa(i). s.c., Cos', 99.997%

94

Rt?f

In Ho C

161

1 4 c

In In Ag

IC0.52 AU

TI co

9x10-3 0.049 1.2~10-5

1

94 53 380

( a ) Randomly oriented single crystals were used. in K Au

Na Rb

Au C

Ce

1.29~ 5 . 8 ~IO-' 9 . 0 ~lo-'

13.52 31.19 36.76

279-326 273-335 272-333

IVa(i), P.c., AU'~*, 99.95% IVa(i), P.c.. NaZZ,99.95% IVa(i), P.c.. Rbss, 99.95%

123 121 124

2.2~ 4.1 10-3 1.8x10-'

75.8 83.7 104.7

873-1 073 (p) 723-1 128 ( p ) 1139-1 170 (y)

IVa(i), P.c., AuigR, 99.97% IVb, P.c., CI4 IVa(i), p.c., Cei4', -

197 404 156

4.7~10-~ 0.3 0.37 0.54 0.21 0.57 0.62 1.04 0.21 0.39 0.62 1.6 x 1.6 x 101zlb) 5.3 x 10141b) 0.41

38.6 41.87 53.72 53.72 46.01 54.34 62.80 59.37 54.05 66.44 66.32(" 105.5 173.8 198.0 52.80

323-394 363-420 340-434 323-423 319-426 33M46 355449 331-447 389-447 348-443 38C-447 401-443 413-449 413-450 325-449

IVa(i), P.c., W4,99.98% IVa(i), P.c., C U ~99.98% ~, IVa(i), P.c., Agl"", 99.98% IVa(i). p.c., Ag"Om, 99.98% IVa(i), P.c., Aul*', 99.95% IVa(i). P.c., ZnS5, 99.98% IVa(i), P.c., Cd"", 99.98% 112 IVa(i), P.c., HgZo3,99.98% IVa(i), pc., GalZ,99.98% IVa(i), P.c.. In"4m, 99.95% IVa(i), p.c., -, 99.95% IVa(i), P.c., -, 99.95% IVa(i), P.c., -, 99.95% IVa(i), p.c., -, 99.95% IVa(i), P.c., Na". 99.8%

113 324 119 325 118 117

In Li Cu Ag Ado)

Zn Cd Hg Ga In Sn Pb

Sb Bi Na (a)

[a) Refs. 326 and 327

report measurements in 95% Lis and in 92.5% Li'.

In Mg

:::::1

Ag

lic 3.62

Zn

0.41

Cd

I1c 1.29

:$::}

2.1 x 10-7 I ~ c 4.27

52.3 149.9

In

C Sn

IC17.9 IC0.46 lie 1.75 IC1.88

119.7

;:;::>

D1cP11= 1

DIJD,, = 1.13 Sb Fe ~i U

/IC 2.57 Lc 3.27 4 ~ 1 0 - ~ 1.2x 10-5 1.6 x 10-5

i: 1

88.8 95.9 95.9

1f2 112 115 114 114 114 114 116

(b) Recalculated values.

IVa(i). s.c., Ag"O", 99.99% IVa(i), pc., ZnS5, 99.875%

126

740-893 733-898

IVa(i), s.c., Cd109, 99.99%

126

747-906

IVa(i), s.c., In114m,99.99% IVb, P.c., C14

405

IVa(i), s.c., Sn1I3. 99.99%

126

IVa(i). s.c., Sblz4, 99.99% IVb, P.c.. Fe5*, 99.95% Ivb,P.c., NiS3, 99.95% IVb, P.c., U235,99.95%

328 328 328

752-913

773-873 748-903 902.3 858.2 781-896 673-873 673-873 773-893

127

126

126

D@iusion in metals

13-22 Table 13.2

TRACER IMPURITY DIFFUSION

C X I E ~ C r e ~ O ~ ~ ~ U e d

A

Q

klmol-’

Temp. range K

Method

2.0 x 10-3 1.04x 10-2 0.19 32 3.4 x 10-2 0.01 1.8 x 10-4 2.9 14 2.9 1.7 x lo-’ 3.5 x 10-4 1.9 1.88 2.5 x 10-4 1.7

115.85 139 337 422.9 297.3 470.6 214.8 473.1 452.6 569.4 379.3 347.5 473.1 342.5 226.1 460.5

493-543 1 533-2 283 2 273-2 493 2 493-2 743 1 238-1 443 1 843-2 243 1473-1 873 1803-1 998 2 123-2 623 1998-2453 1 973-2 373 1 193-1 423 2098-2449 1 273-1 423 1273-1 773 1 973-2 533

Via C precipitation rate IIIb(i), p.c. IVb, s.c., P3’, 99.97% IVa(iii), s.c., S”, 99.97% IVb, P.c., S35 IIIa(i), S.C. natural Li IVb, s.c., Ysl, 99.8/99.9% Ha(?) (EMPA), p.c. IVa(i), pc., Nbg5, 99.98% IIa(i) (EMPA), P.C. IVb, P.c., Nbg5 IVb, P.c., TalE2 IIa(i), p.c. -, s.c.. Cr”, 99.8% rvb, P.c., CrS1 IVa(i) and (ii), P.c., W’*’

4.5 x 10-4 140 9.7 x 10-2 0.15 3.7 x 10-3 18 6 D=2.4-3.2~ 7.6 x

324.5 569.4 396.5 346.2 29 1.8 446.7 324.5

1 973-2423 2 093-2453 1 973-2 373 1273-1 623 1 200-1 478 2 123-2 623 1273-1 773 1623 1773-2 273 2 073-2 373

Ivb, P.C., W’85 IIa(i) (EMPA), p.c. IVa(i), P.c., Re1B5 IVb, P.c., Fe59,99.96% IVb, D.c.. FeJ9 IVa(ij, S.C. and P.c., Co6O. 99.98% IVb, P.c., Co60 IVb, s.c., Ni63 IVb, P.c., UZ3’,99.98% IV, P.C., U’35

389 388 167 166 331 330 175 332 66 332 333 334 332 164 334 67 and 168 334 332 60 232 331 66 334 335 165 57

1.5 x 21.39 3.34~10-4 9.25 Graphical data only 0.08 35.29 0.15 35.55 0.37 40.86 1.79 48.73 0.54 43.92 0.52 42.62

298-351 274-350 297-353 273-365 272-359 272-363 293-363 316363 297-356

IVa(i), P.c., Agl’O, 99.95% IVa(i), P.c., AU”~, 99.95% IVa(i), P.c., Li6, 99.95% IVa(i). D.c.. K4’. 99.95% IVa(i), P.c., RbEk,99.95% IVa(i), P.c., Cd115,99.95% IVa(i), P.c., In114, 99.95% IVa(i), P.c., 1~113,99.95% IVa(i), P.c., TIzo4,99.95%

122 120 122 121 121 122 122 122 122

D=3.71 x IO-’” D= 1.02 x 10-9 1x 10-2 141.92 450 430.1 0.14 330.3

403-2613 1700-2000 2 123-2 663

IVa(i), P.c., C P , 99.9% Combined data from several sources IIIb(ii) IVa(i), P.c., Sn’I3. 99.85%

Element cm2s-l In M o

C

P

S Li

Y V Nb Ta Cr

W

Re

Fe co Ni

U

1.3 x

319.9 316.5

In N a Au Au Li K Rb Cd In Sn TI

~,,. I

~~~

In N b

cu C

AI Sn

P S

Y Ti Zr

5.1 x lo-’ 2.6 x 103 1.5 x 0.4 9.9 x lo-’ 0.47 0.85

V

Ta

cr

Mo

0.47 2.21 1.0 0.3 0.13 92 1.3 x lo-’

215.6 306.0 232.8 370.5 364.0 364 379.4 377 355.9 415.7 349.6 337.5 511 350.4

1 573-2 073

1 370 x 1770 1473-1 873 1 898-2 348 1267-1 765 1 855-2 357 1 923-2 523 1 898-2 348 1273-1 673 1 376-2 346 1 226-1 708 1 220-1 766 1998-2455 1973-2298

233 194 176 66 and 66a Ivb, S.C., P32, 99.9% 167 IVa(i), S.C. and P.c., S3’, 99.6% 177 IVb, s.c., Y91, 99.91993% 175 IVa(iii) and IIa(i) (EMPA),p.c.,99.9% 169 IVa(i), s.c., Ti44, 99.98% 170 IVa(iii) and IIa(i) (EMPA),P.c., 9.9% 169 IVa(i), s.c., Zrg5 336 IVa(iii) and IIa(i) (EMPA),p.c.,99.9% 169 IVb, s.c., V48, 99.98% 171 IVa(i), s.c., TalE2,99.76% 173 IVa(i), s.c., Cr”, >99.98% 172 IVa(i), P.c., Cr5’, 99.96% 337 IVa(iii) and IIa(i) (EMPA), p.c.,99.9% 169 ~ v b P.c., , ~ 0 9 9 333

Mechanisms of dz@iiwn Table 13.2 Element

w Fe

Ru Co

Ni U

TRACER IMPVRrrY DIPPVSON

Q

A

kJmol-I

_.

WEmVontinued

13-23 - .-

Temp.range

K

.-

Method

Re$

-_-.

5x10-4 383.9 7 x lo* 653 1.5 325.3 294.3 0.14 29.3 460.1 4 . 1 8 ~ 1 0 - ~ 257.2 274.7 0.11 295.2 0.74 336.6 9.3 264.2 7.7 x lo-' 321.5 8.9 x

2 073-2 473 2 175-2473 1 663 -2 373 1663-2 168 2 026.2 342 1 347-2 173 1 580-1 920 1 834-2 325 1261-1 519 1433-2 168 1773--2273

Ivb, P.C., w1=. 99.9% IVa(iii) and IIa(i) (EMPA),p.c., 99.8% IVa(ii), P.c., Fe5', 99.74% IVa(i) and (iii), P.c., Fes9, 99.9% Ib, P.c., Rulo3, 99.9% IVa(i), s.c., co6O IVa(iii), P.c., Co6O,99.9% IVa(ii), P.c., co6O, 99.74% Ivb, P.c., NP3, 99.82% IVa(ii) & b, P.c., N P , 99.9% IVb, P.c., Uzs5,99.55%

174 169 68 233 416 234 233 68 338 233 165

Graphical data only See Figure 13.3 4.6~10" 51.1 LOX lo-, 56.9

u and /3 range

IVa(i), P.c., Mn5*, 99.9%

220

In Nd ~

Mn

Fe --

.

. .

__

p-range

1

IVa(i), P.c., Fe, 99.9%

220 . .~

In N i

cu Ag

Au AI

In

0.57 0.61 0.27 8.25 8.94 2.0 1.o

258.3 255.0 255.5 282.2 279.4 272.1 260

1327-1 632 10804 613 1048-1 323 1123-1 323 1 297-1 693 1 173-1 373 914-1 212

A,= 1.26 A,= 1.9 x lo4

Nd

0.12 2.1 4.56 1.39 3.85 1.4 2.6 1.9 x 10-2 1.8"' 0.87 1.1 2.0 2.87 1.o 0.22 0.59 2.77 2.5 0.66 0.44

U

1.O

Pu

0.64"'

C

Ge Sn As

Sb S

Te Be Hf V

cr W Fe

co Pt Ce

137.3 264.0 267.2 251.8 264.0 219.0 254 193.4 251.0 278.4 272.6 299.4 308.1 269.4 252.9 269.6 285.1 286.8 254.6 250.5 236.1 213.5

873-1 673 939- 1675 1242-1 642 1239-1 634 1203-1 674 1078-1 495 1135-1 553 1293 1673 1 023- 1423 1073-1 573 1373-1541 1 373-1 568 1 346-1 668 1478-1 669 1223-1 643 1 123-1 643 1335 1696 1354 1481 973-1 370 973 1373 1248-1 348 1298-1 398

__

la) Estimated values. (b) An average value: 146 quotes ,4=0.14-1.14cm2s-'.

Iva(i), P.c., W4,99.955% IVa(i) (At. abs. analysis), P.c., 99.95% Iva(iii), s.c., Cd4, 99.999% IVb, s.c., Ag"O, 99.99% IVa(i), s.c., Ag110"06, 99.98% IVa(ii), P.c., AuI9', 99.98% IVa(iii) (SIMS), s.c., 99.99% Least squares fit. data of 238 aVa(i) s.c., In114, 99.98%] and 343 [IVa(iii) (SIMS),s.c., 99.99% IIa(ii), P.c., C14, 0.1 wt% C IVa(i) (ion impl.), s.c., G P ,99.99% IVa(i), s.c., Sn113,99.98% IVa(i), s.c., As7'. 99.98% IVa(i), s.c., Sbla5.99.98% IVa(i), s.c., S35, 99.98% IVa(i), s.c., TelZ3,99.99% IVb, P.c., Be7, 99.9% IIa(ii) (EMPA), P.c., 99.99% Ivb, pc., V48, 99.99% IVa(i), P.c., CrS1,99.95% Iva(i), p.c., WS5,99.95% 99.98% -1ValiL - I , I s.c.. W"'. IVa(i), s.c., Fe5*.'99.999% IVb and IIa(i) (EMPA), P.c., 99.999% IVb and IIa(i) (EMPA), p.c., 99.999% IVa(i), s.c., C O ~99.98% ~ , IVb, p.c., h193, 99.99% Iva(i), P.c., CeI4', 99.99% IVa(i), P.c., Nd'"'. 99.99% IVa(ii), P.c., P5, 99.998% IIla(i), pc.. P~'~~(autorad.), 99.997% I

__ ..

...

35 340 45 341 237 37 342 5 50 344 90 345 52 236 346 147 347 143 47 59 49 203 34 and 48 34 and 33 49 222 144

144 145 146 .

Dgusion in metals

13-24 Table 13.2

TRACER IMPURITYDIFFUSION m m m - a i n w d

kJmol-'

Q

h p . range K

Method

Re$

7.9 x 10-3 8.6 x 4.6 x lo-' 4.8 x

33.6 34.2 60.5 60.8

498-598 491-803 39s-598 470-750

IVa(i), p.c. and s.c., W4,IVa(i), s.c., C U ~99.9999% ~ , IVa(i), s.c., Ag"', IVa(i), s.c., Ag"', 99.999%

4.1 x 10-3 5.2 x lo-) 5.8 x 10-3

39.1 38.6 40.2

367-598 334-563 441-693

IVa(i), s.c., A u ' ~ 99.999% ~, IVa(i), sc., Au'~', 99.9999% IVa(i), s.c., A u ' ~ ~99.9999% ,

1.65 x to-'

47.8 88.9 92.8 95.0 86.7 112.2 101.9 94.4 99.4 92.9

453-773 423-593 523823 466-573 523-823 437493 48C-596 523-723 468-595 461-588 383-573 481-593 432-523 470-590 490-593 522-586

IVa(i), s.c., W 5 ,99.9999% Iva(i), s.c., cd"', 99.9999% IVa(i), s.c., Cd'05, 99.9999% IVa(i), sc., HgZo3,99.9999% IVa(i1. sc.. Hezo3. 99.9999% Ivaiiii) (EMFA), kc., 99.999% IVa(i), P.c., ' P O 4 , 99.99% IVa(i), s.c., Sn113,99.9999% Resistivity method IVa(i), s.c., SbIz4, 99.9999% IVa(i), P.c., Bi, 99.99% IVa(iii) (NRA), P.c., 99.9999% IVa(i), s.c., N P . 99.9999% IVa(i), P.c., NP3, 99.999% IVa(i), sd., Pd''*, 99.9999% IVa(i), s.c., (conc. via M.Pt.) 99.9999% IVa(i), s.c., Na", 99.9999%

85 51 85 239 and 348 31 349 239 and 356 242 93 350 141 350 139 32 243 351 140

1373-1523

IVa(i), P.c., Fe59,99.95%

A

Element an's-'

In Pb cu Ag Au

Zn cd Hg In

TI Sn

Sb Bi

co Ni Pd Pt Na

0.409

0.92 1.05 1.5 33 0.511 0.41 0.29 0.29 D=2.66 x lo-'' ~=1.006~10-9 46.4 9x 9.4~10-3 44.5 1.1 x 10-2 45.4 3.4 10-3 35.4 1.1 x 42.3 6.3 118.5

;;::;I

32 241 240 352 239 353 354

In Pd

Fe

0.18

260.0

357

In Pr cu Ag Au Zn

Zn

In La Hb Mn

Fe

co

8.4 x 10-2 75.8 5.7 x 10-2 74.5 1.4 x lo-' 106.3 90.0 3.2 x 4.3 x lo-' 82.5 3.3 x 10-2 [IC D = 4 . 4 ~ ICD = 3.7 x /IC D=4.6 x le D=4.0~ 1.8 x lo-' 103.8 6.3 x lo-' 113.0 D=3.2~10-~" 9 . 6 lo-' ~ 121.0 D = 1.1 x 10-9fe) 1.8 x lo-' 107.6 D=3.35~ 9.5 x lo-) 110.1 Graphical data only. See Figure 13.3 2.1 x 10-3 39.4 4.0 x 10-3 43.5 4.7x 10-2 68.7 0=4.6x 10-5 D = 5.0 x

"r 1

926-1 059 (a) IVa(i), P.c., CuS4,99.9% 1086-1 187 (p)> 886-1 040 (a) IVa(i), P.c., Ag"', 99.93% 1085-1 195 @I)> 870-1 015 (a) IVa(i), P.c., A U ' ~99.93% ~, 1075-1 185 (p)> 1013 (E) IVa(i), s.c., A U ' ~99.94% ~, 1053 (a) 876-1 040 (a) IVa(i), P.c., W',99.97% 1039 (a) IVa(i), P.c., In114, 99.96% 1075-1 200 @)> 1041 (a) 1 IVa(i), P.c., Id 4', 99.96% 1om-i is0 ( p ) l

199 200 200 355

202 201

201

1004 (a) 1085-1 180 (p)> a and p range

IVa(i), P.c., H o ' ~ 99.96% ~, IVa(i), P.c., MnS4, 99.9%

20 1 220

885-1 060 (a) 1075-1 180 885-1 036 (a)

IVa(i), P.c., Fe59,99.9%

220

IVa(i), pc., C O ' ~ O , 99.93%

200

(a)>

1151 (B)

(a) Values estimated from graphical data.

Mechanisms of dzfiion Table 13.2

T R A ~ Rm

m

13-25

DIFFUSION coEmmNrseontinued

Temp. range

A

Q

klmol-’

K

Method

Ref.

0.13 0.13 1.3 x 7.3x10-’ 2.5x10-’ 19.6

258.1 252.0 193.6 122 243.4 310.7

1473-1 873 850-1 265 1373-1 872 1023-1 223 1273-1 673 1023-1 323

IIa(ii) (EMPA), P.c., 99.99% IValil. s.c.. A U ” ~ . 9939% IIa(kj’(EMPA), p:c., 99.99% IVa(i), P.c., MnS4 IIa(ii) (EMPA), P.c., 99.99% IVC, P.C., C060,99.99%

244 245 244 420 244 204

IIa(ii), p.c.

247

I W ) , P.c.,

247

IVa(i), P.c.. Au”* Iva(i), P.c., Cos’ IVa(i), P.c., Cos”

246 253

Elemenr cm2s-’ In Pt Ag Au A1

Mn Fe Co I n Pu Cu A!3 Au Co

1.0~10-~ 51.5 D = 1.08 x lo-’” 40.2 4.9 x 10-15 D = 2 . 3 7 ~lo-’’ 5.7 x 43.1 1 2 ~ 1 0 - ~ 53.2 1.4~ 41.4

713 (6) 78&887 617499 (6) 757-894 ( E )

4.5 205 1.5~-” 54 D=4.1 x lo-’ ~ = 2 . 6 x10-5 D=3.4x lo-’ D=4.4x10e5

1273-1 573 1241-1 528 (a) 1643 (B) 1702 (4) I 755 (;a) 1790 (P)

IVb, P.c., C14

423

IIa(ii) (SMLS), P.c., 99.96%

406

1jc 1.10~10-5 57.8 i c 1 . 7 x 103 iii.o> 2 x 10-3 69.5

333.43 333-423

Ivb, S.C., s35 rvC,p.c., ~ 1 2 0 4

205 206

3.6

773-1 173 (a)

IVb, P.c.. CI4

55

247

In Sc C Fe

1 J

In Se S

T1 In Sm C In

Sn

cu Ag Au Zn Cd

Hg In

TI Sb Fe co Ni

146.4

/IC D = 2 ~ 1 0 - ‘ I c 2 . 4 ~ 1 0 - ~ 33.1 IIc 7.1 x ~ O - ~51.5 I C 0.18 77.0 I!c 5 . 8 ~ 46.1 IC0.16 74.1 Iic 1.1 x lo-’ 50.2 IC8.4 89.2 /IC 220 IC0.18 /IC 1.5 105.91 l c 30 112.21 /IC 12.2 IC34.1 108.0 < 3 ~ 1 0 - ~ 61.5 llc 7 I C 73 4.8 x 51.1 5.5 92.1 Ilc 1 . 9 2 ~ 1 0 - ~18.1 IC1 . 8 7 lo-* ~ 54.2

I I

::::;I

1

cu@

95

IVa(i), s.c., Ag”’

87

408-498

IVa(i), s.c., A U ’ ~ ~

87

408496

Na(i), s.c.. ZnS3, 99.999%

198

463-498

IVa(i), s.c., Cd”’, 999.999%

198

447-499

IVa(i), s.c., HgZo3,99.9999%

136

453-494 4.104489 4-99 387-462 413-490

IVa(i), s.c., In114,99.998% IVa(i) and (ii), P.c., Tl’04, 99.999% IVa(i), s.c., Sb, 99.999% Vd, P.c., Fe”, 99.9995% IVb, S.C. and P.c., Co6’, 99.999% IVa(i), s.c., NiS3,99.999%

30 138

&03 408-498

Iva(i), s.c.,

198 359 382 365

13-26

Dilfusion in metals

Table 132

TRACER IMFWRITY DIFFUSION

A Element cm2s-’

AI C S

Y Nb

Mo Fe

co

co U

Q

klmol-’

1.5 306.2 6.7 x 161.6 0.01 293.1 0.12 302.3 0.23‘“’ 413.2 1.8 x 339.1 0.505 298.9 329.9 5.9 x IO-’ D=1.4~10-~ D = ~ . O X 10-9 ~ = i .xi10-9 D=1.14~ 7.6 x 10-5 353.4 1.03 x 117.2

ammcmm-cuntinzted Temp. range K

1750-2 050 463-2 953 1970-2 110 1473-1 773 1 194-2 757 2 923-2 493 1203-1 513 2053-2330 (b)

2053 28301 1 8 7 3 2 243 2 186-2 530

Method

R4.

IIIb(ii) Combined data, several sources IVb, SJ5, P.c., 99.0% Ivb, Y9’Y, S.C., 99.8/99.9% IVa(i), Nb95,S.C. and P.c., 99.7% IVa(i), Fe59,p.c.

176 194 162 175 77 358 76 360

IVa(i), CoSo,p.c.

360

~ v b~, 0

9 9 ,P.C.

-,-,pc.. -

IVa(i), NiSo, pc. 360 Ivb, u335,p.c.. 57 IVa(ii) (fission fragment, radiography), 329 nat.U, P.c., 99.9997%

(a) Average values-Arrhenius

plot very slightly curved. (h) Values estimated from graphical representation of results.

In Te Hg Sb Se

3.4~ 78.3 /IC 4 . 6 ~ 1 0 - ~ IC1.34 2.6~10-~ 119.7

i:}

543-713

IVa(i), P.c., HgZo3

81

551-647 593-713

IVa(i), s.c., SbIz3 IVa(i), P.c., Se75

410 81

IIa(i) (SSMS),P.c., 99.95% IIa(ii) (SSMS),P.c., 99.95% IIa(ii) (SSMS),ps., 99.95% Iva (via z-emission spectra), pau1, P.c., 99.84% IVa (via z-emission spectra), U233, P.C., 99.84%

248 248 248 207

1713-1 193 1 773-1 873 1 693 1963 1643-1 933 1643-1 933 1648-1933 1698-1 873 1683-1 818 1 6 6 3 1 943 1613-1 898 1613-1 898 1613-1 898

IIa(ii), p.c. IIa(ii) (SMLS),P.c., 99.977%

407 390

IVa(i), P.c., HflS’

391

IIa(ii) (SSMS),P.c., 99.95% IIa(ii) (SSMS),pc., 99.95% IIa(ii) (SSMS),P.c., 99.95% IIa(ii) (SMLS),P.c., 99.977% IIa(ii) (SMLS),P.c., 99.977% IIa(ii) (SLMS), P.c., 99.977% IIa(ii) (SSMS), P.c., 99.95% IIa(i) (SSMS), ps., 99.95% IIa(ii) (SSMS), P.c., 99.95%

249 249 249 390 390 390 248 248 248

973-1 873-1 873-1 923-1

“X-ray di& method”, p.cl 366 IIa(i) (ion impl.) (N.R.A.), P.c., 99.9% 367 IVb, P.c., C14 83 IIIb(i) (ion impl.) (N.R.A.), P.c., 99.9% 368 IVa(i), P3’, S.C. For Ts. Graham and D. H. Tomlin, Phil. Mag., 1963,8, 1269. J6Askill and G. R. Gibbs, Phys. Status Solidi, 1965,11,557. (Contains recalculated values of As and Qs from the measurements on Cr, Mn, Fa, Co, Ni, Nb and Mo reported in ref. 64.However, since these seem, in some cases, to give a much inferior representation of the original data, none is quoted. 65. J. Askill and G. B. Gibbs, Phys. Status Solidi, 1965,11, 557. 66. J. Askill, Thesis Reading, 1964,and ‘Diffusion in B.C.C. Metals’ (American Society for Metals 1965) 247. 66a. J. Askill, Phys. Status Solidi, 1965, 9,K167. 67. S.Z.,Bokshtein, M. B. Bronfin and S. T. Kishkin, ‘Diffusion ProcessesStructure and Properties of Metals’ (Moscow 1964). Translation---ConsukantsBureau New York; 1965, 16. 68. R. F. Peart, D. Graham and D. H. Tomlin, Acta Met., 1962, 10, 519. 69. J. I. Federer and T.S. Lundy, Trans. M a . Soc.AIME, 1963, 227, 592. 70. L.V. Paslinov, Phys. M e t . Metallog., 1967. 24 (2), 70. EL.Grurin, V. S. Emelyanov, G. G. Ryabora and G. B. Federov, Geneva Conference Proceedings, 1959,19, 187. 72. G. B.Federov, E. A. Smirnov, I;.I. Zhomev, F. I. Gusev and S. A. Paraev. Met. Metalloved. Christ. Metal., 1971, 9,30. 73. E.V. Rorisov, Y. G. Godin, P. L. Gruzin, A. I. Eustyukhin and V. S . Emelyanov, Met. i Met. Izdatel Ak. Nauk. SSSR. Moscow, 1959 and in Translation NP-TR-448 (1960)p. 196. 74. Ch. Herzig. J. Neuhaus, K. Vieregge and L. Manke, Materials Sci. Forum, 1987,15-18, (Pt. l),481. 75. R. L. Andelin, J. D. Knight and M. Kahn, Trow. Met. SOC.AIME, 1965,233, 19. 76. Y. P.Vasil’ev, I. F. Kamardin, V. I. Skatskii, S. G. Chermomorchenko and G. N. Schuppe, Trudy. Stred. Gos Uniu. in u. i. Lenina, 1955,65,47. 77. R. E. Pawel and T. S. Lundy, J. Phys. Chem. Solids, 1965, 26,937. 78. N. L. Peterson and S. J. Rothman, Phys. Reo., 1964,136.4, 842. 79. S. J. Rothman, J. mtcl. Mater., 1961, 3, 77. 80. S. J. Rothman, N. L. Peterson and S. A. Moore, J . nucl. Mater, 1962, 7, 212. 81. Sh. Merlanov and A. A. Kulier, Soviet Phys. solid St., 1962,4, 394.

Mechanisms of difision

13-35

82. M. C. Naik, J. M. Dupouy and Y. Adda, Remte Metall., Paris, 1966,63,488. 83. A. I. Nakanechnikov and L V. Pavlinov, Izv. Akad. N d SSSR Metal, 1972, No. 2,213. 84.J. Askill, Phys. Status Solidi, 1971, B43, 1K. 85. B. Dyson, T.R. Anthony and D. Turnbull, J . appl. Phys., 19637 (6). 2370. 86. A. P. Batra and H. B. Huntington, Phys. Rev., 1966, 145, 542. 87. B. Dyson, J. appl. Phys., 1966,37, 2375. 88. 0.Caloni, A. Ferrari and P. M. Strocchi, Electrochem Metall., 1969, 4,45. 89. V.Ya. Shchelkonogov, L. N. Aleksandrov, V. A. Piterimov and V. S . Mordyuk, Phys. Met. Metallog., 1968, 25 (I), 68. 90. A. B. Vladimirov, V. N. Kaygorodov, S. M. Klotsman and I. Sh. Trakhtenberg, Fiz. Met. Meralloued., 1979. 48,352. 91. A. J. Mortlock and P.M. Ewens, Phys. Rev., 1967,156, 814. 92. J. Askill, Phys. Status Solidi, 1%6, 16,63K. 93. J. W.Miller, Phys. Rev., 1969, 181, 1095. 94. T. R. Anthony and D. Turnbull, Phys. Rev., 1966,151 (2),495. 95. B. F. Dyson, T. R. Anthony and D. Turnbull, J. appl. Phys., 1%7,38 (8), 3408. 96. R. M. Dubovstev, V. S. Dbtov, T. I. Miroshnichenko and N. A. Nikolaev, Fiz. Met. Merdlowd, 1976,42, 1314. 97. T. R. Anthony, B. F. Dyson and D. Turnbull, J . appl. Phys., 1968,39, (3),1391. 98. A. P. Batra and H . B. Huntington, Phys. Reo., 1967, 154, 569. 99. K. J. Anusavic and R. T. de Hoff, Met. Puns., 1972,3, 1279. 100. S.M. Klotsman, et a!., Fiz. Met. Metallmed, 1971,31,429. 101. F. D. Reinke and C. E Dahlstrom, Phil. Mug., 1970, 22, 57. 102. S. M. Klotsman, et ul., Fizica Metall, 1970, 29,803. 103. K. Hoshino, Y. Iijima and K-I. Hirano, Met. Trans A, 1977,8A,469. 104. M. C. Savena and B. D. Sharma, Trans. Indiun Inst. Metals, 1970, 23, 16. 105. F. Moya, G.E. Moya and F. Cabana-Brouty, Phys. Status Solidi, 1969,35, 893. 106. J. Bernardini, and J. Cabane, Acta Met., 1973,21, 1561. 107. T. Hehenkamp and R. Wubbenhont, 2.Merallk, 1975,66,275. 108, N.Barbouth, J. Oudar and J. Cabane, C. r. hebd. S&nc. Acud. Sei., Paris, 1967, C264, 1029. 109. J. Geise, H.Mehrer, Ch. Herzig and G. Weyer, Mater. Sei. Forurn, 1987, 1518,443. 110. K. Dreyer, Chr. Henig and Th. Heumann, ‘Atomic Transport in Solids and Liquids’ (Proc. Europhy. Cod.)(Verlag Z. Natu$obrsch. 1971),237. 111. Ch. Herzig and Th. Heumann, 2. Natu@orsck, 1972, n u , 613. 112. A. Ott, Z.Natqforsch, 1970, 25% 1477. in.A. ott, J. appr. phys., 1%9,40,2395. 114. A. Ott, D.Lazarus and A. Lodding, Phys. Rev., 1969,188, 1088. 115. A. Ott, Z.Namrforsch., 1968, 23a, 2126. 116. J. N. Mundy, A. Ott and L Lowenbe& 2. Natsvforsch., 1%7,22a, 2113. 117. J. N. Mundy, A. Ott, L. Lowenberg and A. Lodding, Phys. Status Solidi, 1968,35,359. 118. A. Ott, Z.Natdorsch., 1968, 23a, 1683. 119. A. Ott and A. Norden-Ott, 2. Nuturfmsch., 1968, Ua,473. 120. L. W. Barr, J. N. Mundy and F. A. Smith, Phil. Mag.,1969, 20,389. 121. L. W. Barr, J. N. Mundy and F. A. Smith, Phil. Mug., 1967, 16, 1139. 122. L.W.Barr and F. A. Smith, DIMETARZ, Proc. Intl. Conf. Digusion in Mefalsand Alloys (eds F. J. Kedves and D. I. Beke), Trans Tech Publs., Switzerland, 1983, p. 325. 123. F. A. Smith and L.W. Barr, Phil Mag., 1970,21,633. 124. F.A. Smith and L. W. Barr, Phil. Mug., 1969,20,205. 125. V. M. Ananyn, et al., Sou. J . At. En., 1970,29, 941. 126. J. Combronde and G. Brebec, Acta Met., 1972.20, 37. 127. K.Lal, Report CEA (Saclay) R3136, 1967. 128. J. S. Warford and H. B. Huntington, Phys. Rev., B., 1970. 1, 1867. 129. Mao. Chih-wen, Phys. Rea., B, 1972, 5,4693. 130. S.Badrinarayanan and H. B. Mathur, Inti. J . appl. Radiat. isotopes, 1968.19. 353. 131. D.L. Bdke, I. G6deny and F. J. Kedves, Phil. Mag. A, 1983,47,281. I. Godhy, D. L. Beke and F. J. Kedves, Phys. Stat. SoIidi (a). 1972,13,K155. D. L. Beke, I. Giidtny and F. J. Kedves, Acta Mer.. 1977,25,539. 132. J. J. Blechet, A. Van Craeynest and D. Calais, J. mcl. Marer., 1968,27, 112. 133. G.M.Hood and R. J. Schultz, Phil. Mag., 1971. 23, 1479. 134. G.M. Hood, Phil. Mag., 1970,21, 305. 135. M. S. Anand and R. P.Agarwala, Phil. Mag., 1972,26, 297. 136. W.K. Warburton, Phys. Rev., 1972,B6, 2161. 137. G.M. Hood and R. J. Schultz, Phys. Reu. B, 1975,B11, 3780. 138. L. Bartha and T. Szalay, Int. J . appl. Rudiat. Isotopes, 1969, ZO, 825. 139. J. Kucera and K. Stransky, Can Met. Q.,1969, 8, 91. 140. S. Nishikawa and K. Tsumuraya, Phil. Mag.,1972,26, 941. 141. W.K.Warburton, Pkys. Reo., 1973, B15. 1330. 142. L. V. Pavlinov, A. M. Gladyshev and Y. N. Bykov, Fiz. Met. Metalloued, 1968, 26,946. 143. S. P. Murarka, M. S. Anand and R. P. Agarwala, Acta Mer., 1968,16,69. 144. A. R. Paul and R. P.Agarwala, Metal P a m . . 1971,2,2691.

13-36 Diffusion in metals 145. J. P. Zanghi, A. Van Craeynest and D. Calais, J. nucl. Mater., 1971,39, 133. 146. J. J. Blechet. A. Van Craeynest and D. Calais, J . nucl. Mater.. 1968,28, 177. 147. G. V. Grigorev and L. V. Pavlinov, Fiz. Met. Metdloued, 1968, 25, 836. 148. G. V. Grigorev and L. V. Pavlinov, Fiz. M e t . Metalloued, 1968, 26, 946. 149. G. V. Grigorev and L. V. Pavlinov, Fiz. M e t . Metalloued. 1968, 25, 377. 150. A. Hoshino and T. Araki, Trans. Nut. Res. Inst. Metals, 1971. 13, 99. 151. A. W. Bowen and G. M. Leak, Met. Trans., 1970, 1, 1695. 152. K. Nohara and K. Hirano, Proc. Znt. Conf: Sci. Tech. Iron and Steel, 1970,7, 11. 153. S. M. Myers and H. J. Rack, J. Appl. Phys., 1978, 49, 3246. 154. D. W. James and G. M. Leak, Phil Mag., 1966, 14, 701. 155. G. Salje and M. Feller-Kniepmeier, J. appd. Phys., 1977, 48, 1833. 156. M. Fromont, J. Phys. (Paris) Lett., 1976, 37, 117: 157. L. V. Pavlinov and B. N. Bykov, Fiz. Met. Metalloued, 1966. 22, 234. 158. Bondy and V. Levy, C. r. hebd. Sdanc. Acad. Sci., Paris, 1971, C272,81. 159. G. A. Bruggeman and J. A. Roberts Jr., Met. Trans. A. 1976,6,755. 160. F. De Keroulas, J. Morey and Y. Q u h , J. nucl. Mater., 1967, 2,276. 161. Ye. V. Deshkevish, R. M. Dubovtsev and V. S. Zotov, Fiz. Met. Metallotied, 55,1983, 186. 162. B. A. Vandyshev and A. S. Panov, Zzu. Akad. Nauk SSSR Merally, 1969,1,244. 163. B. A. Vandyshev and A. S . Panov, Iw. Akad. Nauk SSSR Metalty, 1970,2,231. 164. L. M. Mulyakaev, G. U. Scherbedinskii and G. N. Dubinin, Metallou. term. Obrab. Metall., 1971, 8, 45. 165. L. U. Pavlinov, A. I. Makonechnikov and V. N. Bykov, Soviet J. Atom Energy, 1965, 19, 1495. 166. B. A. Vandyshev and A. S . Panov, Fizica Metal!., 1968, 25, 321. 167. B. A. Vandyshev and A. S. Panov, Fizica Metall.. 1968, 26, 517. 168. J. Askill, Phys. Status Solidi, 1967, 23, K2l. 169. F. Roux and A. Vignes. Rev. Phys. appl. (Fr.],.1970, 5, 393. 170. J. Pelleg, Phil. Mag., 1970, 21, 735. 171. R. P. Agarwala, S. P. Murarka and M. S. Anand, Acta Met., 1968, 16. 61. 172. J. Pelleg, Phil. Mag., 1969, 19, 25. 173. T. S. Lundy, et al, Trans. Met. Soc. A I M E , 1965, 233, 1533. 174. G. B. Federov, F. J. Zhomov and E. A. Smirnov, Metall. Metallotied. Chist. Metal, 1969, 8, 145. 175. D. S. Gornyi and R. M. Altovski, Phys. Met. Metallog., 1971, 31 (4), 108. 176. G. I. Nikolaev and N. V. Bodrov, Zh. Fiz. Khim., 1978,52, 143. 177. B. A. Vandyshev and A. S. Panov, Izu. Akad. Nauk SSSR., 1968,1,206. 178. S. N. Balrt, N. Varela and R. Tendler, J. Nuclear Mater., 1983, 119, 59. 179. R. Tendler and C. F. Varotto, 3. nucl. Mater. 1973, 46, 107. 180. G. M. Hood and R. J. Schultz, Phil Mag., 1972,26, 329. 181. G. M. Hood, 'Diffusion Processes', 1970, Vol. 1, New York, Gordon and Breach, p. 361. 182. G. V. Kidson and G. J. Young. Phil Mag.,1969, 20, 1057. 183. F. Dyment and C. M. Libanati, J. Mater. Sci., 1968,3,349. 184. R. P. Agarwala and A. R. Paul, Proc. nucl. Rad. Chem. Symp., 1967, 3, 542. 185. A. R. Paul, et al., Int. Con$ Vac. and Insls. in Metals, Julich, Sept. 1968, 1, 105. 186. E. Ch. Schwegler and F. A. White, Intl. J. Mass Spectr. Zon Phys., 1968,1, 191. 187. L. V. Pavlinov, G. V. Grigorev and G. 0. Gromyko, D o . Akad. Nauk. SSSR Metal, 1969,3,207-Russian Metallurgy, 1969, 3, 158. 188. R. P. Agarwala and A. R. Paul, J. Nucl. Mat., 1975, 58,25. 189. B. A. Vandyshev, A. S. Panov and P. L. Gruzin, Fizica Metall., 1967, 23, 908. 190. N. K. Archipova. S. M. Klotsman, I. P. Polikarpova, G. N.-Tart&nova, A. N. Timofeev and L. M. Veretennikov, Phys. Rev. 8,1984, 30, 1788. 191. L. M. Larikov, V. M. Tyshkevich and L. F. Chorna, Ukr. Fiz. Zk.,1967,12, 983. 192. R. E. Pawel and T. S. Lundy, Acta Met., 1969, 17, 979. 193. M. P. Dariel, M. Blumenfeld and G. Kimmel, J. appl. Phys., 1970,41, 1480. 194. F. A. Schmidt and 0. N. Carlson, 1. Less Common Metals, 1972,26,247. 195. L.V. Pavlinov, Phys. Met. Metallog., 1970, 30(4), 129. 196. A. Languille, Mhm Scient. Reare MetaN., 1971, 68, 435. 197. M. Dariel, G. E r a and G. M. J. Schmidt, Phil. Mag., 1969, 19, 1053. 198. F. H. Huang and H. B. Huntington, Phys. Rev., 1974,9B, 1479. 199. M. Dariel, 3. appl. Phys., 1971, 42, 2251. 200. M. Dariel, G. Erez and 0.M. J. Schmidt, J. appl. Phys., 1969, 40,2746. 201. M. Dariel, G. E r a and G. M. J. Schmidt, Phil. Mag., 1969, 19, 1045. 202. M. P. Dariel, Phil. Mag., 1970, 22, 563. 203. H. Backer, J. Backui and F. Waals, Phys. Status Solidi (b), 1971,45, 633. 1968, 7, 73. 204. A. Kueera and T. Zemcik, Can. Met. 205. P. Briitter and H. Gobrecht, Phys. Status Solidi, 1970, 41, 631. 206. P. BrZtter, H. Gobrecht and D. Wohig, Phys. Status Solidi, 1972, 11, 589. 207. F. Schmitz and M. Fock, 3. nucl. Mater., 1967, 21, 353. 208. D. Treheux, et al., C. r. hebd. Shanc. Acad. S c i , Paris, Series C. 1972,274, 1260. 209. M. P. Dariel, D. Dayan and D. Calais, Phys. Status Solidi, 1972, AlO, 113. 210. R L. Fogel'son, Ya. Y. Ugai and I. A. Akimova, Fiz. Met. Metalloved, 1975, 39,447. 211. R. L Fogel'son, Ya. Y. Ugai and I. A. Akimova, Izv. Vyssk Uchebn Zaued., Tsuem Metall., 1975,2, 142 212. J. Ladet, J. Bernardini and F. Cabane-Brouty, Scr. Met., 1976, 10, 195.

e.,

Mechanisms of diffusion

13-37

F. Sawayanagi and R. R Hasiguti, J . Jap. Inst. Met., 1978,42, 1155. S. J. Rothman, N. L Peterson, L. J. Nowicki and L. C. Robinson, Phys. Stanrs Solidii B, 1974, 63, K29. K. Hirano and S. Fujikawa, J. Nuclear Mat., 1978,69/70,564. R. L. Fogel’son and N. N. Trofimova, Im.Vyssk Uchebn. Zawd., Tsuetz. Metall., 1978, 4, 152. S. M. Meyers, S. T. Picraux and T. S. Prevender, Phys. Reu., 1974.9,3953. V. P. Gladkov, A. V. Svetlov, D. M. Skorov, V. I. Tenishev and A. N. Shabablin, At. Energ., 1976,40,257. V. M. Anan’in, V. P. Gladkov, A. V. Svetlov and D. M. Skorov, Sou. J . At. Energ., 1976,40, 304. M. P. Dariel, Acta Met., 1975, 23, 473. M. P. Dariel, Phil. Mag., 1973, 28, 915. B. Million and J. Kucera, Kououe Mater., 1973, 11, 300. A. Bristoti and A. R. Wazzan, Rev. Bras. Fis., 1974. 4 1. J. M. Dupouy, J. Mathie and Y. Adda., Proc. Int Conf. Metallurgy of Be. Grenoble, p. 159, 1965. D. C. Yeh, L. A. Acuna and H. B. Huntington, Phys. Rev, 1981, 23, 1771. G.Krautheim, A. Neidhardt and V. Reinhold, Krist. Techn., 1978, 13, 1335. V. A. Gorbachev et al., Fiz. Metal. Metalloued., 1973, 35, 889. G.Barreau, G.Brunnel, G.Ciceron and P. Lacombe, C . R. Acad. Sci (Paris),1970. 270, 516. J. Bernardini and J. Cabane, Acta Met., 1973, 21, 1561. S. M. Klotsman e t al., Fiz. Met. Metalloved, 1978, 45, 1104. V. A. Gorbachev et al,, Fiz. Mer. Metalloued, 1977. 44,214. K. Nohara and K. Kirano, Nippon Kinzoku Gakkaischi, 1973,37, 731. D. Ablitzer, Phil. Mag., 1977, 35, 1239. J. Pelleg, Phil. Mug., 1976, 33, 165. F. Dyment, J. Nuclear Mat., 1976, 61, 271. A. B. Vladimirov et at., Fiz. Metal. Metalloved, 1975, 39, 319. A. B. Vladimirov et al., Fiz. Metal. Metullowd, 1978, 45, 1015. A. B. Vladimirov et al., Fiz. Metal. Metalloued, 1978, 45, 1301. D. L. Decker, C. T. Candland and H. B. Vanfleet, Phys. Reo., 1975, B11,4885. C. T. Candland and H. E. Vanfleet, Phys. Rev., 1973, B7, 575. K. Kusunaki and S . Nishikawa, Scripta Met., 1978, 12, 615. D. L. Decker et al., Phys. Rev., 1977, BlS, 507. D. L. Decker, J. D. Weiss and H. B. Vanfleet, Phys. Reu., 1977, B16,2392. D. Bergner and K. Schwarz, Neue Huette, 1978, 23, 210. G.Rein, H. Mehrer and K. Maier, Phys. Status Solidii, 1978, A45, 253. C. Charissoux, D. Calais and G. Gallet, J . Phys. C hem Sol., 1975,36, 981. C. Charissoux and D. Calais, J. Nuel. Mat., 1976, 61,317. W. N. Weins and 0.N. Carlson, J . Less C o m n Met, 1 9 7 9 , 6 9 9 . F.A. Schmidt, R. J. Commius and 0. N. C a r h n , J. Less Common Met., 1978,56, 53. J. Pelleg, Phil. Mag., 1975, 32, 593. J. Pelleg and M. Herman, Phil. Mag., 1977, 35, 349. J. F. Murdock and C. J. McHargue, Acta Met., 1968, 16, 493. C. Charissouxhnd D. Calais, J . Nuclear Mat., 1975,!57,45. R. Tendler and C. F. Varotto, J . Nucl. Mat., 1974, 54, 212. R. Tendler, J. Abriata and C. F. Varotto, J. Nucl. Mat., 1976, 59, 215. G. ErdClyi et ab., Phil. Mag., 1978, 38, 445. G. Tobar and S. Balart, DIMETA-88. Proc. Intl. Conf. Diffurion in Metals and Alloys (eds F. J. Kedves and D. L. Beke) Defect and Diffusion Forum, 1989,66-69, 381. 258. P. Dorner. W. Gust, H. B. Hintz. A. Lodding, H. Odelius and B. Predel, Acta Met., 1980, 28, 291. 259. S. J. Rothman and N. L. Peterson, Phys. Rev., 1967,154. 552. 260. R. L. Fogelson, Ya. A. Ugay and I. A. Akirnova, Izu. Vyssh. Uchebn. Zaued., Tvuertn. Metall., 1977. (1). 172. 261. H. Mehrer and D. Weiler, Z. Metallk., 1984, 75, 203. 262. G. Rummel and H. Mehrer, DIMETA 88. Proc. Inti. Con$ Diffusion in Merals andAIIoys (edsF. J. Kedves and D. L. Beke) Defect and Diffusion Forum, 1989,66-69,453. 263. F. Makuta. Y. lijima and K. I. Hirano, Trans. Jap. Inst. Metals, 1979, 20, 551. 264. G. Neumann, M. Pfundstein and P. Rcimers, Phys. Stat. Solidi (a), 1981,64,225. 265. G.Neumann, M. Pfundstein and P. Rehers. Phil. Mag. A , 1982,45,499. 266. Y. Minamino. T. Yamani and H. Araki, M e t . Trans. A, 1987,18,1536. 267. S. Sudar, J. Csikai and M. BucLko, Z . Metallk., 1977,68, 740. 268. G. P. Tiwari and B. D. Sharma, Indian J . Technol.. 1973.11, 560. 269. N. V. Chi and D. Bergner, in DIMETA82. Proc. intl. Conj:.Diffusion in Merals and Alfoys (edxs F. J. Kedves and D. L. Beke). Trans Tech Publs, Switzerland, 1983, p. 334. 270. G. M. Hood, R. J. Schultz and J. Armstrong, Phil. Mag. A, 19R3-47, 775. 271. Ch. Herzig and D. Wolter, Z . Metallk., 1974, 65. 273. 272. D. Cardis, Thesis. Univ. of Miinster, 1977. 273. R. L. Fogelson, N. N. Kazimirov and I. V. Soshnikova, Fie. Met. Metalloued, 1977, 43, 1105. 774. Ch. Herzig, H. Eckseler, W. Bussmann and D. Cardis, J. Nuclear Mater.. 19’’. 69/70, 61. 275. 4. E. Reynolds, B. L. Averbach and M. Cohen, Actn. Met., 1957,5, 29. 276. R. L. Fogelson, Ya. A. ugdy and I. A. Akimova. Fiz. Met. Metalloued. 1976.41, 653. 277. R. L. Fogelson, I. M. Vorinina and 1.I. Somova. Fiz. Met. Metalloued, 1978, 46. 190. 278. S. M. Meyers and R. A. Langley, J. Appl. Phys., 1975, 46, 1034. 279. G. Danz. R. Le Hazif, F. Maurice, D. Dutilloy and Y. Adda, Comptes Rend. Acad. Sci. (Paris), 1962,254,2328.

213. 214. 215. 216. 217. 218. 219. 220. 221. 222. 223. 224. 225. 226. 227. 228. 229. 230. 231. 232 233. 234. 235. 236. 237. 238. 239. 240. 241. 242. 243. 244. 245. 246. 247. 248. 249. 250. 251. 252. 253. 254. 255. 256. 257.

13-38 Diffusion in metals 280. G. Marbach, C. Charissoux and C. Janot, 'La Diffusion dans les Milieux Condensks-Thkorie et Applications', Proc. Colloque de McWlurgie, CEN Saclay, Vol. 1, 1976, p. 119. Report CEA-Conf. 36734. 281. M. Arita, M. Nakamura, K. S. Goto and Y.Ichinose, Pans.Jap. Inst. Met., 1984, 25, 703. 282. M. M. Pavlyuchenko and I. F. Kononyuk, Dokl. Acud. Nauk. Belorusskoi SSR, 1964,8, 157. 283. 5. Kufera, B. Million and J. RtEiZkova. Phys. Stat. Solidi (a),1986,%, 177. 284. Y.Iijima and K. I. Hirano, Phil. Mag., -977, 35, 229. xrrkdd"v* Phys. Rev. B, 1979.20, 3949. 285. M. P. Dariel, L. Kornblit, B. J. Beaudry lrnd 286. S. Fujikawa, M. Werner, H. Mehrer and A. Seeger, Mater. Sci. Forum, 1987,15/18, 431. 287. V: A. Gorbachev, S. M. Klotsman, Ya. A. Rabovskiy, V. K. Talinskiy and A. N. Timofeev, Fiz. Met. Metalloued, 1972, 34, 879. 288. V. A. Gorbachev, S. M. Klotsman, Ya. A. Rabovskiy, V. K. Talinskiy and A. N. Timofeev, Fiz. Met. Metalloued, 1973, 35, 143. 289. R. L. Fogelson. Ya. A. Ugay, A. V.Pokoev, I. A. Akimova and V. D. Kretinin, Fiz. Met. Metalloved, 1973,35, 1307. 290. G. Krautheim, A. Neidhardt, U. Reinhold and A. Zehe, Phys. Letters A , 1979,72, 181. 291. P. Spindler and K. Nachtrieb, Phys. Stat. Solidi (a),1976, 37,449. 292. Y. Iijima. K. Hoshino and K. I. Hirano, Met. Trans. A , 1977, 8,997. 293. G. Barreau, G. Brunel and G. Cizeron, Comptes. Rend. Acad. Sci. (Paris) C, 1971,272,618. 294. R. L. Fogelson, Ya. A. Ugay and A. V. Pokoev, Izv. Vssh. Ucheb. Zaved.,, Chon. Met., (9), 1973,136. 295. K. Maier. R. Kirchheim and G. Tolg. Microchim. Acta Suppl., 1979, 8, 125. 296. S. Badinarayan and H. B. Mathur, Indian J. Pure Appl. Phys., 1972,10,512. 297. R. L. Fogelson, Ya. A. Ugay and A. V. Pokoev, Fir. Met. Metallwed, 1972,34, 1104. 298. W. Gust, C.Ostertag, B. Predel, U. Roll, A. Lodding and H. Odelius, Phil. Mag. A , 1983,47,395. 299. R. Dohl, M. P. Macht and V. Naundorf, Phys. Stat. Solidi (a),1984,s. 603. 300. K. Monma, H. Suto and H. Oikawa, J. Japan Inst. Metals, 1964, 28, 192. 301. M. P. Macht, V. Naundorf and R.Dohl, DIMETA 82, Proc. lntl. Conf., Difuswn in Metals and AlIoys (eds F. J. Kedves and D. L. Beke), Trans Tech Publs, Switzerland, 1983, 516. 302. S. J. Rothman, N. L. Peterson, C. M. Walter and L. J. Nowicki, J. Appd. Phys., 1968, 39, 5041. 303. K. Majima and H. Mitani, Pans.Jap. Inst. Metals, 1978, 19, 663. 304. T. Egichi, Y. Iijima and K. Hirano, Crystal Lattice Defects, 1973, 4. 265. 305. A. Agren, Scripta Met., 1986, 20, 1507. 306. P. Grieveson and E. T. Turkdogan, Pans. Met. Soc. AIME, 1964,230,407. 307. T. Matsuyama, H. Hosokawa and H. Sato, Pans. Jap. Inst. Metals, 1983,24, 589. 308. P. L. Gruzin and V. V. Mural', Phys. M e t . MetalIog., 1964, 17(5), 154. 309. B. I. Bo% and R. L. LuEiC, J. Mater. Sci., 1976,11,887. 310. K. Hennesen, H. Keller and H . Viethaus, Scripta Met., 1984, 18, 1319. 311. K. Kimura, Y. Iijima and K. Hirano, Trans. Jap. Inst. Me&, 1986, 27, 1. 312. P. L. Gruzin, V. V. Mural' and A. P. Fokin, Phys. Met. M e t d o g . , 1972, 34 (6),209. 313. B. Sparke, D. W.James and G. M.Leak, J. Iron Steel Inst., 1965, 203, 152. 314. J. Geise and C. Henig, Z . Metetairk, 1987, 78, 291. 315. J. Geise and C. Herzig, Z . Metallk, 1985, 76, 622. 31. K. Hirano and Y. I i j i m a , D I M E T A - 8 8 . h o c . Intl. Conf. Di&sion in MetalsandAlloys(eds F. J. Kedvesund D. L. Beke), Defict and Difusion Forum, 1989,6649, 1039. 317. J. S. Kirkaldy, P. N. Smith and R. C. Sharma, Metull. Trans. A. 1973, 4, 624. 318. G . Henry, G. Barreau and G. Cizeron, Comptes Rendus Acad. Sei. (Paris), Series C, 1975, 280, 1007. 319. H. Mehrer, D. Hopfel and G. Hettich, D I M E T A 4 2 . Intl. Conf. Dflusion in Metals and Alloys, 1982 (eds F. J. Kedves and B. L. Beke), Trans Tech Publs, Switzerland, 1983, p. 360. 320. J. Kucera, L. Kozak and H. Mehrer, Phys. Scut. Solidi A , 1984,81. 497. 321. J. cermlc, M. Lubbchusen and H. Mehrer, Z.f. Metdlk, 1989,80, 213. 322. S. Fujikawa and K. Hirano, DIMETA88. Proc. intl. Con5 Diffusion in Metals and Alloys (eds F. J. Kedves and D. L. Beke), Defect and Diffuswn Forum, 1989,6649,447. 323. J. Raisinen, A. Antilla and J. Keinonen. Appd. Phys. A, 1985.36, 175. 324. J. N. Mundy and W. D. McFall, Phys. Rev. B, 1963,8,5477. 325. J. N. Mundy and W. D. McFall, Phys. Rev. B, 1973,7,4363. 326. A. Lodding and A. Ott, Z e i t . f . Natutforsch. (a),1971, 81. 327. A. Ott, J . Applied Phys.. 1971, 42, 2999. 328. L. V. Pavlinov, A. Y.Gladyshev and V. N. Bykov, Fir. Met. Metalloued, 1968,26, 823. 329. C. S. Su, Nuclear Inst. and Methods, 1977, 145, 361. 330. L. N. Larikov, V. I. Isaichev, E. A. Maksimenko and B. M. Belkov, Dokl. Akad. Nauk. SSSR, 1977,237,315. Sou. Physics Doklady, 1977, 22, 677. 331. B. Lesage and A. M. Huntx, J. Less Common Metals. 1974, 38, 149. 332. R. Roux, Thesis, Nancy (France), 1972. 333. G. B. Federov, E. A. Smirnov, V. N. Gusev, F. I. Zhomov and V. L. Gorbenko, Metallurgiya i Metalloued. Chystykh. Metallou, 1973, No. 10, 62. 334. E. V. Borisov, P. L. Gruzin and S. V. Zemskii, Zashch. Pokryt. Metal, 1968, No. 2, Protective Coatings on Metals. 1970,2, 76 (Consultants Bureau). 335. N. A. Makhlin and L. I. Ivanov, Izvest. Akad. Nauk. SSSR Metally, 1971, No. 1 , 222. Russim Metallurgy, 1971, No. 1, 152. 336. R. E. Einziger and J. N. Mundy, Phys. Rev. B , 1978,17,449. 337. J. Pelleg, J. lass Common Metals, 1969, 17, 319.

'.

Mechanisms of diffusion

13-39

338. R. P. Aganvala and K. Hirano, Pans. Jap. Inst. Metals, 1972,13,425. 339. J. E. Murphy, G. H. Adams and W. N. Cathay, Met. Fans. A, 1975,6,343. 340. 0.Taguchi, Y. Iijima and K. I. Hirano, J . Jap. Inst. Metals, 1984, 48, 20. 341. D. Treheux, A. Heurtel and P. Guiraldenq, Acta. Met., 1976,24, 503. 342. W. Gust, H. B. Hintz, A. Lodding, H. Odelius and B. Predel, Phys. Status Solidi (a), 1981,64, 187. 343. W. Gust, H. B. Hintz, A. Lodding, H. Odelius and B. Predel, Phil. Mag. A, 1981,43, 1205. 344. S. Mantl, S. J. Rothman, L. J. Nowicki and J. L. Lerner, J. Phys. F, 1983, 13, 1441. 345. A. B. Vladimirov, S. M. Klotsman and I. Sh. Trakhtenberg, Fiz. Met. Metalloved, 1979, 43, 1113. 346.W. Neuhaus. Thesis. Univ. of Miinster. 1987. 347. D. Bergner,’Krist. Techn., 1972, 7, 651: 348. H. R. Curtin. D. L. Decker and H. B. Vanfleet, Phys. Rev., 1965,139. A1552 349. D. L. Decker, J. G. Melville and H. B. Vanfleet, Phys. Rev. B, 1979, 20, 3036. 350. H. B. Vanfleet, J. D. Jorgenson, J. D. Schmutz and D. L. Decker, Phys. Rev. B, 1977, 15, 5545. 351. S. K. Sen and A. Ghori. Phil. M a g . A , 1989, 59, 707. 352. C. E. Hu and H. B. Huntington, Phys. Rev. B, 1982,26,2782. 353. H. B. Vanfleet, Phys. Rev. B, 1980,21, 4337. 354 C. W. Owens and D. Turnbull, J . Appd. Phys., 1972,43,3933. 355. M. P. Dariel, 0. D. McMasters and K. A. Gschneidner, Phys. Stat. Solidi (a), 1981, 63, 329. 356. J. A. Weyland, D. L. Decker and H. B. Vantleet, Phys. Rev. B, 1971,4,4225. 357. J. Fillon and D. Calais, J. Phys. Chem. Solids. 1977,38,81. 358. E. V. Borisov, P. L.Gruzin and S . V. Zemskii, Zasch. Pokryr. Metal.. 1968, No.2,104. Protective Coatings on Metals, 1970,2, 76 (Consultants Bureau). 359. M. Shimotomai, R. R. Hasiguti and S . Umeyama, Phys. Rev. B, 1978, 18, 2097. 360. D. Ablitzer and M. Gantois, ‘La Diffusion dans les Milieux Condenses. T h b n e et Applications’, CEN Saclay, 1976, Vol. 1 , p. 299. 361. D. B. Moharil, I. Jin and G. R. Purdy, Met. Wans., 1974.5, 59. 362. S . Fukikawa and K. Hirano, DIMETA 88. Proc. Intl. Con5 Diffusion in Metals and AIIoys (eds F. J. Kedves and D. L. Beke) Defect and Dvusion Forum, 1989, 66-69. 447. 363. J. ceramic and H. Mehrer, To be published. 364. J. R. MacEwan, J. U. MacEwan and L. Yaffe. Canud. J . Chem., 1959,37, 1629. 365. D. C. Yeh and H. B. Huntington, Phys. Rev. Letters, 1984, 53, 1469. 366. A. V. Pokoev, V. M. Mironov and L. K. Kudryavtseva, Izu. Vyssh. Uchebn. Zaued. Tsvetn. Metall., Soviet Non-Ferrous Met. Res., 1976,4 (2), 81. 367. J. Raisanen, A. Anttila and J. Keinonen, 1. Appd. Phys., 1985,57. 613. 368. J. Rais5nen and J. Keinonen, Appd. Phys. Letters, 1986, 49. 773. 369. H. Il’akajima, J. Nakazawa, Y. Minonishi and M. Koiwa, Phil. Mug.,1986,53,427. 370. E. Santos and F. Dyment, Phyl. Mag., 1975.31, 809. 371. Y . Nakamura, H. Nakijima, S. Ishioka and M . Koiwa, Acta Met., 1988.46, 2787. 372. H. Nakajima, M. Koiwa and S. Ono, Scripta Mer., 1983,18, 1431. 373. L. G. Korneluk, L. M.Mirsky and B. S. Bokshtein, Titanium Science and Technology’, Vol. 11,1973, p. 905. 374. H. Nakajima, M. Koiwa, Y. Minoshi and S . Ono, Trans. Jap. Inst. Metals. 1983, 24,655. 375. H. Nakajima, S. Ishioka and M. Koiwa, Phil. Mag. A, 1985,53, 743. 376. G. M. Hood and R. J. Schultz, Acta Mer., 1974, 22, 459. 377. 6.B. Federov and E. A. Smirnov, ’Diffudya v. Reactornykh Materailakh’ (Atomizdat Publs, Moscow. 1978). Trans: ‘Diffusion in Reactor Materials’ (Trans. Tech. Publs, Switzerland, 1984). 378. I. I. Kovenski. ‘Diffusion in B.C.C. Metals’, (ASM 1965). p. 283. 379. H. Nakajima and M. Koiwa, Titanium Science and Technology. Proc. 5th International Conference on Ti, 1985, p. 1759. 380. W. W. Albrecht, G. Frohberg and H. Wever, Z. Metallk., 1974,65. 279. 381. M. Stelly and J. M. Servant. J . Nuclear Mat., 1972, 43. 269. 382. W. Chomka and J. Andruszkieicz, Nuklecnik, 1960,5, 611. 383. J. Pelleg, Reviews High Temp. Mat., 1978, IV, 5. 384 D, Ablitzer. J. P. Haellsler. K. V. Sathyarai - - and A. Vimes, Phil. Mag. A , 1981,44,589. 385. J. Pelleg, Phil. Mag. A , 1 9 8 6 , s . L2i. 386. V. I. Iovkov. I. S. Panov and A. V. Ryabenko, Phys. Met. MetalIog., 1972,34(6), 204. 387. S. M. Klotsman. V. M. Koloskov. S. V. Osetrov, I. P. Polikarpova, G. N. Tatarinova and A. N. Timofeev, Defect and Diffusion Forum. 1989, 66-69, 439. 388. G. Lorang and J. P. Langeron, High Temp. High Press.. 1978, 33. 394. 389. K. Yoshioka and M. Kimura, Acta Met., 1975,23, 1009. 390. F. A. Schmidt, M. S. Beck, D. K. Rehbein, R. J. Conzemius and 0.N. Carlson, J . Electrochem. Soc., 1984,131. 2169. 391. S. J. Rothman and N. L. Peterson, ‘Diffusion in B.C.C. Metals’ (ASM 1965), p. 183. 392. W. J. Muster, D. N. Yoon and W. J. Hippmann, J. Less Common Mer., 1979, 65, 211. 393. F.A. Schmidt and 0. N. Carlson, Met. Trans. A, 1976. 7, 127. 394. 6. V. Kidson, Phil. Mag. A , 1981,44401. 395. G . M. Hood and R. 5. Schultz, Materials Science Forum, 1987, 15-18. (Pt. l), 475. 396. L. Manke and Ch. Herrig, Acta Mer., 1982.30, 2085. 397. G. B. Federov, E. A. Smirnov and S . M. Novikov. Met. Metallooed. Christ. Metal., 1969, No. 8,41. 398. G. P. Tiwari, M. C. Saxena and R. V. Patil, Tians. Ind. Inst. Metals, 1973,26,55. 399. L. I. Nicolai and R. Tendler, J. Nuclear Mater., 1979,87, 401.

13-40

Diffusion in metals

400. 401. 402. 403. 404. 405.

Th. Hehenkamp, Acta Met.. 1966, 14, 887. Ye. V. Deshkevich, R. M.Dubovtsev and V. S. Zotov, Fiz. Met. Metalloued. 1985,60, 1206. G. Ya. Meshcheryakov, R. A. Andriyevskiy and V. N. Zagryazkin,Fiz. Metl. Metallov., 1968, 25, 189. 0. N. Carlson, F. A. Schmidt and J. C. Sever, Mer. Trans., 1973,4, 2407. R. M. Dubovtsev. V. S. Zotov and T. I. Miroshnichenko, Fb. Met. Metalloued, 1982.54, 1128. V. S. Zotov and A. P. Tsedilkin, Scuiet Physics Jl, 1976,14, 1652. 406. S. C. Axtell, I. C. I. Okafor, R. J. Conzemius and 0. N. Carlson, J . Less C o m m n Metals, 1986,115,269. 407. D. T. Peterson and T. Carnahan. Trans. A I M E , 1969,245,213. 408. L. V. Pavlinov, Phys. M e t . Metallog., 1970, 30(2), 149. 409. 0. N. Carlson, F. A. Schmidt and D. T. Peterson, J . Less Common Metals, 1966, 10, 1. 410. M. Werner, H. Mehrer and H. Siethoff, J . Phys. C: Sol. State Phys., 1983. 16, 6185. 411. V. D. Rogazin, L. M. Gert and A. A. Babad-Zakhryapin, Izvest. Akad. Nauk. SSSR Metally, 1968, 3, 228. Russian Metallurgy, 1968 (3), 159. 412. V. P. Gladkov, A. V. Svetlov, D. M. Skorov and A. N. Shabalin, Fb. Met. Metalloued, 1979,48,871. 413. I. C. I. Okafor and 0. N. Carlson, J . Less Common Metals. 1982.84,499. 414. H . Nakajima, G. M.Hood and R. J. Sehultz, Phil. Mag. B, 1988,58,319. 415. D. D. Pruthi and R. P. Agarwala, Phil. Mug. A , 1984,49,263. 416. K. V. Sathyraj, D. Ablitm and C. Demangeat, Phil. Mag. A, 1979, 40,541. 417. J. N. Mundy, C. W.Tse and W . D. McFall, Pkys. Rev. B, 1976,13,2349. 418. I. Richter and M. Feller-Kniepmeier, Phys. Stat. Solidi (a), 1981,68, 289. 419. J. Fillon and D. Calais, J . Pkys. Ckem. Solids. 1977, 38, 81. 420. D. Ansel, J. Barre, C. Mezihre and J. Debuigne, J . Less C o m n Metals, 1979,65, 1. 421. D. D. Pruthi and R. P. Agarwala, Phil.Mug. A, 1982,46, 841. 422. V. P. Gladkov, V. S.Zotov, I. I. Papirov, D. M. Skorov and G.F. Tikhinski, ‘Poluchenie i Issled. Svoitstv. Chistykh Metallov. (Kharkov)’, F.T.I. Akad. Nauk. Ukr. SSR, 1970, 2,56. 432. V. S. Zotov, T. M. Miroshnichenko and A. M. Protasova, ‘Diflwion Processes in Metals’ (Tulskiy Politkh. Inst.), 1974, 2, 73.

Table 13.3 DIFFUSION IN IiOMOGENEOUS ALLOYS Tracer difusion-Self-dz#usion of alloys Element I (purify) At.%

Element 2 (purify At.%

A:

Q:

cmzs-l

kTmol-i

A: cm2s-I

Q:

Temp. range

kJmol-’

K

ReJ

-

973-1 123

1

673-868

69

A1 (-)

2.05 9.47 14.1 (99.996)

-

As (5N) 0-4.15 M.79 c-3.49 Cb3.19 Au (99.99) 0 8 17 35 50 66 83 94 100

0.25 0.83 0.73 0.39

IVa(i) 177.9 179.6 172.5 IVC 121.0

p.c. I

I

p.c. (indep. of conc.)

IVc (modified), P.c., Ag”O b,=57 =40 = 33 = 19

0.49 0.52 0.32 0.23 0.19

0.1 1 0.09 0.072 0.072

}

b,=3371 =2901 =2257 =I554

-

IVa(i) 186.2 187.5 184.4 182.3 181.7 174.7 171.2 168.6 168.3

S.C.

0.85 0.82 0.48 0.35 0.21 0.17 0.12 0.09 0.09

-

202.1 202.2 198.0 195.4 189.6 186.4 180.2 176.2 174.6

’}

26

998 1073

903-1283

2

Mechanisms of diffusion Table 13.3

1341

DIFFUSION IN HOMOGENEOUS AL.LOY%Onlh&?d

E[emenf I

Eiemen? 2

(purity) At.%

(purity At.%

A?

QT

c n ~ ~ s ' ~ Idmol-'

4':

cmzs-l

Wmol-'

Cd (99.999) 0 6.50 13.60 27.5 28.0

0.44 0.31 0.23

IVa(i) 185.3 178.4 171.5

and p.c. 0.44 0.33 0.22 0.25

174.9 169.5 161.7 150.5

-

0.16

-

156.0 IVa(i) -153 151'" 151

--

31 34 37

-

(-)

IVa(i), s.c., Ag"O b,=9.19 = 13.69

0-3

-

Ql

Temp. range K

Rex

773-1173

3

S.C.

-

p.c.

I

-

-

-

147.4 74 146.1

-

1133 1197

200

'I

973-1 163

1

I

cu

(-4

0.66 1.84 0.51

IVa(i) 187.6 195.1 182.1

1.50 3.00 4.30 5.43 In

0.55 1.59 1.89 2.18

IVb 184.2 189.7 186.3 185.1

(4

IVa(i), s.c., Ag1Iom b, = 11.6 IVa(i) 0.44 185.3 0.36 178.7

1.75 4.16 6.56

p.c.

-

I

-

Ge (-)

0-0.94 (99.99) 0 4.40 4.70 12.40 12.60 16.60 16.70 Mg (99.95) 45.8 49.8 52.0 (99.9+) 41.10 43.60 48.48 48.72 52.82 57.15 60.88

-

0.12

I

156.6

IVa(i) and D,, greater than for infinite dilution by -15%At.% Ge

S.C.

-

0.41

170.8

0.45 0.57

168.7 160.7

-

973-1 123

1 and 7

1054

151

773-1173

3

773-973

12

773-973

13

-

-

-

0.57

151.9

-

IVb 172.9 170.0 159.1 IVa(i) 139.0 0.095 147.8 0.15 165.4 0.37 166.2 0.39 0.33 153.7 0.051 120.2 D.&=4.37 x lo-" at 773.5K

1

and p.c.

0.18

1.53 0.28 0.134

p.c.

p.c. -

I

P.C.

-

I

-

153.3

'I -

-1 -

I

-

773-813

Pb (-)

0.21 0.25 0.52 0.71 1.30 1.32 (99.999 9)

-

(a)

0.22

IVa(i) 177.9

-

-

0.89 0.70

187.1 182.1

D&./D$urePb

-

p.c. I

0.22 0.38

158.3 162.0

-

913-1 073

9

and 1

I

-

0.46

IVa(i)

S.C.

='.'I5> =I25

(b=136.8)

Activation energies read from graph in Reference 74.

- 1

161.2 1257.3

63

13-42

Diffusion in metals

Table 13.3 EIement I (purity) At.%

DIFPUSION IN I~OMOOEMEOUSALLOYs--cofltiflued

EIemenl2 (purity At.%

Ag Pd ('Spec. Pure') 0-21.8 0-20.4 Sb (99.99) 0.53 0.89 1.42 (5N) 0-6.5

Qt

Q:

Ar cm2s-1

klmol-'

IVa(i) 0 2 7 ~ - ~ . ~ ' 183.0

-

-@I

gzs-I

(-1

-

12se-7.5c

239.5

IVa(i) S.C. 0.38 182.1 (c) 0.30 179.4 0.275 175.8 IVa(i), P.c., Ag"Orn See Figure 13.7

(-)

25

6-9

-0 1.7 0.108 0.8 3.0 4.7 6.0

0

M.77 ON) 0 0.948 0.963 1.41 1.44 2.35 2.54 2.62 3.0 3.06 3.47 4.32 4.33 4.48 4.49 5.71 6.60 7.04 7.71 8.67

-

988-1215 1123-1173

4 5

3

823-1173

6

890-1048

204

- 1

:I

p.c. 174.6 171.2 169.6 165.0 161.6 166.2 161.6 154.9 p.c. IVb Ag"Om Sn"' 1.03 x 93.8 4.01; 95.5 p.c. and S.C. IVa Sn113,Ag"O 191.3 0.17 160.8 1.o 0.125 156.8 0.13 172.9 0.12 168.3 0.085 160.8 0.07 157.0 0.07 154.9 IVa(i), s.c., Ag"Om b,=20.2 IVb, P.c., 10"'D' 10412 946 K 989 K 1108K 0.237 0.666 2.47 8.51 2.77

0.13 0.13 0.17 0.28 0.1 0.23 0.2 0.16

Ref.

p.c. -(b)

Sn 0.18 0.48 0.91 0.97 2.8 4.56 5.1 7.45

kJmo1-I

Temp. range K

I

=I

J

973-1 123

-

}

25 24

1

25

473-673

128

893-1073

129

-

151

1052

I

-

-

-

0.373

0.990

I

-

-

0.540

1.46

-

-

0.880

2.48

-

-

3.06

-

4.33

-

16.1 1

-

-

-

-

6.57

-

-

5.01

-

15.4

3.36

7.32

1.77

10.4

-

-

-

-

-

-

(b) c=conc. of Pd. (c) In 0.7 At. % Sb alloys, DSb*same as D in pure Ag. In At. % Sb alloys, Dsb* -20% greater than D in pure Ag.

19.6

30.6

-

41.1

-

1145K 16.6 1

17.6

-

1

25.6

-

31.0

-

42.4

-

1

-

1- 170

Mechanisms o f d i h i o n Table 13.3 DIFFUSION IN HOMOGEK~OUS& m m o n t i n u e d

Element I (purity) At. Yo

Af

Q:

A:

Q:

range

At.%

cm's-l

klmol-'

cm's-l

kJmol-'

K

R4.

91S-1073

7

TI

100

0 1.1 2.6 5.5

Ag (99.999) 0.00

(-4

-lie -l!c

le

0.68

-ile

le 0.89

-lie IC

1.40

-llc

(99.999) -

(99.999) 0

__

1.10

-

2.08

-

3.10

-

4.05

(99.99)

(99.999)

IC

85

15

70 (Merck.) 52.4

30 (99.999) 47.6

K (5N)

Au

1.6 3.0

(5N)

-

-

5!3

-

AI (99.9)

co (Carbonyl] 10

42 49 50.7

49/57

AI (99.999) -.

0

IVaW and IVb D.C. 0.724 0.42 0.35 0.10

(99.999) --IC

--IC

0.57

Temp.

190.5 182.1 175.4 157.4

-

IVa(i)

S.C.

109.3 115.6

0.13 0.18

158.7 169.1 165.0

6.15 0.72 0.57

-

Zn le

0.35

__

Element 2 (purity

Ay,

(-1

13-43

0.31 0.45

-

0.49

-

0.35

-

115.8

-

-

0.14 0.22

1092

-

-

92.4

-

0.17 0.26

96.8

-

0.42 0.69

-

I

1:

110.1 117.3

-

-

-

Iva(i) D, = 1.43 x IO-'' = 1 7 . 2 ~lo-'' =1.63 x lo-'' = 19.9 X IO-'' =1.80X IO-" 521.8 X IO-" =2.0x 10-10 =24.1 X lo-'' =2.28 x 10-"' ~ 2 6 . 2X lo-'' IVa(i) 150.7 0.29 150.7 IIb 4.55 x 73.7

-

71 and 23 of

91.7 96.3

S.C.

-

-

Table2

59M88

70

-

1 020 1153 1020 1153 1 020 1153 1 020 1155 1 020 1153

150.7 147.4

773-973

10 8

-

-

673-883

11

I- 1

55CL1150

112

282.6 355.9 427.1 272.1

1313-1493 1273-1 473

14

I

p.c. 0.11

0.46 p.c.

Vb, P.c., AIz7 7x10-3 1.3 x lo-' ~ x I O - ~

135 123.5 106

-

-

TVC

p.c. 2.65

-

-

-

lo2 333 x lo= 1.84 x

0.013 x 10'

1273-1 473 16

Individual Da* values plotted at 1250

cu IVa(i)

(-1

-

S.C.

0

-

IVb

p.c. 0.43

1 .o

0 2.80 5.50

-

8.83 11.7 14.5

I

D=4.02~10-'' D=7.92~10-~

0.46

1

72

203.1 201.o

0.30

1073-1313

0.46

0.61 4.2

762 881

197.6 213.9

73

l3-44 Diffusion in metals Table 13.3 Element I (purify) At.%

(99.994)

-

DEEUSON IN HOMOGENEOUS ALLoYs-COnti~Ued

Element 2 wiry At.%

0

0 0.15

AI

cu

0

0

(99.99)

(99.99) 0 0.69 1.23 1.57 1.86

-

-

AI

-

cu (99.99) 0 0.69 1.23 1.57 1.86

AI

Fe

(-4

(-)

(99.99)

-

-

-

3.47 7.95 13.5 20.6 23.6 35.5 42.0 47.3 52.0

I

I

Fe (4N)

A1 (4N) 6 10 10 18 18 (a phase)

-

5.7

-

0

0

0

'AIFe,' 'AIFe' A1,Fe A1,Fe

I

Li

0

0

0

0

51.7 50.6 50.0 48.1 46.9

g's-'

kJmol-'

0.10 6x

vb 127.7 100.9

50

48.3 49.4 50.0 51.9 53.1

At

p.c.

Temp. ranBe

Idmol-'

K

Ref-

-

- 1

-603-733

127

Vb, P.c., AI'? -

-

750-1 030

.190

116.9 115.2 120.0 120.9 125.2

714-894 714-894 714-872 754-855 779-844

Diff. of Zn 0.18 116.9 %:=9.6 (Av. 0.20 116.9 115.5 BZ" a-11.7 - values) 0.17 0.20 116.3 0.38 120.2

714-894 714-854 714-872 754-855 779-844

I

IVa(i), P.c., Zn65

Diff. of Zn

0.28 0.33 0.67

2.04 2.04 2.04 2.04

Qt

-

IVa

Diff. of Co 0.1 221.9 1.9 234.5 6.8 144.9 22.0 251.2 27.0 251.2 210.0 280.5 580.0 297.3 6 300.0 330.8 148.p 280.5

-

-

-

0

AI

50 (P)

e:

I

1.74~10' 8.5 x lo-' 3.99 x lo3 8.9 x

1 1

41

41

p.c.

3.2 4.5 0.4 32.0 27.0

247.0 251.2 217.7 263.8 261.7

-

-

60.0

276.3

-

17

-

IVb, P.c., FeSg 0.42 197.7 1088-1 478 (p) 0.06 195.9 765-941 (fl 0.02 183.5 0.01 197.7 816-953 (f) 0.01 171.5 973-1 450 (p) p =paramagnetic, f =ferromagnetic Ivb p.c. 3.7 245.8 1123-1458 75 Na(i) 211.4 Individual Re 823-903 105.1 (:;:usion coeficients) 76 232.4 are reported in 117.2 reference 71 823-873

-

I

& ;;

}

Vb, P.c., Li'

-

-

2.63 x lo-'

10.2

1004GO

-

2.54~ 1.56~lo-' 8.34~lo-' 2.34 x 2.58 x lo-'

12.4 11.7 10.9 9.2 8.4

300-368 Mo-368 300-473 300-368 300-419

Vb, P.c., Li7

-

I

-

111

Mechanisms of diffusion Table 13.3

13-45

DIFFUSION IN HOMOGENEOUS ALLoys--eontimred

Etemenr I @uriry)

EIement 2 lpurity

A?

At.%

At.%

61112S-'

Qr klmol-'

Temp.

At

QZ

range

cm2s-*

kJmol-'

K

5 0 5

9.26 x

11.1

3Oc-353

Li 50 50

1.66 x 3.63 x

8.88 6.95

300-368 300-419

L1

In

0

0 2.2 5.5

Vb 127.7 128.1 116.0

0.10 0.93 0.21

Ni (-)

!3 7x10-z

IVC

Diff. of Cod'

47x

47.3 48.5 49.4 50.7 53.1 55.1

4.4 x lo-' 7.2 x

237.0 250.8 219.8 337.5 283.0 197.2

1

-

127

1323-1 623

18

965-1 625

30

1273-1 623

78 and 130

1 173-1 573

I06

1 173-1 573

106

673-837

41

pc.

-

132

IVb

146 f 1.1 x lo-' 105 4-2.0~ p.c.

(NiN

0

Diff. of In"4* 1.29 x 237.0 3.98 x 242.8 1.83 x 170.0 -

48.3 48.6 49.0 49.2 50.0 53.2 54.5 58.0 58.5 58.7 73.20 74.71 76.20

1.2 x 10-4 1.04~10-3 53 x 10-4 0.23 4.461 0.63 0.15 0.035 0.096 0.725 3.11 1.oo 4.41

141.1 342 121.8

177.9 209.8

200.5 275.9 307.3 274.2 250.4 216.5 253.7 303.1 306.3

Ti

0 0 5.13 5.01 5.13

Si (99.99) 0 0.05 0.10 0.15 0.20

-603-733

IVb, P.c., Ni63

0

-

Ni

150

Ag

2 3

MI3

-

ReJ

0.055 0.039 0.085

Iva(i), P.c., Zn6s @:=23 (Av. value.) (See AI

Cu for definition)

0.26 0.23 0.30 0.32 0.29

262.79 259.7 266.9

Diff. of Zn 119.1 118.2 119.5 120.2 119.8

13-46 Table 13.3 Element I

Di@$on in metals DQTLBION IN HOMOGENEOUS ALLOYS-COnthUed

Element 2

Temo.

Si

Zn

(99.99)

(99.99) Na(i), P.c., Zn65 1.48 1.48 1.48 B@=9 (Av. value) 1.48

0

0.05 0.10 0.15 0.20 0 0.05 0.10 0.15 0.20

1.18

2.13 2.13 2.13 2.13 2.13

B$:=7.5

0

7.06 15.17 24.24 31.27 41.51 52.52 53.28 55.04 56.85 57.28 57.50

0

20 28.9 40 58.5

-

-

0 8

0.10 0.087 0.035 0.025

Vb 127.7 122.7 117.2 113.5

1.14 2.77 2.80 2.83 2.86 4.43 6.63

0.31 0.24 0.27 0.21 0.17 0.28 0.50

0 11.5 18.8

I

673-837

41

613-893

149

116.7 118.1 121.2 118.9

B@=30(A~.value)

Zn (99.99) 0 1.16 1.73 2.15 2.80 3.29 3.76

50

Diff. of Zn 116.9 120.6 121.1 0.29 119.1 0.33 119.6

pc. 0.27 0.25 0.18 0.22 0.22 0.24 0.23

zn65

0.170 0.324 0.209 0288 0.229 0.162 0.575 0.692 1.514 0.575 1.35

112.46 113.17 108.27 105.67 103.54 100.53 106.64 108.10 111.87 106.81 111.41

0.25 0.22 0.17 0.23 0.036

109 105 101 100 91

120.4 119.0 116.7 117.6 117.1 117.5 116.9

621-783 588-611 632-714 558-611 528-611

P.C.

-

-613-733

-

Zn (99.99) -0

0.71 1.49 2.11 0 0.71 1.48 2.11 0 0

119.5 119.0 119.0 116.8 115.1 118.6 121.1

688-848

149

127

Mechanisms of dimion Table 13.3

DIFFUSION IN HOMOGENEOUSAmws-continued

Ehent 1

Element 2

@wiry)

(pwity

At.%

Au (99.99) 50 (99.999 + )

At.%

cd (99.95) 50 (99.999 ) 47.5 49.0 50.5

+

(a) Between 863 K and

Au

0

0.17 0.23 0.61 0.12

IVa(i) 116.8 IVa(i) 117.6 125.6 109.7

S.C.

0.23

117.2

573-863'"'

129.8 130.6 113.5

623-873 713-823 713-823

1.36 1.50 0.22

the m.p. at 8WK there is marked upward curvature in the Arrhenius Plot.

0

75

25

75

1.25 2.5

-

6.5 x

IVC 159.9

p.c.

-

I Diffusion of Cos'

1 4 . 2 lo-' ~

(5N)

7.48 12.44 14.25 17.43 Au (99.96) 100

Ni (99.9) 0

0.26

I

10

-

20 35 36

0.05

90 0

0.04

0.015 0.04 0.06

0.08

1.a

-

-

50

0

lO"DX, 1.7

2.08 2.40 3.08 3.36 3.88

I

65 80

Au

-

192.6

IVa(i) 189.7 I

168.3

-

-

0.091 0.51 1.1

181.7 204.3 253.3

p.c. 0.30 0.80 0.82 1.10 1.10 0.09 0.005 0.05

-

-

2.0

272.1

0.04 0.40

IVafi)

S.C.

-

0 -

(b, = 5726)

Zn

0

so 51

923-1 173

89

1133

174

32(Au) 186.3 165.8 206.0 213.9

temp. ranges only)

0.19 0.33 0.016

IVali) 133.6 138.6 113.0

S.C.

0.84 1.93 0.047

23(Ni)

472.4

488.2

-

49

81

4.18 4.62 5.88

-

Pb (99.999 9 )

823-1173 (Disord.)

IVa(i), P.c., Cu6' A U ' ~ ~ ldloD& 1.83 1

(a) Samples pn-annealed More diffusion. Au

20

S.C.

cu

25

5.0

1347

63

13-48

Dz@ion

in metals

T9bk 133 DIFFUSION IN HOMOGENEOUS M

Element I @wity) At.%

Etetnent 2 (purity At.%

Be

Ni

0 -

0

-

1.68 7.9

C

Cr

Fe

C

Cr

i.5) 1.0 Ta

0

-

'

-

ce

0 0 1.0

, ~ O ? I t ~ ? I W d

Temp.

Z's-'

Q€

-

kimol-'

z2s-l

IW

p.c.

-

0.41 0.23

IVb 4 5 ~ 1 0 - ~ 111.0 20x10-3 100.5

IVb 5 ~ 1 0 - ~ 1m.6

QZ

kJmol-'

:;ti::}1173-1373

p.c.

-

p.c. I

K

-

}

-

Ret

80

1673-1873

85

1573-1773

85

1273-1573

28

Fe

(-1

0 1.15

(-1

-.

-

2.46 3.39 4.97 6.21

-

cu

Fe

(-)

(-) (Y)

C% C% (a) These values

.::)

IVa(i)

p.c.

-

0.44

IVb

p.c. 18.10-0~92c 314-25c 71.10-0.65' 330.8-21c

-

0.052

280.5 247.0

0.015 0.021 0.029 0.050

225.2 225.2

Ni (-)

20 25

-

-

~

% 29 ~

also repnsemt the best fit to the original (reference 26) and later measurements when plotted altogether. See

reference 27.

C 0.104

Cd

0

Fe Si (99.97) (a) 5.5 cu (99.998)

0-1.8

-

Cd

Mg (-1

(-1

75 75 25 25

cd

0

25

25

75 75

V(a) ps. 0: 'virtually' the same as im Si-free Fe

-

I

b, =35

IVb S.C. 1 1 . 2 ~ 1 0 - ~ 51.9 (Ord.) 0.074 69.9 (Disord.) 4.10-' 68.2 (Ord.) 1.2 x lo-' 53.6 (Disord.) -

Pb (99.999 9 )

IVa(i)

b2=1400

26-70

67

1076

109

ii;} 574

52

506.7

186

-

-

-

S.C.

Effect of Cd on OW (See eq. 13.9a) b,

45.197 30.028 19.138

0 to 5

(5N) 0 0.37 0.86

1.01 I .36 2.64 3.66

(5N)

-

-

-

Diff. of Ni 1O5D=2.O4

b2

438.1 407.7 1070.2

b,

44286

-

IVa(i), P.c., NP3

= 1.88

=1.73 = 1.58

=1.56 =1.17 = 1.02

-

-

~

~

Mechanisms of diffusion Table 133

13-49

DIFFUSION mi HOM~~ENEOUS aLLOm-continued

Elemem I

EIemenr 2

@wiry) At.%

(purity

Temp.

At.%

z Z s - I

Q: kJmol-l

m3s-1

0.67 56.3

IVb 275.5 332.0

-

6.3 0.4

1% 301.9 268.8

4

Qt

range

kJrnol-'

K

R ~ .

-1

1373-1623

33

1373-1623

33

1325

158

-

Cr

co

(-4

(-)

4 7

Cr

(-)

(-)

(-1

9 18

26 26

Cu Si (99.99) ( ) 0.54

(99.99) 0-2 68

I

Ni

co

co

p.c.

B,= -9

IVa(i), P.c., c~~~

co

0

{ ;:i3

50

-

0 -

0.54

0

I

I

-

0

0

3 6.8 28.6 49.6 67.2 89.6 100

(99.8) 0 8

10 15 20

co

IVa(i) 290.6 25 1.2 556.8 IVb 272.1 IVa(iii) Diffusion of Ni DN,=13.10-'2 = 11.5

p.c. 1.26 0.25

-

p.c.

-

I

286.8 230.3 556.8

1285-1 437(./) 1068-1218(a) 928-995(CsC1)

-

1373-1 573

33

1409

82

34

p.c.

1)

I .83 0.77) 9.17 0.469 5.72 x 0.109 1.25x 3.36 x 6.59 x 0.154 6.04~ 3.15 x IO-' 6.44~ 1.61 x 0.50 0.17

IVb 234.0 265.0 266.3 187.1 146.5 326.2 198.0 266.3 247.0 349.6 190.9 265.0 251.2 234.0 273.8 260.4

IVb

PC.

0.029 20.54 15.65 1.98 0.31

247.4 321.5 369.0 289.7 261.7

1233-1493

131

-

-

1081-T, T,-1573 1081-T, T,-1573

176

0.008

IVb 214.4

1373-1473

33

10.5

IVa(i), p.c. Cos' 313'"' -

1277-1 570

152

1223-1 633 903-1 023(F) 903-1 073(F) 1153-1 193 1283-1 583

1333-1 583 ' 1073-1 283(F) 1333-1 153 1045-1 321(F) 1465-1 570

IVb, s.c., Fe59

0

I

I

I

Fe

co

Ti

0 i5'

)

fie -- v 0 0

co

0

15

60

25

(a) Reports Ds below

T, but these scattered and alfeaed by g.b. diffusion.

Diffusion in metals

13-50

Table 13.3

DIFFUSION IN HOMOGENEOUS ALLO%ontinvc?d

Elerneet I

Element 2 (pwtfy

(puritu) At.%

bt[jZs-l

At.%

co (5N) 48.6 52.4 54.3 57.2

Ga (5N)

-

0

45.2

I

(a)

-

48 50

-

56

-

60

-

co

Mn

0

0

100

+

IVb

-0

-

5.22

-

31

co

Ni (99.98)

(99.5) 100

100

(8)

-

1.8

0

0.5

11 20 30 51

0.61 5.96 1.16 0.0%

0 11 20 30 51 100 (99.8)

0.17 0.21 2.42 0.78 0.12 0.75

range K

319.4 309.7 307.8 275.9

1248 x 1 353 1256-1 386

326

651-1 100

308

704-1 150

1193-1 345

494 301 417 303 430 28 1 395

639-1150 625-1 150 600-1 150

Mn54

p.c.

-

ReJ

I

3.15 x lo-' 1.1 x lo-'

232.4 217.7

1133-T, T,-1519

-

1.38 0.501 1.36

268.4 256.7 263.3

1141-T, T-1473 1 176-1 421

194

-

IVb

Pa.

273.8 280.9 307.7 287.2 257.5

-

}

132

133

-

1.66 7.4 2.52 0.99 0.70 0.18 0.52 0.33 0.66 0.49 1.11

._

1125-1645

0.34 0.46 1.66 2.01 0.36

269.2 274.7 291.8 286.8 266.3

Ferromag.'" 1045-1 321 1 137-1 321 1118-1 321 1045-1 172 974-1 072

260.4 266.3 297.3 280.5 252.0 270.9 IVb

0.10 0.17 0.41 0.67 0.21 1.70

252.0 262.5 275.1 271.3 253.7 285.1

1465-1 570 1417-1 570 1363-1 519 1323-1 523 363-1 463 973-1 463

287.6 305.2 290.1 275.9 270.5 250.4 262.1 255.8 263.8 261.3 271.7 IVb

3.35 5.40 6.42 1.89

2973 302.3

1320-1 584(0) 1493-1 693(?Ui) 1483-1 643

285.5 281.4 61.1 267.1 262.1 276.3 284.7 275.9

1433-1 683

156

1

P.C.

lb)

93.8 89.0 80.6 72.6 49.4 43.3 21.1 10.8 4.3 0.03

0

0

50

50

I

Diffusion of FeS9 125 320.3 Diffusion of CI4

5.25

Temp.

Qz kJmol-'

IVa(i), p.c,, Con

0 0

2

99.5

+

m z r

0

(99.4)

IVa(i), P.c., Co60,Ga7' 311.6 2.7 x 103 310.7 1.3 x 10' 305.9 1.5 x 103 275.9 1.4 x 10' IVa(i), P.c., Co60, GaS7 247 766 x lo3 1.91 f4.68 x 103 326 +O 554 2 . 1 0 ~10-3 209 + 1.5 x 103 308 +2.65 x 109 245 220 0.379 878 301 f8.11 x lo6 235 475 1.02 +2.30 x 107 + 1.60 x 103 303 0.303 80.8 216 343 281 1.99 x IO6

+

10.24

co

2's-l

2.0 x 103 2.7 x 103 2.0 x 103 2.0 x 103

-

0

e: kJmol-'

1.60

0.25 0.69 0.45 1.47 2.86 1.39

>

)

1 373-1 623

1433-1 683 1483-1 643 1423-1 663

P.C.

I -

IVb

-

1

1273-1523

84

p.c. 873-1173

36

(a) According to reference64 measurements in pure Co, in Co+ 11% Ni and &+XI% Ni alloys do not convincingly demonstratea difference in A' and Q* values for the paramagnetic and ferromagnetic regions. ( b ) All alloys contain 0.14.2 Mg.

Mechanisms of diffusion Tabk 13.3 Element I (purity)

lS51

DIFFUSION IN UOMOGENEOUS fiLoys-contiirued

At. %

Element 2 (purity At.%

co

Mn

Z2s-'

e: kJmol-'

kJmol-'

Temp. range K

-

1293-1 393 1293-1 433 1333-1 433

145.3 140.3 160.4 162.9

1233-1 777 1166-1 617 1076-1 573 1076-1484

121

-1

1074-1 323

199

1266

118

Qt 2's-l

Ref.

~~~

0

Ni

0 0

19.5 40.6 59.7

20.3 60.0 20.45 38.9 20.6 19.5

CO

Ti (99.97)

(99.97) 1.6 3.3 4.9 7.4

co (9999.9)

-

co

Zr

0

0

[Co3Ti)

0.395 0.747 1.22 1.61 1.995

-

cr

Fe (99.9)

(99.9) 9.13 15.22

2 6 13 16 19 15

Wa(i), P.c., Co60 4.3 x 10-2 203 1.2 x 10-2 188 174 3.7 x 10-3 IVa(i)

0

2.0

0

0.87 1.43 3.09 5.05 6.68 8.18 11.93

(wt.%)

99.997) 18 26wt.% 34 (99.9) 0

0.93 1.53 3.31 5.4 7.2 8.8

I

1

14

-

0.861

-

0.820

3.21 1.21 0.64 0.19 0.18 238.6

-

(99.997) I

-

-

p.c.

0.948 1.3228 1.668 2.143 3 2.223 9

0.900

-

-

D$.IDArezr

DE, in pure ~r

-

0

0

p.c. I

p.c. 1.26~ 1.58 x 1.41 x lo-' 2.50 x lo-'

I

19.75

0

IVb 253.3 240.7 228.2

Ti (99.8) 21.5 22.8 24.0

-

0.86 0.22 0.05

1%

-

IVb 244.5 237.4 231.9 218.1 216.9 -

IVb

-

I

-

-

1

p.c. 9.27 0.42 0.12 1.25 0.27 0.65 0.18 p.c.

-

pc. 4.4 4.3 4.2 4.0 3.7 3.6 3.3 2.9

230.7 219.4 237.4 226.5 215.6 217.3 208.1

'1

963-1 098(Para.a)

-

88

Fe5' 253.3 252.9 252.5 251.6 250.0 249.1 247.9 244.9

Paramag. a phase

134

1123-1 473

164

1 223-1 473

192

-

6.18 x lo-'

177

1.16 1.30

276.7 286.0

-

I

-

-

0.35

__

0.13

-

37

IVb, p.c. SJ5

Diff. of S 0.166

(99.9)

-

1073-1 673

-

-

-

1173-1 313 868-950(Ferro.a)

-

273.8 -

261.6

-

IVb, P.c., Cr5', Fe5' 0.72 278.7 I

0.73

283.1

I

0.41

276.4

0.069

257.1

-

13-52

Difision in metals

Tabk 13.3

DIFFUSION w HOMOGENEOUSALLo-onrimred

Element I tpurify)

Element 2 (purity

4 ':

At.%

At.%

(298) (298) 26 51 69 ('Electrolytic') 27 51 84

0.156 40.0 24.6

202.6 293.1 316.1 IVa(i)

-

I

0.376

0

202 5.73 9.47 14.1 20.1

-

Cr

Fe

0

0 0

'a

cmls-'

kJmol-'

4 ':

I

0

19.9

Q:

I

Diffusion of Ni63 274.6 0.282 278.1 0.12 265.4 0.016 237.4 0.007 224.4

24.7

0 0

0

( )

0

0 0

0.19

12

(wt.%)45 55 65 75

EN)

0 (19) I5 ) 15 22 t5

0 17

0.13

i2)

19

(99.99) 10.1 10.1 9.9 10.1 20.0 19.9 wt.% 19.6 20.0 19.1 30.4 30.4 30.4

6.3 x

II

(99.44) (99.95) 78.1 2.26 64.6 1.35 55.1 5.22 35.0 8.49 63.5 2.18 55.1 4.72 43.0 4.69 34.9 1.95 19.1 0.425 65.3 1.945 54.8 0.536 34.8 5.82 I

(5N) ( ) low.% -

0 0

-

W 10.4

45 45 2(r"

I

1223-1 593

38

1313-1 673

39

95 bcc bffi

IVa(i) p.c. 346.2 1.74 (Ni) IVb p.c. 282.6 IV Cr5', Fe5g,Ni6j 264.2 0.37 AN:= 8.8 p.c. IVa(i) 243.3 p.c. Ivb 2.5 x 10-3 1.o 1.2 4.5 1.o 4.10'

IVb, P.c., Cr5', Fes8 278.2 1.13 273.4 1.10 290.1 4.9 1 299.1 3.75 282.3 2.22 295.8 7.62 293.2 1.19 282.8 4.75 269.8 0.545 219.3 1.23 264.3 0.817 294.5 2.42

I

284.3

1113-1 563

-

1113-1 568

p.c. 279.7

873-1 573

135

-

1023-1 473

136

217.1 278.4 255.4 255.4 272.1 343.3

1 173-1 473

137

102

281.3 276.5 295.2 295.1 286.7 307.8 284.1 298.7 278.4 280.1 273.0 291.0

(Fe) 1298-1 548

-

1 173-1 473

166

1216-1311

171

1286-1 536

}

162

(Cr)

I

o.46 Diff. of S213.6

5.59 8.3 4.0 4.1 7.1

0 $0 0 -

-

fcc

2x104 401.9 2.8 297.3 2.6 297.3 7 . 2 ~ 1 0 - ~ 253.3 Diff. of Ni

-

-

ReJ

Ni

0 17

268.8 IVb

211.0 312.3 342.9

K

1 0.356

4.06 17

kJmol-'

p.c. 0.195 249 146 p.c.

-

Temp. range

QZ

296.5

Ivb, P.C.,

-

s3s

IVa(i), P.c., Cr5'

-

-

IVa(i), P.c., Cr5', Fe5', Fe", Ni5' 309 5.3 308 293 2.1 288 295 1.5 286 5.1 303 303 1 233-1 673 K IVa(i). P.c., FeSg 1.18 x 228.5

1

i:; ii; 4.8

310

1178-1483

1

177

78

Mechanisms of difficsion Tsbk 13.3

-

13-53

DIFFUSION INHOM~OENEOUSALLoYs-continued

Efement I

Element 2

(puriry) At.%

(purity At.%

0

0.74 4.65 18

(

0.52 0.36

-

(99.8)

-

Temp.

Qt

41

At em's-'

kJmol-'

an's-'

-

-

IVb p.c.

Diffusion of C1* 0.1 142.4 0.5 154.9 6.18 186.8

8

AS

kJmol-'

range

K

Rex

1223-1523

122

(a) Plus 0.55 Nb,0.74 Mn,0.69 Si, 0.03 Ti. (a) +1.33% Mn. 0.65% Si,O.46% Ti, 0.44% Cu.(321 St. Steel). (c) i2.3% Mo.

cr

Ni 1%

('Electrolytic') 4.9

-

-

6.35

0.01

9.93 11.69 19.7

-

211.4

-

0.037 0.01

pc. 0.15

253.3

0.039

-

238.6

0.0063 p.c. 1.9

220.2

-

0

1.1

229.0 242.8 IVa(i) 272.6

10

1.4

278.4

3.3

293.4

20

1.9

283.4

1.6

286.8

0

(9")W -

-

wt.%

-

-

0

(99.95)

(99.95) 95.8 87.1 78.5 73.0 68.3 64.4 55.3

-

0

0

Cr

7.40

__

-

297.8

-

Diff. of Fe 2.48 285.9 4.63 296.5 5.33 299.9 1.475 287.0

259

1373-1543 1

(Ni Self D)J

12864 536

162

1 123-1 473

173

1223-1 473

192

1223-1 633 1423-1 688

68

1 198-1 453

44

(99.9)

-

279.5 289.3 293.8 285.4 289.5 290.4 288.9

-

Ti (99.4)

10.0 18.0 Cr (99.99) 1.5 (99.95) 0 2.05 3.49 4.08 7.86

-

0

20 (9").9) 0 4.1 14.3 23.6 29.4 34..4 38.4 47.7 35(wt.%) 80(wt.%)

IVb, P.c., Crsl, FeS9

-

284.7

pc. 0.02 0.09

IVa(ii) 168.3 186.3

I

Zr (99.9) (wt.%) (nuclear)

-

-

IV

p.c. 191.3 IVa(i), P.c., Cr3', Zr95 4.53 x 137.84 6.80 x lod4 5 . 1 6 ~lo-.' 2.05 x lo-' 1.38 x lo-' 1 . 5 9 ~lo-'

0.19

I

I

Cr5'

-

1233-1 373(8) 49

145 1652) 169 169.2 173.4

1218-1 518 1m 1 4 9 7 1196-1518 1218-1 516 1227-1 516

195

13-54

Diffusion in metals

Table 13.3

cu (99.998 5)

D m s i o N IN HOMOGENEOUSAuoY-ntinued

Fe p.c. and S.C.

0

0.2 1.38 1.38 1.44 1.45 1.82 2.40

cu (99.998)

-

(4NW

-

-

-

cu (99.99)

=0.91

In (5N

-

0 0.8 1.7 3.1 5.1 (5N) 0 0.4 0.8 1.2 1.7

-

-

0.6 2.0 0.4 0.6 0.2 b, =42 =43 =48

Ni (99.95)

Ni

0

00 -

10.3 20.5 30.8

0

0

(8)

19.4 24.4 33.4

(7)

1089

-

IVa(i), P.c., CuS4 210 220 200 200 190 b2=3500 =2300 = 790 IVa(i) 258.3 263.8 252.5 231.5 201.8 Resistance method.

179

= 18

-

IVa(i)

= 34

-

-

1005-1 145

1 089 I145

1.9 35.0 17.0 0.063 1.7 p.c. 1.95 0.95 0.23

10.4 20.8

-

10.6 21.0 31.4

D.C. 6.24 0.64 0.35 - Diffusion 0.32 - of ZnS5 0.36 0.49 1.41 0.39

-

10.1 20.5 30.2

-

Sb

lO''D&= 7.0 =9.8 13}

284.1 313.6 279.7 208.1 231.5 236.5 233.1 225.5

1323-1 633 1323-1 633 1 133-1 343 OooOOOO

1053-1 310

182

Zn

9.3 . .-

cu

-

-

9.3 9.1 18.2 18.8 18.6 28.6 28.2 28.2 21.9

IVa(i), ps., In114m

-

cu

or)

p.c. 0.57 1.5 2.3 1.9 0.33

0

0 1.08 2.81

-

1293 1265 1293

=0.90

-

100 89.9 79.5 69.8 90.7 80.4 70.2 60.1 81.8 70.8 60.6 71.4 61.2 50.8 40.7

120

=0.94 =0.91

0 13.0 45.4 78.5 100.0

0

(b, = - 5 f 1.5)

=OM

-

-

-

-

I

-

IVC

08"

4.107x -10-9

188.8 190.9 176.7 164.5 200.1 195 196.4 173.3 214.8 199.7 187.1 226.5 220.2 208.9 198.5

I

1073-1 313 1 022-1 252 1021-1 213 973-1 175 1068-1313 1023-1 278 1623-1 248 973-1 173 1068-1 278 1073-1 313 1021-1 213

90

1128-1 313 800-1 005 1033-1 249

D.C.

ilk 3.10-" 3.1 x 2.7 x 10-9

663

61

Mechanisms of diffusion Table 13.3

1S55

DIFFUSION IN HOMOGENEOUS A L L O Y S - C O ~ ~ ~ W ~

Efement I

Element 2

@uritu) At.%

(purity

Temp.

Q?

At.%

Idmol-’

IVb 43.8 30.4 24.3 IVa(i), P.c., Cu64 0.6 210 0.4 200 0.6 200 0.7 200 b,=79 bz=27000 =loo = 14OOO =130 =12OOO

0

8.57 x 1.99 x 10-3 5 . 8 0 ~10-3

21 25 29 (5N) 0 0.3 0.5 0.8

range

Qt

K

Re$

793-903

91

p.c.

-

I

I

-

1005-1 145 191

I

1005 1089 1145

Sn (99.999) 20.5

IVa(i)

4.7 1 . 4 lo-’ ~ 3 . 6 lo-’ ~

{ ;;:: 15N) 0 0.8 1.7 3.Q 4.9 (6N) 0 0.4 0.8 1.1 1.7

-

129.4 74.5 84.6 Iva(i), P.c., Sn113

p.c. 2.4 x 103 0.33 9.2 x

-

713-848

10’oD&=8.1 =9.6

-

1;:

210 200 180 180 170 bz=9600 =3300 =2600 IVa(i), P.c., Cd4, 83 0.22 8.3 x 10-3 82 3.5 x 10-2 1.8 x lo-’

0.6 0.4 0.07 0.06 0.03 b, =40 =48 =54

(5N)

16.6 20.2

I

1

92

1089

179

’} =26

ma(i), P.c., W4

1

873-998)

-

1005-1 145 1014 1089 1145

118 107

897-1 003

0.73

170.4

850-1178

Zn

(‘spec. p’) 31 (99.99)

1

S.C. 0.34

IVa(i) 175.4

S.C.

IVa(i)

0.011

92.3

0.0035

78.6

Disord.

180

155.3

78.103

185.2

770-1 090 Ord. 653-723

150.8

163.0

152.0

Ord.

537-653 DiSd.

C) 46.7

(-4

1

45

46

771-867

{

0.020

98.1

0.08

129Xfb’

p.c.

IVa(i)

Diffusion of Ag

47.2

191

-

p.c. IVa(i) 0.022

1.o

92.3

Disord.

1

134.0 573

Diffusion of Co Disord.

743-973

48

Arrbenius plots in the ordered region are curved.The values of A and Q reported described straight line approximationsto the data over the temperature ranges indicated. (b) Ditto.Tkvaluesd.4 andQgiven bererefertothedataatthelowerendoftheorderedtcmperaturerangeinvestigated,viz:300K. (e) Values of D* for the ordered region an shown only in Braphicllr form in reference 48. (Q)

13-56

Dijhion in metals

Table 13.3 N-D Element I (purity) At.%

IN HOMOOENEOUS ~~~~ys-contimred

Element 2 (purity At.%

0

Q€

Ref. IVa(i)

-

0.62 1.09 2.17 2.68 2.99 4.06 4.13 (Electrolytic) (99.99) 0 0 0.2 0.2 0.3 0.3 0.4 0.4 0.5 0.5

-

Temp. range

1O'O x DE. 2.71 6.70 2.81 7.42 3.12 3.23 8.33 3.71 9.23

-

p.c. 10'' x D k 9.66 22.7

-

:I;: } :I:: j

93

1167

1Vb

-

-

-

1220

SS.

IC1.62

108.9 79.5 108.9 79.3 108.9 79.5 108.9 79.5 108.9 83.7

I/c 0.013

3.2 llco.021 I C 3.4 Ilc 0.025 I C 3.4 Ilc 0.029 IC 3.5 IIc 0.035 IC

823-903

56

( d ) Additions of0.5 at % AI to this range ofCuZn alloys have a negligibk eKcot on e,."* but decreaseA , by -20% and A by -40%.

Fe

0 Fe (99.97) At.%

0

Ge

0

4.8

4.8

(99.94) 1.04 2.03 2.97 4.90 7.04 10.41 18.15 25.5 33.98

wt.% Fe

Mo

(wt.%)

0

0.54 1.06 1.50 2.50

Fe

Nb

0

0 -

0-1.24

0-0.90 0-0.53

IVb 265.4 262.9 255.8 255.0 262.1 275.5 282.2 277.6 276.7 IVb Diffusion of Nib3 0.495 279.8 0.144 270.5 0.132 267.5 9x10-a 1.05 x lo-' 5.8 x lo-' 6.6 x 10-a 1.1 x lo-' 3.5 x lo-' 6.4 x lo-' 8.5 x lo-' 6.0 x lo-'

0

Mn (4N) 1.5 1.5 0

0

p.c.

-

-

1 173-1 473

Mn

wt.% 0.42 1.26 4.60 9.7

Fe (4N)

IVa 242.8

p.c. 5.5 x 10-2 2.0 x 10-2 9.6 x 10-3 1.7 x 10-f 7.2 x 10-a 2.9 x lo-' 1.9 x lo-' 1.2 x 10-1 7.3 x 10-2 p.c.

248.3 266.7 261.7 251.6 242.0

Fe 1263-1 573 Mn 983-1 573

fccrange

95

1354-1 474

184

953-1 173 Paramag.

141

Si ( )

IVa(i), P.c., Nb94'95

Diff. of Nb

0 0.6 0.6

271.7

15.5 23.6 23.6 47.7

IVb p.c. Fe5g 263.3 257.1 257.1 264.2 -

rVa(i), pc., Nb95

-

-

-

b, =ma =56.8 =55.0

E;) 2 261

201

Mechanisms of diffusion Table 133

DIPFUSION IN HOMOGENEOUS ALLoYsconthZ&?d

EIemPnr 2

Eiement I (purity) At.%

(purity At.%

Fe

Ni

0

\ 19.34 (Electrol.)

0 0

(Electrol.) 5.8 14.88

0

20 25

0

50

80

0

0 to 1.46

13-57

0 -

At Cd0-1

-

Qt

At cm2s-'

IVb

p.c. 1.09 1.09 0.593 0.497 0.409 p.c. 2.11 5.a p.c.

kJmol-I

I

-

-

-

-

18 71

-

__

-

Nc

IVb 314.0 330.8 IVa(i) -

-

-

290.3 290.3 28 1.8 278.0 273.9

I

1 -1 316.5 307.7

I

K

Re5

sol.sol. range

95

1433-1663

50

1073-1573 1323-1 603

29

12861508

96

Pa.

-

66 4.8

IVa(i)

S.C.

-

Temp. range

Qt

Umol-'

286.4

DS,nearly independent

1226 and 1 326 97

of composition (99.44)

-

wt.%

-

I

(99.99)

-

wt.%

-

(99.57) I

I

-

-

Fe (99.97) 0 10 20 30 40 45 50 60 70 80 90 100

(99.95) 0 15.5 30.7 46.6 61.7 71.1 76.2 80.6 90.5 100 (99.9) 0 5 10 15 20

IVb, P.c., Fe59,CrS' 0.88 279.7 1.96 2.86.5 5.35 298.9 4.73 295.4 16.6 306.0 14.1 304.1 8.61 299.1 1I .48 302.9 12.88 303.4 5.83 293.3 IVb, P.c., Ni63

-

(99.97)

0 14.9 29.7 45.3 60.5 70.0 75.3 79.8 90.0 100

0.72 2.13 9.98 8.75 28.77 11.99 20.28 12.30 17.99 9.21

-

Diff.of Cr 280.5 28 1.2 1298-1 548

162

243.2 270.5 281.8

1193-1 513

172

283.5 289.4 291.9 303.4 300.5 305.3 307.3 301.5 299.6 290.0

-

-

1.10 17.70 13.90 23.82 14.39 10.69 9.75 2.06

286.4 324.1 320.5 324.3

287.4

5x 1.5 x 1.9 x 10-2 0.277 0.797

IVa(i), P.c., FeS9,N P , W183 278.7 1.12 286.3 1.88 305.7 2.36 301.8 8.04 311.3 7.76 302.7 13.90 309.9 13.31 304.2 8.73 307.1 7.67 297.1 3.44 1258-1 578 K

232.4

Diff of W

-

S?8.2 317.0 317.5

-

299.5

Pd (99.95)

(At.%)

0.9 1 0.91 0.60 0.69 0.79 0.95 0.95 0.66 0.93 0.79

275.9 269.6 259.6 258.7 260.0 262.5 264.2 262.5 271.7 277.6

0.37 0.79 0.73 0.79 0.67 0.70 1.05 1.66 1.84 0.70

268.4 271.3 266.1 266.3 263.8 264.6 270.9 279.3 284.7 278.8

'

1373-1 523

142

l3-58

D i f i i o n in metals

Table 133

Fe

0

DIEFUSION IN HOMWBNBOLJS . 4 u o w o n t i n u e d

Pt IVb p.c. Ptlggm 2.7 1.1 0.34 1.17 0.28 0.15 1.3 1.13 2.1 0.85 0.34

0 0

15 20 25 30 34 40

45 50 55 60

Fe

0

0

0

0

2.9

0 7.64 11.1

0

0

-

0 1.48 1.87 6.55 8.64 12.1

(99.95)

0

-

-

5.5 6.4 7.8 11.6 15.3 192

(4N)

(4N)

-

-

-

IVa 216.9

P-C.

0.5 1

Naaadb 236.6 232.4 229.9 213.1 213.9 216.5

P.C.

1.39 1.63 0.50 050 1.11 1A6

(99.99)

(At.%) -

138

1169-1370

75

1073-1 573

100

1240-1 689

123

1 173-1 373

139

1073-1 373

188

1013-1 373

203

875-957(a-f) 1005-1 178

197

si 0 4.7 6.3 8.2 11.3 11.7

0

1053-1 693

Sb 2.5

Fe (99.999)

296.0 264.2 265.0 265.0 264.2 264.2 289.7 284.3 292.2 286.8 280.9

10

IVb 0.44

218.5

IVa(i) S.C. 1.38 0.63 2.73 1.03 76.7 5.2 4.93 0.8

228.2 212.3 IVa(i),P.c., Fe59 242 276 276 242 236 213

7.2 250 3.15 238 8.6 244 0.63 212 2.1 219 3.4 216 IVb, P.c., F P 5.59 219.1 0.25 m.6

-

-

p.c. Fes9 -

-

-

(K-P)

Fe (99.97) -

Fe

0

0 0 (=I

sn (5W &26

IVa(i), P.c., Fe5' b, =98 =63 =63

1168 1093

159

1009

Ti

0

2

2.8

0 2 4 6

0

33.32 50.0

0.56 0.27 0.40 11.7 0.135

IVa 242.0 IVa(i) 216.5 204.7 209.9 IVa(i) 314.0 239.5

1 173-1 473

75

1273-1 673

99

1 123-1 373

125

Mechanisms of dgision Tabk 13.3

DIFFUSION IN HOMOGENEOUS ALLOYs-continued

Element 1 (purity) At.%

Element 2 (purity At.%

(Spec. P.) 5 10 15

(99.7)

Fe

V (-1

(4 (Y 1 (Y1

(4

0.53 1.09 2.11

(-)

(-1

QT

IVa(ii) 9.2x IO-' 2.14 52.5

(99.98)

(-)

-

2.1

(99.999)

0

-

0

0

0

_-0 -

wt.%

-

0 04.11 (M.96 0-1.11

(nuclear)

0198 1.35 1.64 3.54 6.37

-

Ga

PU

0 1 .O(wt)

0

-

kJmol-'

Temp. range K

Ref.

I 123-1 533 1123-1 373

1

1-

Diffusionof Hf'*'1.31 290.1 IVa 1.4 237.0 1.87 240.3 IVb

1373-1573

I

(Paramag.)

244.9

11531473

55

3.92

241.2

1273-1673

94

1273-1723

99

-

88

p.c.

-

-

p.c.

3.92 3.00 2.28 2.12 1.66

236.1 236.6 234.0

Diffusion of Crsl

2.04 2.10 2.2 2.02 10 1.8 45 530 3.47x104 164

229.8 231

1233-1511 1255-1511 1255-1511 1233-1 466

234

235 255 238 293 346 403 355

1255-1 511 1503-1 593 1 233-1 466 1233-1 466 1233-1 466

6,=18.7 = 10.0 = 12.615.6 IIa(ii), pc.,C14

B, -0 IVa(i), P.c., Fe5', Zr95 4.47x 117.1

54

p.c. 3.9 p.c.

-

zr 0 -

0

288.5 2772 257.5 IVa(i) 258.3

0 -

Ft

(99.9)

Diffusion of Nb95 1.82~ 196.1 2.9 x 172.9 234.5

5.4 10.9 16.25 20.0 27.65 47 65 75 90

(Man) 2.45

0-3.5

p.c. 165.8 203.5 243.3

!I)

(Man) -

0

kJmol-'

Nb

0

1.7

-

7.0

1.8 5.3 2 5 9 14 19

Q%

A: crnls-'

IVb

1.46 0.53 0.10

18.0

-

13-59

169 2001

-

-

-

b1=47 -

1

I

6 . 8 ~ 1 0 - ~ 145 149.04 1.52 x lo-' 150.9 2.08 x 1.62x lo-' 145.97 140.8 2.9 x 10-3 5.26 x lo-* 155.45

1173-1 598

185

1221 1078-1 578

156

1218-1 518 1258-1518 1218 x 1518 1 196-1 520 1188-1 470 1276-1 513

195

p.c.

76.4 6.98 x

152.0 56.1

847-9 17(e)

114

13-60 Difusion in rnetafs Table 13.3

DIFFUSION IN HJ3MOG6NEOUS ALLOY-tttimd

Element I

Element 2

@tufty)

(purity

At.%

At.%

A: Cm's-1

Ga (6N) 25

V (99.9) 75V3(Ga)

-

Ge

Ni (3N6)

(3N6) 0-8

-

Q€

kJmol-'

4

Q:

Temp. range

cm*s-l

kJmol-'

K

w.

414.8

129g1449

160

Na(i), P.c., V4* 1.52 x 104

IVa(iii), P.c., c~~~

-

-

b, =6 = 10 =3 =2

51

Enhancement not of DRj but of the closely similar (sic) D&.

In

0

7

12 0-30

0

0 2 7

12 20 30 45 In (6N) 51 50 47

44

IVa(i), P.c., PbZ1O -

-

7.2 x 5.1~10-4 b2=28S.3

b,=64.5

IVa(i), P.c., Ag1lom -

-

468-558

516

}

187

Diff of Ag

-

3.66 x lo-' 1.33 x lo-' 6.5 x 10-3 4.4x 10-3

52.4 45.0

40s523

0.12

207

1056-1 270

2.30

243

996-1 327

0.60

222

996-1 425

0.20

205.5

1039-1 473

-

IVa(i), pc.. Pd'", 84.10-3 192 +5x102 314.5 5 . 0 ~ 1 0 - ~ 181 + 1.06 x lo3 318 1 . 6 ~ 1 0 - ~ 191 + 20.0 293 0.14 215

69.1 64.0

In"4m

145

]

161

K (99.97)

IVa(i)

-

-

p.c.

DB x 109

0

0.13 0.14 0.19 0.33 0.49 0.56 0.67 1.03

1.58 1.81 1.79 1.90 2.12 Dfi, x lo8

108

0 0.13 0.18

0.38 0.55

0.73 1.25

313 2.61 2.86 3.40

Mn

0

18 25 35

IVa(i), P.c., MO'" 2.1x10-'0 53 3 . 0 ~ 1 0 - ~ 222 2 . 3 ~ 1 0 - l ~ 57 -

102&1284 10264284

Mechanisms OfdiBsion Table 13.3

DIFFUSION IN HOMOGENEOUS ALLOYS-continued

EIemene 1

EIement 2

(purity)

(purity

Mn (99.97) 9.7 13.3 17.9 20.6

Ti

Mn

2 1

0

0

An.%

0

At.%

(99.97)

0.5 1.o 1.5 2.0

Mo

Ni

0

0

8 16 18 20 23

(99.4)

MO

Ti (99.62

Mo (-)

U (-1

0

0

0

0.1

0

-

44 55

-

Nb

Ni

0

25

(99.9) 1.2 8 10

-

-

IVa(i) 5.38 x 10-3 2 . 9 2 ~10-3 1.38 x 4.6~ 8.0 x lo-'

p.c.

IVb

Temp. range

kJmol-'

K

1 133-1 723 1073-1 623 1070-1 573 1083-1 523

kJmol-'

Z2s-l

IVa(i)

p.c.

-

1.9~ 2.06 x 2.60~ 5.47 x 10-1

171.2 172.1 176.3 207.7

MnS4 0.31 x lo-& 0.71-* 1.2 x 121.8 3.36 x

Zr95

140.7 135.7 125.5 2.nX 10-4 104.6

IVa 229.9 228.6 218.6 210.6 207.2

pc.c 2.55 0.63 0.34 0.19

-

IVb

p.c.

105.3 112.3 116.7 125.3

i

236.1 218.6 218.6 204.3 198.5

Ref.

I

121

1173-1 473

143

1272-1 673 1273-1 623 1 2 2 3 1 623 1223-1.573 1373-1 573

126

873-1 173

36

1 173-1 673

116

1073-1 313

51

Diffusion of C"

p.c.

-

-

QT

159.1

1

IIa(ii)

1.45 2.88 2.69

270.5

p".

-

1.8 x 10-3 2.5 x lo+

W 15 20 25 35 50 65 75 80 85 99.9

0

Qt

-

10

Mo

A: cmzs-'

1.31 1.3 0.45 0.25 0.20

(99.4) 2.94 (99.98) 5 10 15 20 25 30

13-61

0

75

(99.99)

142 265 146

47 28 12 1.3 0.2 0.1 1

0.08 0.002 5 0.17 0.12

IVa 468.9 448.8 427.1 397.7 385.2 368.4 360.1 353.8 342.3 334.9 326.6 IVa 448.0 431.2 IVb

2.4 x I@

-

-

-

p.c.

0.0075 1.4 1.7 2.2 6.9 14 16

20 22 25 24 p.c.

S.C.

448.0

-

2 073-2 673

I 1

-1

1673-2 673 1773-2 673

1973-2 113 2 073-2 873

104

2 073-3 073 2 473-3 073

-

2 173-2 673

105

-

-

0.18

304.8

1543-1 623 1363-1 6 4 3 1

144

1303-1 503

113

NP3 NbgS

IVa(i)

p.c.

-

0.12 0.20 1.80

-

297.3 305.6 312.3 322.4 355.9 397.7 427.1 485.7 498.2 570.8 544.3

280.9

13-62 Diffusion in metals Table 13.3

DIFFUSION IN HOMOOENBOUS ALLOYS-continued

(purity) At.%

Element 2 (purity At.%

Nb (99.6)

Ti (99.7)

Element I

0.1 1.o

IVa(ii) 125.2 151-1 164.5 209.3 268.0 301.4 381.0

80.4 64.3

2.9 x 10-4 1 . 7 9 ~10-3 1.18 x 10-2 2.98 x 10-1

IVa(i) p.c. 129.9 160.0 198.2 258.5

0

IVb

p-c.

5 10

15 31 54 66 89

Mb

0 (At.%)

AP

p.c. 1.2 x 10-4 5.8 x 10- 4 1.5 10-3 9 x 10-3 8 x 10-2

Ti (99.97) 100

94.6

Temp. range

Qf

K

R&

1123-1 573

53

Diffusion of FeS5 115 x 10-3

1323-2 073

1473-2 073 1773-2 273 1973-2473 Ti44 4.54 x 1.27~ 3.15 x 2.51 x lo-’

58

Nb95 131.0 149.1 175.7 247.1

1223-1 784

147

1175 673

116

Diffision of U235

10 15

20 2s 30

0.2s 0.42

Nb

U

0

0

0 5 10 20 35

1.2 x 10-5

3.1 x lo-’ 3.1 x to-’ 7.6 x lo-’ 1.1 5.2 0.91

so

65 80

90 100

0 Nb

0

0 2 5 10

0 2 5

Nb (99.99) 2.3

Zr (99.9)

5.5

-

0

2.5wt.%

p.c. 1.1 x 3.2 x 3.5 x 10-5 1.25x 2.5 x lo-‘ 4 . 0 lob3 ~ 6.3 x 2.5 x 6.5 x p.c. 1 . 6 6 10-4 ~

‘1

150.7 142.4 147.4 165.8 222.7 239.5 274.7 280.5

1223-

321.1

1323-1 493 1475-1 123 1473-1 773 1823-2 073 1973-2 173 2 073-2 273

118.1

1073-1 313

57

2 680

153

305.6

153

w

-

15.3 28.1

288.1 304.4 324.5 383.1 421.2 421.2 IIa(ii)

-

10

0 -

IVb 119.3

201.0 215.6 226.1 235.7

10

wt.%

o

-

IVa(i), P.c., Nb9’, WIa5, Zrg5 DAb=1.434x D S = ~ . ~xS10-9 = 1.277 x lo-’ =4.35 x 10-9 =1.065x10-* =3.30x 10-9 =7.60 10-9 =2.38 x 10-9 b,=-5.7

-

Bz‘ 1 --5.7

Diff. of Zr D=4.42x lo-* =3.86 x =3.28~10-’ =2.42 x B,=(

1

IV p.c. Nb95 1.63 x 162.4 1173-1 433 IVa(i), p.c., ZrgS. D&=A, exp (-Qz/kT)exp(B/kTZ) B 4 Q, 0.44 315 1 . 3 4 ~ 1 0 ~ 0.43 285 8.30~lo4 104 0.13 261 5 . 5 0 ~~. Diff. of Ni IVa(i), p.c. NiS3 1120.8 D=8.9x IO-’’ ~ = i .xi 10-13 893.6

49

194

I 155

Mechanisms of digusion Table 13.3 Element I (purity) At.%

DIFFUSION INHOMOGENEOUS Auow-eontinued

Element 2 (purity At.%

I

32

0

(

Nb

Zr

5 10

95 9 0 85 - 2.5 - 5 - 7.5 95 5 90 10 85 15

0 15

2.5 5

7.5 -

-

1363

At

Qt

Cds-1

kJmol-'

Diff. of co 8 . 7 ~ 1 0 - ~ 154

Temp. range K

Ref.

1 125-: 645

156

169.6 196.8 211.4 180.0 207.2 230.3 175.8 205.2 224.0

1473-1773

119

p.c. 018 1.83 x 10-3 110.1 1.07 x 108.4 4.11 x 103.4 (0Diffusion)

873-1 373 873 x 1373 873-1 373

f46

At

1

Qt kJmol-'

IVa(i), p c , cos'

Mo 4.6 x lo-' 4.4 x lo-' 5.5 x 10-1 7 . 6 ~lo-' 3.1 x lo-' 1.1

-

IVb 209.5 230.3 242.8 213.5 234.5 251.2

p.c.

4.1 x 10-3 2.8 x 8.6 x lo-' 9.0 x 5.4 x 10-2 2.8 x lo-' 6.4 x 6.6 x lo-' 2.10-1

-

(a) Values read from graphically piotted results.

Nb

Zr

0

0 0

wt.%

Ni

0

0

0.5 0.8 1.o

Pb (6N)

sol. soh

sat.

IV -

-

IVb, s.c., Ni6' 8,=77000 =50000

Fitted to Dii=ZA(c=O)/[1+(1-4B,~)'

'1

=15oM) =7000 Ni

Sb

0

0

71.7 72.9(8) 73.7 75.0

0 50w 53w

530) Ni (3W

-

0

50 p.c. 41 p.c. 47 S.C. Si (3N6) '38

-

5.4 10-4 4.9 x 10-4 6.3 x 10-4 6.9 10-4

IVb 61.5 62.0

p.c.

-

-

-

873-1 272

101

0.019 0.051 IC0.095 \IC 0.082

860-1 373 (Nip 1150-1 373 (Sb)

154

b, =3 =2

IVa(iii), P.c., c059 b, = 156 =174

1 465 410

Sn (5W

IVb, P.c., NiS3, Sn113 6, =770

-

(r2.0

b, =55

-

&4

(3N6)

(3N6)

-

0-90

-

(r7.3

0&=3.1~10-'~exp0.191N(at.%) IVa(iii), p.c., ~ 0 5 9 ' " b2=276b, = 3 =3 =225

.o

202

J

69.1 66.2 IVa(i), S.C. and P.c., Ni6', SblZ4 161 1.84 159 0.58 163 3.4 165 7.3 284

Enhancement not of DE,but of the closely similar (sic) D Z .

Ni (99.98)

4

416 450 515

Enhancement not of Df,but of the ciacly similar (sic) Db.

1

51

13-64

Difision in metals

Table 13.3 DIFFUSIONIN HOMOGENEOUS aLLous--continued

At.%

Elemenr 2 (purity At.%

Ni

Ti

0

0

Element I (purit.v)

Ni (99.95)

Ref.

1202-1501

124

2.24 1.51 0.91 6.6 3.0 6.9 x 10-3

IVa(i) 287.2 282.6 277.2 296.0 319.0 389.0

0

1.9

IVa(i) 284.7

p.c. 2.0

299.4

1.7 5.3

30.0 58.0

320.3 337.5

2.2 17.0

306.1 337.0.

9.2

1.1

294.3

1.4

311.9

2.44 4.86 7.24 9.63 12.68 25

2's-l

W

(5N 0 5 8.4 12

0

K

kJrnol-'

Sn

Pu

LJmol-'

CIll's-1

Pb

Pb (99.99) 100

Temp. range

Q?

(5N) -

-

Q:

A?

Diff.of Ag 4.6x10-' 4.8xlO-' 2 . 0 ~lo-' 2.2x 10-2

1369-1.668 1 (DNA 13731568

I

66

IVa(i), pc., Agllom 61

60 56 55

423573

168

479-596

59

913-1113 923

148

TI (99.99) 0 5.21 10.27 20.2 34.6 50.3 62.4 62.6(s.c.) 74.5 76.2 81.8 87.1

1.372 1.108 0.880 0.647 0.367 0.231 0.393 0.287 0.691 0.862 2.575 17.0

IVa(i) 109.1 107.8 106.6 104.9 102.7 102.3 107.3 105.9 112.3 113.6 118.2 124.4

p.c. (except 62.6%) 0.511 101.9 0.364 0.361 0.353 99.6 0.193 96.8 0.091 0.101 0.126 0.194 99.9 0.330 102.5 0.957 1.20 106.9

1 I

Zr

0

At.%

40 10

sc

Zr

0.04

IVb p.c. PU240 124.1 D , = 1.05 x 10-7 -

0

0

rva(i), pc., Zrg3

6.7 13.5

-

-

-

-

-

(99.6) 0

IVb

-

-

-

1.o 1.85 2.75

-

0

99.99)

0 0.45 1.75

-

-

-

Diff. of Cr 4.5 x

-

}

D&=A,exp (-Q,/kT)exp (BikT') Az Qz B 1.0 336 1.63~10' 13W1906 1.3 343 1 . 7 2 ~ 1 0 ~ 1416x1873) p.c. 5.9 x 10-2 9231 100 5.0 10

194

268 .O

IVa(i), P.c., Cr51 137.8

12551513

165

Mechanisms of diffusion Table 13.3

DIFFUSION 1N HOMOGENEOUS ALLOYS-continued

Elernmr 2

Elentenr I (purity) At.%

(puritj

A:

Q:

At.%

em's-'

kJmo1-l

Ta

V

0

0

0-1.04

-

(-)

(99.98)

0 10 20 30 40 50 60 70 80 90

-

0

0

-

9.4 19

0

-

-

-

0

Temp.

A€

IVa(i), P.c.. V4' b,=1.68 IVa(i)

-

U

Zr

(-)

(-1

0

0

10

95

0 11 27 39 59 78 85 100

V (99.95)

Zr (nuclear) 0

-

(99.95) 0 0.5 1.a 1.5 2.0

0.5

1.o

1.5 2.0

(nuclear)

-

IIa(ii) 92.1 IIa(ii)

1 . 2 6 ~lo-'

-

D,* = 1.5 x 10-9

0

0 0.5

K

Re$

-

1960

169

1173-2073

115

p.c.

Ai

Qi

1.1 1.9

307 310

177.9 195.5

5 900

235.7 288.9 365.1

115and 194

-

1073-1 313

p.c.

IVa(i)

Dz,*=

-

=

1281K 2.8

57

1

62

273 J 1323

-

4 . 2 ~10-9 p.c, 0.12 2.8 x lo-' 3.9 x 10-4 2.4 x 10-5 3.8 x 10-6 7.5 x 10-7 1 . 6 10-7 ~

IVa(i). P.c., v4', Zrg5 389.3 81 383.2 115 379.4 153 376.7 195 58 373.0 242 1578K 1633K 1688K 1738K 19.9 b , = -28.7 26.5 24.4 IVa(i), P.c.. V4', Zr95 89x 116.55 5.5 x lo-' 112.47 3 . 0 ~10-5 106.88 1.5 x 100.55 0.7 x l W 5 94.15

116

117S1673

p.c.

-

118 86 72 68

IVa(i), P.c., V4' 0.64 312.6

i

B 1.08~10~ 1.00~10~

0.025 0.089

D,*

IVa(i) 127.7 141.9 160.8 168.7 245.3

1223K 0

1

3 . 2 ~10-9

-

5.7 x lo-* 7.5 x 3.65 x 10-3 7.1W3 8.96

1167K b,=-4.14

-

kJmol-'

Diffusion of Uz35 172.5 0.063 182.1 182.1

p.c.

Ivb

1.85 x 10-9

0

-

rutiye

IVa(i). P.c., V48

D"* =

0

-

Q:

Curved Arrhenius plots Curved Arrhenius plots See Figure 13.8b See Figure 13.8a The lines of Figures 13.3a and 13.3b are drawn at 10 at.%intervals of composition as shown in column 1

5

15 15 20 25 30 40 50 60 70

-

13-65

205.6

":)

1 173-1 338

369.2 373.0 376.0 378.6 380.8

1578-1 888

118.5 99.2 83.7 68.7

1783K 15.0

i

3.1 x lo-' 4.5 10-5

105.25 109.02

9.3 x 14.0 x lo-'

116.83 120.79

1318K 5.09

-

1375K 8.71 -

16.9

1888K 17.7

1428K 10.41

1476K 13.60

1848K

1428-2 078

117

iJ

167

189

13-66 Diffiswn in metals

Figure 13.7

REFERENCES TO TABLE 133 1. R. E. HoBman, D. Turnbull and E. W.Hart, Acta metaZZ., 1955, 3,417. W. C. Mallard,A. B. Gardnex, R. F.Bass and L. M.Slifkin, Phys. Rev., 1963, 129, 617. A. Schoen, Ph. D. Thesis, University of Illinois, 1958. N. N.Nachtrieb, J. Petit and J. Wehrenberg, J . chem. Phys., 1957, 26, 106. R. L. Rowland and N. H. Nachtrieb, .I. phys. Chem., 1963, 61, 2817. E. Sonder, Phys. Rev., 1955, 100, 1662. R. E. Hoffman, Acta metall., 1958, 6, 95. D. Lazarus and C. T. Tomizuka,Phys. Rev., 1956, 103, 1155. 11 E. Hoffman and D.Turnbull, J. appl: Phys, 1952,23,1409. 10. C T.Tomizuka. Unpublished data. 11. T. Heumann and P. Lohman, Z. Electroch@m, 1955,59, 849. 12 W.C. Hagel and J. H. Westbrook, T r a m metall., Sac. A I M E , 1961,221,951. €3. H. A. Domian and H.I. Aaronson, ibid, 1964, 230,44. 14. S. D. Gertsricken and I. Y. Dekhtyar, Proc. 1955 Geneva Con$, 1955,15,99. 15. S. D. Gertsricken and I. Y. Dekhtyar, Ffzfkametall. Metallov., 1956, 3, 242. 16. F. C. Nix and F.E. Jaumot, Phys. Reu., 1951, 83, 1275. 17. S. D. Gertsricken et af., Issled. zharpr. Splau., 1958, 3, 68. 18. A. E. Berkowitz, F. E. Jaumot and F. C . Nix, Phys. Rev., 1954,95, 1185. 19. J. Cermak, K. Ciha and J. Kutera, Phys. Stat. Solidi A , 1980, 62,467. 20. H. B. Huntington, N. C. Miller and V. Nerses, Acra Mer., 1961, 9, 749. 21. D. Gupta, D. Lazarus and D. S. Liebermann, Phys. Rev., 1967,153, 863. 22. A. D. Kurtz, B. L. Averbach and M. Cohen, Acta metall., 1955,3, 442. 23. J. E. Reynolds, B. L. Averbach and M. Cohen, ibid., 1957, 5, 29. 24. M. Yanitskaya, A. A. Zhukhavitdcii and S. 2.Bokstein, Dokl. Akad. Nawk SSSR, 1957, 112 720. 25. S. D. Gertsricken and T. K. Yatsenko, %p. Fiz., 1957,8, 101. 26. C. Kostler, F. Faupel and T. Hehenkamp, Acta Met., 1987.35, 2273. 27. R. P.Smith, Trans. metall. SOC, A I M E , 1962, 224, 105. 28. H. W. Mead and C. E. Birchenall, J . Metals., 1956, 8, 1336. 29. P. L. Gruzin and E. V. Kuznetsov, Dokl. Akad. Nauk SSSR, 1953, 93, 808. 30. K. Hoshino, S. J. Rothman and R. S . Averbach, Acta Met., 1988, 36, 1271. 2. 3. 4. 5. 6. 7. 8. 9.

Tempemtore (' C J X10-7 10-~

5

2 10-8

7$

5 2

-.-109 .g

$

c

8

.s

s

5 2 1o-10

Y

6

5

2 10-"

5

2

I

,

2

I

10"

0.45

055

0.65 104

0.75

0.85

~

7YK) Figurc: 13.8a Temperature dependence of diffusion of Tib4 in titanium-vanadium all1, Y S * ' ~ at 10 at.% intervals

1 P

0.45

0.55

0.65 104 T(K1

-

0.75

0.85

Figure: 13.8b Temperature dependence of diffusion of V4' in titanium-vanadium alloys"5 at 10 at.% intervals

x

13-68

Digusion in metals

31. B. Khomka, Acta Physica Polonica, 1963, 24,669. 32. B. Khomka, N u k h i k a , 1963,8, 185. 33. p. L Gruzin and B. M. Noskov, ‘Problems of Metallography and Physics of Metals,’ 4, 509 (MOSCOW, 1955) and Aec. tr 2924, p. 355. 34. S. G. Fishman, D. Gupta and D. S. Liebermann, Phys. Rev., 1970, B2, 1451. 35. K. Hirano, R. P. Agarwala, B. L. Averbach and M. Cohen, J. appl. Pkys., 1962, 33, 3049. 36. D. L. Gruzin, Yu. A. Polikarpov and G. B. Federov, Fizika metail. Metalloo., 1957,4,94. 37. A. W.Bowen and G. M. Leak, Metal Trans., 19741,2767. 38. H. W.Paxton and T. Kunitake, Trans. metall SIX.A.I.M.E., 1960,218,1003. 39. L. I. Ivanov and N. P. Ivanchev, Izv. Akad. Nauk. SSSR,Otdel, Tekhn. Nauk., 1958,8, 15. 40. A. Ya Shinyayev, Conference on Uses 06Isotopes and Nuclear Radiations, Met. Metallogr., 1958, p. 299, Moscow. 41. D. L. Beke, I. Godiny and F. J. Kedves, Phil. Mag. A, 1983. 47, 281. 42. K. Monma, H.Suto and H. Oikawa, Nippon Kink. GawC, 1964, 28, 188. 43. K Monma, H.Suto and H.Oikawa, ibid, 1964,28, 192. 44. A. J. Mortlock and D. H. T o m b Phil. Mag., 1959,4, 628. 45. J. Hino, C. Tomizuka and C. Wert, Acta Metalt., 1957,5,41. 46. A. B. Kuper, D. Lazarus, J. R. Manning and C. T. Tomizuka, Phys. Rev., 1956, 104, 1536. 47. P. Camagni, Proc. 2nd Geneva Con/: Atomic Energy, P/1365, Vol. 20, Geneva, 1958. 48. C. Bassani, P. Camagni and S. Pace, I l Nuouo Cim, 1961, 19, 393. 49. G. P. Tiwari, M. C. Saxena and R. V. Patil, Trms. I d Inst. Met., 1973,26,55. 50. 1. R. MacEwan, J. U.MacEwan and L. Yaffe, C a n J . Chenr, 1959,37,1629. 51. F. Faupel, C. Kostler, K.Bierbaum and T. Hehenkamp, J. Phys. F, 1988,18,205. 52. J. W . Miller, Pkys. Rev., 1969, 181, 1095. 53. R. F. Peart and D. H. Tomlin, Acta metall., 1962, 10, 123. 54. M. S. Zelinski, B. M. Moskov, P. V. Pavlov and E. V. Shitov, Physics Metals Metallogr., 1959, 8 (5), 79 and Fiz. Metall. Metallov., 1959, 8, 725. 55. J. Stanley and C. Wert, J. appl. Phys., 1961, 32,267. 56. I. A. Naskidashvili, Soobshoheniya Akad. N d . Gauzin, SSSR, 1955, 16, 509. 57. Y. Adda and A. Kirianenko, 1.nucl. Mater, 1962, 6, 135. 58. G. B. Gibbs, D. Graham and D. H. Tomlin, Phil. Mag., 1963,8, 1269. 59. H. A. Resing and N. H. Nachtrieb, Physics Chem. Solids, 1961, 21, 40. 60. V. S. Lyashenko, V. N. Bykov and L. V. Pavlinov, Physics Metals Metallogr., 1959, (3) 8, 40. 61. T. Heumann and F. Heinemann, 2. Electrochem., 1956, 60, 1160. 62. Y. Adda, C. Mairy and J. M. Andreu, Revue Mdtall., Paris, 1960,57, 549. 63. J. W. Miller, Phys. Rev., 1970, B2, 1624. 64. R. J. Borg, J. appl. Phys., 1963, 34, 1562 65. S. D. Gertsricken and I. Ya. Dekhtyar, Proc. 195s Geneva Con$ Peaceful Uses of Atomic Energy, 1955, 15, 124. 66. K. Monma, H. Suto and H.Oikawa, Nippon Kink. Gakk., 1964, 28, 197. 67. D. A. Leak and G. M. Leak,J. Iron St. Inst., 1958,189,256. 68. J. Askill, Phys. Stahcs Solidi, 1971, a8, 587. 69. Th Heumann and H. B6hmer, J. Phys. Chenr Solids, 1968,29,237. 70. C J. Santoro, Phys. Reu., 1969,179, 593. 71. S. J. Rothman and N. L. Peterson, Phys. Rev., 1967, 154, 552. 72. W. B. Alexander and L. M. Slifkin, Phys. Rev., 1970, B1, 3274. 73. J. Kucera and B. Million, Metal Trans., 1970, 1, 2599. 74. A. B. Gardner, R L. Sanders and L. M. Sliflrin, Phys Stahrs Solidi, 1968,30, 93. 75. D. Y. F. Lai and R J. Borg, USAEC Rept. UCRL 50314,1967. 76. L. N. Larilcov, Avronr Suarka, 1971,24, 71. 77. L. N. Larikov, et al., hot. Coat. Met&, 1970,3,91. 78. G. F. Hancock and B. R. McDonnell, Phys. Status Solidi, 1971,4, 143. 79. D. Gupta and D. S. Liebermann, Phys. Rev. B, 1971, 4, 1070. 80. V. M. Ananin, et al., Soviet J . At. Energy, 1970, 29, 220. 81. S. Benci, et al., J . Phys. C h m Solids, 1965, 26,687. 8 2 M. Badia and A. Vignes, C. r. hebd She. A d . Sei, Pmis, 1%7,264C, 858. 83. A Hg;sSner and W.Lane, Phys. Status Solidi, 1965,a 77. 84. P. Guiraldenq and P. Poyet, C. r. hebd. Sdanc. Acad. Si%, Paris, 1970, C270, 2116. 85. E. V. Borisov, D. L. Gruzin and S. V. Zemskii, Prot. Coat. Metals, 1968,2, 104. 86. S. P. Ray and B. D. Sharma, Acta Met., 1968, 16, 981. 87. S. P. Ray and B. D. Sharma, Trans. Indian Inst. Met, 1970,23,77. 88. L. V. Pavlinov, E. A. Isadzanov and V. P. Smiraov, Fizica MetaL, 1968,25, 836. 89. S Benci,G. Gaspamini and T.Rosso, Phys. Letters., 1967,24,41& 90. H. Oikxwa, et al., ASM Trans. Quart., 1968,61,354. 91. Th. Heumann, H.Meiners and H. Stiier, 2. N a t @ i i h . , 1970, M.,1883. 92. R. Ebeling and H. Wever, 2. Metall., 1968, 53, 222. 93. N. L. Peterson and S. J. Rothman, Phys. Rev., 1970, BZ, 1540. 94. A. W. Bowen and G. M . Leak,Metal Trans., 1970, 1, 1695. 95. G. F. Hancock and G. M . Leak, Met. Sei. J., 1967, 1, 33. 96. A. Ya. Shmyaev. Im. Akad. Nauk SSSR,Mal.. 1%9,4,182

Mechanisms of difision

13-69

97. H. Bakker, J, Backus and F. Waals,Phys. Status Solidi, 1971,345,633. 98. K.Nohara and K.Hirano, Proc. Int. Con5 Science Tech. Iron and Steel, Tokyo, 1970, Sect. 6 1267;and J. JQP.Inst. Met., 1973, 37, 51. 99. A. W.Bowen and G. M. Leak, Metal Trans., 1970, 1,2767. 100. D. Y.F. Lai and R. J. Bor& UCRL Rept. No 50516, 1968; J . appl. Phys., 1970, 41, 5193. 101. TILHeumann and H. Stus, Phys. Status Solidi, 1966,15, 1966. 102. A. F. Smith and G. B. Gibbs, Metal Sci. J., 1969,3, 93; 1968,2, 47. 103. R. P. Agarwala, et al., J. NucL Mater., 1970, 36, 41. 104. I. N. Fmtsevich, et al., J. Pkys. C h Solids, 1969, 30,947. 105. Larikov, et a l , Ukr. Fiz. Zh., 1967, 12, 983. 106. G.F. Hancock, Phys. Status Solidi, 1971,A7, 535. 107. K.Hirano and M. Cohen, Trans. Jap. Znst. Met., 1972,13, 96. 108. J. N. Mundy and W. D. McFall, Phys. Reu., 1972, B5.2835. 109. K.Hoshino, Y. Iijima and K. Hirano, Proc. Yarn& Copferene, Point Defects and Defer Znteractions in Metals. N. Holland, 1982, p. 562. 110. G. B. Federov, E. A. Smirnov and V. N. Gusev, Atomn. Energ., 1972,32,11. 111. K. Kishio, 3. R. Owers-Bradley, W. P. Halperin and J. 0. Bnttain, J. Phys. Chem. Solids, 1981,42, 1031. 112. B. Giinther, 8.Kanert and W.Tietz, J . Phys. F , 1986,16, 1639. 113. A. Ya. Shinyaev, Im.Akad. Nauk SSSR Metal., 1968,No. 1, 203. 114. W. Z.Wade, J . nuel. Mater., 1971,38,292. 115. J. F. Murdock and C. J. McHargue, Acta Met., 1968,16,493. 116. L. V. Pavlinov, Fiz. Met. Metalloued., 1970,30, 379. 117. G. B. Federov, E. A. Smirnov and F. I. Zhomov, Met. MetaNowd Chist. Metal., 1968, No. 7, 116. 118. G.V. Kidson and J. S. Kirkaldy, Phil. Mag, 1969,N 1057. 119. G. B. Federov, E.A. Smirnov and S . M. Novikov, Met. MetaZlowd. Ckist. Metal, 1969,No.8,41. 120. J. L. Bocquet, Acta Met., 1972,20, 1347. 121. E. Santos and F. Dyment, Phil. Mag., 1975,31,809. 122. G. B. Federov, E. A. S m b o v and F. I. Zhomov, Met. M e t d ~ dChist. . Metal.,1963, Na 4, 110. 123. B. Milk,G.K Walker and G. M. Leak, PhiL Mag., 1965, 12,939. 124. A. Ya. Shinyaev, Phys. Met. Metallogr., 1966,21, 76. 125. A. Ya. Shinyaev, Izu. Akad. Nauk SSSR Metal, 1971,No. 5, 210. 126. I. N. Frantsevich, Kalinovich, I. I. Kovenski and M. D. Smolin, 'Atomic Transp. in Solids and Liquids' (Verlag Z.Natudorsch, Tubingen, 1971). p. 68. 127. Stoebe, et al., Acta Met., 1965, 13, 701. 128. T.Okabe, R. F. Hochman and M. E. McLain, J. Biomed. Mater. Res., 1974,8, 381. 129. P.Gas and J. Bernardini, Scr. Met., 1978,12, 367. 130. A. Lutze-Birk and H. Jacobi, Scr. Met., 1975,9,761. 131. G.Henry, G.Barreau a d G. Cizeron, C. R. Hebd. A d . Sei. Seuie C, 1975,280,1007. 132. N. A. Stolwijk, M. Van Gend and H.Bakker, Phil. Mag., 42,783. 133. Y. Iijima and K.I. Hirano, Phil. Mag.,1977,35. 229. 134.J. Kuceta et a!., Acta Met., 1974,22, 135. 135. R.A. Perkins, R. A. Padgett and N. K. T u ~ l i Met. , Trans., 1973,4,1665,2535. 136. A. F. Smith, Metal Sci, 1975, 9, 375. 137. P.Guiraldenq and P. Poyet, Mern. Sci. Rev. Met., 1973,70,715. 138. J. Kucera and B. Million, Phys. Scat. Sol. A, 1975. 31. 275. 139. H. V. M.Mirani et ai., Phys. Stat. Sol. A, 1975,29,115. 140. A. T. Donaldson and R. D.Rawlings, Acta Met.. 1976.24.285. 141. J. Ruzickova and B. Million, Kououe Mater., 1977, 15, 140. 142. J. Fillon and D. Calais, J . Phys. Chem. Solids, 1977,38, 81. 143. D.D.Pruthi, M. S. Anand and R. P.Agarwala, Phil. Mag., 1979,39,173. 144. Y. Muramatsu, Trans. NatL Res. Inst. Met., 1975,17,21. 145. I. Sbi, S. Mei and H. B. Huntington, J . Appd. Phys., 1987,62,451. 146. R. A. Perkins and R. A. Padgett,Acta Met., 1977,25.1221. 147. A. E.Pontau and D. Lazarus, Phys. Rev. B, 1979,B19,4027. 148. J. P. Zanghi and D. Calais, J. Nuclear Met., 1976,60, 145. 149. D. Beke, I. Godeny, F. J. Kedves and G. Groma, Acta Met., 1977, 25, 539. 150. S. C. Chen, J. C. Tarczon, W.P. Halperin and J. 0.Brittain, J . Phys. C h m . Solids, 1985,46,895. 151. U . KBhIer, P. Neuhaus and C. Herzig, Z.5Metallk., 1985, 76, 170. 152. S. Mantl, S. J. Rothman, L. J. Nowicki and D. Braski, Phil. Mag. A. 1984,50,591. 153. J. N. Mundy, S. T. Ockers and L. C. Smedskjaer, Phys. Rev. B, 1986,33,847. 154. R. Hiihnel, W. Miekeley and H.Wever. Phys. Stat. Solidi A, 1986, 97,181. 155. G.M.Hood and R. I. Schultz, Mater. Sci. Forum, 1987,15/18,475. 156. Ch. Herzig, J. Neuhaus, K. Vieregge and t.Manke, Mater. Sci. Forum, 1987,15/18,481. 157. D.D.Pruthi and R. P. Aganvala, Phil. Mag. A, 1982,46. 841. 158. D.L. Beke, I. Godeny, G. Erdelyi, F. J. Kedves and B. Albert, DIMETA 82. Proc. Inti. Con5 DffuJion in Metals and AIfoys (eds F. J. Kedves and D. L.Beke), Trans Tech Pubs, Switzerland, 1983, p. 374. 159. A. Kumagai, Y. Iijima and K. Hirano, DIMETA 82 (see. ref. 158), p. 389. 160. A. van Winkel, M. P. H. Lemmens, A. E.Weeber and H. Bakker, DIMETA 82 (see ref. 158). p. 473. 161. H. Hahn, G.Frohberg and H. Wever, Phys. Stat. Solidi A , 1983,79,559. 162. B. Million. J. RtiiiEkovB and J. VieSiBl, Mater. Sci. and Eng., 1985,72,85.

13-70

D i f i s i o n in metals

163. Y. IUima, K. Hoshino, M. Kikuchi and K. Hirano, Trans. Jup. Inst. Met., 1984, 25, 234. 164. C. Fillastre, N. Barbouth and J. Oudar, Scripta Met., 1982,16, 537. 165. L. I, Nicolai, R. Migoni and R. H. de Tendler, J . Nuclear Mat., 1983,115,39. 166. H.Talah, N. Barbouth and P. Markus. J . Nuckar Mat., 1987,148,61. 167. D. D. Pruthi and R. P.Agarwala, Phil. Mag. A, 1984,49,263. 168. C. K. Hu and H. B. Huntington, Phys. Rev. B, 1982,26,2782. 169. D. Ablitzer, J. P. Haeussler and K. V. Sathyaraj, Phil. Mug., 1983, 47, 515. 170. Th. Hehenkamp and F. Faupel, Acta Met., 1983, 31,691. 171. H. S . Daruvala and K. R. Bube, J . Nuclear Mat., 1979,87, 211. 171. G. Henry and C. S. Cizeron, Ann. Chim., 1978,3, 167. 173. D. Delauney, A. M. Huntz and P. Lacombe, Scripta Met., 1979, 13,419. 174. Th. Heumann and T. Rottwinkel, J . Nuclear Mat., 1978,69/70, 567. 175. A. Bo%, G. Frohberg and H.Wever, Phys. Stat. Solidi A, 1979,52,509. 176. A. Bristoti and A. R. Wazan, Rev. Bras. Fis., 1974.4, 1. 177. S. J. Rothman, L. J. Nowicki and G. E. Murch, 1.Phys. F. Metal Phys., 1980,10,383. 178. R. V. Patil and E. D. Sharma, Metal Sei., 1982,16, 389. 179. Y. Iijima, K. Hoshino and K. Hirano, Trans. Jap. Inst. Met., 1984, 25, 226. 180. P. T. Carlson and R. A. Padgett, Scripta Met., 1979, 13, 355. 181. D. Ansel, J. Barre, C. Meziere and J. Debuigne, J . Less Common Met., 1979, 65, P1. 182. M. B. Dutt, S. K. Sen and A. K. Barua, Phys. Stat. Solidi A , 1976,56, 149. 183. K. Obrlik and J. Kukra, Phys. Stat. Solidi A, 1979,53, 589. 184. S.Kurokawa, J. E.Ruzzante, A. M.Hey and F. Dyment, Metal Sci., 1983,17,433. 185. S. N. Tewari and J. R. Cost, J. Mater. Sa., 1982,17, 1639. 186. H. Nakajima, Scripta Met., 1981,15, 577. 187. L. Cheriot and H. B. Huntington, Acta Met., 1987,35, 1649. 188. D. Treheux, L. Vincent and P. Guiraldena. Acta Met., 1981, 29, 931. 189. J. Pelleg, Phil. Mag., 1981, 43, 273. 190. G. Gunther and 0. Kanert, Solid State Comm., 1981,38, 643. 191. K. Hoshino, Y. Iijima and K. Hirano, Acta Met., 1982,30, 265. 192. J. RbZiEkovi and B. Million, Mater. Sci. and Eng., 1981,50, 59. 193. B. Million, J. REi5kov6, J. Velisek and J. VM&, Mater. Sei. and En&, 1981,Jo, 43. 194. C. Herzig and U.Kohler, Materials Sci. Forum, 1987,15/18,301. 195. R. V. Patil, G. P. Tiwari and B. D. Sharma, Phil. Mag.A, 1981,44, 717. 196. N. Prim and H. Wever, Phys. Stat. Solidi A, 1980,61, 505. 197. V. S. Raghunathan and B. D. Sharma, Phil. Mag. A, 1981,43,427. 198. I. Godkny, D. L. Beke, F. J. Kedves and G. Groma, 2.f.Mezallk., 1981, 72, 97. 199. H. Nakajima, Y.Nakamura, M. Koiwa, T. Tabasugi and 0. Izumi, Scripta Met., 1988, 22, 507. 200. S. Bharati and A. P. B. Sinha, Phys. Star. SoIidi (a), 1977,44,391. 201. D. Ablitzer and A. Vignes, J. Nuclear Mat.,1978,69/70,97. 202. H.Amenmu-Badrour. G. Moya and I. Bernardini, Acta Met., 1988,36,761. 203. B. Million, Czech. J . Phys., 1977, BZ7, 928. 204. T. Hehenkamp, W.Schmidt and V. Schlett, Acta Met., 1980,28, 1715.

Table 13.4 CHEMICAL DIFFUSION COEFFICIENTMEASUREMENTS Element I At.%

Element2 At.%

A V. small

Ag

A V. small Ag

Mg

-100

-100

Idmol-'

D cm2s-'

Temp. range K Method

R@.

0.12

140.7

-

873-1 073

IIIb(ii)

1

104

218

-

603-813

IIIb(ii)

104

0.21 0.30 0.33

120.6 123.5

IIa(i)

2

A1

0.5

1.o 1.5 2.0 2.5 3.O 3.5 6.5

0.55

8.5

-

Q

A cmZss-'

0-20

(c =mol fraction)

0.78 1.50 3.O 141.1 11.0 154.9 16.0 159.1 1.63 153 lOgb= -13.360+7.316~ l o g s = - 10.601 -1.084~+11.392' log d= - 10.322+ 1.79%

648-793 723 793

Electrochem. 292 method

Mechanisms of diffusion

13-71

Table 13.4 CHEMICAL DIFFUSION COEFFICIENT MEASUREMENTS-continued

EIement I At.%

Element2 At.%

Q

A cm*s-l

kJmol-’

0.0242

154.9

D cm*s-‘

Temp. range K

Method

Re5.

1079-1 290

IIa(ii)

3

1213

IIIa(i)

4

1 0 3 6 1 238

IIaCi)

5

IIa(i). p.c.

291

IIa(i), S.C.

51

Au 4.7x 10-9 4.1 x 10-9 3.7 x 2.sX 10-9 i.9x 10-9 0.14 Cd 0-25 8.6 16.5 3.4 10.4 10.7 16.45 17.1

-

3.4 10.8 16.5 17.1 (a)

174.6

I

SeeFigures 13.9 and 13.10 = 150 DCd/DNi 1 54. 11.2x 10x10-9 4.3 x 10-9 ‘“’5.4 x 10-9 wj.71 x 10-9 9.36x 10-9 109~,, 1094, 1.85 11.53 1.67 5.76 1.32 ‘“7.79 2.77 10.72

873-1 073 1073

1

1179.5 1072.4 1087 1073.5

073’5 1179.5 1086.6 1073.5 1073.5

Average values.

__ cu c-2

0.012 0.52

149.1 183.8

-

99&1 140 1023-1 073

IIs(ii) IIa(ii)

6 156

Ga 1.9-9.5

0.42

162.9

-

1023-1 073

IIb

219

-

611-873

IIb(ii)

7

H &sol. limit

2.82 x l W 3 31.4 (D indep. of conc.)

Kr V. small

1.05

146.5

-

773-1 073

IIIb(ii)

8

Mn M.5

0.18

179.6

D indep. of conv.

849-1206

IIa

151

V. small

2.5

249.1

-

1073-1 213

IIIb(ii)

105

0 &sol. limit

3.66~

46.1

-

685-1 135

IIIb(ii)

9

Ne

Pb 7.4 x lo-’

63.6

-

493-558

IIa(ii)

10

Pd 50

1.5 x

103.0

-

873-1 173

I1

152

S Sol. s o h

2 . 3 4 ~10-3

110.1

-

877-1 025

Xe V. small

0.036

157.0

-

773-1 073

50 40-55 26.8 27.6

0.0164

69.1

0-18 7487

See Figures 13.12 and 13.13 See Figure 13.19

Zn D,,-3 to 4DA, Figure 13.11

]

8.7 x 10-9 2.45 x lo-’ DZn- 1.5-2.2DA,

673-883

220 IIIb(ii)

{ &)]

13

11

2

IIIa(i)

12

823-1 023 583-673

IIa(i), p.c. IIa(i)

312 221

13-72

Difision in metals

Table 13.4 CHEMICAL DIFFUSION COEFFICIENT MEASUREMENTS-mntinued Element I At.%

Element2 At.%

A1 33.33 'a-phase' (Au Al)

Au

A1

66.66

Q

A cm2s-'

Iclrnol-'

6.8

105.5

D cm2s-I

-138

Be 0.015 0.022 0.03

Temp. range

K

Method

Ref.

393-553

IIC, p.c.

263

P.c., IIa(ii)

265

2.6 x 10-13 1.1 x 10-10

;;;1

-

773-908

IIa(iii) and IIc

14

1 273-1 473

IIa(i), p.c.

257

550

163.3 168.7} 180.5

-

10.5

295

-

Cr G6

1.3 x lo6

240

-

659-726

IIa(i), p.c.

276

A1

cu 130.29 126.02

-

778-908 775-8 11

IIa(ii) IIC

15 154

185.22 187.74 187.57 187.19 189.37 194.43 191.46 115.1 136.1 138.2

-

985-1 270

IIa(i)

153

919-1 023

IIC

17

673-808

IIC

155

1 073-1 223

IIa(ii), p.c.

264

A1 0-10.2 A1

52 126

co

M.215

0.29 0.18 (sol. sol. range) 0.131 0.231 0.287 0.364 0.588 1.033 1.293 0.19 &-2

0 2 4 6 8 10 12 25

-

11-13

0.65

P-phase

A, = 0.13 A,2.2

wt.%

(a) logA=-0.86(9+0.0829 Q=44.27+0.14 C,

AI 9 17 25 33

127.7 176.7 QAl=162.9 Q,=181.7

} Least quam fit

CAI

!

')

~

-

-

1

-

}

to the data of reference 153.

Fe

2.7 x lo-' 3.6 x 10 - 3 7 x 10-2 7.3 x 10-2

188.0 142.4 167.1 129.8

2.1 x 104

290.6

-

1.5 x los 30.1 1.6

305.2 234.5 306

Al

H &sol. limit

0.11

110.95

633-873

IIIb(ii)

19

Al -100 Al

He

v. small

3.0

152.8

-

IIIb(ii)

105

Li &sol. limit

4.5

139.4

690-870

IIa(ii)

20

119.2

-

Electrochem. 293 method

1 4.4 12 2.4 x 10-4 9.9 x 10-1

129.8 140.3 143.6 56.9 117.6

33 41 0--52 0-15

(u-phase AI Li) A1

(4

0.155 Mg 0

0-10 0-20 B phase Y ph=

1193-1 483 (Disordered)

1

1373-1 483 18 (Disordered) 'Ia 1073-1 273 (Ordered) 1073-1 193 1223-1 373 IIa(ii) 120 1048-1 173 Ion impl. c(x) 283 via NRA

157 623-693 598-698

IIc

213

Mechanisms of diffusion

13-73

Table 13.4 CHEMICAL DIFFUSION COEFFICIENT MEASUREMENTS-continued EIemenr I At. Yo

Element2 At.%

A1

Mg 0

-

1 2 3 4.06

Al

Mmot-'

0.42 0.49 0.61 0.32 0.45

125 124 127 122 122

Mn 0.02-0.15

A1

Na 0-0.002

AI

Nb

33 25

67 75

A1

Ni

10.0

(a-phaes)

Method

Ref.

@ 0.101 Mpa. Data also at 2.2 and 3.3 Gpa.

690-818

IIe(i), p.c.

273

Figure 13.14

873-923

IIa(iii)

21

-

82?-923

IIIb(i)

22

2xlO-' 2.5

230.3 366.3

-

-1

1427-1773

Ila

222

-

1373-1 553

IIa(ii)

23

IJIa(i)

288

1223

-

K

134.0

-

0.7

Temp. range

D

1.1

1.87

0-0.7

14.0 25.0 38.0

Q

A cm2s-l

1.5 2.4

-

-

(e-phase) (&phase)

-

-

268.0 1O"B @ 1273 1323 2.2 3.0 7.9 3.8 11.5 4.9 6.3 29.5 62.0 -

1373 11.0 24.0 "'O

33.0 36.0 270

1423K

i:: ] Q-234

116.0

-

Q-266 Q * 208

1

\

)

B(S)varies rapidly with composition, with minimum close. to the stoichiometriccomposition (50%).Max Q=60 @ 45% AI, decreasing to 44 @ 36%, 32 @ 53%.

0-10.2

-

0 16

1.3 lnA=3.1 x 10-'0 -4.49

257 284'"' 258

-

1273-1 473

f "2; "5;

IIa(i), p.c. lIa(i), p.c.

157 313

(a) 0 decreases linearly with inctease in concentration over this range.

A1

Pu

3-9.1

(8)

A1

Si 0-0.5 0-0.5 0-0.7

AI 10.0

106.8

-

623-790

IIa(ii)

186

123.9 136.1 Qsi= 140.1 Q,,=143.1

-

617-904

IIa(ii)

224

753-893

IIa(i)

24

Ilaciii)

21 and 25

2.25 x 10-4 0.346 2.02 A,=3.95 A-5.07

--

-

Figure 13.15

723-853

1.4~ 9.0 x 1.6~

91.7 106.8 99.2

B increases

1256-1 523

0.27

118

-

Ti (a)

A1

Zn

-

0-4.49

linearly with c

383-433

X-ray analysis272 OP g.b.

-

depletion 0 3.5

0.406 0.280

723481

Ila(i), p.c.

485°C 149 174 2.2

540°C 610 610

277

Measurements also at 2 and 3 Gpa pressure. -0 9.0 18.1 37.6

10" x 6 @ 330°C i.84 1.95 3.64 -

To very good approximation

360°C 3.98 4.85 6.12 1.10

400°C 12.7 19.3 20.0 -

440°C 49.2 69.6 74.8 51.1

DZa=B/cA,(cA, =fractional at. conc.)

-

-

27

13-74

Diffusion in metals

Table 13.4 CHEMICAL DIFFUSION COEFFICIENT MEASUREMENTS-continued

Q

Elemenl I

Element2

A

At.%

At.%

cds-'

kJmol-'

AI

Zr 9.2 x lo-' 2.3 x lo-' 5.2 x lo-' 7.6 x lo-' 8 x io-' 9.2 3A 1.6 x 105

169.1

8 10 12 14 16 M3& M233 AI&.,

As 0.6-4.6

Temp. range

K

Method

ReJ

1373-1 573

189.2 192.2 192.2 283.0 272.1 382.3

-

219.8 246.6

-

-

Figures 13.12 and 13.13

-

223 1373-1 573 1273-1 573 1 2 7 3 1 573

-

-

Fe 4.3 0.58

Au

D

cu 10-90

(r)

1223-1653

IIa(i)

255

1006-1 130

IIa(i)

160

:;:$:}

IIa(i)

167

1133

IIa(i)

267

659-827

Hectrochemical method

280

0.5 4.2 7.2 11.2 14.6 21.8 28.3 38.6 55.3 63.9 79.0

2.36 x 7.94x 10-8 10'06 1.84 2.10 2.70 3.41 5.40 6.30 8.20 8.99 x 10-3 1.24 x lo-' 1.56 x IO-' 2 . 1 7 ~lo-' 2.99 x lo-' 5.36 x lo-' 8.91 x lo-' 0214 0.828 1.690 6.092

57.1 44.9 10'oDA, 1.8 2.0 2.4 2.8 3.1 2.5 3.o 133.1 135.9 138.0

Au

Fe 0-18.3

1.16 x

102.2

-

1023-1273

IIa(ii)

28

Au

H 2.08 x 10-3

20.8

-

523-1073

Ib

29

Au

In

'Au Cu' 1.25 2.50 5.0 7.48 12.44 14.25 17.43

-

-

-

-

50

-

-

-

~

~~

(Disordered) (Ordered) 10'oDc, 4.2 1 4.5 I 6.4

)

22.5 25.2

153.5 161.1 1732 179.4 190.7

d at 142°C d at 151°C 3 33 50 69 80 91

(Au In,) (Au In) (Au, 1%) 6% In)

Au

Ni 2 10 20 30 40 50 55

60 65 70 75 98

0.47 7.0 2.6 5.8 0.49

0.24 4.3 x 10-2 3.9 x 10-2 9.5 x lo-' 7.8 x lo-' 2.2 x 10-2 1.3 x 5.9 10-3 6.8 x lo-' 1.4 103 2.0 107 6.2 x 10' '1.8 x 104

( x 10-12) 24.0 29.0 6.6 9.8 0.68 0.28

-

IIa(i) (Values of D,, listed, calculated assuming D*"

4

s

- 2

a*

0

10 20 Concentration(At. XZd

30

Figore 13.23 Chemical and partial di$uswn coefflients in a&-Zn system at 780"C6'

13-110

Dzfision in metals

Figure 13.24 Chemical and partial diffusion coeflcients in or-Cu-Zn systems at 855"C61

Concentrotion (A { l l l ) 10" br: twist b'dies 44.9 4.4 (screwdislocations) 36.8 soodOO 99.999% edge dishations in bent 92.0k2.0 1400-2200 99.992% 0 Q the same for sub-boundary (e10") diffusion

15 16 and 28

*

45.8 42.7

690-750

850-1 050

(B1 P.C.

(VI D.C.

24 LC'S

27 21 22

23

AI1 values of Agb are calculated assuming a grain boundary width S=5 x lo-' cm. pc. = polycrystals. b.c. = bicrystals. S.C. =single crystal. Values of Agb, and to a lesser extent of Qgbi depend on the mathematical methods used to analyse the results: (F) indicates results calculated from Fishers solution of ab. difhrsion; (W) indicates results calculated from Whipple's solution of g.b. diffusion: (S) indicates resultscalculated from Suzuoka's solution; indicates the results am reported calculated from more than one solution, in addition to the one listed : ( (Dp) signifiesthat Agb refers to dislocation pipe diffusion-see references 2 and 27.

13-118

Difisioii in metals

REFERENCES TO TABLE 13.5 R. E Hoffman and D. Turnbull, J . appl. Phys., 1951,U, 634. D. Turnbull and R. E. Hoffman, Acta metall., 1954, 2, 419. G. Love and P. G. Shewmon, ibid., 1963, 11, 899. R. E. Hoffman, ibid., 1956, 4, 97. E. S. Wajda, ibid., 1954, 2, 184. F. Voigtmann, Thesis,Dresden, 1961. 7. E. S. Wajda, G. A. Shim and H. B. Huntington, Acta metall., 1955, 3, 39. 8. W. Lange and D. Bergner, Phys. Stat. Sol., 1962, 2, 1410. 9. B. Okkerse, Acta metall., 1954, 2, 551. 10. B. Okkerse. T. J. Tiedema and W. G. Burgers, ibid., 1955, 3, 300. 11. S. Z. Bokstein, S. T. Kishkin and L. M. Moroz, UNESCO Int. Conf: Rad. Isotopes and Sei. Res., 1957, Pap. 193. 12. C. Leymonie and P. Lacombe, M h , scient. Revue Mitall., 1960,57, 285. 13. P. Guiraldenq and P. Lacombe, Acta metall., 1965, 13, 51. 14. S. D. Gerzricken, T. K. Yatsenko and L. Slastnikov, Vaprosyfiziki metallou i metallouedeniva, Kiev, 1959, 9, 154. 15. W. Lange, A. Hassner and G. Mischer, Phys. Stat. Sol., 1964, 5, 63. 16. W.R. Upthegrove and M. J. Sinnott, Trans. Am. SOC.Metals, 1958, 50, 1031. 17. J. T. Robinson and N. L. Peterson, Surf: ScL, 1972,31, 586. 18. F. Guenther, A. Haessner and L. Oppermann, Isotopenpraxis, 1969, 5, 461. 19. R. N. Goshtagore, Phys. Rev., 1967, 155, 603. 20. A. Haessner and G. Voigt, 2.Metallk., 1968, 59, 559. 21. K. G. Kreider and G. Bruggeman, Trans. Met. Soe. AIME, 1967, 239, 1222. 22. G. B. Federov, E. A. Smirnov and S. S. Moiseenko, Met. Metdloved Chist, Metall., 1968, No. 1, 124. 23. G. B. Federov and E. A. Smirnov, Met. Metalbued. Chist. Metallov, 1967, No. 6, 181. 24. R. F. Cannon and J. P. Stark, J . appl. Phys., 1969, 40,4366. 25. J. P. Stark and W . R. Upthegrove, Trans. ASM, 1966,59, 479. 26. D. W. James and G. M. Leak, Phil. Mag., 1965, 12, 491. 27. M. Wuttig and H. K. Birnbaum. Phys. Rev., 1966, 147, 495. 28. R. F. Cannon and J. P. Stark, J . appl. Phys., 1969,40,4361. 29. D. Gupta, J . appl. Phys., 1973,44,4455. 30. D. Gupton and K.K.Kim, J . appl. Phys., 1980,51,2066. 1. 2. 3. 4. 5. 6.

Table 13.6 SELF-DIFFUSION lN LIQUID METALS Element

A

Q

1.44~ 12.0 8.6 x 9.29 K 7.6 x 10-4 8.46 D=5.344x 10-10TZ-2.443x W 5 Rb 6.6 x 8.29 D = 3.824 x 10-laTZ- 1.479 x 4.8 x 7.79 cs 1 . 4 6 ~lo-’ 40.7 cu 32.1 1243-1 573 Agz5.8 x Li Na

Zn

8.2 x 21.3 1.2~10-3 23.4 Cd 3.62 10-4 13.9 7.54 10-4 18.5 Hg ~ = 4 . 4 8 X10-10~1.854 0 = 4 . 3 4 ~10-9T3’Z-4.81 x Ga D = 2 . 2 ~10-’”T2 ~ = 6 . 0 1x 10-9~3/2-1.60X10-5 In 2.89 x lo-* 10.2 TI 3.17~ 15.2 Sn 3.24 10-4 11.6 D C1.8 +0.012(T- TM)]10-5 D = 6 . 8 5 ~10-”T2 Pb 2.37 10-4 24.7 Bi 8.3 x 10-5 10.5 Fe 1 x 10-2 65.7 4.3 x 10-3 51.1 Te 1.36 x 10-3 23.1 (a) Average values. A and Q both increase with temperature.

(b) Supercooled.

Temp. range “C

Method

Ref-

465-723 375-563 355-563 35-68 330-503 337-856 323473 1413-1 543 IIIb(ii), Capillary 723-893 703-893 603-783 603-773 213-567 24&525 292 -556 304474 443-1 023 623-1 073 540-956 628-1 925 5434 048 623-783 540-980

IIIb(ii). Capillary IVa(i), Capillary IVa(i), Capillary IIa(ii), Capillary Electrotransport method IIa(ii), Capillary Calculated IIIb(ii), Capillary

1 and 2 2 2 22 2and3 22 2 and 4 5

710-873

IVb(ii), Capillary

6 IIIb(ii), Capillary IIIb(ii), Capillary IIIb(ii), Capillary IIIa(i), Capillary IIIb(ii), Capillary IIa(ii), shear cell IIa(i), Capillary IIa(i). Shear cell IIIb(ii), Capillary IIIb(ii), Capillary IIa(ii), Capillary IIa(ii), Shear cell IIa(ii), Capillary IIIb(ii),capillary IIIb(ii), Capillary

7 8

9 23 11 10 12 13 14 15 21 16 17 9 18 19 20

Mechanisms of &&ion

13-119

REFERENCES TO TABLE 13.6

1. A. Ott and A. Lodding, Z . Naturforsch., 1965, uh,1578. 2. S. J. Larsson, C. Roxbergh and A. Lodding, Phys. Chem. Liquids, 1972,3, 137. 3. A. Nordh and A. Lodding, Z . Naturforsch, 1968,220,215. 4. A. Lodding, Z . Naturforsch., 1972,27a,873. 5. J. Henderson and L. Young, Trans. met. Soc. AIME, 1961,221,72 6. V. G.Leak and R. A. Swalin, Trans. met. Soc. AIME, 1964, 230,426. 7. N. H.Nachtrieb, E. Fmga and C. Wahl, J . phys. Ckm., 1963,67,2353. 8. W. L a n e W. Pippel and F. Jbdel, Z . phys. Chem, 1959,212,238. 9. M.Mirshamshi, A. Cosgarca and W. Upthegrove, Trans, metal!. SOL, AIME, 1966, 236, 122. 10. E.F. Broome and H.A. Walls, Trans. Met. Soc. AIME, 1968,242,2177. 11. R. E. Meyer, J . phys. Chem., 1961,65, 567. 12. S. Larsson et al., 2.Naturforsch., 1970,25a, 1472. 13. E. F. Broome and H.A. Walls, Trans. Met. SOC.AIME, 1969, 245, 739. 14. A. Lodding, Z.Naturjbrsch., 1956,lla,200. 15. N. Petrescu and L. Ganovici, Rev. Roum. de Chim., 1976,21, 1293 16. A. Bruson and M. Gerl, Phys. Rev. B, 1980,21,5447 and J . de Phys., 1980,41,533. 17. U. Sdervall, H. Odelius, A. Lodding, G. Frohberg. K.-H. Kratz and H. Wever, P m c . ‘SIMS V’ Conference, Washington D.G.. 1985. 18. N. Petrescu and M. Petrescu, Reuue Roum. Chim., 1970, 15, 189. 19. L.Yang, M.T. S i n a d and G. Derge, Trans. Met. Soe. AIME, 1956,206,1577. 20. L.Nicoloiu, L.Ganovici and I. Ganovici, Rev. Roum. Chim., 1970,15, 1713. 21. G.Careri, A. Paoletti and M.Vincentini, N m Cimen., 1958,10, 1088. 22. M. Hseih and R. A. Swalin, Acta Met., 1974,22,219. 23. I. Ganovici and L. Ganovici, Rev. Roum. de Chim.,1970, 15,213. 24. M. Shimoji and T. Itami, Atomic Transport in Liquid Metals. Diflusion and Defect Data, 1986,43, 1.

General physical properties 141 The physical properties of pure metals Many physical properties depend on the purity and physical state (annealed, hard drawn, cast, etc.) of the metal. The data in Tables 14.1 and- 14.2 refer to metals in the highest state of purity available, and are sufficiently accurate for most purposes. The reader should, however, consult the references before accepting the values quoted as applying to a particular sample. TsMe 14.1

THE PHYSICAL PROPERTIES OF PORE METALS AT NORMAL TEMPERATURES

Melting point

Metal

"C

Thermal conductivity

Mean specijic heat

CL100"C

0-100"C Jkg-' K-'

Boiling

Density

point

nt2O"C Wm-'

"C

g c ~ n - ~ K-' #

238 23.8

at20"C 2.67 40.1 33.3 60 (0°C) 3.3

CoefieMlt of expansion

0-100"C 10-3K-I

0-100"C 10-6K-I

4.5 5.1

9.0

23.5 8-1 1 5.6 18 12

4.6 4.3 4.8 4.57 87

13.4 31 97 22 8

214 6.6 4.3 1.19 2.01

6.5 12.5 17.0 8.6 9.2

Aluminium 660.323t Antimony 630.63t Arsenic (817) Barium 729 Beryllium 1287

2520 1590 616 2130 2470

2.70 6.68 5.727 3.5 1.848

Bismuth Cadmium Caesium Calcium Cerium

1564 767 670 1484 3430

9.80 8.64 1.87 1.54 6.75

9 103 36.1(s) 125 11.9

124.8 233.2 234 624 188

2680 2930 2 560 (2630) (2600)

7.1 8.9 8.96 8.536 9.051

91.3 96 397 10.0 9.6

461 427 386.0 173 166

13.2 6.34 1.694 91 86

8.8

298

134

4 I .O(s)

377 310 130 147

-89x10' 2.20 32.2

4.0 4.4

6.4 18.3 5.75 14.1 6.0

80.0 146.9 78.2

164 243 1N.6 456

94 8.8 5.1 10.1

1.71 5.2 4.5 6.5

9.5** 24.8 6.8 12.1

13.8

200

57

2.18

4.9

34.9

129.8 3517 154 1038 486

4.2 4.35

29.0 56 125** 26.0 23

217.403 321.069t 28.5 839 798

Chromium 1860 Cobalt 1495t Copper 1084.62t Dysprosium 1500 Erbium 1530

(3000) a7.895 p7.80 Gallium 29.7646t 2205 5.91 5.32 Germanium 937 2 830 Gold 1064.18t 2860 19.3' Hafnium 2227 4 600 13.1 Gadolinium 1350

Holmium Indium Iridium Iron

1461 156.5985t 2446t 1536

Lanthanum 920

2600 2070 4390 2860

8.803 7.3 22.4 7.87 K6.174

(3420)

p6.186

194

56.4 315.5 22.9

-

917

Temp. coeff: of resistiResistivity vity

209

331 285 2052

117 7.3 20 3.7 85.4

*

-

-

0.911.76

-

75.97 Lead 327.062t Lithium I81 Lutetium 1652 Magnesium 649 Manganese 1244

1750 1342 3327 1090 2060

11.68 0.534 9.842 1.74 7.4

See 'Electrical properties', **at 400°C.

$Densities of higher allotropes not at XI'C. f IM5ned fixed point at IlS-90-s~~Chapter 16.

76.1

-

155.5 7.8

20.6 9.29 68 4.2 16O(a)

-

4.25

-

14-2 General physical properties Table I41 THE PHYSICAL PROPERTIES OF PURE METALS AT NORMAL TEMPERANRES-continwd Thermal conductivity

Boiling point "C

Density 0-100°C at20"C Wm-I gem-'$ K-'

Mercury -38.87 Molybdenum2615

357 4610

13.546

Neodymium 1024

Metal

Melting point 'C

Nickel Niobium

1455t 2467

(3 2915 4740

Osmium Palladium Platinum Plutonium Polonium

3030 1554t 1768t 640 246

5000 2960 3 830 3 235 965

Potassium

63.2

(3020)

Rubidium Ruthenium Samarium

38.8 2310 1072

688 4 120 I 803

Scandium Selenium

1538 220.5

(2870) 685

silicon

1412 961.78t 97.8 770 2980

3270 2163 883 1375 5370

silver Sodium Strontium Tantalum

8.9 8.6

22.5 12.0 21.45 19.84

$r

138 251

1.53 7.536 7.40 2.99 4.79

234 10.5 0.97 2.6 16.6 8.272

Tellurium

450

988

6.24

Thallium Thorium Thulium

304 1755 1543

1473 4290 1727

11.85

Tin Titanium Tungsten

231.928t 2270 1667 3285 34207 5555

Uranium

1132

4400

Vanadium

1902

3410

Ytterbium

824

1427

Yttrium

1520

3300

Zinc

419.527t 911 1852 4400

* Sae'EIectrical propmis.'

11.5

9.322

61

452 268

6.9 16.0

6.8 2.6

13.3 7.2

86.9 75.2 13.4 8.4

130 241 134.4 142

8.8 10.8 10.58

4.1 4.2 3.92

11.0

-

146.5

-

6.8

1.0

5.7

-

47.6 148

138 243

18.7 4.7

4.5 4.4

356 234 181

12.1 7.7 92

4.8 4.1 1A8

558 339

66 12

-

-

138.5 425 128

-

57.55

-

-

729

1@-106

-

4.1 1.63 5.5 4.7 23 (0"C) 13.5 3.5

234

1227 137 142

4.57 9 .O 55

-

83

1.71

68

-

58.3(s) 116.3

5. I 6.7

1.64

-

172

116

3.8

134

1.6 x 105 (0°C)

45.5 49.2

130 I00

16.6

160

4.8

6.6 8.5 9.0 9.6

-

12 37 7.6 19.1 71 100

6.5

-

7.0

ICaxis 30

90

5.2 4.0 1.95 4.6 3.8 4.8 3.4

23.5

117

12.6 54 5.4 27

498

19.6

3.9

-

145

28

1.30

25.0

10.2

309

53

2.71

10.8**

119.5 22.6

394 289

44

4.2 4.4

31 5.9

-

1.3 73.2 4.5 21.6 19.3 174 19.05(a) 18.8918) 28 6.1 31.6 6.977 6.54 4.478 4.25 7.14 6.49

10-6K-'

88.5 54.1

192

12.2

0-1OO"C

209

754

5 690 3 700

Coefficient of expansion

4.35

11.7

1500

Temp. coefi of resistb Resistiuity uiry at2O"C 0-100°C IO-'K-' pRcm

95.9 5.7 64

1W(s)

(2500)

'*

K-'

0.86 a'782 86.64 5 21.0 12.4

1356

(s)=solid

Jkg-'

-

Terbium

zirconium

0-100"C

-

759

F'raesecdymium 932 Radium 700 Rhenium 3180 Rhodium 1962t

8.65 137 13.0

10.2

Mean specific heat

$ aUranium

226 528 138

a 11 a axis -3.5 I1 b axis 25-300°C 17 (I c axis

}

14

5.96

&Uranium 4.6 I(c axis 23 I caxis

11.2

11.6** 8.9 4.5 $

8.3

}

20-720"c

At 400°C. $Densities of higher allotropes not at 20'C. Rare Earths and Rare Metals ( ). Melting and boilins points (1) see also 'Thermochemical data' p. 8-1. Electrical resistivity (2,3) see also 'Electrical properties, p. 19-1. Spoifio heat (4.5) Thermal conductivity(6). t Defined fixed point of ITS-%= Chapter 16.

The physical properties of pure metals

14-3

Table 84.2 THE PHYSICAL PROPERTIES OF PURE METALS AT ELEVATED TEMPERATURE§

Thermal

Coeficient of expansion

Metal

Aluminium

Temperature t "C 20 100 200 300

400 Antimony

Beryllium

Bismuth

Cadmium

Chromium

20 100 500 20 100 200 300 500 700 20 100 250 20 100 300 20 100

400 700 Cobalt

20 100 200 3w 4w

rn

800 10CO 1 200 Copper

Gold

Hafnium

Iridium

20 104 204 500 loo0 20 100 5w) 900 20 100 200 400 lo00 1400 1800 20 100 500 lo00

20-t"C

K-'

23.9 24.3 2J.3 26.49

8.4-1 1.0 9.7-11.6

12 13 14.5 16 17

!3.4

-

31.8 (38)

6.6 8.4 9.4

12.3 13.1 13.6 14.0

-

17.1 17.2 18.3 20.3

14.2 15.2 16.7

6.3 6.1 6.0 5.9

6.8 7.2 7.8

Resistiuiiy at t"C cm

"")

conducriuiiy at t'C W m-' K - '

Specijic heat aft C Jkg-' K - ' References 900 938 984 1030 1076

7, 8, 9

238

7, 10, 6

5.99 7.30

40.1 59 154

18.0 16.7 19.7

205 214 239

3.3 5.3 10.5 11.1 21.8 26

180 152 130.2 117.7 103.0 85.8

1976 2081 (2215) (2353) (2 621) (2 889)

117 156 260 7.3 9.6 18.0 13.2 18 (152°C) 31 (407°C) 47 (652"C) 5.68 9.30 13.88 19.78 26.56 40.2 58.6 77.4 91.9 1.694 -

2.93 4.6(497"C) 8.1 (977°C)

11

8.0 7.5 7.5

121 130 147

7, 12

84 87.9 104.7

230 239 260

7, 13, 14

91.3

444 490 582 649

7, 15, 16

42,45

-

434 453 478 502 527 575 716 800 883

394 394 389 341(538"C) 244(1037"C)

'385 389 402 (427) (473)

7, 17, 16, 18

-

76.2 (426°C) 67.4 (760°C) -

-

-

2.2 2.8 6.8 11.8

293 293

7

-

126 130 142 151

35.5 46.5 60.3 84.4

(22.2) 22.0 21.5 20.7

144 148 152 160 185

43,44,48

130 134 142 159

19

-

5.1 6.8 15.1

-

-

-

148(0"C) 143

-

-

14-4

General physical properties

Table 14.2

THE PHYSICAL PROPERTIES OF PURE METALS AT ELEVATED TElMPERATvREs-continued

Resistivity at t"C

Thermal conductivity at t"C

Specifc heat at f"C

PO

Wm-'K-'

Jkg-* K - a

COe$jiicient of expansian

Temperature t"C

Metal

u)-t"c K-'

-

Iron

Lead

Magnesium

Molybdenum

Nickel

20

122 12.9 13.8 14.5 14.6

20 100 200 300

-

20 100 200 400

-

20 100 500 lo00 1500 2 500

-

20

100 200 300 400 500 900 Niobium

Palladium

20 200 400 600 800 lo00

20 100

m loo0 Platinum

u)

100 500 lo00 1500 Plutonium

20 a+a 100 a+a 200 a+

300 a - r y 400 a 4 500 a+& Rhenium

20 100

2500 Rhodium

-

100 200 400 600 800

20 100 500 lo00

29.1 30.0 31.3 26.1 27.0 28.9 5.2 5.1 5.75 6.51

-

13.3 13.9 14.4 14.8 15.2 16.3

7.19 1.39 1.56 1.72 7.88

11.1 12.4 13.6

9.1 9.6

10.2 11.31 47 203 173 181 109 101

12.4 11-axis 4.7 1 4 s 7.29(2 OOO "C)

8.5

9.8 10.8

10.1 14.7 226 43.1 69.8 105.5

73.3 68.2 61.5 48.6 38.9 29.7

444

20.6 27.0 36.0 50

34.8 33.5 31.4 29.7

130 134 134 138

4.2 5.6 7.2 12.1

167 167 163 130

5.7 7.6 17.6 31 46 77

142 138 121 105 84

6.9 10.3 15.8 22.5 30.6 34.2 45.5 14.6 25.0 36.6 48.1 59.7 71.3

10.8 13.8 27.5 40 10.58 13.6 27.9 43.1 55.4 145.8 141.6 107.8 107.4 100.7 110.6

F} 132 4.7 6.2 14.6

-

R&rences 7, 20

477 523 611 699 791

1022 1063 1110 1197

7, 6, 11

7

247 260 285 310 339 (mean)

7, 21, 22, 23

43 5 477 528 578 519 535 595

24

268 271 284 292 301 310

42,45

75 74

243 247 268 297

19

72 72

134 134 147 159 176

7, 19, 23, 25

131 138 145 153 154 144

4 5 45

-

88 82.9 73.3 63.6 59.5 62.0

-

56.5 60.7 65.3

-

-

-

67 63 (8.4

-

48

149 147

-

-

-

134 138 209(2 527°C) 243 255 289 331

26, 16, 27

19

The physical properties ofpure metals

14-5

Table 142 THE PHYSICAL PROPERTIES OF PURE METALS AT ELEVATJD TEMPERATURES-continued

Thermal

Coeficient of Metal

Silver

Tantalum

Temperature t "C

20

19.6 20.6 22.4

20

-

m 1 500 2 500 20

100 200 Tin

Titanium

Tungsten

20 100 200 20 100 200 400 600 800 20 100 500

lo00 2000 3000 Uranium

20a

600 a J00 B 800 Y Vanadium

Zinc

-

100 Mo 900 100

Thallium

expansion 20-t "C 10-6K-'

20 100 500 700

6.5 6.6

30 -

23.8 24.2

8.8 9.1 9.4 9.7 9.9

4.5 4.6 4.6 5.4 6.6

-

-

8.3 9.6

-

900

10.4

20 PO0 200 300 400

31 33 34

-

Resistivity

t"C VQcm

at

1.63 21 4.7 7.6

13.5 17.2 35 71 102

conductiuity at t"C W m-' K-'

Specific heat at t"C

J kg-'

K-'

Re/eences

419 419 (377)

-

57 54

-

-

138 142 151 167 234(2727"C)

7,29,30, 31, 32

16.6

46 45 45

134 138 142

33, 6

12.6 15.8 23.0

65 63 60

222 239 260

7, 34

54 70 88 119 152 165

16 1s 15 14 13 (13)

519 540 569 619 636 682

35, 36

5.4 7.3 18 33 65 100

167 159 121 111 93

134 138 142 151

37,33 38

116 186 116 160

Expansion

-

30 59 55.5 54 24.8 31.5

-

5.96 7.8 11.0 13.0 16.5

-

27 38 40 42.3

-

anisotropic 42,45

4&45

-

492 505 570 603 636

113 109 105 101 96

389 402 414 431 444

39, 13,40, 41,6

31 36.8 35.2

REFERENCES TO TABLES 14.1 AND 14.2 1. W. Slough, Primate Communication, Chemical Standards Division, NPL, 1972. M.J. Swan, Private Communication, Electrical Science Division, NPL, 1972. G. W.C.Kaye and T. H. Laby, 'Tables of Physical and Chemical Constants', Longmans, London, 1966. 'Thermophysical Properties of Matter', TF'RC Data Series, Volume 4. R. J. G~mecinand i J. Guiewek,Nat. Bureau of Stds. Monograph; 1960. 'Thermophysical Properties of Matter', TF'RC Series Volume I; 1970. US Bur. Stds. Circular (2447,'Mechanical Properties of Metals and Alloys', Washington, 1952. 8. R. Hase, R. Heierbcrg and W. Walkenhorst, Aluminium, 1940,22, 631. 9. T. G.Peason and H. W. L. Phillips, Met. Rev., 1957, 2, 305. 10. H.Tsutsumi, S c i Rep. Toihoku Uniu. (I), 1918,7, 100. 11. R W. Powell, Phil. Mug., 1953,44, 657.

2. 3. 4. 5. 6. 7.

14-6

General physical properties

E. F. Northrup and V. A. Suydam, J . Franklin Inst., 1913, 175, 160. Saldau, 2.Metallogr., 1915, 7, 5. S. Grabe and E. J. Evans, Phil. Mag.,1935, 19, 773. R. W. Powell and R. P. Tye, J . Inst. Metals, 1957, 85, 185. C. F. Lucks and H. W. Deem, ASTM Special Tech. Pubn., 1958, No. 227. C. S. Smith and E. W. Palmer, Trans. AIMME, 1935, 117, 225. C. J. Meechan and R. R. Eggleston, Acta Met., 1954. K.680. R. F. Vines, ‘The Platinum Metals and their AUoys’, New York, 1941. BISRA, ‘Physical Constants of Some Commercial Steels at Elevated Temperatures’, London, 1953. C. Zwikker, Physica, 1927, 7, 73. E. P. Mikol, US Atomic Energy Comm. Publ. ORNL-1131, 1952. 0.H. Kirkorian, UCRL-6132, TID-4500, Sept. 1960, USA. Mond Niche1 Co. Ltd., Nickel Bull. 1951, 24, 1. K. S. Krishnan and S. C. lain, Er. J . appf. Phys., 1954, 5, 426. C. Agte, H. Alterthum, et al., 2.anorg. Chem., 1931, 196, 129. R E. Taylor and R. A. Finch, US Atomic Energy Com. Rep., 1961 NAASR4334. US Bur. Min. Circular C412, Silver, its Properties and Industrial Uses’,Washington, 1936. L. Malter and D. B. Langmuir, Phys. Rev., 1939, 55, 743. M. Cox, Phys. Rev., 1943, 64, 241. I. B. Fieldhouse, et al., WADC Tech. Rep. 55-495, 1956. N. S. Rasor and J. D. McClelland, WADC Tech. Rep. 56-400, 1957. A. E. van Arkel, ‘Reine Metalle’, Berlin, 1939. Int. Tin R. and D. Council. Tech. Publ. B1,1937. E. S. Greiner and W. C. Ellis, Metals Tech., Sept., 1948. L. Silverman,J . Metals, N.L, 1953, May, p. 631. C. J. Smithelk, Tungsten’, London, 1952 V. S. Gurnenyuk and V. V. LeWen, Fizica Metall., 1961,11,29. F. L. Uffclmann, Phil. Mag., (7),1930, IO, 633. Lees, Phil. Trans. R. SOC.,1908, A208, 432. Dewar and Fleming, Phil. Mag., 1893, 36, 271. C. A. Hampel ‘Rare Metals Handbook‘, Chapman & Hall, London, 1961. H. K. Adenstedt, Pans. A.S.M., 1952,44,949. 44. R. P.Cox et aI., I d . Eng. Chem., 1958, 50, 141. 45. Thermochemical Data Section. Met. Ref: Book. 46. R W . Powell, R.P. Tye and M. J. Woodman, 3. less Common Metals, 1967,17., 1.

12. 13. 14. 15. 16. 17. 18. 19. 20. 21. 22. 23. 24. 25. 26. 27. 28. 29. 30. 31. 32. 33. 34. 35. 36. 37. 38. 39. 40. 41. 42. 43.

142 The physical properties of liquid metals Table 1438 THE PHYSICAL PROPERTIES OF LIQUSD METALS Density, suface tension and uiscosity ~~

~

~

The values of the properties listed in Table 14.3a are the weighted mean of the experimental values due to the investigators listed, usually in order of the reliance placed on their results, in the column of references. The references are grouped, and relate to density, surface tension and viscosity in that order. The properties given in parentheses are estimates. 14.2.1

Density

The variation of the density D of most liquid metals with temperature t is found to be well represented by a linear equation D = D o + ( t - t o ) (dD/dt)

where Do is the density of the liquid metal at its melting point 14.2.2

to.

Surfacetension

The surface tension y of most liquids can be represented over temperature ranges of usual interest by the linear equation Y=Yo+(t--to)

(dyldt)

The physical properties of liquid metals 14.2.3

14-7

Viscosity

For most liquid metals the variation of viscosity q with temperature T(K)may be written '1=v0 exp (EIRT)

where qo and E are constants, and are given in the table, and R is the gas constant, 8.3144JK-' mol-'.

Table 1-

THE PHYSICAL. PROPERTIES OF LIQUID METALS Surface

Temp

Density dDldt

960.7

Viscosity

tension dddt

903 914

0.453 2 0.1492

22.2 16.5

1,26, 27/86/90, 91 2-6/86/90,91 71-19, 8/86/90, 91 10/86/-

-

11, l2/89/13186114/86/90, 9 1 12/86/90, 91 15, 16, 17, 18, 77/86/90, 91 19-22186159 23, 24, 25/86/90. 91 25, 29186130130, 84/90, 91 31, 32, 33, 26, 34, 8/73, 34, 87, 88/90, 91

817 1063 2 077

9.346 2385 5.22 17.36 208

-0.907 -0.28 -0.535 -1.5

-

-

1140 1070

-0.52 -

727 1283 271 865 321

3.321 1.690 10.068 1.365 8.02

-0.526 -0.1162 -1.33 -0.221 -1.16

224 1390 378 361 570

-0.095 ( -0.29) -0.07 -0.10 -0.26

-

1.80 1.22 2.28

0.445 8 0.065 1 0.300 1

6.45 27.2 10.9

ce

804

-

0.255 0

-

-

8.000

-0.33 -0.49 ( -0.32) -0.047 -0.13

2.88 4.18

CU

740 -0.227 -0.988 1873 -0.30 1700 69 -0.638 1 -0.801 1285

-

1493 1875 28.6 1083

6.685 7.76 6.28 1.854

-

co

0.68 4.0

0.1022 0.3009

4.81 30.5

Fe

1536

7.015

-0.883

1812

5.5

0.369 9

41.4

Fr Ga

(2.35) 6.09 (7.14) 5.60

(-0.792) -0.60

(62) 718 810 621

(0.765) 2.04

-

Gd Ge

18 29.8 1312 934

Hf

1943

-38.87

11.1 13.691 13.595 1 13.5459

-

Hg

Ag AI As

Au

B Ba

Be Bi Ca

Cd

Cr

cs

660.0

0

20

-

-0.625

-2436

1630 498

-0.16 -0.35

-0.49 ( -0.044)

3.88 1.30 5.0 -

-

1.132

-

15.9 -

44.4

0.435 9

0.73

-

-4.00 -

(-021)

-

-

-

-0.20

210

0.556 5

2.51

0.302 0

-6.65

-0.10 -0.16 -0.26

-

36, 23, 25, 33, 37/86/90. 91 38/38/38 39, 40186190, 91 86186141,42 28, 13,43 WP4 8618645, 46/86/90, 91

average over

0-1Oo"C In 1Ir

K

100 13.351 5 156.6 7.023 -0.679 8 2 443 (20.0) 0.827 0 -0.228 5 63.5

-

La Li

930

Mg Mn

651 1241 2 607

Mo Na

180.5

Nd

96.5 2468 1024

Ni

1454

Nb

os

2 127

5.955 0.525 1.590 5.73 (9.34) 0.927 (7.83) 6.688 7.905 (20.1)

556 2 250 111.0

-0,237 -0.1863 -0.2647 -0.7

720 395 559 1090 2 250

-0.2361

195 1900 689 1778

-

-0.528 -1.160

-

2 500

-0.09 1.89 (-0.31) -0.062 5 0.51 2.45 -0.32 0.57 -0.150 1.25 -0.35 -0.2 (-0.30) -0.089 5 0.68 (-0.24) -0.09 4.90 -0.38 (-0.33)

-

-

0.1340

5.02

-

-

0.145 6 0.024 5

5.56 30.5

-

-

0.1525

-

-

5.24

0.1663

50.2

-

-

47/86/90, 91 48186130/30/90, 91 59/85/59 30/30J90,91 49-51/86/90,91 52153148, 54186130/30/90,91 48186122186136, 25, 55, 37, 56, 23, 34/86/90, 91 481861-

14-8

General physical properties

Table 14.h THE PHYSICAL PROPERTIES OF LIOUID METAIS-cantinued Swfioee tension

Temp

Density

to

dD/dt dMt Do m g ~ m - ~70 mNm-' g ~ m -K-' ~ mNm-' K-'

Metal

"C

P Pb Pd Pr

Pt

44 327 1552 935 1769

-

-

10.678 10.49 6.611 19

-1.3174 - 1.266 -0.240 -29 -1.450 -0.486

52 468 1500

-

Pu

640

Rb Re Rh Ru

38.9 3 158 1966 2 427

16.64 1.437 (18.8) 10.8 (10.9)

S

119 630.5 217 1410 232

1.819 6.483 3.989 2.51 7.000

-0.800 -0.565* -1.44 -0.32 -0.6127

770 2 977 451 1691 1685

248 ~... (15.0) 5.71 10.5 4.11

-0.360 -

T1

302

U W Yb

1133 1912 3 377 824

11.280 17.90 5.7 (17.6)

Zn

419

Zr

1850

Sb se Si Sn SI

Ta Te

Th Ti

V

-

6.575 (5.8)

-

viscosity

-0.13 (-0.22)

-

)Imp ?O E mNsm-z mNsm-2 kJmol-' Rgerences

-

2.80

1800

(-0.17)

-

550 83 2 700 2000 2 250

(-0.10) -0.052 (-0.34)

6.0 0.61

(-0.31)

-

61 361 106 865 544

-0.07 -0.05 -0.1 (-0.13) -0.07

-12 1.22 24.8 0.94 1.85

-0.702

303 2 150 180 978 1650

-0.10 (-0.25) (-0.06) (-0.14) (-0.26)

-1.43 -1.031

464 I 550

-0.08 -0.14 (-0.31) (-0.29)

-

1950 2 500

-

-1.10

-

(-0.30)

-

782

-0.17

1480

(-0.20)

-/86/95 57, 58, 15/86/90, 91 26186159, 201-159 26,60/86/-

1.71 2.65

1.089 0.0940

-

0.0812

5.59 5.15

-

22.0

-

-

0.5382

-

-2.14 0.2983 0.4848

10.5 30.4

-

1.07

-

3.85

0.413 1

12.7

-

w,

64/86/95 65,13/86/90,91 66-69186194 14, 34, 70/86/94 71/86/90, 91 72~361W6f27, 73,43, 74/86/94 72/86/75/86/93

5.2 2.64 6.5

61, W W 2 30130, 91 48,54/86f48/63/86/48/86f-

-

8.0

76-78/86/90,91 79/96/9491 75/48/86 48, 54, 80/86/-1-194 73, 81, 16, 82, 83/86/90, 91 44, 48, ?5/86f93

For antimony the simple linear equation is adequate to ahout IOOO'C. Howew, the resultnfor all the tcmperatura within the liquid range am betta represented by the equation D =65%

+2022 x IO-'

T- 3.629

x IO-'

T2

where Tis in degrres K (ref. 65).

REFERENCES TO TABLE 14.3a 1. A. D. Kirshenbaum, J. A. Cahill and A. V. Gross+ J . inorg. nucl. Chem., 1962, 24, 333. 2. J. D. Edwards and T. A. Moorman, Chem. metall. Engng, 1921, 24, 61. 3. E. Gebhardt, M. Baker and S. Dorner, Z . Metallk., 1953,44, 510.

G. D. Ayushina, E. S. Levin and P. V. Gel'd, Zh. Fiz. Khim., 1969, 43, 2756. V. N. Naidich and Yu. V. Eremenko, Fuika Metall., 1961, 6, 62. W. J. Coy and R. S. Mateex, Trans. Q. ASM, 1%5,58,99. P. J. McGonigal and A. V. Grosse, J . phys. C h m , 1963, 67, 924. 8. E. Gebhardt and G. Whvag, Z . Metallk, 1951,42, 111, 358. 9. E. Gebhardt and S. Dorner, 2. Merallk.. 1951, 4 2 353. 10. F. N. Tavadze et. af., Dokl. Akad, Nauk SSSR,1963, lSO,544; Studii Cerc. Met., 1%5,10,49. 11. C. C. Addison and R. J. Pulham, J . chem. Soc., 1962, 3873. 12. A. V. Grosse and P. J. McGonigal, J . phys. Chem., 1964,68, 414. 13. A. V. Grosse and J. A. Cahill, Trans. Q. A S M , 1964, 51, 739. 14. L. D. Lucas and G. Urbain, C. r., hebd. Sianc. Acad. Sci., Paris, 1962, 255, 2414. 15. H. T. Greenaway, J . Inst. Metals, 1947-48.74, 133. 16. T. R. Hogness, J . Am. chem. Soc., 1921,43, 1621. 4. 5. 6. 7.

The physical properties of liquid metals

14-9

17. A. Stauffer, Thesis, Gottingen, Dec. 1952 18. H. J. Fisher and A. Phillips, J . Metals, 1954, 6, 1060. 19. J. F.Eichdbergex, Mound Lab. Rep. 1113, 1961, p8. M. J. F. Eichelberger, Mound Lab. Rep. 1118, 1961. pl2. 21. R. H. Perkinq L. A. Geoffrion and J. C. Biery, Trans. AIME, 1965, 233, 1703. 22. W.G . Rohr, J . lesscommon Metals, 1966, 10, 389. 23. L. D. Lucas and M. P. Pascal, C. r. hebd. S4anc. Acad. Sci., Paris, 1960,250,1850. 24. A. D. Kirshenbaum and J. A. Cahill, Trans. Q. ASM.. 1963, 56, 281. 25. T. Saito and Y. Sakuma, J. Japan Inst. Met., 1967. 31. 1140. 26. L. D. Lucas, C. r . hebd. Sianc. Acad. Sci., Paris, 1961. 253, 2526. 27. ld. Wobst and R. Rentzsch, Z . phys. Chem. (Leipzig). 1969. 240, 36. 28. E. S . Levin et. al., ‘Poverkhinio Yavleniya Rasplavakh’, 1968. 191-202, Edited by V. N. Erenenko, Naukova Dumka, Kiev, USSR. 29. \1. N. Eremenko and Ya V. Naidich, Izu. Akad. Nauk SSR., 1959, 2. 111. 30. J. Freund, ‘Thermophysical and Nuclear Parameters of Molten Li, Na, K,Rb and Cs’, Inst. Kerntech. Tech. Univ. Berlin, (13). 184: 1969. 31. J. A. Cahill and A. D. Kirshenbaum. J . phys. Chem., 1962. 66,1080. 32. A. E. El-Mehairy and R. G. Ward. Trans. AIME. 1963. 221, 1226. 33. M. G. Froberg and R. Weber, Arch Eisenhutt Wes., 1964.35, 877. 34. R. F. A. Freeman,Private Communication, Fulmer Research Institute, 1973. 35. E. Gehhardt, M. Becker and S. Dorner, Alwninium, 1955,31, 315. 36. A. V. Grow and A. D. Kirshenbaum, J . inorg. m c l . Chem., 1963, U,331. 37. S, 1. Papel, L. M. Shergin, and B. V. Tsarevskii. Zh. Fiz. Khim., 1969, 43,2365. 38. Yu. P. Os’minin, Zh. Fiz. Khim., 1969, 45, 2610. 39. V. I. Nizenko, L. I. Sklyarenko and V. N. Eremenko, Ukr. Khim. Zhur., 1965, 31, 559. 40. W.H. Hoather, Pol. phys. Soc., 1936,48, 699. 41. 17. N. Tavadze et a!., ‘Vap. Metalloved. Korroz. Metal’. 1968, 11-18, Edited by F. N. Tavadze, Iz. .Metsniereba, Tbilisi, USSR. 42. F. N. Tavadze et al., ’Poverkhinio Yavleniya Rasplavakh’, 1968. 159-162, Edited by V. N. Eremenko; Naukoua Dumka, Kiev, USSR. 43. A. IKlemm et al., Mh. Chem., 1952, 83, 629. 44. A. W. Peterson, H. Kedesdy, P. H. Keck and E. Schwarz, J. appl. Phys., 1958, 28, 213. 45. A. V. Grosse, US Atomic Energy Comm. Contract AT 30-1-2082, May 1965. 46. A. H.Cook, Phil. Trans. R . SOC.,A, 1961, 254, (1038), 125. 47. P.J. McGonigal, J. A. Cahill and A. D. Kirshenbaum, J. inorg. nucl. Chem., 1962, 24, 1012. 48. 15. C . Allen, Trans. AIME, 1963,227, 1175; 1964,230, 1357. 49. .?I J. McGonigal, A. D. Kirshenbaum and A. V. Grosse, J . phys. Chem.. 1962 66, 737. 50. B Pelzel and F. Sauerwald, Z. Metallk. 1941,33, 229. 51. E. Gebhardt, M. Bedm and E. Tragner, Z . Metallk.. 1955, 46, 90, 52. S. I. Popel, B. V. Tsarevskii and N. K. Dzhemilev, Fizica Metall., 1964, 18, 468. 53. N. A. Vatolin and 0. A. Esin, Fizica Metall., 1963, 16, 933. 54. A. I. Pekarev, Izu. Ussh ucheb. Zaved., 1963, 6, 111. 55. S. Y. Shiraishi and R. G. Ward, Can. Met. Q., 1964,3, 117. 56. V. N. Eremenko and V. I. Nishenko, Ukr. Kkim. Zhur., 1964,30, 125. 57. A. D. Kirshenbaum, J. A. Cahill and A. V. Grosse, J . inorg. nucl. Chem, 1961,22, 33. 58. S. W. Strauss, L. E. Richards and B. F. Brown, Nucl. Sci. Engng., 1960, 7, 442. 59. L. J. Wittenberg, D. Ofte and W. 6.Rohr, ‘Rare Earth Research’, 2, p. 257, K. S. Vorres, Gordon and Breach, NY, 1964. 60. Yu. V. Eremenko and V. N. Naidich, Izu. Akad. Nauk. SSSR, 1959, 6, 129. 61. C. E. Olsen, T. A. Sandenaur and C. C. Herrick, Los Alamos Lab. Rep. LA-2358, 1959. 62. L. V. Jones, D. Ofte, W. G. Rohr and L. J. Wittenberg, Trans. AS M, 1962, 55, 819. 63. V. N. Eremenko and Yu. V. Naidich, Izu. Akad. Nauk. SSSR, 1961, (6), 100. 64. Y. (Onoand S . Matsushima. Sci. Rep. Res. Insts. Tdhoku Univ., 1957,9. 309. 65. A. D.Kirshenbaum and J. A. Cahill, Trans. ASM, 1962, 55, 849. 66. L. D.Lucas and G. Urbain, C.r. hebd. Sianc. Acad. Sci., Paris, 1962, 254, 1622. 67. S. Shirai et al., J . chem. Soe. Japan, 1%3,84,968. 68. S. Dobinsky and J. Weselowsky, Bull. int. Acad. Pol. Sei. Lett., 1936, A. 446. 69. A. N. Campbell and S. Epstein, J. Am. chem. Soe., 194264,2679. 70. V. P. Elyutin, V. I. Kostikov and V. Y a Levin, Izu. Vjssh. whet. Zaued.. 1970. 13, 53. 71. A. D. Kirshenbaum and J. A. Cahill, Trans. ASM, 1962.55, 844. 7 2 J. F. Elliott and M. Gleiser, Thermochemistry for Steelmaking’, Addison-Wesley, London, 1960. 73. L. D. Lucas, M6m. Scient. Revue Mitall., 1964, 61, 1. 74. C. S. Smith and D. P. Spitzer, J. phys. Chern, 1962,66,946. 75. M.Maurach, Trans. Indian Inst. Met., 1961, 14, 209. 76. V. N. Eremenko, Yu. V. Naidich and G. P. Khilya, ‘Poverkh. Yavleniya Rasplavakh’, 1968, p. 165. 77. A. Schneider and G. Heymer. Z. anorg. allg. Chem., 1956, 286, 118. 78. F. A. Kanda and D. V. Keller. US Energy Comm. Repts. TID 15863; 1961; TID 20849; 1964. 79. A. V. Grosse, J. A. Cahill and A. D. Kirshenbaum, J. Am. chem. Soc., 1961, 83, 4665. 80. A. Calverley, Proc. phys. SOC.,1957,70B, 1040. 81. E. Uhelacker and L. D. Lucas, C. r. hebd. Sianc, Acad. Sei., Paris, 1962, 254, 1622.

14-10

General physical properties

82. Y. Matuyana. Sci. Rep. TGhoku Univ., 1929,lE. 737. 83. C. M. Saeger and E. J. Ash, Bur. Stand. J . Res., 1932.8, 37. 84. A, A. Kiriyanenko and A. N. Solov’en, Teplofiz. Vys. Temp., 1970,8,537. 85. G.R. Pullism and E.S. Fitzsimmons, ISC-659,1955. 86. B. C.Allen, ‘Liquid Metals’, S. Z.Beer, Dekker; 1972. 87. B. C. Allen and W. D. Kingery, Trans AIME, 1959,215, 30. 88. G. Metzger, Z.phys. Chem., 1959,211, 1. 89. C. C. Addison, J. M. Coldrey and R. J. Pulham, J. chem. Soc., 1963,1227. 90. L. J. Wittenberg and D. Ofte, ‘Techniques of Metals Research’, Vol. 4, 193, Interscience, 1970. 91. R. T. Beyer and E. M. Ring, ‘Liquid Metals’, S. 2. Beer, Dekker, p450; 1972 92. L. V. Jones, D. a t e , W.G. Rohr and L. I. Wittenberg, Trans. ASM, 196555, 819. 93. V. P. Elyutin, M. A. Maurakh and I. A. Penkov, Im.VLr. Chem Met., 1965, 128. 94. V. M. Glazov, S. N. Chizhevskaya and N.N. Glagoleva, ‘Liquid Semiconductors’, Plenum Press,New York, 1969. 95. R. C.Weast, ‘Handbook of Chemistry and Physid, 52nd edn., Chemical Rubber Co., 1971. 96. J. A. Cahill and A. D. Kirshenbaum, J. inorg. nucl. Chem., 1965,27, 73.

TaMe 14% THE PHYSICAL PROPERTIES OF LIQUID METALS Specific heat, thermal conductivity, and electrical resistivity

Element

Ag

Temperature ”C

960.7 loo0 1100 1 200 1300

speeifc heat

J g - l K-1

Wm

Reference 1

1,21

-

1300 1400

(0.149) (0.149) (0.149) (0.149) (0.149)

104.44 105.44 108.15 110.84 113.53

0.3125 0.3180 0.331 5 0.348 1 0.363 1

2077 727

2.91 0.228

-

(2.10)

1, 21

Ba Be

1283

3.48

-

2,21 1, 21

Bi

271 300 400

1.33 (0.45) 1.290

(0.2W

1,21 2. 5, 6

1400

660 700

AS

800 900 1000 817

Au

1063 1 100 lux)

B

500

600 700

Ca Cd

Ce co

865 321 400 500 600 804 loo0 1200 1 493

-

1.08 1.08 1.08 1.08

-

0.146 0.143 0.1475 0.1375 0.1336

-

174.8 176.5 180.8 185.1 i89.3 193.5 94.03 95.37 98.71 102.05 105.35

Electrical resistivity

0.1725 0.1760 0.184 5 0.1935 0.202 3 0.211 1 0.242 5 0.248 3 0.2630 0.2777 0.2924 (2.10)

AI

0.283 0.283 0.283 0.283 0.283

Thermal conductivity Wm-l K-1

17.1 15.5 15.5 15.5 15.5 15.5

(0.775) 0.264 0.264 0.264 0.264 0.25 025

-

025

-

0.337 0.343 0 0.3510 0.3607 1.268 1.294 1.310

(0.59)

-

1.02

42

47 54 (61)

-

1

1

3, 4, 8,21

15,21

5 3,21

The physical properties of liquid metals Table P#b

THE PHYSICALPROPERTIES OF LIQUID METALS-continued

EIement

Temperature "C

Cr

cs

(1903) 28.6 100 200 400

cu

Fe Fr Ga

600 800 1600 1083 1 loo 1 200 1400 1600 1536 18 700 29.8 100

m

300

Gd Ge

Hf Hs

Ho In

K

La

(1 350) 934 lo00 (2227) -38.87 0 20 100 500 lo00 I460 (critical temp.) 1500 156.6 200 400 600 63.5 100 200 500 1OCO 1500 930 loo0 1100

Li

1 200 180.5 200

400 600 800 lo00

1 600

Specific heat Jg-lk-'

(0.78) 0.28 0.265 0.240 0.21 0.22 0.25

-

0.495 0.495 OA95 0.495 0.495

Thermal conductivity Wm-'K-'

-

0.200 0.202 0.212 0.233 0.253 1.386

1, 21

9, IO, 21

-

(0.87)

1, 11

(25.5) W.0 35.0 (39.2)

0.26 0.27 0.28 0.30 (0.278) 0.672 0.727

4, 8, 9 12,13, 21

(0.213)

-

(0.142) (0.142) 0.139 0.137 (0.137)

6.78 7.61 8.03 9.47 12.67 8.86 -0.0004

(0.203) (0.259) (0.259) (0.259) (0259) 0.820 0.810 0.790 0.761 (0.838)

-

-

-

(0.0575) (0.0575) (0.0575) (0.0575) 4.370 4.357 4.215 4.165 4.148 4.147 (4.36)

Referenee 1, 21

-

(0.404)

a m

(0.316) 0.370 0.450 0.565 0.810 1.125 1.570

19.7 20.2 20.8 20.2 18.3 16.1 4.0 165.6 166.1 170.1 176.3 180.4

(0.795) (0.142) (0.134) 0.398 0.398 0.398 0.398 (0.404)

Eiectrical resistivity

1, 7

-

(2.18) 0.905 0.940 0.957 1.033 1.600 3.77 -1000

1, 21

8,9, 14 21 1

1, 8, 21

(1.93) 0.323 0 0.3339 0.4361 (0.5131)

1, 21

53.0 51.7 47.7 37.8 24.4 15.5 (21.0)

0.136 5 0.154 0.215 0.444 (0.110)

1, 7

-

1.38 1.43 1.50 1.56

17,21

46.4 472

0.240 -

1, 7, 9

(42)

53.8

57.5 58.6 58.4 52.0

-

-

16,21

14-1 1

14-12

General physical properties

Table 143b THE PHYSICAL PROPERTIES OF LIQUID METALS-COiUi&

Element Mg

Mn

Mo Na

Temperature "C

650 700 800 lo00 124 2607

Nb

97 100 200 400 600 800 lo00 1 200 2468

Nd

1 024

Ni

454 44 327 400 500 600 800

p @lack) Pb

OOO

Po

254

Pr

935 1770

R Pu Ra Rb

640 960 38.8 100

si Sm

Sn

Electrical resistivity

Jg-'K-'

Wm-'K-'

a m

R&rence

0.274 0.277 0.282

4,5, 21

(1.36) (1.36) (1.36) (1.36) 0.838 0.57 1.386 1385 1340 1.278 1.255 1.270 (1.316) (1.405)

-

89.7 89.6 825 71.6 624 53.7 45.8 38.8

0.152 0.144 0.137 0.135

15.4 16.6 18.2 19.9

-

(0.238) (0.178)

(0.136) 0.398 0.383 0.364

119 630.5 700 800 lo00 1 539 217 1410 1500 1 600 1072 232 300 400 500 1 0

-

-

0.348 (0.378)

3 158 2427

78 81 88 100

-

0.232 0.620

500 1M)o

sc se

T

conduciivity

UX)

1500 Re Ru S Sb

Sp?C$C

heat

-

0.984 (0.258) (0.258) (0258) (0.258) (0.745) 0.445 1.04 1.04 1.04 (0.223) 0.250 0.242 0.241 (0.24) (0.26)

-

-

-

33.4 33.4 31.6 26.1 17.0 8.0

21.8 21.3 20.9

-

0.3

-

30.0 31.4 33.4 35.4

-

M

-

0.40

1, 9,21

(0.609

1,21

0.096 4 0.099

1, 7

0.134 0.224 0.326 0.469

-

(1.05) (1.26) 0.850 (2.70) 0.948 5 0.986 3 1.034 4 (1.rnS) (1.169) (1.263) (3.98) (1.38) (0.73) (1.33) (1.71) 0.2283 0.273 0 0.366 5 0.689 0 (1.71) (5.32)

(1.45) (0.84) > 10'0 1.135 1.154 1.181 1.235 (1.31)

*lob 0.75 0.82 0.86 (1.90) 0.4720 0.4906 0.5171 0.5435 (0.670)

1

1, 21 9,21 1 5, 16

1 1, 21 1, 21 1 1, 21

1, 7

1

1 2, 21

4, 9,21

1, 21 2, 18,21 1, 2, 14.

21 1, 21 5, 16,21

The physical properties of liquid metals

14-13

Tablo l 4 3 b THE PHYSICAL PROPERTIES OF LIQUID METALS-continued Temperature “C

specific kat Jg-’K-’

Thermal conductivity Wm-’ K-’

Electrical resistivity flm

770 (2996) 1 365

0.354

-

Ta Tb

-

-

(0.58) (1.18) (244)

Te

450

(0.295) (0.295) (0.295) (0.295) (0.295)

2.5 3.0 4.1 (6.2)

Element Sr

m 600 800 OOO

Ti

Tl

Tm U

V W

Y Yb Zn

685 303 400 500 600 133 200 1300 1912 3 377 1530 824 419.5 500

Zr

600 800 1850

(0.700)

-

-

5.50

4.80 4.30 (3.9) (3.8) (1.72)

Rderence

1, 21

1 1

5 9, 14 19,21

1. 21 9, 21

(0.377)

-

0.731 0.759 0.788 (1.88) 0.636 0.653 (0.678) (0.71) (1.27) (1.04)

-

-

(1.64)

1

0.481 0.48 1 0.481 0.481 (0.367)

49.5 54.1 59.9 (60.7)

0.374 0.368 0.363 0.367 (1.53)

5, 9

0.149 0.149 0.149

(24.6)

(0.161) (0.161) (0.161) (0.780)

-

-

-

1 20,21

1, 21 1 1, 21

1, 21

REFERENCES TO TABLE 14.3b 1. A. V. Grosse, Revue Hautes Temp. & Refrac., 1966,3, 115. 2. R. S. Allgaier, Phys. Rev., 1969, 185, 227. 3. 6. V. Samsonov, A. D. Panasyuk and E. M. Dudnik, Izu. Vuz. Tsuet. Met., 1969, 12, 110. 4. D.S. Viswanath and B. C. Mathur, Met. Trans., 1972,3, 1769. 5. C. Y. Ho, R W. Powell and P. E. Liley, NSRDS-NBS 16th February 1968. 6. G. R. B. Elliott, C. C. Herrick, et d.,High Temp. Sei., 1969, 1, 58. 7. J. Freund, ‘Thermophysicaland Nuclear Parametem of Molten Li,Na, K, Rb and Cs’, Inst. Kerntech. Tech. Univ. Berlin, 1969,(13),184. 8. G.Bush and J. Tieche, Phys. condens. Matter, 1963, 1, 78. 9. J. Wilson, Met. Rev., 1965,10,381. 10. I. A. Pavars, B. A. Baum and P. V. Gel’d, Zh.frz. Khim., 1969,43,2744. 11. Yn. P. Os’midin, Zh. jz. Khim, 1969,43,2610. 12 H.J. Guentherodt and H. U. Kuenzi, Phys. condens. Matter, 1969,10, 285. 13. M. J. Duggin, Phys. Lett., A, 1969,29,470. 14. V. M.Glazov, S. N. Chizhevskaya and N. N. Glagoleva, ‘Liquid Semiconductors’, Plenum Press, New York, 1969. 15. G.Busch et a)., Phys. Lett., A, 1970,31, 191. 16. H.A. Davies and J. S. Leach, Phys. Chem, Liquids, 1970,2, 1. 17. G. M. Kreig, R. B. Genter, and A. V. Grosse, Inorg. nucl. Chem. Lett., 1969,5, 819. 18. B. M. Mogilevsky and A. P h Chudnomky, Proc. Infernat. ConJ Phys. Semiconductors (Moscow), 1968, 2, 1241. 19. J. C.Perron. Phys. Lett., A, 1970,32, 169. 20. 6. Busch, H. J. Guentherodt and H.V. Kuenzi, Phys. Lett., A, 1970,32, 376. 21. D.R. Stull, and G. C. Sinke, ‘Thermodynamic Properties of the Elements’, Amer. chem. Soc., 1956: K.K. Kelley and E. G. King, ‘Contributions to Data on Theoretical Metallurgy’, X I V , US.Bur. Mines Bull. 592: R.Hultgren et al., ‘Selected Values of Thermodynamic Properties.’ Wiley, 1963.

14- 14

General physical properties

14.3 The physical properties of aluminium and aluminium alloys Table 14Aa THE PHYSICALPROPERTIESOF ALUMINIUM AND ALUMINIUM ALLOYS AT NORMAL lEMPERATuREs ~

~

SdCaa Y

Nom'nal composition Material

7%

AI

Al Al

AI-cu

cu a cu

AI-Mg

Mg Mg Mg Si Si

AI-Si

Si cSiu

Al-si-cu

cu

AI-Si-Cu-Mg*

si

AI-CU-Mg-Ni

Mg Cu

cu

2

(Yaw)

cu

Al-Cu-Fe-Mg

Fe Mg

Al- Si- Cu- Mg -Ni

Si

cu

O-Ex)

2 Si

cu Mg

Ni

d

O

Themull conduclivly 100°C Wm-lK-1

f

cxponslon

Densify

20-1OO'C g ~ m - ~ IO-~K-~

99.5 99.0 4.5 8 12 3.75 5 10 5 11.5 10 1.5 4.5 3 17 4.5 0.5

2.70 270 2.75 2.83 2.93 2.66 2.65 2.57 2.67 2.65 2.14

24.0 24.0 22.5 225 225 220 23.0 25.0 21.0 20.0 20.0

218

2.76 2.73

4

1.5 2 10 1.25 0.25 12 1 1 2 23 1 1 1

Resistivity

barn

MoaWus of elasticity m a xld 69

180 138 130 134 130 88 159 142 100

3.0 3.1 3.6 47 4.9 5.1 5.6 8.6 4.1 4.6 6.6

21.0

134

4.9

71

18.0

134

8.6

88

278

225

126

5.2

71

2.88

220

138

4.7

71

2.71

19.0

121

5.3

71

2.65

16.5

107

-

88

u)9

-

71

-

71 71

-

71

*Die cast.

Table 14.4b THE PHYSICAL PROPERTIES OF ALUMINIUM AND ALUMINIUM ALLOYS AT NORMAL TEMmuATuREs ~~

wrought

CorBScirnr

nmp.

~

Of

expansion

NoRiinol composition

Specification

%

1199

Al

Densify gcm-3

20-IQO'C 10-6~-1

Hlll H18

2.70

23.5

Hlll H18

270

23.5

Hlll H18

271

23.5

HI11 H18

2.71

23.5

T6

28 2.8

22 22

T3

277

23

T6

277

23

T8

259

23.6

T8

2.58

23.9

Condition* 99.992

Sheet EKrmded

lwlOA

Al

99.8

sheet

1200 2014A

Al

Al99

cu Mg

si

Mu 2024

CU

Mg

Mn 2090

cu Li

Zr 2091

99.5

cu Li

Shed ExtNded Sheel

T4

239 234 239 230

Resistivity p~cm 2.68 270 268 274 2.76

cocftof Moddusof resistance elasticity 2 0 - 1 0 0 ~ Mpax103 0.0042 0.0042 0.0042 0.0042 0.0042 0.0041 0.0041 0.0041 0.0041 0.0040 0.0040 0.0040

69 69 69

69 69

230

279 280

230 226 226 226 226 142 159

282

285 2.87 2.89 286 5.3 4.5

151

5.7 5.7

73 73

88.2

9.59

76

84

9.59

75

m

EXtNded

4.4 0.7

Wrn-1K-1

234

Enruded 1WA

conmMiviry 1oO'C

69 69 69

69 69 69

69 74

0.8

0.75 4.5 1.5 0.6 2.7

2.3 0.12 2.1

2.0

Series of alloy8 and steels

14-15

Table 14Ab THE PHYSICAL PROpERTlEs OF ALUMINIUM AND ALUMlNlUM ALLOYS Ar NORMAL TEr@E&xTuREs ~

Wrought Comient 100°C

Temp. C O G of Resistivity reaistancc

10-6K-1

Wm-l K-'

pQnan

20-100'C

MoalIulus of elashary m x 1 d

23.0

180

3.9

0,0030

69

151 109

4.8 6.1

0.0024

-

24.5

0.0019

71

24

155

4.7

0.0025

70

H1 11 H14 267

23.5 24

4.9 5.3 5.4 5.7 5.1

0.0023 0m21 0.0021 0.0019

H l l l 268

147 142 138 134 147

-

--

of expansion

NOm'MI

Specqicalion

compoaiiion 46 CWtiOn*

3103

Mn

1.25

gcm-

Hlll H12 H14 2.74 H16 H18

shed

5083

Mg

5251

Cr Mg Mu

EXrmded 4.5 Sheet 0.7 0.15 2.0 Shed 0.3

5154A

Mg

3.5

5454

Mg

27 0.75

Mu

Dendry 20-100'C

H l l l 2.67 1.112 H14 H l l l 2.69 H13 ni6

ExtIudfd sheet

ExtIuded

Mu

cu Al-W Al-Mg-Li

Al-Li-Mg 6061

6063 6063A 6082

2.0 3.0 2.0 Li 3.0 Me 2 0 i$ 1.0 0.6 CJ 0.2 Cr 0.25 M n 0.5 Si 0.5 Mg 0.5 Si 0.5

ME 1.0 Mu

6082

g;

6463

Mg

Al-Cu-Mg-Si (Duralumin)

2 Mn

Sheet

T6

2.46

Bar

K l l l 2.7 T4 2.7 T6 2.7

cu

2 ZU cu

Mn Mg Zn Ms Cu Cr Li CU

Mg

Zr

193 201 197 209

23.0

shed

Si

180 154 161

21

Sheet

0.6 0.4 0.6 shed 4.5 0.5 0.75 0.75 4.0 Forgings 1.5 2.0 12.0 Forgings 1.o 1.o 1.0 10.0 Forgiogs 1.o 0.7

-

23.6 236 23.6

2.70

T4 T6 T4 T5 T6 BarExtmded T4

4.0

Al-Si-Cu-Mg @-EX)

-

Bar

Si

Cu Mg Ni

-

ExtIuded

Cu

Al-Cu-Mg-Ni (YdOY)

8090

2.56 2.52

Bar

cu

7075

T6 T6

0.65 0.4

2 Mn

Al-Zn-Mg

n24

Sheet Sheet

1.0 0.7

;:;

-

70 70

H22

0.12

Li Me Li-

si

Sheet

ntermal co?ujucIrvq

T6

2.1 2.1

24 24 24 23 23

T4 T6 T5 T6 T6

2.69 2.7 1 2.71 280

23.0 23.4 23.4 225

T4 T6

2.81

T6 T6

201

172 184 188

193 209

mi

-

-

71 79 84 68.9 68.9 68.9

3.5 3.3 3.5 3.2 3.3 4.1 3.7

0.0033 0.0035

3.6 3.4

0.0033 0.0035

0.0031 0.0031

3.1

71

-

69 69 69 69 69

69

-

69 69 73

147

3.3 5.0

0.0023

225

147 159

53 4.5

0.0022 0.0026

73

2.78

22.5

151

4.9

0.0023

72

2.66

19.5

151

4.9

0.0023

79

291

23.5

151

4.9

0.0023

-

2.80

23.5

130

5.7

0.002Q

72

2.55

21.4

93.5

9.59

-

OA

5.7 Extmsior. 2.6 1.6 0.25 2 5 Plate 1.3 0.95 0.1

Hlll =A d e d . H12.22 = Quarier hard. H14.24 = Half hard. n16,26 = Tluee-quartem hard. Hl8.28 =Hard

T6

T4 = Solution treated ard naturally aged T6 = Solutim veafed and artificially aged.

77

14-1 6

General physical properties

Table 14.4b THE PHYSICAL PROPERTIES OF ALUMINIUM AND ALUMINIUM ALLOYS AT NORMAL TEMPERATURES-continued

Wrought Coeflcient

of

Spec$cation

Thermal Qmp. expansion conductivity coefi of Modulus of Density 20-100°C 100°C Resistivity resistance elasticity MPa x lo3 g ~ m 10-6K-' - ~ Wrn-lK-'

Nominal composition % Condition*

AI-Cu-Mg-Si Cu 4.0 Sheet (Duralumin) Mg 0.6 Si 0.4 Mn 0.6 Cu 4.5 Sheet Mg 0.5 Si 0.75 Mn 0.75

T F 2.80

22.5

147

5.0

0.002 3

73

TB 2.81

22.5

147 159

5.2 4.5

0.002 2 0.002 6

-

TF

73

Cu 4.0

Forgings

TF 2.78

22.5

151

4.9

0.002 3

72

Al-Si-Cu-Mg (Lo-Ex)

Mg 1.5 Ni 2.0 Si 12.0 cu 1.0 Mg 1.0 Ni 1.0

Forgings

TF 2.66

19.5

151

4.9

0.0023

79

Al-Zn-Mg

Zn 10.0

Forgings

2.91

23.5

151

4.9

0.002 3

-

Extrusion TF 2.80

23.5

130

5.7

0.002 0

72

Plate

21.4

cu 1.0

Mn 0.7 Mg 0.4 7075

8090

Zn 5.7 Mi3 2.6 cu 1.6 Cr 0.25 Li 2.5 Cu 1.3 Mg 0.95 Zr 0.1

'O=AUnealed. H12,22=Quarter hard. H14,24=HaIf hard. H16,26=Three-quarters hard. H18.28 =Hard.

2.55

93.5

9.59

77

T4=Solution treated and naturally aged. T6=Solution treated and artificiauy aged. See also pp. 22-1 and 22-2.

14.4 The physical properties of copper and copper alloys Table 14.5 THE PHYSICAL PROPERTIES OF COPPER AND COPPER ALLOYS AT NORMAL TEMPERATURES Melting point of liquidus

"c

Co&cient Electrical of expansion conductiuity Thermal 25-300°C 20°C conductivity Wm-'K-' Refs. %IACS* 10-6K-'

Material

Composition Yo

Density g~rn-~

conductivity high copper

a

8.94

1083

17.7

101.5

399

1

Tough pitch HC copper Phosphorus-deoxidized non-arsenical copper Deoxidized arsenical copper

0, 0.03 P 0.005-0.012 PO.0134.050 P 0.03 As 0.35 0, 0.02 Ag 0.05

8.92 8.94 8.94

1083 1083 1083

17.7 17.7 17.7

101.5 85-96 70-90

397 341-395 29&372

2,3,4 5 5

10.82

17.4

45

177

2

1079

17.7

101

397

Silver bearing copper

*,99+

8.94

x.92

The physical properties of copper and copper OIIOYS

14-17

T&b 145 THE PHYSICAL PROPERTIES OF COPPER AND COPPER ALLOYS AT NORMAL TEMPERATUREScontinued

Composition Material

%

Tellurium copper

c u 99.5 Te 0.5

Chromium copper Bery'ilium copper

cu Cr

99.4 0.6

Melting point of Density liquidus g ~ m - ~"C

C&cient Eieetrieal of expansion eonduetiuity Thermal 25-300°C 20°C conductivity

8.94

1082

17.7

8.89

1081

8.25

10-6K-1

%IACS*

Wrn-'K-'

Refs.

98

382

2

17

491' 82'2'

167 188

6

lo00

17

84 105 126 210

7

Be

1.85

Co

025

Be

0.5 2.5

8.75

1060

17

17'" 23"' 23"' 47"'

Cadmium copper

Cu 99.2 Cd 0.8

8.94

1080

17

85

376

6

Sulphur copper

Cu 99.65 S 0.35

8.92

10.75

11

95

373

5

f i P copper

c u 95 Zn 5

8.85

1065

18.1

56

234

5

8.80

1040

18.2

44

188

5

8.75

lOz0

18.7

37

159

5

8.65

loo0

19.1

32

138

5

8.55

965

19.9

28

121

5

8.50

940

20.2

27

121

5

8.45

920

20.5

26

125

5

8.40

900

20.8

28

126

5

Co

Gilding metals CuZnlO CuZn15 CUzn20

Brass CuZn30

Cu Zn Cu Zn Cu zn

90 10 85 15 80 20

Cla Zn Cu Zn

70 30 61 33 Cu 63 zn 37 Cn 60 Zn 40

CuZn33 CuZn37 CuZn40

7

Aluminium brass CUzdZAlz

Cu 76 Zn 22 A1 2

8.35

1010

18.5

23

101

5

Naval brass CuZn36Sn

Cu 62 Zn 31 Sn 1

8.40

915

21.2

26

117

5

Free cutting brass CuZn39Pb3

c u 58 Zn 39 Pb 3

850

900

20.9

26

109

3,5

c u 58 Zn 40 Pb 2

8.45

910

20.9

26

109

3.5

990 approx.

21 approx.

20-25

88-109

5

8.60

1010

16.4

8.31

31

8.9

8.64

1025

16.2

1.71

30

8-9

8.69

1060

16.2

7.01

27

8,9

8.72

1100

16.0

6.3

28

8.9

8.82

1160

17.0

5.1

21

8.9

Hot stamping brass CuZn4OPb2

High tensile brass Nickel silver 10% 12% 15%

18%

Cu 54-62 Others 7 max. 8.3-8.4 Zinc-balance Cu Ni Zn Cu Ni Zn Cu Ni Zn Cu Ni

25%

zn Cu Ni Zn

62 10

28 62 12

26 62 15 23 62 18 20 62 25 13

14-18

General physical properties

Table 145 THE PHYSICAL PROPERTIES OF COPPER AND COPPER ALLOYS AT NORMAL TEMPBRATUcontinued ~

Comp'tion

Density

Material

Yo

gcm-3

"C

of expansion conductivity Thermal conductivity 25300°C 20°C Wm-'K-' Ref. W6K-' %IACS*

Phosphor bronze CuSn3P

Sn P Sn P Sn P Sn P

3.5 0.12

8.85

1070

18.8

18.8

85

5,lO

8.85

1060

18.0

16.8

75

5,lO

8.80

1050

18.5

14.0

67

5,lO

8.80

1040

18.0

14.0

63

10

Ni Fe Mn Ni Fe Mn Ni Fe Mn

5.5 1.2 0.5 10.5 1.5 0.75 31.0 1.0

8.94

1121

17.5

12.5

67

11

8.94

1150

17.1

8.0

42

11

8.90

1238

16.6

4.5

21

11

8.52

lo28

18.0

8.1

50

5

8.15

1065

18.0

17.7

85

2

7.8

1045

17.0

14.0

0

5

7.57

1060

17.0

13

62

5

CnSn5P CuSn7P CuSn8P Copper-nickel CuNi5Fe CuNilOFeMn CuNi30FeMn Silicon bronze Aluminium bronze CuA15 CuAl8Fe

CuAllOFe5NiS

5

0.09 7 Q.12 8 0.05

Coefficient

Electrical

Melting point of liquidus

1.0

Si 3 Mn 1 c u 95 5 cu 9 A I 8 Fe 2 A1 9.5 Fe 4.0 Mn 1.0 Ni 5.0

A1

*The International Annealed Copper Standard is material ofwhich the resistance of a wire 1 metre in length and weighing 1 grain is 0.15328ohm at 20°C. 100% IACS at 20°C=58.00MSm-'. (1) Solution heat treated. (2) Fully heat treated (to maximum hsrdness).

REFERENCES TO TABLE 14.5 1. OFHC" Copper-Technical Information, America1 Metal Climax Inc., 1969. 2. R. A. Wilkins and E. S. BUM, 'Copper and Copper Base Alloys', New York, 1943. 3. C. S. Smith, Tmns. AIMME, 1930,89, 84. 4. C. S. Smith, Trans. AIMME, 1931,93, 176. 5. Copper Development Association, Copper and Copper Alloy Data Sheets, 1968. 6. Copper Development Association, High Conductivity Copper Alloys, 1968. 7. Copper Development Association, Beryllium Copper, 1962 8. M.Cook, J . Inst. Metah, 1936, 58, 151. 9. I n t q a t i o n d Nickel Limited, Nickel Silver Engineering Properties, 1970. 10. M. Cook and W. G. Tallis, J . Inst. Metals, 1941, 67, 49. 11. International Nickel Limited, Cupronickel Engineering Properties, 1970.

14.5 The physical properties of magnesium and magnesium alloys Table 14.6 THE PHYSICAL PKOPERTiFS OP SOME MAGNESNErP AND MAGNESIUM ALLOYS AT NORMAL ll3MPERATuRE

cm of

Nominal cotnpositiont Maierial

Density ai 20'C g~rn-~

Melting point "C Sol. Liq.

99.97 T1 0.75 approx. T1 1.5 T1

1.74 1.75 1.76

650 650 650

651 651

27.0 26.9 26.9

167 146 142

3.9 5 5.0

0.75 approx. T1

1.75

630

640

26.5

117

Condition

90

~

Pure Mag Mg-Mn

Mg-Al-Zn

Mg (MN70)Mn

ALSOAI Be (AZ31)Al

Weldabiliv by argon arc processs

Relative damping capacitys

1050 1050 1050

A A A

C

6

1050

A

10.0

1050

A A

C

A

C

A

pQcm

Spcc@c heat

20-200" C Jkg-' K-'

3

T1

1.78

575

630

26.0

8

AC AC T4 AC AC T4 AC T6 T1

1.81 1.81 1.83 1.83 1.83 1.80

475* 600

84 84

13.4

47V 595

84 84 84 79

14.1

610

27.2 27.2 27.0 27.0 21.0 27.3

14.3

lo00 lo00 lo00 lo00 lo00 14OOO

T1

1.80

475* 600

27.2

19

14.3

1000

T1

1.78

1'1

1.80

625

645

27.0

134

5.3

lo00

A

T1

1.80

600

635

27.0

125

5.5

960

C

AC T6

1.81

560

640

27.3

113

6.6

960

C

T5

1.83

530

630

26.0

117

6.0

1050

C

Zn

0.5

(AZ91)AI

9.5

(AZM)Al Zn (AZ855)Al Zn (ZM21)Zn Mn (ZW1)Zn

6 1 8 0.5 2

zn 0.5

Mg-Zn-Zr

Electrical resistivity

0.05

zn 1

(A8)AI

Mg -Zn-Mn

K-'

Thermal conduciivity Wm-' K-'

~

(AM503)Mn Mg-AI

thermal expansion 20-200°C

zr

(ZW3)Zn Zr (Z5Z)Zn

Zr (ZW6)Zn

Zr

510

-

-

-

2

A

A

27.0

1

1.3

A

0.6

3 0.6

4.5 0.7 5.5 0.6

c P I c \o

continued overleaf

Table 14.6 THE PHYSICAL PROPERTIES of SOME MAGNEsRlM AND MAGNESIUM ALLOYS AT NORMAL 1BMpERA'IuRE- continued CWlT

Nominal compositiont Material

Mg-Y-RE-Zr

Mg-RE-Zn-Zr

Mg-'Ih-Zn-ZiC*

w

P

I N 0

of

thermal expansion 20-200°C

Condition

Density Meltin8 point at20T "C g ~ m - ~ Sol. Liq.

(WE43)Y 4.0 RE(A) 3.4 Zr 0.6

AC T6

1.84

(wES4)Y 5.1 RE(A) 3.0 Zr 0.6 (ZRE1)RE 2.7 ZN 2.2 Zr 0.7 (RZ5)Zn 4.0 RE 1.2 Zr 0.7 (ZE63)Zn 6 RE 2.5 Zr 0.7 (2lY)Th 0.8 zn 0.5 Zr 0.6

AC T6

1.85

550 640

24.6

52

17.3

960

A

AC Ts

1.80

545 640

26.8

100

7.3

1050

A

AC T5

1.84

510 640

21.1

113

6.8

960

B

AC T6

1.87

515 630

21.0

109

5.6

960

A

T1

1.76

600 645

26.4

121

6.3

960

A

%

550 640

K-l 26.1

Thermal conductivio Wm-' K-'

51

Electrical resistiviry M S cm ~

14.8

Specqi heat 20-200°C Jkg-' K-I

966

Weldabiliry by argon arc pmcesst

Relative

damping capacity5

2

b

2. Q

A

b

a

2

3.

B

2 % I

3 (b

3

Mg-Ag-RE-Zr

Mg-Zn-Cu-Mn

(ZT1)Th 3.0 Zn 2.2 Zr 0.7 (TZ6)zn 5.5 Th 1.8 Zr 0.7 (QE22)Ag 2.5 W D ) 2.0 Zr 0.6 (EQ21)RE(D) 2.2 Ag 1.5 cu 0.07 Zr 0.7 (ZC63)Zn 6.0 Cu 2.7 Mn 0.5 (ZC71)Zn 6.5 Cu 1.3 Mn 0.8

MG-Ag -RE - **

m-zr

(QH21)Ag RWD) Th Zr

Mg-Zr

2.5 1.0 1.0 0.7 (ZA)Zr 0.6

AC Sand cast. T4 Solulion heat treated

AC T5

1.83

550 647

26.7

105

7.2

AC "5

1.87

500 630

21.6

113

6.6

AC T6

1.82

550 640

26.7

113

6.85

AC T6

1.81

540 640

26.6

113

6.85

AC T6

1.87

46.5

600

26.0

122

5.4

962

B

T6

1.87

465 600

26.0

122

5.4

62

B

.a

za

AC T6

1.82

540 640

26.1

113

6.85

1005

A

AC

1.75

650 651

27.0

(146)

(4.5)

1050

A

%

T1 Extmded, mUed or forged.

T6 Puuy heat treated.

RE Cednm miscbmetalmntaining qpmL 50% Ce. * Non-equilibrium solidus 42Q'C. 0 Estimated value.

t Mg-A

JW@) Miscbmeial enriched in

TS Precipitation heat teated.

-

weldability rating:

A

8 Damping capacily rating:

A Fully weldable.

A Outsranding.

B Weldable.

B Etquident to cast imn.

C Not recommended where

fusion welding is involved. type ~ O Y SM ~ Y contain 0 . 2 - O M Mn to improve wrmsion resistance. ** Thorium containing alloys are being replacad by allemativc Mg alloys.

nmdynium.

RE(A) Neodynium t Heavy Rare Farh

il

e3

5. ii

P

Q

il

OQ

C Inferior to cast imn but better than A-base Caa alloys.

-$

E'

I

w 9 I

c!

W22

General physical properties

14.6 The physical properties of nickel and nickel alloys Table 14.7 THE PHYSICAL PROPERTIES OF WROUGHT NICKEL AND SOME HIGH NICKEL ALLOYS AT ROOM TEMPERATURE

Alloy*

%

Coeflcient of expansion Specific Thermal heat conductiuity Density 20-100°C ~ C I I - ~ 10-'K-' Jkg-'K-'Wm-' K-'

Nickel

99.4 Ni

8.89

13.3

456

74.9

9.5

Nickel 205

99.6 Ni

8.89

13.3

456

75.0

9.5

Monelt alloy 400

30 Cu 1.5 Fe 1.0 Mn

8.83

13.9

423

21.7

51.0

Monel450

31.0 Ni 0.7 Fe Rem. Cu

8.91

15.5

380

29.4

41.2

Monel alloy K-500

29 Cu 2.8 A1 0.5 Ti

8.46

13.7

419

17.4

61.4

Cupro-nickel

55

cu

8.88

14.9

42 1

19.5

52.0

Inconelt alloy 600

16 6

Cr Fe

8.42

13.3

460

14.8

103

60.5 23.0 1.4 15.1

Ni

Inconel 601

8.11

13.75

448

11.2

119

Ni Cr

Inconel 617

55.7 21.5 12.5 9.0 1.2 0.1

8.36

11.6

419

13.6

122

Inconel alloy 625

22 4 9

Cr Nb Mo

8.44

12.8

410

9.8

129

Ni Cr Fe

Inconel 718

52.5 19.0 18.8 5.2 3.1 0.9 0.5

8.19

13

435

11.4

125

825

12.6

425

12.0

122

8.3

12.2

14.26

107.5

8.08

14.9

460

12.4

101.7

8.05

14.7

500

12.3

108

Nominal composition

Cr AI Fe

co Mo A1

c

0.3 Ti 0.3 A1

Nb Mo Ti A1

Cr 7 Fe 2.5 Ti

15

Inconel alloy X-750

Electrical resistivity pcm

Inconel MA 754

78.0 20.0 1.0 0.6

Ni Cr Fe Y203

INCO 330

35.5 44.8 18.5 1.2

Ni Fe

INCO 020

35.0 38.4 20.0 3.5 2.5 0.6

Ni Fe Cr cu Mo Nb

Cr Si

0.6 A1 0.8 Nb

The physical properties of nickel and nickel alloys

14-23

Table 14.7 THE PHYSICAL PROPERTIES OF WROUGHT NICKEL AND SOME HlGH NICKEL ALLOYS AT ROOM TEMPERATURE-continued

Alloy*

Coeflcient of expansion

Nominal composition Yo

Density 20400°C g ~ m - 10-6K-1 ~

Specifc Thermal heat wnductiuity 3ka-IK-l Wm-' K-'

Electrical resistivity

dcrn

49.0 Ni

INCO G-3

INCO 6-276

INCO-HX

22.5 19.5 7.0 2.0

Cr Fe Mo cu

8.3

12.2

59.0 16.0 15.5 5.5 4.0

Ni Mo Cr Fe W

8.89

12.2

48.3 22.0 18.5 9.0 1.5

Ni Cr Fe 8.23

Mo

14.26

107.5

427

9.8

122.9

13.3

461

11.6

116

1.95

142.

460

11.5

93

814

14.0

441

11.1

113

1.91

14.2

450

12.0

108

8.10

7.6

502

12.1

101

9.22

10.3

373

11.1

137

8.64

10.8

406

10.1

125

8.23

13.8

485

9.1

118

CO

0.6 W

0.1

c

45 Fe 21 cr 0.4 Ti

Od AI

Incolay alloy 825

32 21 3

Fe Cr Mo

2 cu 1.0 Ti

Incoloy alloy DS

40 18 2

Fe Cr %

Ni Span? alloy C-902

41

Fe

Incoloyt alloy 800 : Incoloy alloy 800 H

0.5 Al

5.5 Cr

2.5 Ti Haste.loy B 2

28

Mo

Hastelloy C 4

16 16

Mo

Hastelloy alloy X

9 21 18

Cr

Mo

cr Fe

Nimonict alloy 75

20 Cr 0.4 Ti

8.37

11.0

46 1

11.7

102

Nionic alloy 80A

20 Cr 2.0 Ti 1.5 AI

8.19

12.7

460

11.2

117

Nimonic alloy 81

30 Cr 1.8 Ti 1.0 AI

8.06

11.1

461

10.9

127

20 Cr 17 c o 2.4 Ti

1.4 A1

Nimonic alloy 90

8.18

12.7

445

11.5

114

Nimonic alloy 105

15 20 5

Cr co Mo

5 A l 1.2 Ti

8.01

12.2

419

10.9

131

14 13

Cr Co Mo

5 4

1.85

12.0

444

10.6

139

Nimonic alloy 115

3

AI Ti

14-24

General physical properties

PHYSICAL PROPERTIES OF WROUGHT NICKEL AND SOME HIGH NICKEL ALLOYS AT ROOM TEMPERAmRE-continued

Table 14.7 THE

Co~cient of expansion Speclfic Thermal Denary 2&100"C heat conductivity g ~ r n - ~10-6K-' J k g - l K - l W m - l K - l

Electrical

8.36

11.1

461

11.7

115

8.16

13.5

419

-

-

8.02

11.3

544

11.7

110

18.0 Cr 14.0 Co 7.0 Mo 2.25 Ti 2.1 AI

8.21

12.1

419

11.3

126

54.8 Ni 15.0 Cr 17.0 Co 5.3 Mo 4.0 A1 3.5 Ti

7.91

Nominal composition Alloy*

%

20 20 6

Cr

Nhonic alloy 263

13 35 6

Cr Fe Mo

3 Ti

Nimonic alloy 901

16 32 3

Cr

Nimonic aUoy PE16

1.0 Ti 1.0 AI

Nimonic PK33

Astroloy

Rene 41

Rene 95

Co Mo

Fe

2

Mo

55.4 19.0 11.0 11.0 1.5 3.1

Ni Cr

61.5 14.0 8.0 3.5 3.5 3.5 2.5

Ni

co Mo

8.25

9

130.8

Al' Ti Cr

Co

Mo

8.7

Nb

A1 Ti

Udimet 500

53.7 Ni 18.0 Cr 18.5 Co 4.0 Mo 2.9 A1 2.9 Ti

Ni Cr

Udimet 700

55.5 15.0 17.0 5.0 4.0 3.5 58.7 19.5 13.5 4.3 1.3 3.0

Ni

Waspaloy

Ti 0.5 Al

resistivity Qcm

Co Mo

8.02

11.1

7.91

19.6

8.19

10.7

120.3

AI Ti Cr

Co Mo

124

A1 Ti

* Where trade marks apply to the name of an alloy there may be materials ofsimilar composition available from other producers who may M may not

use thesamesuffixalong withtheirowntradenamckThesuffixaloneegAUoy800issometimcsusedarsdescriptivc termfor

the type ofalloy but trade m a r k s can be used only by the registered user d t h e mark.

t Registered Trade Mark. t A variant on alloy 800 having 000troUed earboo and h a t traatmmt to givc s i g n i k t l y improved creepmptw strength.

The physical properties of titanium and titanium alloys

14-25

14.7 The physical properties of titanium and titSnium alloys Table 1 4 8 PHYSICAL PROPERTUB OF TITANRlM AND TlTANNM Ways AT NORMAL

Temp.

coe@cient Themull

of Material

IMI

Nominal wm@tion

&signation 9%

IMI230 Cu 2.5 IMI 260/261 Pd 0.2 IMI 315 Al 2.0 Mu 2.0 IMI 317 A1 5.0 Sn 2.5 IMI 318 AI 6.0 V 4.0 IMI550 Al 4.0 Mo 4.0 Sn 2.0 Si 0.5 JMI 551 Al 4.0 Mo 4.0 Sn 4.0 Si 0.5 IMI 679 sn 11.0 Zr 5.0 A1 2.25 Mo 1.0 Si 0.2 J M I 680 Sn 11.0 Mo 4.0 Al 2.25 si 0.2 IMI685 A1 6.0 Zr 5.0 Mo 0.5 Si 0.25 MI 829 Al 5.5 sn 3.5 zr 3.0 Nb 1.0 Mo 0.3 Si 0.3 IMI 834 Ai 5.8 Sn 4.0 zr 3.5 Mb 0.7 Mo 0.5 Si 0.35 C 0.06

of

con-

spec* heat

Magnetic suscepr.

expansion ductivity Resistivity resistivity 10-6 Densify 20-100T 20-100°C 20'C 20-100°C 50°C Cgs units gcm-' K-l W mdl K-' pC2cmK-' Jkg-l K-' g-l

man

7.6

16

48.2

0.0022

528

+3.4

4.51

9.0 7.6 6.7

13 16 8.4

70 48.2 101.5

0.0026 0.0022 0.0003

528 460

+4.1

4.46

7.9

6.3

163

0.0006

470

+3.2

4.42

8.0

5.8

168

O.OOO4

610

+3.3

4.60

8.8

1.9

159

0.0004

-

-

4.62

8.4

5.7

170

0.m

400

+3.1

4.84

8.0

7.1

163

0.m

-

-

4.86

8.9

1.5

165

0.0003

-

-

4.45

9.8

4.8

167

O.ooo4

-

-

4.53

9.45

7.8

-

-

530

-

455

10.6

CP Titanium CommerciaUy 4.51 Pure

wefjcient

4.56 4.52

--

14-26

General physical properties

148 The physical properties of zinc and zinc alloys Table 149 PHYSICAL PROPERTlES OF ZINC AND ZINC ALLOYS Electrical conductiuity Coefficientof Thermal expanswn conductivity % IACS K-' Wm-' K-' 20'C Condition

Melting polnt (liquidus) "C

Material

Nominal composition

Density gcm-'

Zn

99.993% Zn

1.13 39.7 (25°C) (20-250°C)

113

28.27

4% AI 0.04% Mg

6.1

21 (20-100T)

113

27

21 (20-1Oo0C)

109

26

Pressure die cast

28

115

28.3

Chill cast 432

26

123

29.7

Chillcast 487

~~

Polycrystalline ZnAlMg BS1004A

ZnAlCuMg BS1004B ZnAlCuMg I U R O 12 (ZA12)

W

I

4%AlI%Cu 0.04% Mg 11%AI 1% Cu 0.02% Mg 27% AI 23% Cu 0.015% Mg

6.7

6.0

5.0

c2o-roo "C)

Cast

419.46

Pressure

387

die cast

388

(20-100°C)

149 The physical properties of zirconium alloys Table 14.10 PHYSICAL PROPERTIES OF ZIRCONIUM ALLOY ~

Composition Alloy

%

Zirconium 10

Commercially Pure Cu 0.55 Mo 0.55

coe$icieni of expansion 20-100°C

Elecnicol resistivity Pcm

Density g~rn-~

Thermal c o d . at 25°C Wm-'K-'

6.50

21.1

5.04

-

6.55

25.3

5.93

-

~

Zirconium 30 Zircalloy I1

Sn Fe Cr Ni

1.5 0.12 0.10 0.05

6.55

12.3

5.61

-

Zr 102

Commercially pure with up to 4.5 Hf Cr Fe 0.244 sn 1-2

6.51

22

5.89

39.1

+

6.57

-

Zr 705

Nb 2.5

6.64

17.1

6.3

55

Zr IO6

0, 0.18 Nb 2.5

6.64

17.1

6.3

55

Zr IO4

0, 0.16 See also Table 26.36 page 16-52.

14.10. The physical properties of pure tin Melting point Boiling point Vapour pressure at 727°C 1127°C 1527°C Volume change OF freezing Expansion on melting Phase transformation Density at 20°C Specific heat at uI"C

aeB

231.9"C 2270°C 7 . 4 ~10-6mmHg mm Hg 4.4 x 5.6mmHg 2.7% 2.3% 13.2"C 7.28 g/cm3 222Jkg-IK-'

The physical properties of steels

1427

59.6 kJ kg-' 2497Jkg-' 23.5 x K66.8 W rn-l K-' 15.6 IACS 12.6pQcm

Latent heat of fusion

Latent heat of evaporation Linear expansion coefficient at O-lWC Thermal conductivity at 0-100°C Electrical conductivity at 20°C Electrical restivity at 20°C Temperature coefficient of electrical resistivity at 0-100°C Thermal EMF against platinum cold junction at 0°C hot junction at 100°C Superconductivity, critical temperature ( Viscosity

0.0046K-'

+0.42mV 3.122 K 0.01382 poise at 351°C 0.01148 poise at 493°C 548 mN m- at 260°C 529nMm-I at 500°C

Surface tension Gas solubility in liquid tin: Oxygen at 536°C Oxygen at 750°C Hydrogen at 1OOO"C Hydrogen at 1300°C Nitrogen

0.00018% 0.0049% 0.04% 0.36% Very low

14.11 The physical properties of steels TaMe 1411 PHYSICAL PROPERTIES OF STEELS Thermal properties (see N o m ) -

Material and condition Cotnposition

70

Temperature "C

Specific gravity gcm-3

Specifc heat K-1

CoPificient of thermal Thermal Electrical expunsion . conductivity resistivity 10-6 K - ! w m-' K - 1 pncm

-

-

48.2 520 595 754 a75 -

12.62 13.08 13.83 14.65 14.72 13.19

-

-

J kg-'

Carbon steels RT lop 200 400 600 800 1 000

Mn 0.4 Annealed

RT 100 200 400 600 800

Mn 0.31 Annealed

7

.ai

7.86

1 000

Mn 0.6 ,4nnealed

MA22

RT 100 200 400 600 800 1OM)

7-86

482 523 595 141 960

-

12.19 12.99 13.91 14.68 14.79 13.49

-

-

486 520 599 149 950

12.18 12.66 13.47 14.41 12.64 13.31

-

65.3 60.3 54.9 45.2 36.4 28.5 21.6

12.0 17.8 25.2 44.8 12.5 107.3 116.0

59.5 57.8 53.2 45.6 36.8 28.5 27.6

13.2 19.0 26.3 45.8 73.4 108.1 116.5

51.9 51.1 49.0 42.7 35.6 26.0 21.2

21.9 29.2 48.7 75.8 109.4 116.7

15.9

Notes: 1. Where specifrc heats are quoted at temperatures above RT the values have been determined over a range of 50 C u p to the temperature quoted. 2. Coefficients of expansion are mean values from RT up to the temperature quoted. 3 Elecrricul rrsistiidtp values are uncorrected for dimensional changes of the specimen with temperature. Original dimensions as a1 RT.

14-28

General physical properties

Table 1411 PHYSICAL PROPERTIES OF STEELS-continued Thermal properties (see Notes) Material and condition Composition

% C 0.42 En 8 Mn 0.64}060A42 Annealed

C

Mn

t!;}

Annealed

Mn

0.35

Annealed

gcm-3

K-I

Coefficient of thermal Thermal expansion conductivity 10-6 K - I w m - l K - I

RT 100 200 400 600 800 lo00

7.85

-

-

486 515 586 708 624 -

11.21 12.14 13.58 14.58 11.84 13.59

RT 100 200 400 600 800 lo00

7.85

-

-

490 532

11.11 11.72 13.15 14.16 13.83 15.12

RT 100 200

7.83

Temperature "C

Specijic gravity

1

607

-

400 600

Annealed

Mn 0.61 Ni 0.12 Annealed

RT 100

7.85

200 400 600 800 lo00

0 100 200 400 600 800 lo00

J kg- '

712 616

800 loo0

C 0.23 En 14 Mn 1.51 150M19

Specijic heat

-

-

486 540 599 699 649

-

10.6 11.25 12.88 14.16 14.33 16.84

-

-

477 511 590 741 821

11.89 12.68 13.87 14.72 12.11 13.67

-

7.84

Electrical resistivity pR cm

51.9 50.7 48.2 41.9 33.9 24.1 26.8

16.0 22.1 29.6 49.3 16.6 111.1 122.6

47.8 48.2 45.2 38.1 32.7 24.3 26.8

17.0 23.2 30.8 50.5 77.2 112.9 119.1

45.2 44.8 43.5 38.5 33.5 23.9 26.0

18.4 25.2 33.3 54.0 80.2 115.2 122.6

46.1 46.1 44.8 39.8 34.3 26.4 27.2

19.7 25.9 33.3 52.3 78.6 110.3 117.4

435 494 528 599 754 833 657

16.3 22.6 29.6 48.2 14.2 110.0 119.4

Low alloy steels

1 I

0.40 1%Ni Mn 0.67 En 12 Ni 0.80 Hardened 850°C OQ Tempered 600°C (Ih) OQ C

C 0.37 Mn-Mo Mn 1.56 En 16 Mo 0.26 605A37 Hardened 845°C OQ Tempered 600°C (lh)

RT

7.85

100

200 400

600 RT 100 200 400 600

7.85

*-

-

-

486 507 544 586

11.90 12.55 13.75 14.45

49.4 46.9 40.6 34.8

t

-

-

456 417 532 599

12.45 13.20 14.15 14.80

48.2 45.6 39.4 33.9

21.9 26.4 33.4 52.0 71.5 25.4 30.6 39.1 60.0 88.5

Notes: * Where a group is marked with an asterisk the Values are a mean from RT up to the temperature quoted. 1. Where specijic heats are quoted at temperatures above RT the values have been determined over a range of 50°C up to the temperature quoted. 2. Coefficientsof expansion are mean values from RT up to the temperature quoted. 3. Electrical resistivity values are uncorrected for dimensional changes of the specimen with temperature. Original dimensions as at RT.

The physical properties of steels

14-29

T a b 1411 PHYSICAL PROPERTIESOF STEELs--eontfnued Thennalpperties (= N e )

Moteriol and condition Composition

Temporoturc

%

"C

Hardened 850°C OQ Tempered 620°C (lh)OQ

Anwaled

C 0.39 1%Cr Mn 0.79 En 18D

}

Cr

1.03 530A40 Hardened 8 W C OQ Tempered 640°C(Ih) OQ

C Mn Si Cr Mo

1

0.28i0.33 0.4/0.6 0.2/0.35 0.8/1.1

1% Cr-Mo

0,15/0.25 HIardened and tempered

Mo 023 Hardened 850°C OQ

Sp.eiFc gramty, gcm-

RT 100 200 400 600

7.85

RT 100 200 400 600 800 loa0

7.84

RT 100 200 400 600

7.85

0 RT 100 200 300 400 500 600 700 800 loo0 1200

speeijic co&zient heat ofthermal Thermal Jkg-' expansion conductivity K-' 10-6K-1W m - ' R-' 8-

-

-

482 494 519 595

12.45 13.00 13.90 14.75

45.6 44.0 39.4 33.9

-

-

494 523 595 741 934

48.6 46.5

-

12.16 1283 13.72 14.46 1213 13.66

8-

-

-

452 473 519 561

1235 13.05 14.40 15.70

44.8

7.85

RT 100 200 400 600

7.85

28.1

43.5 37.7 31.4 42.7

-

477 515

42.7

-

40.6

-

595 657 737 825 883

7.83

26.0

-

544

RT 100 200 400 600

44.4 38.5 31.8

*-

473 519 561

37.3

-

31.0

-

28.1 30.1

-

-

1225 1270 13.70 14.45

427 423 37.7 33.1

-

-

12.3 12.6 13.7 14.4

-

41.9 41.9 38.9 32.7 26.0

-

-

12.5 12.9 13.5 14.0

31.1

Ekctricul resiptiuity pshll

22.5 27.2 34.3 52.5 77.5 20.0 25.9 33.0 51.7 77.8 110.6 117.7 22.8 28.1 352 53.0 78.5

22.3 27.1 34.2

52.9 78.6 110.3 117.1 122.2

22.2 26.3 32.6 47.5 44.6

Tempered 600°C (Ih) OQ

Cr

1.1 Mo 0.7 Hardened and tempered

800

M o 0.8

v

0.2

RT 100 200 400 600

7.83

-

-

37.7 34.8 31.0

Hardened and tempered

Notes: *The values are a mean from RT up to the temperature quoted. 1. Where spscific heats are quoted at temperatures above RT the values have been determined over a range of 50°C up to the temperature quoted. 2 Co&cienrs sf expansion are mean valw from RT up to the temperature quoted. 3. E[ecnicol resistivity values are uncorrected for dimensional changes of the specimen with temperature. Original dimensions as at RT.

General physical properties

14-30

Table 14.1 1 PHYSICAL PROPERTlES OF STEELS-2Ontinued Thermal properties (see Notes) Material and condition Composition

%

__

Ni 0.20 Cr 0.88 Mo 0.20 Annealed

I

C Mn Si Cr

0.23 0.45 3%Cr-W-Mo-V 0.45 2.87 W 0.59 Mo 0.51 V 0.77 Hardened and tempered

c

1

0.32 3% Ni

Mn 0.55 En 21 Ni

Ni Cr

Temperature "C

3.47 Annealed

3.4 0.8 Hardened and tempered

Mo 0.26 Hardened 8 3 0 T OQ Tempered 630°C (lh) OQ

Mo 0.51) Hardened 830°C OQ Tempered 650°C OQ

C 0.34 3% Ni-C-Mo Mn 0.54 En 27 Ni 0.76 Cr 3.5.)

Mo 0.39 Hardenefl and tempered

Specific gravity g

RT 100 200 400 600 800 1000

7.84

RT 100 200 400 600 800

7.83

RT 100 200 400 600 800 1000

7.85

RT 100 200 400 600 800 lo00

7.85

RT 100 200 400 600

7.84

RT 100 200 400 600

7.85

RT 100 200 400 600 800 lo00

7.86

Specific heat J kg-

K-'

Coeflcient of thermal Thermal Electrical expansion conductivity resistivity K-' W m - l K-' pRcm

-

-

477 515 595 737 883

12.67 13.11 13.82 14.55 11.92 13.86

'

-

11.9 12.4 13.1 13.6 14.1

-

-

482 523 590 749 604

-

11.20 11.80 12.90 13.87 11.10 13.29

-

-

494 523 599 775 557

11.36 12.29 13.18 13.72 10.69 13.11

-

42.7 42.7 41.9 38.9 33.9 26.4 28.1

21.1 27.1 34.2 52.9 78.6 110.3 117.1

38.5 33.6 33.1 30.6 29.3 28.9

35.5 39.0 46.2 63.0 85.4 -

36.4 37.7 38.9 36.8 32.7 25.1 27.6

25.9 32.0 39.0 56.7 81.4 112.2 118.0

34.3 36.0 36.8 36.4 31.8 26.0 27.6

25.6 31.7 38.7 56.7 81.7 111.5 117.8 24.8 29.8 36.7 55.2 79.7

12.40 13.60 14.30

-

27.7 32.1 38.7 57.3 82.5

11.55 13.10 13.85

-

-

486 523 607 770 636

11.63 12.12 13.12 13.79 10.67 12.96

-

33.1 33.9 35.2 35.6 30.6 26.8 28.5

27.7 33.7 40.6 58.2 82.5 111.4 117.6

Notes:

1. Where specific heats are quoted at temperatures above RT, the values have been determined over a range of 50°C up to the temperature quoted. 2. Coefficients of expansion are mean values from RT up to the temperature quoted. 3. Electrical resistiuity values are uncorrected for dimensional changes of the specimen with temperature Original dimensions as at RT.

The physical properties of steels

14-31

Table 1411 PHYSICAL PROPERTIES OF STEELS-continued

Thermal properties (see Notes) Material and condiiion Comjwsition

%

Sped&

Temperature

"C

gravity gcm-3

RT 100 200

1.83

RT 100 200

7.85

RT 100 200

7.85

RT 100 200 400 600

1.86

RT 100 200 400 600

1.84

RT 100 200

7.85

RT 100 200

7.87

RT 100 200

7.84

Specific heat J kg-' K-1

Coefficient of thermal T h i expansion conductivity 10-6

K-1

W

m-l K-I

-

-

10.55 1200

21.6 29.7

Electrical resistivity Pcm

37.0 41.6 49.3

Hardened 820°C AC Tempered 250°C (lh)

12.50 13.10

24.9 29.6 37.1

Blank carburized 920°C Hardened 800°C OQ

11.30 12.55

36.3 40.1 46.7

M o 0.20 Blank carburized 920°C Hardened 800°C OQ

CP

0.48

Mo 0.17

12.00 12.75 14.00 14.75

24.1 28.2 34.0 52.0 14.1

Hardened 850°C OQ Tempered 620°C (lh) OQ

Mo 0.14 Hardened 840°C OQ Tempered 650°C (lh) OQ

gi Cr

% q ky i 3 5Ni-Cr l 0.71 635A14

12.00 12,65 13.65 14.30

12.80 13.10

24.8 29.2 35.6 54.0

78.0 29.1 34.2 41.1

Blank carburized 910°C Hardened 820°C OQ

11.30 12.45

31.8 366 43.2

Blank carburized 910°C Hardened 810°C OQ

11.80 12.30

34.5 39.2 45.1

Blank carburized 91OOC Hardened 810°C OQ Notes:

1. Where specific heats are quoted at temperatures above RT, the values have been determined over a range of 50°C up to the temperature quoted. 2. Coeficients of expansion are mean values from RT up to the temperature quoted. 3. Electrical resistivity values are uncorrected for dimensional changes of the specimen with temperature. Original dimensions as at RT.

14-32

General physkal properties

T a b 1411 PHYSICAL PROPERTIES OF STEELS-cmthied Thermal properties (see Notes) Material and condition Comp.tion

%

cu

0.64

Annealed

Specific Temperame "C

gravity,

RT 100 200 400 600 800 loo0

1.13

Specijic heat J kg-' K-1

expamion conductivity 10-6 K-1 w ,-1 K - I

-

-

498 523 603 149 528

-

11.19 12.21 13.35 14.09 13.59 14.54

461

-

0

si

RT 100 200 400 600 800

0.1

B

1.96 AI 0.03 Hot worked

c

0.10

0

4.2 Al 0.53 A8 cast

RT 100 200 300 400

B

1.12

7.40

523

Typically 0.10 MO 0.5

B

Mo-B 'Fortiweld'

0.004

RT 100

-

-

39.9

50.6 61.5 723 83.3

11.2

-

11.8

-

13.0

-

106.5

-

'440

1200

465 494

12.55 1325 1430 15.10 15.40

551

Cr 4.0/6.0 Annealed

-

30.9 38.1 51.4 81.9

-

632 614 30 100 200 400 600 800 1 200

10.0 11.0 11.9 11.8 13.3

10.4

200

1.1

41.9 47.0 52.9 68.5 91.1 117.3 122.3 24.9

-

7.86

Electrical resistivity

-

95

500

} 94

25.1 28.5 30.1

-

600 700 800 loo0

c

Coeflcient sfthermal Thermal

11.0 11.6 12.6 13.3

-

129.4

46.1 45.2 44.4 415 36.9 35.2

20.0 24.5 31.0 48.5

74.5 88.0

36.0 35.2

-

-

26.8 26.8

w&.poYRT

Si 3.5 Cr 3.5 Hardened and tempered

1.6

-

100

13.0

300 Mo 700 900

13.0 13.0 14.0

80

-

Notes

*

The values are a mean from RT up to the temperature quoted. am quoted at tcmpcrptures above RT, the values have been determintd over a range of 50°C up to the temperature quoted. 2. Co@ieiews sf expansion are mean values from RT up to the temperature quoted. 3. Electrical resistivity valuca are uncorrected for dimensional changes of the specimen with temperature. Original dimensions as at RT. 1.

WhQC spec@c heou

The physical properties of steels

14-33

Table 1411 PHYSICAL PROPERTIES OF STEELS-continued Thermal properties (see Notes) Materia! and condition Composition

%

1

C 0.45 Mn 0.5 Cr 8.0 Si 3.4 Hardened C Mn

8% Cr-3% Si En 52 401845

and tempered

t?}ll%Cr

Cr 11.5 Hardened and tempered

Er

@:)9%Cr-Mo

Mo 1.0 Normalized and tempered

Annealed

C

0.071

Cr 17.0 Annealed

Mn C

::?}21%Cr

Cr 21.0 Annealed

3:?}30% Cr-Ni Ni 0.26 Hardened and tempered

Temperature "C

RT 100 300 500 700 90

Specific grauity g cm-3

Specific Coeficient heat of thermal Thermal J kg-I expansion conductivity K-' K-' W K-'

-

7.6

13.0 13.0 13.0 14.0

-

RT 100 300 500 700 750

7.75

RT 100 200 400 600 700

7.78

-

RT 100 200 400 600 800

7.75

RT 100 200 400 600 800 lo00

7.74

RT 100 200 300

7.7

RT 100 300 500 700 900

7.76

RT 100

7.90

80.0

-

110.0

31.4 23.5

60.0

-

-

-

24.3

119.0

11.15 11.30 11.60 12.10 12.65 12.85

26.0 26.4 26.8 27.6 26.8 26.8

49.9 55.5 63.0 79.5 97.5 106.5

10.0 11.0 12.0 12.0

*402 427 461 528 595 624

22.2

-

Electrical resistivity VRcm

9.3 10.9 11.5 12.1 12.2

-

-

473 515 607 779 691

10.13 10.66 11.54 12.15 12.56 11.70

26.8 27.6 27.6 27.6 26.4 25.1 27.6

48.6 58.4 67.9 85.4 102.1 116.0 117.0

-

21.8

62.0

21.8

62.0

12.6

80.0

-

10.0 11.0 12.0 482

-

10.0 11.0 11.0 12.0 13.0

10.0

Notes: * The values are a mean from RT u p to the temperature quoted. 1. Where specific heats are quoted at temperatures above RT, the values have been determined over a range of 50°C up to the temperature quoted. 2. Coeflicients ofexpansion are mean values from RT, up to the temperature quoted. 3. Electrical resistivity values are uncorrected for dimensional changes of the specimen with temperature. Original dimensions as at RT.

14-34

General physical properties

Table 1411 PHYSICAL PROPERTIES OF STEELS-ContifIued Thermal properties (see Notes)

Spec&

Material and condition

Specrfic he&

Jkg-'

Coeficient of thermal Thermal nprmsiOn ronduetiay

res&tWy

10-6 K-1 W m - l

pi2 cm

compositioa

Temperature gravity

%

"C

gem-3

K-1

RT 100 200 400 600 800 loo0

7.87

519 565 607 704 649 673

.-

RT 100 200 400 600

8.16

-

-

502 519

13.73

540

17.02 17.82 18.28 18.83

1

C 122 13%Mn Mn 13.0 1050°C Air-cooled

Ni

28.4 950°C. WQ

586 586 599

800 lo00

Cr AI

12.0 4.5 Soffened

RT 100 300 500

1.42

502

W

J".'

18.5 Annealed 830OC

200 400 600

800 lo00 RT 100 300

Cr

16.5

7.7

11.0 12.0 120

410 435 502 599 716 -

11.23 11.71 12.20 12.62 1297 12.44

-

-

482

10 11 12

700 850 a.69

15.28

13.0 -

600

RT 100

18.01 19.37 21.71 19.86 21.86 23.13

500

K-I

-

Electrical

13.0 14.6 16.3 19.3 21.8 23.5 25.5

6&5 75.7 84.7 100.4 110.0 120.4 127.5

12.6 14.7 163 18.9

829 89.1 94.7 103.9 111.2 116.5 120.6

22.2

25.1 27.6

25.1

2as -

122

125 129

-

136 141

24.3 26.0 27.2 28.5 27.2 240 27.6

40.6 47.2 54.4 71.8 92.2 1152 120.9

18.8 -

-120

24.3

103.0

15.9 16.3 17.2 20.1 23.9 26.8 28.1

69.4 77.6 85.0 97.6 1072 114.1 119.6

15.9

72

-

-

sofielled

Cr

18/20 1100°C WQ

RT 100 200 400 600 800

792

511 532 569 649 641 -

lo00

RT

7.9

14.82 16.47 17.61 18.43 19.03

-

300

16.0 18.0

500

180

700

19.0

100

Nb 1.2 Softened

-

-

172 18.8 20.1

Notes:

1. Where spee3c heats are quoted at temperatures above RT, the values have been determined o w a range of 50°C up to the temperature quoted. 2. Coe&iciea&s cfexponSon are mean values from RT, up to the tempc#atun quoted. 3. Electrical resistiuity values are uncorrected for dimensional changes of the specimen with temperature. Original dimensions as at RT.

The physical properties of steels

14-35

Ta& 1411 PHYSICAL PROPERTIES OF STEELS-continued Thermal properties (see Notes) Material and condition Composition

%

Ternporotwe

Specific gravity

Specific Coeficient heat of thermal Thermal S kgexpansion condwtiuby

"C

gm-3

K-1

RT 8.5 Ti 1.2 Softened

RT Cr. Nb

w

,,,-1

K-'

pan

82

15.0

15.0 16.0 17.0 18.0 7.92

100 200 400

19 1.7

K-I

-

7.72

100 300 500 700 900

Ni

10-6

Electrical resistivity

600

-

-

17.0 17.2 17.6 18.6

15.1 16.8 20.1 24.3

softened

RT Ni 8 Cr 20 w 4 Softened

Ni Cr

8.5 18.5

Ti AI

0.8

C Mn Cr Ni

7.61

900

RT

29

125

-

18.0

85

15 15 15 16 17

26.0

125

15.5 16.8

70 77

126 13.8 15.4 18.8

14.1 80.0 86.7 99.4 108.4 114.4

17.0 18.0 18.0

100 300 500 700

0.3 IZ%Cr-IThNi lzy}En 58D 12.5

-

17.0

700 900 1050

1.4 Normalized and tempered

85

16.0

Mo

RT

13

7.8

100 300

8.01

490

18

100

Softened C Mn

RT

~~}15/10/6/1

7.94

100

Cr

mo

Ni

400 600 700

15.0 Cr-Ni-Mn-Mo 10.0 M O 1.0 J Solution treated 1IOO"C

RT

8477 494 511 536 557 565

-

8.08

100

Ni 36 Cr 11 Softened

c

0.1

Mn Si Ni

13 i2 1.8

}

300 500

RT

29.0 softened

Cr ~

~~

~

7.5

~~

~

21.8

23.0 12.1

-

97

-

14 15 16

-

-

18.4

117

10

15.9

88

26.4

126

11

200 800 lo00 1 loo

W/,Cr-Ni

14.80

15.70 16.75 18.25 18.95 19.30

13 13

~

~~

Notes * The values are a mean from RT up to the temperature quoted. 1. Where spec$c heats are quoted at temperatures above RT, the values have been determined over B range of M"Cup to the temperature quoted. 2 Co&cimks qfexpansion are mean values from RT up to the temperature quoted. 3. Elmtricd redstidty values are uncorrected for dimensional changes of the specimen with temperature. Original dimensions as at RT.

Genera[ physical properties

1436

Table 1411 PHYSICAL PROPERTIES OF STEELS-COntinued

Thermal properties (see Notes) Material and wndition Composition

%

RT 100 200

63 14

Ni

Cr

Temperature "C

gem-)

c

0.G Mn 3.0 17% Cr-17% Ni-Mo Ni 17.5 -Co-Nb Cr 16.5 Mo 3.0 Nb 25 Co 7.0 , Softened

.

RT

13.0 13.0 2.3 0.9

C 0.4 13% Cr-13% Ni-W Mn 0.8 -Mo-Co-Nb Si 1.o Ni 13 Cr 13 W 2.5 Mo 2.0 Nb 3.0 c o 10.0 ~ o ~ u t itreated oi

Cr 19.1 Mo 22

? J: Co 46.6

8.0

15.5 16.5

28.9

110

-

126

93.8

15 16 16 17

8.03

16.8 17.3 18.3 18.9 19.3

8.13

100 200 400 600 800

RT 100 200

105

14.5

100 200 400 600 800

RT

126 12.0 12.5 13.5

100 300 500 700

RT

speclyic coeficiant heat sf thermal Thermal Electrical J kg-I expansion conductivity resistivity K-' K - I W m-I K-' p2cm

8.1

400 600 800 loo0

Soltcoed

Ni Cr W Nb

Specgc gravity

8.26

400 600 800

-

-

15.6 15.8 16.9 17.3 18.0

13.4 17.2 18.8 22.2

-

-

14.8 15.0 152 15.9 16.8

14.1 16.3 19.7 23.0 26.0

122 126 13.2 13.6 13.9 14.2

48.6

25.5

Solution treated and aged cast steels

C Mn

0.11 Plaincarbon 0.35)B.S. 1617A A 950'C. N 950°C

100 200 300 400 500 600

19.5

Notes: 1. Where speeifie heats are quoted at temperatures above RT, the values have been determined over a range

of 50°C up to the temperature quoted. 2. Coeficients of expansion are mean values from RT up to the temperature quoted. 3. Electrical resistivity values are uncorrected for dimensional changes of the specimen with tempcrature. Original dimensions as at RT.

The physical properties of steels Table 14.11

14-37

PHYSlCAL PROPEBTlES OF S T E E ~ ~ n t i n u c d

T h l prope~~ia (see Notes) M a t d and condition Composition

%

;:;}

C nob;;:;;

Mn

A900"C,OQ83O0C T65O"C

C

Mn

Temperature "C

12.4 12.8 13.1 13.4 13.8 142

100

Mn

200

300

400 Mo

600

MO

10-6

100 200

C

I&, Cr Ni Mo BS 1458

K-1

11.8 12.4 12.8 13.3 13.7 14.2

400 500 600

C Cr Ni

gm-3

speajc co&icient heat dfhermal Thermal J kg-' exponsion eonducfivity

100 200 300 400 500 600

MO

A 950°C, WQ 910% T 660°C

Specifi gravuy

100 200 300

400 500 600

Mo

13.0

100 200

400 500

600 C Cr

100 200

Mo 400 500 600

C cr

Mo Si

mistiuity

42.3

23.5

flcm

24.2

27.6

12.5 12.7 13.0 13.4 13.9 14.4 12.0 12.3 126

C Cr Mo

w m - l K-1

132 13.3 13.7 14.1 14.7 15.2

C Ni Cr

600

K-1

Electrical

39.4

27.3

13.5 13.9 12.2 12.4 12.7 12.9 13.3 13.6 11.8 12.0 12.3 12.5 12.7 13.0

37.1

11.9 11.6 11.7 11.7 11.8 11.9

Notes:

1. Where specijSe heats are quoted at temperatures above RT, the values have been determined over a range of 50°C up to the temperature quoted. 2 C@cienrs qfexpansion are mean values from RT up to the temperature quoted 3. EIectrical resistivity values are unwrrected for dimensional changes of the specimen with temperatux Original dimensions as at RT.

14-38

General physical properties

Table 14.11 PHYSICAL PROPERTIES OF STEELS-tind

Thermal properties (see Notes) Spscrfic Co&icimt

Moterial and condition Composition

%

Temperature "C

C Cr

100 200

Speci~5c grauity,

heot Jkg-'

gan-

IC-'

ofthermal Thermal expansion w d w t i u i t y 10-6K-i W m - ' K - ' 11.5 11.8 124 126 12.7 12.9

Ni Si

C Cr

0.47 Carbon Cr 0.85) BS 1956A N 870 "C, T 635 "C

125 129 13.2 13.4 13.5 13.6

C Ni

0.1 3&,Ni 100 200 3.35} BS 1504-503 WQ 880"C, T 650°C 300

11.3 11.9 12.2 12.7 13.5 13.6

4(x1

500 600

Mo

25.1

11.8 12.4 12.6 13.3 13.7 13.9

100 200 300 400 500

C Cr

600

E k W resistivity flcm

28.7

Cast corrosion-resisting steels

7.73

Hardened and tempered

100 300 500 600

7.75

Harde-&

100 300 500 600 100

7.93

502

17.0

16.3

100 300

7.93

502

17.0

Mn

~

and tempered

482

11.0 11.0 120

24.7

-

56

27.6 482

11.0 11.0 120

-

24.3

-

57

26.0

72

8.5 J Ni Cr 18.0 Normalised

4

Mn 0.50 18%Cr,8%NiNb Ni 9.00 BS1631BNb Cr 18.0 NbNormalised 0.9

15.9

500

18.0 18.0

-

700

19.0

20,1

Nores: 1. Where specijic heats are quoted at temperatures above RT, the values have been determined over a range of 50°C up to the temperature quoted.

2. Coefficients ofexpansion are mean values from RT, up to the temperature quoted. 3. Electrical resistiuity values are uncorrected for dimensional changes of the specimen with temperature. Original dimensions as at RT.

The physical properties of steels

14-39

Table 14.11 PHYSICAL PROPERTIES OF STEELS-continued Thermal properties (see Notes) Material and condition Composition

%

SpeciJc heat K-1

Coefficient of thermal Thermal expansion conductivity 10-6 K - I w ,-I K-1

Electrical resistivity p a cm

7.78

444

17.0

15.5

70

RT 100

7.96

502

-

16.3

RT 106) 200

7.96

Specific gravity

J kg-’

gcm-3

100

Temperature “C

Cr 19.00 Ti 0.6 Normalised 16.0

Cr 19.0 Mo 3.6 Water quenched 502

16.3

73

16.3 17.6

73

16.0

-

15.5

78

16.5 16.9 17.2 17.4 17.9 19.0

406) 500

600 Normaiised

-

800 RT 100

7.96

RT 100

7.78

RT 100

7.93

502

-

Normalised

448

17.0

Norinalised

c

0.063

502

-

16.3

16.0

MQ 2.5 J Normalised Cast heat-resisting steels (7

0.25)

RT 100

Cr 12.5 Hardened and tempered

300 500 600

7.75

482

-

24.3

11.0 11.0 12.0

-

-

57

-

26.0

Notes: 1. Where specjfic heats are quoted at temperatures above RT, the values have been determined over a range of 50°C up to the temperature quoted. 2. Coefficients ofexpansion are mean values from RT, up to the temperature quoted. 3. Electrical resistivity values are uncorrected for dimensional changes of the specimen with temperature.

Original dimensions as at RT.

14-40

General physical properties

TaMe 1411 PHYSICAL PROPERTIES OF STEELS-ontinued Thermal properties (see Notes) Specific gravity g cm-3

Specific heat J kg-' K-'

Coeficient of thermal Thermal expansion conductivity K - ' W m-' IC-'

Electrical resistivity pQcm

RT 100 200 400 600 800 lo00

7.63

482

-

20.9

70

k

RT 100 200 400 600 800 lo00

7.63

20.9

70

0.307 C Si 20% Cr 10% Ni Mn BS 1648D Ni Cr 20.0

RT 100 500 800 1100

7.74

-

-

-

80

15.5

RT 100 300 500 700 900 lo00

1.92

RT 100 200 400 600 800 lo00

1.92

RT 100 300 500 700 900 lo00

7.90

RT

7.90

Material and condition Composition

x

-

i :Mn

::$}27%Cr 0.90 BS 1648B

Cr 29.0 Tempered

::]27%Cr Mn 0.70 BS 1648 C Cr 27.0 J Tempered

::::

i

0.35)

C Si Mn Ni Cr W

4.0

J

C Si Cr 25.0 J Normalised

c

0.201

Mn

o,80 25%Cr 12%Ni

'"I

ril!8E

Ni 12.0 Cr si 23.0 w 3.0 J Normalised ~~

c

Temperature "C

~

0.201

Cr 25.0 J Normalised

100 200 400

600 800 lo00

10.2 10.8 11.0 11.5 12.4 13.3 482

-

10.2 10.8 11.0 11.5 12.4 13.3 502

435

544

17.8 18.5 19.6

-

-

10.9

13.6 14.5 15.4 16.5 17.1 18.3

-

-

13.8

85

12.6

87

26.8

-

86

26.8

16.5 16.6 16.9 17.6 18.2 18.7 502

15.0 16.0 16.0 17.0 19.0

544

-

29.3

-

15.9

90

16.5 16.9 17.5 18.3 19.2 20.0

Notes: 1. Where specific heats are quoted at temperatures above RT the values have been determined over a range of 50°C up to the temperature quoted. 2. Coeficients of expansion are mean values from RT up to the temperature quoted. 3. Electrical resistivity values are uncorrected for dimensional changes of the specimen with temperature. Original dimensions as at RT.

The physical properties of steefs

14-41

T a b 1411 PHYSICAL PROPpTIES OF SIXEWontinued Thermal properties

(see Notes) Material and eondirion Composition

% C

0.353

gravity

spccifie cwgietent hear ofthermal Thermal J kg-' expansion eonductiviry

gcm-3

K-1

10-6

7.90

502

-

Specific Temperature "C

RT

700 900 lo00

RT 100 500 Ni 35.0 Cr 15.0 CW

c

0.501

460

C

0.507

8.02

460

800 1100

RT 100

500 800 1100

88

-

-

I O

13.4

16.0 16.5 17.6

100 500

Ni 40.0 Cr 20.0 J Can

12.6

K-I

29.3 7.93

800 1100

RT

Wm-l

15.0 16.0 17.0 17.0 18.0

100 300 500

Cr 15.0

K-1

Electrical resistivity @ cm

8.12

460

-

-

160 144 17.4

-

-

-

-

14.2 15.3 165

105

13.4

23.9

-

108

13.4

-

23.0

-

Notes: 1. Where sped& hears are quoted at temperatures above RT, the values have been determined over a ranp oi 50°C up to the temperature quoted. 2 C@cienrs ofexpansion arc mean values from RT, up.to the temperature quoted. 3. Electrical resisriuity values are uncorrected for dimensional changes of the specimen with temperature.

Original dimensions as at RT.

REFERENCES TO TABLE 14.11 1. 'Metals Handbook', 4th edn. 2. J. Woolman and R. A. Mottram, 'Mechanical and Physical Properties of

BS En Steels (BS 970, 1950), Pergamon Press 3. Sundry technical information issued by industrial organizationseg. Britkb Steel Corporatios M o d Nickel Co. Ltd

General physical properties

24-42

Table 1412 SOME LOW TEMPERATURE THERMAL PROPERTIES OF A SELECTION OF STEELS

There is particular interest in the thermal properties (especially the thermal expansion) of steels used under conditions well below normal atmospheric temperature, and available information is set out below in respect of some such steels. Coelficient of thermal Material and condition Analyses %

Temperature "C

Typical1y :09}9

-200 - 150 100 - 50 RT 100

&

Ni

Double normalized and tempered

C

E:

:%}I$

Ni-Cr-Mo

Mo

0.24 Hardened 840°C OQ Tempered 650°C (1h)/AC

Hardened 960'COQ Tempered 700'C (ih) AC

Mo 0.49 Hardened 9 o T O Q Tempered 650°C (1 h) AC Mn Ni

6.23 9.88 Cr-10 Ni-6 Mn-Mo-V-B-Nb

V

0.28

Nb

-

expansion 10-6~-1

-9.5 - 9.7

200

-9.9 -10.2 10.5 11.0 11.7

ux,

12.3

- 150 - 100 - 50

- 10.4

RT

12.1

- I50 - 100

- 10.5

-50

-11.8 12.2

RT

-11.2

- 11.8

- 11.2

-150 - 100 - 50 RT

- 10.3 - 10.8

- 150 -100 - 50

- 14.7 - 15.3 - 15.7

RT

16.2

- 9.8

11.5

0.94

:it,$$

1150'C AC

Ni-Cr-Mo

Mo 0.19 Blank carburized 890'C AC 820°C (ih), transferred to 580°C (4h) OQ

- 10.2

- 150 -50

- 10.1

- 100 Hardened 930 COQ Tempered 700 (4 h ) AC

2; :ij3$ c

-9.4

-150 -100 - 50 RT

-9.8

10.8

-9.1 - 10.5

RT

11.2

- 150

- 100

- 10.1 - 10.6

-50

- 11.0

RT

11.6

0.127

Ni-Cr-Mo

Mo 0.16 Blank carburized 910 C A C Hardened 840 C (ah) OQ Tempered 760 COQ

Thermal wnductiuity wm-I~-l

16.0 19.5 23.0 26.5, 29.5 32.0 34.0 34.5

The physical properties of steels

'hbk 14.12

SOME LOW TEMPERATURE THERMAL PROPERTIES OF A SELECTION OF STEELS-

continued cotgident ofthermal Material and condition Analyses %

Temperature

"C

- 150 Hardend 850°C AC Tempered 650°C (fh) AC C

Mo 0.22 Blank carburized 910°C AC Hardened 870"COQ Tempered 770°C OQ

Hardened 870°C OQ

10-6~-1

- 10.6

RT

12.3

-154 -100 -54

-as

RT

- 100 -50

RT

Therm~l conductimty wm-1 K - 1

-9.6

- 100 -50

- 150 Ni 3.04 Blank carburized 91O"CAC

expadon

- 11.6

-9.5 - 10A 11.3

-9.9

- 10.5

-11.0 11.5

Tempered 7lO"COQ Thermal expansion values shown for temperatures other than RT are the mean valucs from RT to that toinperature. For RT the instantaneous value is given.

REFERENCE TO TABLE 14.12 1. Sundry tahnical information issued by British Steel Corporation and Mond Nickel Co. Ltd.

14-43

15 Elastic properties, damping capacity and shape memory alloys 15.1 Elastic properties The elastic properties of a metal reflect the response of the interatomic forces between the atoms concerned to an applied stress. Since the bonding forces vary with crystallographic orientation the elastic properties of metal single crystals may be highly anisotropic. However, polycrystalline metals and alloys with a randomly oriented grain structure behave isotropically. Table 15.1 lists elastic constants for polycrystalline metals and alloys in an isotropic condition. Any preferred orientation or texture resulting from rolling, drawing or extrusion, for example, will result in departures from the listed values to a degree that depends upon the elastic anisotropy of the individual crystals (which may be deduced from the single crystal elastic constants of Tables 15.2 to 15.6 that follow) and the nature and extent of the preferred orientation. Since the elastic properties are determined by the aggregate response of the interatomic forces between all the atoms in the me.tal, the presence of small quantities of solute atoms in dilute alloys or their rearrangement by heat treatment will have relatively little effecton the absolute values of their elastic constants. Consequently, the elastic constants of all the plain carbon and low alloy steels will be approximately the same unless some prelerred orientation is present. Similarly with Cu-, Al- and Ni- base dilute alloys, etc. In the case of concentrated alloys there may be larger variations in elastic moduli, especially where there is a drastic change in the relative proportions of differentphases in a multiphase alloy. In the case of ideal solid solutions the elastic moduli vary linearly with atom fraction. The elastic moduli of non-ideal solid solutions may show positive or negative deviations from linearity. Ordering produces an increase in elastic moduli. Increase in temperature causes a gradual decrease in elastic moduli. The decrease is fairly linear over wider ranges of temperature but sharply increases in magnitude as the melting point is approached. Discontinuities are observed at structural transformations. Ferromagnetic materials having a high degree of domain mobility may exhibit considerably higher elastic moduli below the Curie point in the presence of a high magnetic field. The lower elastic moduli in the absence of a magnetic field are due to magnetostrictive dimensional changes caused by stress-induced domain movement.

15-1

15-2

Elastic properties, damping capacity and shape memory alloys

Table 15.1 ELASTIC CONSTANTS OF POLYCRYSTALLINE METALS AT ROOM TEMPERATURE Rigidity modulus

Bulk

modulus

modulus

Poisson's

GPa

GPa

GPa

ratio

Rei:

70.6 54.7 77.9 12.8 318 34.0 100.6 62.6 1.7 19.6

26.2 20.7 19.3 4.86 156 I28 37.3 24.0 0.65 7.9

75.2 -

-

0.345 0.25-0.33

0.28 0.02 0.33 0.35 0.30 0.295 0.31

1 2, 3 4 2 5 2 1 5 2 Z6

Young's

Metal

Aluminium Antimony Barium Beryllium Bismuth Brass 70Cu 30211 Cadmium Caesium Calcium Cast Iron-Grey, BS 1452:1977 Grade 150 Grade 180 Grade 220 Grade 260 Grade 300 Grade 350 Grade 400

110 -

111.8 51.0

-

17.2

-

40 44 48 51 54 56 58

-

-

0.26 0.26 0.26 0.26 0.26 0.26 0.26

7, 8 7, 8 7,8 7, 8 1, 8 7, 8 7, 8

-Blackheart malleable BS 3101972 Grades B340/12 to B290/6 169

67.6

-

0.26

7, 9

Pearlitic malleable BS 3333:1972 Grades P444017 to PS40/5 172

68.8

-

0.26

7, 9

Whiteheart malleable BS 309.1972 Grades W34013, W410/4

176

70.4

0.26

7, 9

169 169-1 74 176

66 65.9 68.6

0.275 0.275 0.275

7, 10 7, 10 7, 10

172

67.1

0.275

7. 10

Cerium Chromium Cobalt Constantan 45Ni 55Cu Copper Cupro-nickel7OCu 3ONi Duralumin Gallium Germanium Gold Hafnium Incoloy 800 mr,32Ni bal Fe Indium Invar 64Fe 36Ni Iridium

33.5 279 21 1 162.4

0.248 0.21 0.32 0.327 0.343

11,12 1 13, 16

144 70.8 9.81 79.9 78.5 141 1% 10.6 144 528

13.5 115.3 82 61.2 48.3 53.8 26.3 6.67 29.6 26.0 56 73 3.68 57.2 209

a34

14 1 2 2 15, 16 17, 18 38 2

Iron (pure) Lanthanum Lead Lithium Magnesium Manganese

211.4 37.9 16.1 4.9 I 44.7 191

81.6 14.9 5.59 4.24 17.3 79.5

Nodular BS 2189: 1973 Grades 370117, 420112 Grades 500/7,600/3 Grades 700/2,800/2 (pearlitic, normalized) pearlite 700/2,80012 (hardened, tempered)

100 109

120 128 135 140 145

129.8

-

-

160.2 181.5 156.4 137.8

-75.4 -

171 109

-

99A

371

a345 0.47 0.32 0.42 0.26 0.334 0.45 0.259 0.26

1

1

1 1% 19,

20, 21 169.8

-

-45.8 35.6

-

0.293 0.28 0.44 0.36 0.291 0.24

1

2,12 1

23,28 1

2.24

15-3

Elastic properties

T&?

15.1 ELASTIC CONSTANTS OF POLYCRYSTALLINE METALS AT ROOM TEMPERATURE-conrinued

Metal

Bulk

Young's modulus

Rigidity moduhrs

d h r s

GPa

GPa

GPa

93

22.4

-

-

25

0.293 0.32

26

Poisson's ratio

Manganese-copper 70Mn 3OCu (high damping alloy) Molybdenum Monel400 63-70Ni 2 MR,2.5Fe. bal Cu Nickel Nickel silver 55Cu, 18Ni, 27 Zn Nimonic 80A ZOCP, 2.3Ti, 1.8A1, bal Ni (fulIy heat-treated) Niobium Ni-span C902 (constant modulus alloy) Osmium

324.8 185

1256 66

261.2

199.5 132.5 222

76.0 49.7 85

177.3 132

104.9 186 559

37.5 66 223

170.3 373

0.397 0.41 0.25

Palladium

121

43.6

187

0.39

Platinum

170

60.9

276

0.39

34.5

-

Plutonium Potassium (- 190°C)

87.5 3.53

1.30

-

-

-

0.312 0.333 0.31

-

0.18 0.35

Ref:

1

1 1

27 1

28 16, 21, 29 18, 19, 21, 29 16, 19, 29, 30 31 15

(room temp.) Rhenium

466

181

334

0.26

Rhodium Rubidium Ruthenium Selenium Silicon Silver Sodium Steel-Mild 0.7SC 0.75C (hardened) Tool 0.98C. 1.03 Mn,0.65Cr, 1.01 W Tool 0.98C, 1.03Mn, 0.65Cr, 1.01 W (hardened) Maraging Fe-18Ni 8Co 5 M o Stainless austenitic (Fe-I8Cr, &IONi) Stainless, ferritic (Fe43Cr) Stainless, martensitic (Fe-l3Cr,0.1-0.3C) Stainless, martensitic (Fe18Cr. 2Ni, 0.2C) Strontium Tantalum Tellurium Thallium Thorium Tin Titanium Tungsten Tungsten carbide Uranium Vanadium Yttrium Zinc; Zirconium

379 2.35 432 58 113 82.7 6.80 208-209

147 0.91 173

276

0.26 0.30 0.25 0.447 0.42 0.367 0.34 0.27-0.3 0.293 0.296 0.287 0.295

-

39.7 30.3 2.53 81-82

210

81.1

201.4 211.6 203.2

77.8 822 78.5

186 190-201 200-206 200-215 215.3

72 74-86 78-79 80-83 83.9

15.7 185.7 47.1 7.90 78.3 49.9 120.2 41 1 534.4 175.8 127.6 66.3 104.5 98

6.03 69.2 16.7 2.71 30.8 18.4 45.6

160.6 219 73.1 46.7 25.5 41.9 35

-

286

-

103.6 160-169 168.7 165 165.3 165.2

166

12.0

196.3

-

28.5 54.0 58.2 108.4 311 319 97.9 158

69.4 89.8

2, 16 32 16, 19.29 2 18, 21,29 15

2, 33 1 2, 23 34 1 1 1 1

0.30 0.25-0.29 0.27-0.3 0.27-0.3 0.283

35 36 36 1, 36

0.28 0.342 0.16-0.3 0.45 0.26 0.357 0.361 0.28 0.22 0.20 0.365 0.265 0.249 0.38

2,6 1 15 2, 6

1

2, 6 1 1 1 1

37 1

12 1 17,

18

15-4

Elastic properties, damping capacity and shape memory alloys

REFERENCES TO TABLE 15.1 1. G. Bradfield, ‘Usein Industry of Elasticity Measurements in Metals with the help of Mechanical Vibrations’, National Physical Laboratory. Notes on Applied Science No. 30, HMSO, 1964. 2. W. Koster, 2. Electrochem. Phys. Chem., 1943,49, 233. 3. W. Koster, Z . Metall., 1948, 39, 2 4. ‘Metals Handbook’, Amer. SOC. Metals, VoL 1, 1961. 5. D. J. Silversmith and B. L. Averbach, Phys. Reo., 1970, B1, 567. 6. S. F. Pugh, Phil. Mag. Ser. 7, 1974,4!5, 823. 7. H.T. Angus, ‘Cast Irons, Physical and Engineering Properties’, Butterworths, London, 1976. 8. ‘Engineering Data on Grey Cast Irons’, Brit. Cast Iron Res. Assoc., 1977. 9. ‘Engineering Data on Malleable Cast Irons’, Brit. Cast Iron Res. Assoc., 1974. 10. ‘Engineering Data on Nodular Cast Irons’, Brit. Cast Iron Res. Assoc., 1974. 11. M. Rosen, Phys. Rev., 1969, 181, 932. 12. J. F. Smith, C. D. Carlson and F. H. Spedding, J . Metals, 9; ?).am. AIME, 1957, 209, 1212. 13. ‘Physical and Mechanical Properties of Cobalt’, Cobalt Information Centre, Brussels, 1960. 14. ‘Cupro-Nickel Alloys, Engineering Properties’, Publ. 2969, Inco Europe, London, 1966. 15. Landolt-Bornstein, ‘Zahlenwerte und Funktionen’, Vol. 2, Part 1, Springer-Verlag, Berlin, 1971. 16. A. S. Darling, Int. Met. Rev., 1973, 91. 17. Private communication, Imperial Metal Industries, Witton, Birmingham. 18. A. S. Darling, Proc. Inst. Mech. Eng., 1965, Pt 3D, 180, 104. 19. W. Koster, Z. Metall., 1948, 39, 1. 20. A. Roll and H . Motz, Z. Metail, 1957,48, 272. 21. K. H. Schramm, Z. Metall., 1962, 53, 729. 22. P. W. Bridgman, Proc. A m . Acad. Arts Sei., 1922, 51,41. 23. 0. Bender, Ann. Phys., 1939,34, 359. 24. M. R o s a , Phys. Rev., 1968, 165, 357, 25. D. Birchon, Engineering Mater. and Design, 1964,7,606. 26. ‘Wrought Nickel-Copper Alloys, Engineering Properties’, Puhl. 7011, Inco Europe, London, 1970. 27. ‘Nmonic Alloy 80A: Publ. 3663, Henry Wiggin Ltd., Hereford, 1975. 28. ‘Controlled Expansion and Constant Modulus Nickel-Iron Alloys’, PubL 6710, Inco Europe, London, 1967. 29. W. Koster, 2. Metall., 1948, 39, 111. 30. E. Griineisen, Ann. Phys., 1908,25, 825. 31. ‘Plutonium Handbook: Ed. 0. J. Wick, Gordon and Breach, New York, 1967, p. 39. 32. T. E. Tietz, B. A. Wilcox and J. W. Wilson, Standford Res. Instit. Calif., Report SU-2436, 1959. 33. R. L. Templin, Metals and Alloys, 1932, 3, 136. 34. J. Woolman and R. A. Mottram, ‘The Mechanical and Physical Properties of the British Standard En Steels’, Vol. 1, Pergamon, Oxford, 1964. 35. ‘18% Nickel Maraging Steels’, Publ. 4419, Inco Europe, London, 1976. 36. J. Woolman and R. A. Mottram, ‘The Mechanical and Physical Properties of the British Standard En Steels’, Vol. 3, Pergamon, Oxford, 1969. 37. ‘Commercial Uranium’, Brit. Nuclear Fuels Ltd., Warrington. 38. ‘Incoloy goo’, Publ. 3664, Henry Wiggin Ltd., Hereford, 1977.

15.1.1

Elastic eompliaoees and elastic stBksses of single crystals

Single crystals are generally anisotropic and therefore require many more constants of proportionality than isotropic materials. The relations between stress and strain are defined by the generalized Hooke’s law, which states that the strain components are linear functions of the stress components and vice versa. That is,

and correspondingly

Elastic properties

15-5

where a ,, E*,

u,,, u,, and, up, a,,, ax, represent normal and shear stresses, respectively; E,, and e,, e, E ~ represent , normal and shear strains, respectively.

e,

The elastic constants S , and C, are called the elastic compliances and elastic stiffnesses, respectively. Many of the constants are equal, the number of independent constants decreasing with increasing crystal symmetry. For example, in the hexagonal system there are five independent constants, while in the cubic system there are only three elastic compliances S,,, Slz,S4, with corresponding elastic stiffnesses C, Clz, C44. The tensile and shear moduli will vary with orientation in a single crystal of a cubic metal according to 1

-=SII-2[(S1, -S12)-+S44] (hZ +m2n2+I%') E

1

-=S44 -2[(s,

G

-s,z)-fs44] (PmZ+mzn2i Pn2)

where I , m, n are the direction cosines of the specimen axis with respect to the crystallographic axes. For an isotropic crystal s44=2(sl

1)ZI'-

and

c4,=&c1 1 - c l Z )

hence

Therefore, the degree of anisotropy is conveniently specified by

15.12 Principal elastic compliiances and elastic stiffnesses at room temperature

The units are TPa-' for S,j (elastic compliances) and GPa for C, (elastic stiffnesses). Table 152 CUBIC SYSTEMS (3 CONSTANTS) ~~

~

Metal

Ag A1

Au ca

Cr CS (78 E40

55% Ni45% Ti 2.5% Thoria

26 10.7

Nickel alloys Ni-Ti (Nitinol) T-D Nickel Mallow No-chat Titanium alloys Ti-AI-V-Mo Refernee: D.Bircbon, Enginee-

-

Ti-5.56.75% AI-1-5% V-1-5% (V+M0>6%), all wt%

9.4

Mo

Materials and Design, Scpt., Oct., 1964; atso 307,312.

0.5

34.5 34.5

34.5 34.5 34.5 34.5 35 69 69 69

15-10 15.2.1

Elastic properties, damping capacity and shpe memory alloys Anelasticdamping

Of interest to the physical metallurgist is the fact that a phase lag between stress and strain can give rise to a peak in energy dissipation or damping as a function of temperature or frequency. Several quite distinct atomic processes have been identified with damping peaks and measurements on these peaks in a wide variety of metals and alloys have been used to give diffusion data and to study precipitation, ordering phenomena and the properties of dislocations, point defects and grain boundaries. Table 15.8 identifies the damping peaks found in a number of pure metals and alloys with the relaxation process thought to be involved and also give an indication of the magnitude of the damping peak height. Detailed information on the specific mechanisms involved can be obtained from the reviews below and the references given for the respectivedamping peaks. The main types of peak that are observed are as follows. In cold worked pure metals movement of dislocation lines results in a number of low temperature peaks known as Bordoni peaks. Interaction of dislocations with point defects give rise to a further series of unstable peaks at higher temperatures; these are now called Hasiguti peaks. In alloys the stress-inducedredistribution of solute atoms results in two types of peak, the Zener-type peak in substitutional solid solutions and the Snoek-type peak in interstitial solid solutions. The interaction of interstitial solute atoms with substitutional solute atoms give rise to a modified Snoek peak in ternary alloys. In cold worked alloys the interaction of interstitial solute atoms with dislocations results in the Kostler-type peaks at higher temperaturesthan the Snoek-typepeaks. In pure metals and alloys the stress-induced migration of grain boundaries and/or polygonised (sub-grain) boundaries give rise to a further series of high temperature damping peaks. In the ideal case, for a relaxation process having a single relaxation time (t)the logarithmic decrement (6) will be given by

where w is the angular frequency and A is the modulus defect. The relaxation time, being diffusion controlled, varies with temperature according to an Arrhenius equation of the form T = T , exp ( H / R T )where tois a constant, H is the activation energy controlling the relaxation process and T is the absolute temperature. The condition for maximum damping (6,) is that O M = 1 and hence

The modulus defect which is a measure of the strength of the relaxation can be highly orientation dependent and therefore the values given in the table below must be interpreted with caution. It must also be noted that for many measured damping peaks a distribution of relaxation times is found to be present. This leads to a broader peak being observed than would be present if a single relaxation time were operative. The decrement will be given by

where each i refers to a component of the total peak that has the same form as that of a peak arising from a single relaxation time. This theoretical aspect of the analysis of broad peaks in terms of a spectrum of T’S has been comprehensively dealt with by A. S. Nowick and B. S. Berry in IBM Journal of Research and Development, 1961, 5(4), 297-311, 312-20. REVIEWS 1. C. Zener, ‘Elasticity and Anelasticity of Metals’, Chicago: Chicago University Press, 1948. 2. K. M. Entwistle, ‘Progress in Non-Destructive Testing’ (edited by E. G. Stanford, J. H. Fearnon), vol. 2, p. 191, London: Heywood, 1960. 3. D. H. Niblett and J. Wilks, Ada. Phys., 1960, 9, 1. 4. K. M. Entwistle, Metall. Rev., 1962, 7, 175. 5. A. S. Nowick and B. S. Berry, ’Anelastic Relaxation in Crystalline Solids’, Academic Press, 1972.

Damping capacity

1S11

In Table 15.8, metals and alloys are listed in alphabetical order with the highest concentration constituent h t . The values of the modulus defect are deduced using the equation

where 6, is the peak decrement and Q is the peak value of Q - I . These relationships are valid only if the damping arises from a process having a single relaxation time. In most cases a distribution of relaxation times exists and the peaks are broader, but there is only rarely sufficient published data to permit this distribution to be deducted. As many authors do not make it clear which damping units they use, the quoted values of Modulus Defect-in the table .must not be interpreted too precisely. The aim is to record the existence of peaks and list the suggested mechanism giving rise to them, and the values of A serve to indicate the approximate strength of the relaxation.If detailed quantitative data are sought peaks should be analysed in particular cases using the method of Berry and Nowick. Table 15.8

Alloy

ANELASTIC DAMPING

Peak temp.

Frequency Modulus Hz defect

99999% Ag (CW' 16%at 4.2 K) 99.999% Ag single crystal deformed at RT 43.PA [1211 5.4% [lll] Single crystals deformed at (5.4% [lll]) RT 99.99% Ag

37 K 50 K -50 K

0.7 0.7 -600

2.6 x 1.2 x 10-2 13x10-4

0.84 0.84

-

Bordoni type

-600

6 ~ l O - ~

-

Bordoni type

3

173 K

103

-

21.3

4

(CW* at RT)

200 K

103

-

35.6 etc.

1.04

38 x 10-4 39 x 10-4

92.0 177

Point defect/ dislocation interaction Point defect/dislocation interaction Grain boundary Grain boundary

-

50 K

99.998% Ag (84% area 163°C reduction, then annealed 356°C at S O O T for 1 h) 99.999% Ag 150 K 25-80 A t % Au 42 At. % Au Ag-Cd Ag-Cd Ag-In Ag-In Ag-In Ag-ID. Ag-In Ag-Sb AgSn Ag-Sn Ag-Sn Ag-Zn

Activation energy Mechanism kJ mol-' or type

Composition and physical condition

29 At. % Cd 39 At. "/, Cd 32 At. % Cd 0.9-32 At. % Cd 9.6 At. % In17.9 At. % In 7.5 At. % In15.6 At. % In

0.98

1.5

1.0 364398 "C 0.36 460°C 230°C -1 -1 0.6 220°C 1.5 367452°C -1 580536 K -1

-

-

'Cold worked.

5 5

92

Grain boundary

6

Zener

7

165.3 152.3 123.0 146.9 159-188

Grain boundary Zener Zener Zener Grain boundary

8 9 9 10 6, 11

152.8130.5 159 133.1

Zener

12

Zener

9

1469139.7

zener

13

Zener Grain boundary

14 6, 11

-

Zener Zener

6. 11

131.8 171-184

Zener Grain boundary

15 6, 11

142-136

Zener

16

2 x 10-2 0.104 max

-

4 x 10-2

9.2 x lo-'1.38 x lo-' < 3.5 x 10-37 x 10-3 6.5 x 10-46 x 10+

10-3-10-1 5 10-3 1.5 1.08~ lo-'1.27 x IO-' 0.68 1.2 x 10-21.4 x lo-'

-550 K

4

175.7-

8.1 At. % Sn 0.9 At. % Sn8.0 At. 7; Sn 15 At. % Zn30 At. % Zn

390440°C 280232°C

Bordoni type

1.3 x lo-'

10-3-

-

Bordoni type

z X10-3-

10.8 At- % In-500K 18.1 At. % In 16 At. % In 270°C 1 At. % In46 At. % In 355450°C 6.3 At. % Sb 510 K 0.93 At. % Sn 200°C

10-1 1.6 1.5

Ref:

-2oX 10-3 2.9 x lo-' 9.5 x 10-21 . 2 7 ~10-1

10-3-10-1 -5 x 10-3 1.5 1.3 10-3

-

-

172-188 136

15

15-12

Elastic properties, damping capacity and shape memory alloys

Table 15.8 ANELASTIC DAMPING-continued Activation energy Mechanism kJmol-' orrype

Composition and physical condition

Peak remp.

Freqwncy Modulus Hz defer

99.W/, AI (CW* 3% at RT) 99.999% AI deformed at 20 K then at 80 K

24 K

12x10'

70 K 100 K 115 K 155 K

3

99.99% A1 (CW* 6% at RT) 99.999% AI 2 h at 470 K, then CW* by 0.5% at 77 K 99.999% A1 deformed at 85 K by and cycled lo2 times

83 K 119 K 110 K 155 K

1.08 x lo3 1.6 x lo-' 1.06~103 24x10-3 4 ~ 1 0 - * -lo-' 2x103 -2x10-3

130 K

-1

99.994% [111] c1001 1101 99.999% AI (CW' 18% at RT)

139 K 153 K 196 K 213 K

5x107

l@

-

AI

99.6% AI reduced by 69%

270°C

5xlO-l

-1.2~10-' -

A1

99.6% A1 reduced by 99.3%

270°C

5 x lo-'

-2 x lo-'

-

400°C

5x10-1

-lo-'

-

-1

48.2

2.32

10-3-10-2 depending on CW 7 . 8 5 ~lo-'

0.69

1.4x10-'

134

Grain boundary

26

25

1.6xlO-'

-

Point defect/

241

Alloy

AI AI

A1

AI AI

A1

AI

AI

c

Al

99.999% A1 deformed -300°C by 65%, annealed and deformed again 99.96% A1 area reduced 340°C by 75% annealed at 325°C for 2 h 99.991% A1 275 "C

AI

99.9990/, AI CW' 4%

A1

A1

A1 A1

AI

A1 A1-Ag

Al-Ag

then irradiated by neutrons at 80 K, annealed 360 K 99.9999wt% A1 (bamboo boundaries) 99.999wt% (3 h at 402°C) 99.999wt% (single crystal sheet) 99.9999wt% AI (jmlycrystallinewires) (grain sjzecwire dia.) (grain size>>wiredia.) %.999wt% (single crystal) 20% Ag (quenched from 520"C, aged at 155°C) 25% ~ e 3 0 0 / ,~g

annealed

*Cold worked.

110 K

3 3 3

10'-

Rex

1 . 5 ~ 1 0 - ~ 23

Bordoni type

17,18

-

Bordoni type Bordoni type ?

19

-

11.6 18.3

-

1

16.3 28.9 24

-

-30~10-3 -

-

4.1 6.0 19.5 38.5

144.3

Bordoni type Bordoni type Hasigutitype Hasiguti type

20

21

Bordoni type with 22 contribution from impurity-dislocation interactions Bordoni type 23 Bordoni type Bordoni type Point ddectfdis4 location interaction Relaxation of stresses by shear deformation and recrystallization Relaxation of stresees by shear deformation and recrystatlition Associated with gain boundaries Associated with dislocations Grain boundary

24

24

24 25

5

dislocation interaction -300°C

-1

396°C

8x1Ow3 0.52

400°C

1.3

1.44eV 1.S eV

Grain boundary

251

Polygonization

256

Dislocation network 258 212

210°C 170°C 365°C

-1 1

140°C

0.25

1.2 X lo-'

-

-1

-

140-170°C

-1

184eV 105-113

- 5 ~ l O - ~ 155 8 x lo-'

Grain boundary Not known Point defectsf 265 dislocation interaction Stress induced 27 change of local degree of precipitation Diffusioncon28 trolled rehatian of partial dislocations around precipitates

Damping cupacity

15-13

Table 15.8 ANELASTIC DAMPING--continued

Alloy

AI-Ag Ai-Ag AI-Ag

AI-CU AKu Al-Cu Al-CUMg-Si

Composition and physical condition

15% Ag (quenched from 200T) Al+30% Ag (1) quenched (2) aged at 520K Al-2,5,10,3Owt% Ag (lmm dia. wires of g.s. 0.75mm)

Peak temp.

Frequency Modulus Hz defect

-4 x

210°C

0.45 0.45

410K

-

8x

420K

-

14 x 10-3

400K; 450 K;

-1

16&

0.9

2 x 10-3

0.5

2.4~10-3

92

0.3

0.44

2x103

A1-0.25% Fe (annealed at 600°C for 6 h)

-280°C -310°C

2x10'

AI-Fe

AI-O.OS% Fe

-280°C

-1

Al-Fe

AI-0.16% Fe-0.5% Fe

31O-36O0C -1 440-480°C -1

AI-Fe

AI-FeCe

Al-MgSi Al-Mg

Rapidly quenched 475 K A-8.6wt% Fe-3.8wt% Ce (extrusioncompacted, rapidly solidified) AM.6% M e 215°C 0.6% Si (quenched from 480°C and aged at 230°C for 2 g h ) A1-0.03at% Mg (0.5% 243 K; tensile strain at 208 K) 333K

AI-Mg AI-Mg

2% Mg 5.45% Mg (quenched from 500"C, aged at 250'C)

AI-Mg

7.5% M g (annealed at 400°C then quenched)

AI-Mg

7.5% Mg (annealed at mot,cooled slowly)

AI-Mg

0.93% Mg-12.1% Mg

AI-MDFtSi Al-Si Ai-Si

RT 165°C

----

20-

Stressinduced change of shape of precipitate Polygonization

6x max

56.5

5 x 10-4 -2~10-3

117 167

-

-

140

RF$

-

25 247 247 301

30,31 30 256

Stressinduced 32 ordering of complex atom group ? 33 ? 33 Grain boundary

34

Depends on grain size Depends on grain sue

140 200

0.8

96 x 10-4

150

2.25

5.5 x 10-2

126

Stressinduced diffusion of solutes

0.32eV; 0.22 eV

Dragging of 299 solute atoms and atom/vacancy pairs Thermoelastic 36 Zener 37

-

Grain boundary 34 Related to relaxa- 34 tion of stresses and precipitation of Fe on grain boundaries zener 263

35

(9 -1

2.5 x io4 1.5

1.2 x 10-5 7 x 10-4

116.3

66.9

-

80°C 120°C 221"C 203°C

102.5 125.5 125.5 0.4-98

10-4-2 x

135.0

ZOOT

1 440K Al-l.O7wt% Mn0.52wt% FeO.llwt%Si (cold worked and precipitated) -1 Insoluble Si Dartkles 420 K in AI (solution-treatedand 110-180°C 1 aged)

Cold worked.

-4 x

40°C

100-

-

Associated with y Associated with clustering Zener in 92 solid solution Zenerinyphase 110 Zener; partial reversion of G.P. zones; garr.ma precipitation 128(117) Zener

variable

4% Cu (quenched from 175°C 520°C r e ~ r t e dat 200°C) 120°C 4% Cu (quenched, reverted, aged at 200°C for 144h) Al-O.OlSwt% CU 580°C (3 h at 402°C) Quenched from S O O T , zooc aged at 50°C

Activation energy Mechanism kJ mol-' or rype

Relaxation of solute 38 clusters Zener Zener ?

ZMla

39

Ke, 3 times wider 305 than single relaxation 0.92 eV

Relaxation at 298 Al-Si interface Migrates and falls to 311 zero during ageing; 312 vacancyjsi clusters

15-14 TnMe 15.8

Alloy

AI-Zn

E k i c properties, damping capacity and s h p memory alloys ANELASTIC DAMPING-COntiflUed

Composition and physical condition

3.7%Zn(quenched

Frequency Modulus

Peak temp.

Hz

21°C

026

A1050/SiC Composite Au 99.999% Au. (CW* 16% at 4.2 K)

300 K 43 K 65 K 77 K

0.07

Au

120 K 180 K 210 K

4 x 102 x 103

from 450°C to RT)

Au Au

Au Au

99.999% Au (annealed at 1 170 K for 4 h, then CW* 3% at 77 K) 99.999% Au (CW' 16% at 70 K)

130 K 190 K 210 K 99.999% Au (quenched) 160 K from 700°C) 230 K

0.5

0.5 0.5

4.0 4.0 4.0 -1

-

-

99.999% Au (quenched 290 K from 800'C) 99.999% (qwched 210 K from 1000°C) 220 K

defer

-

2 x 10-3

-1 -1

53

1.4 x IO-' 1.6 x IO-' 1.6 x lo-'

9.62 18.4 18.4

10-4 -5 x 10-3

-

-

10-4

4x 2.2 x 10-2 6 x lo-" 2 10-3

-

-2 x 10-3 1

Activation energy Mechanism k.f mol-' or type

-4~10-3 -4x10-*

-

Stress induced ordering of zinc atom-vacancy complexes Interface Bordoni type Bordoni type Bordoni type

Hasiguti type 35.7 Hasiguti type 58 177 Hasiguti type (two stages) 21.3 Hasiguti type Hasiguti type 32.84 34.7 Hasiguti type Associated with w9 . dislocations Associated with dislocations Associated with dislocations 57.7 Stress induced reorientation d

Rei: 40

252 1, 41 1, 41 1, 41 21

21 21 42 42 42 43 43 43

44 44

divacancis

Hasiguti type

Au

99.999 9% Au (quenched 0°C from looO°C)

99.99% Au (CW*, annealed at 6OO"C) Au 99.9998% Au (CW' 3@k annealed, 650-870 "C') Au 99.999 95% Au (annealed at 900°C) Au-Ag-Zn Au-42 At. % Ag15 At. % Zn Au

Au-CU

10 At. % 01-

90 At. % Cu Au-CU

10 At. % CU90 At. % Cu

Au-CU

10 Ai. % CU% Cu Au-25at% Cu (quenched) 90 At.

Au-Cu

Au-CUZn

(quenched and annealed) (quenched and annealed) 42 At.% Cu15 At. % Zn 21At.%Cu17 At. % Zn

Au-CUZn Au-Fe

63 At. % CU17 At. % Zn 5%Fe

Au-CU-

Zn

Au-Fe

7%Fe

*Cold worked.

330'C

* 10

7 x 10-48 x lo-'

62.7

0.7

Depends on

141.4

1.0 1.0

grain size 4.4 x 10-2 3.2 x lo-'

144.3 242.7

238°C 404°C -400°C

-1

-10-1

435

260°C

0.7

0.1 1

146

326392°C 552753 'C

1.0

3 . s ~10-30.57 0.14 0.76

114.6165.3 201.7342.3

175250°C 490K

1.0

5 x 10-22x104

-

1.0

-1

Stress induced reorientation of divacancies Grain boundary

45

Grain boundary Associated with grain boundaries Sliding at grain boundaries zener

47 47

%48

48

Point defects/orde.r

267

Zener Grain boundary

300°C

0.5

0.14 0.50

49

Adsorption of solute atoms on grain boundaries Grain boundaries

760K (all) 0.5

48

zener

(quenched only) 635K (all)

380°C

46

48

-

Order-disorder

49

-

pealr order-diS0rde.r

49

peak 340°C

0.5

2.6 x lo-'

-

365°C535"C 380°C564°C

-1

z.4x 10-3 1.5 x 10-2 1.9 x lo-'1.2 x 10-2

159 177.8 159 177.8

-1

Zener

49

Zener

51 51 51 51

Precipitation ofFe Zener F'recimtation of Fe

Damping capacity

15-15

Table 15.8 ANELASTIC DAMPING--continued

Alloy

Composition and physical condition

Peak temp.

Frequency Modulus Hz defect

Au-Fe

10% Fe-27% Fe

390°C

-1

3.5 x 10-2-

Actiuation energy Mechanism kJ mol-' or type

Re$

151-151.9 Zener

51

1.5x 10-2 AwNi

30 At. % Ni

397°C

1.0

-

1820

Zener

52

Au-Ni

Au-30 At. % Ni (quenched)

-380°C

-0.5

-10-1

88.3

53

Au-Ni

7.7 At. % Ni90.8 At. % Ni 15 At. % Zn Stoichiometric AuZn annealed

397°C 652°C 250°C 260°C290 "C 210 K 135°C

1.0

-

Zener, modified by quenched-in vacancies

Zener

52

0.7 0.2-1

4.2 x lo-' -10-2

182.0251.0 218 140

Zener Concerned with short-range order (1) Bordoni type Solute atom/defect interaction

49 54

Au-Zn

Au-Zn Be

Be

Cd-Mg Cd-Mg co CO

C0-C Co-Fe-Cr Cc-Ni Co-Ni Co-NiCr-W

Cr

-3

135°C

-1

4x 10-4

1oD

Be-l.4 % Fe interstitial impurities including oxygen Cd-29.3% Mg 5% Mg-3% Mg 99.23% Co (0.69% N)

05°C

1.22

10-2

63.6

Cold work induced 56 line defect interaction (?) Solute interaction 56 with lattice (?) Snoek type 57

026 0.29 max

80 79.5 40.6

Zener Zmer BordonitypeO)

99.23% Co (0.69% N) CW' at RT

103 263 K (two peaks)

51.0

io3

36.8 723

Point defecbldislocation interaction Twin boundaries (?) Movement of divacancies and dislocations Motion of C atom pairs in lattice

+

20°C 0.75 20°C 1.0 215 K 103 (two peaks)

2 8 0 ~ Heated in C atmosphere at 1050°C and quenched i i i ~ Co-37.8% Fe8.7% Cr. In magnetic field of 0.6 x lo3 A/M 340°C C0-2% Ni 430°C 150°C Co-23% Ni 310°C Co-22wt% Ni370°C 22wt% Cr-l4wt% W (wrought alloy) 99.8% cr 38°C

Cr-N Cr-Re-N

cu

Cr-35% Re (quenched from 1oOO"C in NH, atmosphere) 99.999% Cu (CW' at 77 K

~~

*Cold worked.

x

-

105x10'

1-16 x 105 4 x 10-4 103

159

3 x w3

-

-

-

1.8 x lo4

2.5 x -28 X 10-2 -2.9 x lo-' -3.1 x lo-'

-

2 10-3

-

160'C -36°C

1.0 3

1.5 10-3 -4x

101.7 115.1

155°C

1

up to 2.zX 10-3

130°C 190°C

1

-10-3

1

-10-3

-1 -1

-

-

Cr-0.004 5% N 35 ppm N (quenched from 83"C) (Annealed in NH3 at 1150°C for 48 h)

Cr-N Cr-N

~

-1

297 K 99.999% Co (quenched) 410K 600 K

CO

50.2

55 55

213K

98.6% Be (annealed)

BeFe-0

51.9 101.7

1.0 1.0

-

1.51.8 x 10'

1.5-

-

-

Ele&on spin redistribution at Curie point a-8 P b transformation a-8 phase transformation Snoek effect (C-C pairs)

58 59 4 4 4

60 61 62 63 63 63 63 259

64

85.8

Electron spin re distribution at Nee1 temp. (40°C) Snoek type Magnetomechanical damping Snoek type

89.1 126.4

Snoek type Snoek type

68

434 11.6

Niblett-Was type Bordoni type

69 69

65 66 67

15-16

Elastic properties, damping capacity and shape memory alloys

Table 15.8 ANELASTIC DAMPING-continued Activation

Peak temp.

Frequency Modulus Hz defict

anergy

Alloy

Composition and physical condition

cu

99.999% Cu (single

38 K

i.09X104 2 x 1 0 4

4.2

Bordoni type

77 K

79 K

1.09 x 10'

4 x lo-'

11.7

Bordoni type

99.999% Cu (single crystal (100) orientation) W.W% Cu (single crystal (110) orientation)

80°C

13

34 10-4

-

Bordoni type

19,41, 70,71, 19,41, m,71 238

70°C

13

11.4 x 10-4

-

Bordoni type

238

140 K Electrolytic Cu (Fatigued, 4 x 10' cycles)

0.3

-4x 10-4

-

Dislocation-

72

225 K

0.3

- 4 ~

-

240 K

0.3

.-2x10-*

-

165 K

0.3

-1x10-4

-

30K

6x10' 6 x 10' 6x10' 1.o

10-3 -3 x lo-' 10-4 4 x 10-5

-

1.o

1.2 x 10-1

33.9

238 K

1.o

1 x lo-'

41.4

1.0

211 x 10-2

157

cu

99.999% Cu (annealed at 215°C 500°C for 4h) 99.99% Cu (area reduced216"C 47%, annealed at 600°C for 2 h)

interaction 72 Dislocationvacancies interaction 72 Dislocationinterstitials interaction Dislocation72 interstitiah interaction Niblett-Wilks type 73 Bordoni type 13 Hasiguti type 73 Point defect, ds74 location interaction Point defect, d i e 74 location interaction 74 Rotation of split interstitiah (7) 75 Grain boundary

1.17

1.65 x lo-'

132

Grain boundary

5

cu

99.9999%

416°C

-1

-

435

48 76

735°C

-1

-0.2

169.5

Sliding at grain boundaries Sliding at grain boundaries Grain boundary Grain boundary Dislocation/ silver atom/ point defect interaction Bordoni type.

crystal) CW* YA at

cu

cu

cu

cu

99.999%Cu(deformed

cu

2.5% quenched in 70 K liquid He) 190 K 99.999% Cu (CW* 5% at 148 K 17 K) 170 K

cu

cu

-

0.2

31.0

99.999% Cu Cu4.71% Ag

300"C 550°C

5.0 1

4 x 10-2

-

1569 154.1

CU-Ag

Cu-0.1 At. % Ag cw*5%

223 K 283 K

5 x 103 5 x 10'

2.6 10-4 2 s 10-4

-

CU-AI

2% A1-10% AI (Deformed 3% at RT) C~-15wt% A1 (cold

145K

1.5 x 107

-

-

-60°C

-2

0.04

worked) CU-Al

CU-Al-Ni

CU-AU CU-AU

-

0.66 7~ 10-3 CU-16.8 At. % AI 360°C Cu-lSwt% AI 323 K at 520-680 -7.%t% Ni (solution- all rates treated at 1223K and cooled at various rates) Others at high rates &-25at% Au 680K -1 (annealed) 800 K -50°C -1 CU-l.Sat% Au (cold worked and annealed atlWC)

'Cold worked

Ref

&Vacancies

cu cu-Ag

Cu-A1

Mechonism

kJ mol-' or type

24

76

75 237 2so

77 308

174.9

Zener

Twin boundary relaxation of gamma-mart.

Zener

78 28 1

266

Grain boundarv Interaction betkeeu 310 dislocations and Au clusters

Damping capacity

1S17

Table 15.8 ANELASTIC DAMPING-continued

-

Activation Composition and vhysical wndition

Feak temp.

Frequency Modulus

energy

Hz

wect

kl mol-’ or type

cu-co

(Aged at 575°C for 3 min)

230°C

1

184.9

CuGa Cu-Fe

Cu-16 At. % Ga 0.5% Fe-lO% Fe

330°C 320°C350°C 480~550°C

1.0

7 x 10-4 (depends on ageing) 2 x 10-2 Depends on grain size Depends a

Alloy

-1 -1

grainsize

-

10-1

159 209

-

Cu-Fe

Up to 1.5% Fe 800°C(Quenched from 820°C) 850°C

-1

Cu-N1

25% Ni-75% Ni 34K (Quenched from 7 2 0 T to 240°C) 150K

-1 -1

-

Cu-3%Ni (Annealed at 1100°C) Cu45%Ni (Reduced by 90”/.at RT)

-580°C

-1

21 x 10-3

151

-600°C

-1

-2x 10-2

-

-800°C

-1

-5 x lo-’

208

59c 726°C 381°C

-1

Cu-NiZn

5.6 At. % Ni94.9 At. % Ni 20 At. % Zn10 At % Ni

1

0.1290.112 5.3 x 10- 3

Cu-NiZn

C~ZNiI.15a 0 . 9 2 single crystal

76 K

6.9

Cu-Pd

0.01% Fd-0.3% Pd

cu-R

Cu-Si Cu-Si

Cu-N.i Cu-Ni

Cu-Ni

79.9 111.3

RQ

Grain boundary

75

Zener Grain boundary

33 79

Connected with precipitation of Fe on Cu grains Connectedwith ageing of alloy

79

Associated with precipitation Associated with precipitation

81

80

81

zener

82 83

368-264

Associated with recrystallization 0 Associated with dislocations Grain boundary

197

Zener

a5

3 x 10-2

-

zener

244

71 K 6.9 3c150 K 5 x lo6

1.2 x 10-2 10-4-10-3

-

244 86

0.01% Pt-0.3% Pd

30-150 K 5 x lo6

1 0 - ~- 10-3

-

Cu+5.09 wt. % Si Cu-5.09wt% Si

200°C 200°C

7.5 x 10-3

118 28 k y l

l .74 eV 151-205

Ordering Overdamped resonance of dislocations Overdamped resonance of dislocations Precipitation of K’ Relaxation at ppt. interfaces in stacking faults Grain boundary Grain boundary

-

3 3

mol-

(precipitation treated)

86 248 306

R.T. 6x103 290-350°C 0.7

1.8 x 10-4 (At. :m Zn)l59-178

Thennoelastic

3.5 x lo-’9.2 x lod3 0.12 2.6x

Zener

s9

Grain boundary Diffusion of Zn accelerated by vacancies

90 91

Cu-Zn Cu-Zn

(a) Cu-31% Zn

Cu-za Cu-Zn

17.6 At. % Zn657-614 K 1.3 29.4 At. % Zn Cu-30% Zn 425°C 0.5 (8) 01-45 At. % Zn 70°C 0.9 (Quenched from 400°C)

Cu-Zn

(B) Cu-45 At.

% Zn

84

0.14-0.152

3% Sn-9% Sn 10% Zn-30% Zn

83

366°C 3 490-500°C 1.8

cu-sn

cu-z.n

12s

Mechanism

177°C

1820161.1 172(?) 69.5

zener

87 88 12

0.9

Stress induced

91

reorientationof C u atom pairs Stress relaxation at 8-a interfaces Stress relaxation at 8-y interfaces

91

Zena

92

eu-zn

(a+) C0-43 At.

% Zn

285°C

0.9

8x10-3

159

Cu-Zn

(8-y) Cu-50 At. % Zn

190°C

0.9

2.2~10-3

130

Cu-Zn-AI

77% Cu-890/. Cu 5% Zn-20% zn 2% AM% A1

623472K -1

2x10-3-

-

8.5 x 10-3

91 91

15-18

Elastic properties, damping capacity and shape memory alloys

Table 15.8 ANELASTIC DAMPING-continued

Alloy

Composition and physical condition

Cu-Zn-AI Cu-29.5% Zn-2.4% AI

Frequency Modulus Hz defect

593 K

1

3.5 x 10-2

1-6

zener

1

3.27 x 10-2 -1.5 x 10-3

-

1632

zener

Fe

Cu-17.00/. Zn-9.00/, AI 615 K (Re4ectrolytk) (CW* -50 K 5% at RT, in magnetic field of 7.5 x 104 A b ) Anaco (CW* at RT) 198 K

Fe

Armco (CW* at

Fe Fe

Cu-Zn-AI Fe

Fe

Fe-A1

Activation energy Mechanism W mo1-I or type

Peak temp.

230 K

103

-

54.8

CW* 40% at RT

275 "C

2.9

1.55 x 10-3

174

99.98% Fe ( 4 10-~CN) ~ Fe pure (R ratio 1600) irradiated 2 x 1OI8 cm-' at 20 K

526°C

1.03

192

Grain boundary

96

110 K

1.4

Depends on grain size 4 x 10-4

1.4

13 x loT4

155 K

1.4

55 x 10-4

180°C

0.6

3.5 x 10-3

121

320°C

0.6

6x

163

Magnetic relaxation of point defects Magnetic relaxation of point defects Relaxation of selfinterstitiah Movement of AI within tetrahedral lattice Movement of AI within tetrahedral lattice Movement of AI within tetrahedral lattice Zener zener

246

128 K

-

RT)

Fe-40 At. % AI

103

44.4

Fe-40 At. % AI

440"C 550°C

0.6 0.6

1x 10-3 5 x 10-4

-

Fe-Ai

Fe-17 At. % Al

520°C

1.3

1x 10-2

234

FC-AI-C

Fe-19.3 At. % AI(101%c (QWCW from 720% aged)

130°C

1.4

-1~10-3

99.6

1.4 12

-5 x IO-' -10-2

-

12 14.0 -1

-3 x lo-'

-

-

-10-4 -3 x 10-3

-

Fe-O).02%C 27 "C Fe-0.4% C (Martensite). 200°C (Quenched from 850°C, tempered at 300°C for 1h) Fe-0,02% C (Quenched 210°C from 700"C, CW* 52%, aged)

0.27 -1

2 x 10-2 -10-2

84.1 84.5

1

-5 x lo-'

-

FC4I-C Fe-B Fe-B Fe-C Fe-C

Fe-C

168°C 41 "C Fe-0.7 At. % AI0.01% c Fb9At. % Al-O.Ol% C 100°C Fe405% B 79 T 260 K Fe-So ppm B (C impurities) 50 "C

-

184

63 54

FbC Fe-C

-

FA.Ol% C (CW* 25%) 235°C 353 "C

2.20 8 x lo-' 6.65 x lo6 -3 x IO-'

Fe-C

Fe-O.O22% C

520°C

1.0

380K

6xW

Depends on 347 grain size -5~lO-~-

526°C683"C 661°C

1.0

3xlO-'-

Fe-Co-Cr Fe-54%C+lff/.

Fe-Cr FbCr

93

93 Associated with 94 motion of kinks in dislocations Pointdefect/dis4 location interaction Point defect/&4 location interaction 95 Kdster type

105

Fe-AI

Fe-Al-C

Ref:

1.2% Cr-43% Cr Fe-16xCr

*Cold workad

Cr

10-2

-1

3.18 x loS2

138 80.17

215.5296.2 233

246 246 97

97 98

Stressinduceddif- 99 fusion of C in ordered FePM lattice

0

Snoek type

99

0 99 Snoek type 100 Snoek type due to B 101 Snoek type due to C Snoek type Associated with dislocations

102 103

Dislocation movement between pinning points (precipitates) Koster peak Snoek type

104

Grain boundary

107

105 106

Macro-eddycurrent 108 peak Grain boundary 109 Grain boundary

110

Damping capacity

15-19

T a k 15.8 ANELASTIC DAMPING--continued Activation Alloy

Composition and physical condition

Peak temp.

FeCr

Fe-22.5% Cr

662°C

FsCr Fe-Cr

Fe-22.5% Cr -560°C Fel7wt% Cr-250K Deuterium (cold worked) F+13at% Cr-6at% Al- 450°C; 2at% MA.OSat% Ce 624°C; 690°C Fe-27at% Cr-7at% Al- 523°C; 2at% Mo-0.056at% Ce 663°C; 713°C F+23at% C r d a t % Al- 529°C; 632°C; 0.065at% Y 690°C Fe-(1.2% Cr-5.2% Cr)- -320K C (Quenched from 750°C) Fe-4.2% Cr-N (Several Peaks) 266 K339 K Fe-16.6wt% Cr270/250"C 130/200ppm N (quenched from 1OOOT) F+16.6wt% CrPeak 480/580ppm N broadened 304L stainless steel 335340 K (cold worked)

F&-

Al-RE

F4r-C Fe-Cr-N

Fe-Cr-'N

Fe-Cr-Ni

Fe-CrNi (-HI Fe-Cr-Ni

304, 316 and 310s (+-loat% H) (electrolytically charged with H) Sus 310S, 316 and 304 (H charged only) (pluscold-work)

Frequency Modulus Hz defct

222

Grain boundary

110

-1

1.1 x 10-2

222

Zener Snoek

111 264

3OC-2000

-1

(CW* 0.5%)

Fe-Mn-C Fe-l8.5% Mn-0.7% C Fe-Mn-C

-

-

3.6eV; 4.0eV-; 3.3 eV; 3.9eV Snoek type

112

u p to 2.3 x 10-3

67.892.0

Motion of N atoms in various environments

113

-0.9

Snoek

290

-

AsFociated with

-1

martensitic phase 0.6eV ? but height (other depends on amount peaks at of cold work 0.4, 0.4eV) 49.0 Stress-induced 49.0 ordering of H pairs

1000

2OC-2ooO

300K

-550

1.5

1.0 1.0

H-H Snoek

289

303

280

Bordoni H-lattice defects

8x 1.6 x 10-3

-

150K -180K 130K; 170K; 330 K

8 x lo4 -2 x 10-4 8 ~ 1 0 ~- 6 . 5 ~ 1 0 - ~1 0.22; 0.35;

35 K 120 K 250°C

1.0 1.0

Fe-15.5% Mn-0.35% C 285°C

Zener ( F 4 r pairs); 294 solute G.B. peak of FeCr: ditto F e R E

75.3182.72

30K 1P6K

aFe-D

3.3eV; 4.0eV

10-2

230K 300K

-

_.

0.67, 0.59: 0.55 0.61; 0.56; 0.51

aFe-H aFe-H

Fe-H (aged at 60°C for 5 h) Fe (-H) Pure Fe electrolyticaUy charged with H (deformed before charging)

Ref:

0.55 x 10-2

FeCr-Ni 304L stainless steel (cold-worked)

Fe-H

Mechanism

kJ mol-' or type

-1

3WK+ 330 K (CW) and 230K (H+CW) 325 and -500 360 K

Fe( 0.029% 0)(CW*) Nb-0.014% C

152°C 283°C

1 1

-9x10-3 -1~10-3

410°C

1

-1~10-3

-

259°C

0.57

4x

139.3

Nb

Nb-AI

Nb-AI Nb-C

Ref:

Hz

Associated with point defect complexes Associated with point defect complexes ?

Dislocation damping

151, 163, 164 151, 163 164 164 164 153, 165, 166

Snoek type due to N 167 Snoek type due to 0 167 167 Relaxation of 168 ordered cluster of interstitials near dislocations Snoek type due to N 169 Snoek type due to 0 169 Dislocation/solute interaction

Snoek type

169 170, 171

Nb Nb

High purity single 270 K crystal 180 at ppm H. CW at 320 K Nb single crystal 143 K R. ratio 2500

+

a2 121 K

Nb-Mo Nb

1 . 3 ~ 1 0 ~3 . 0 ~lo-'

-

Snoek-Koster type

239

29.7

Formation of kinkpairs in non-screw dislocation Kink difiusion in screw dislocation Type of Bordoni mechanism Motion of dislocations Motion of dislocations Bordoni type (?)

249

Motion of dislocations Interaction of dislocations and impurity atoms Motion of dislocation

162

0.5

10~10-3

0.5

6 ~ 1 0 - ~ 19.8

180-220 K 2-2 x 10' 1.3yi M0-16% MO (CW* at RT) 3.24 K 8x104 99.97% Nb(CW*) (Superconducting type) 2.08 K 8 x lo4 (Normaltype)

w:

5~10-*1 10-4 -2x10-'

24.1 0.18

- 4 ~ 1 0 - ~ 0.15

-

Nb

Zone re6ned (CW* 5% at RT)

11-19 K (Broad)

8.8

10-4

Nb

99.9% Nb (CW*)

-39K

2x1041 x 105 2x10'1 105

-2x10-4

1.6

-1 x10-4

24.1

12 x 10-2

-

-180K Nb

High purity single crystal 190 K CW at 320 K

*Cold worked.

1.3 x lo3

249 153, 166 160 160 161

162 239

Damping capacity

15-25

TaMe 158 ANELASTIC DAMPING-continued

Composition and physical condition

Alloy

Nb-MO0

Nb-N

Nb5.3 At. 04 MO0.16 At. 5; O (Homogenized at 12OO’C for 15 min) Nb-0.018”/,N

Nb-0.0667; N (CW*100,b) Nb-N-T Nb-O.SOat% N0.3at% T (Tritium) N b (-0) ‘Pure’ nobium (wire) Nb-N

Activation energy Mechunism kJ mol-’ or type

R&

-

Snoek type

172

temp.

Frequency Modulus Hz d@t

167°C

0.6

-

274‘C

0.55

1.1x 10-2

145.6

Snoek ?ype

170, 171

500°C

0.31

2.4 x lo-*

20 1

Koster type

113

Ped

10-2

N/H pairs; N/T pairs 297

57K;85K -1

Nb-0 Nb-0

M . 1 8 At. % 0 W.026% 0

152°C 168°C

0.6 2.13

Nb-0

Nb-50 to lOOOppm 0

543-575K 692-726K 618K (10W 0) 621K (high 0) 420K

1 1 1

ExtriniSic 287 double-kwO atoms Intrinsic doubk0.8 eV kink on screw disloc. T h d unpinning of scaew disloc. from 0 Snoek type 172 114.2 Snoek type 174 171 2.W2.06eV 170 1.68-1.81eV 1.49eV

1

1.5OeV

-1

-5 x

500K

-1

-1 x 10-3

0.6eV

W 3 5 0 K -1 350-360K -500K

(worked polycrystals)

Nb-0-N

W

T

Nb (-Ta)

Nb-1.2 At. % 00.11 At. % N [cw*34%)

-10-2 1.6 x

-

50K;80K -1 M . 5 6 a t % 00.3at% T (tritium) 470 K M . O 3 w t % Ta (70 ppm 0 , 3 0 ppm N) (neutron irradiated and annealed 1.25mm wires) 670 K

0 plus irradiation defeas

Nb48% Ti

100°C

0.6

- 7 ~ 1 0 - ~ 100.0

Nb-Ti

Nb48% Ti (N atmosphere at 1200°C for 1 h) Nb-Sat% Ti (plus D)

340°C

0.6

-

50K IOOK 170~

20 x lo3 20x103 20~103

-200K 645and 685 K

2-2x10’ -1

Nb-V Nb-W-N

M.3% v Nb-N (wires)

10-2

Nb-Zr

Nb-1.0% Zr Nb-l%Zr-O+traces ofN

2.5~10-3

143 and 153 respeaively 143,153 and 167 respectively

1 x 10-3

-

-200K -500°C

2-2x10’ 5x104

-500°C

5 ~ 1 0 ~-

111.3

-

123.4

- 5 0 0 ~ 5x104

*Cold worked.

-

defects Snoekdueto 0 impurities

176

Snoek due to N

176 273

-1 Nb-2,6md 12at% W-N 645,685 and 745K

Nb-Zr

283

N plus irradiation

Nb-Ti

Nb-Ti

Segregation of 0 175 atoms to dislocations Segregation of N 175 atoms to dislocations O/H pairs; O/T pairs 297

-

110.9

Ti-D complexes reorientation Dislocation damping 153 Snoek 285

Dislocation damping Snoek due to 0 in Nb Substitutionah interstitial process involving 0 Substitutionalinterstitial process involvine -0 oairs .

153 177 177 177

15-26

Elastic properties, damping capacity and shape memory alloys

Table 15.8 ANELASTIC DAMPING-continued

Alloy

Composition and physical condition

NbZr

Ni

Zone refined (CW*)

Ni

Zone refined single crystal (CW*)

Ni

99.99% Ni (CW* at RT)

Activation energy Mechanism kJ mol-’ or type

Peak temp.

Frequency Modulus Hz defect

-500°C

5x104

-

146.4

-500°C

5 ~ 1 0 ~-

147.3

2x10-335 10-3 248K 3x104 1x 10-2-0.10 145-123 K - 2 x lo4 u p to 1.6 10-3 223-263 K - 2 x lo4 u p to 3.0 x 10 155 K lo’ 29.7 138 K

3x104

4

Grain boundary

5

183

-1

Grain boundary Stress relaxation at polygonized boundaries Diffusion of C in Ni-AI All grain boundary

-1 0.5 -1 2

Diffusion of C in Ni Dislocation-C Grain boundary

184 216 185

Long range order

282

370 200

Grainboundary Grain boundary

257 257

98.3

Diffusion of C in Ni-Cr Magnetomechanical damping Magnetic ordering Magnetomechanical damping Grain boundary

186

350 K

103

-

51.0

397 K

103

-

69.4

0.7

-

77.0

Ni

99.999 9% Ni

150°C

1

-0.1

-

Ni

99.99% Ni. (Area reduced 90%. annealed at 905°C for 1 h) 99.98% Ni

432°C

1.41

3.4x10-*

308

44s 460°C 63& 720 “C 280°C

0.5

0.10

0.5

0.12

0.5

-

-

Ni-B Ni-C Ni-C Ni-Cr

Ni-0.0035wt% B (quenched) (cold-worked) 0.5% Cr

Ni-Cr

Ni-33.3at% Cr

Ni-Cr Ni-20wt% Cr Ni-Cr-Ce Ni-Mwt% Cr180 at ppm Ce Ni-Cr-C Ni-20% Cr-1.87”/. C (Quenched) Ni-Cu Ni-20% Cu Ni-Zr

0.1%Zr-0.5% Zr

470°C; 670°C 550°C 230°C -430°C 53cL 800°C 390°C; 570°C -700°C -700°C

Dependson grain size

-1 -1

250°C

0.9

-

-140°C

1

-10-2

(Varies) -200°C

1 -1

Pd-H

-450°C

-1

600700°C 147°C

-1

Amorphous Pd6at% Cu-16.5at% Si (1 m m wire) 99.999% Pd (Annealed, 7cL80 K electrolytically loaded with H) 40 At. H75 At. 04 H

., 1940.58. 473. 37. W. G. Nilson, Canad. 1.Phys., 1961,39, 119. 38. B. N. Dey and M. A. Quader, Canad. J. Phys., 1965,43(71, 1347. 39. J. Belson, D.Lemercier, P. Moser and P. Vigier, Phys. Status Solidii, 1970,40,647. 40. H.Haefner and W. Schneider, Phys. Status Solidii, 1971, 4a. K221. 41. S. Okuda. J. appl. Phys, 1963,34, 3107. 42. S. Okuda and R. R. Hasiguti, Acra Met., 1963, 11, 257. 43. C. H. Neurnan. J. Phys. C k m Solids, 1966.27 (2),427. 44. S. Okuda and R. R. Hasiguti, J. p h p . SOC. Japan. 1964, 19 (2).242. 45. D. G. Frankiin and H. K. Birnbaum, Acta Met., 1971, 19 (9),965. 46. W.Koster, L. Bangert and J. Hafner, 2 . Metall, 1956,47,224. 47. D. R. Mash and L. D. Hall, Trans. AZMME, 1953, 197. 937. 48. M. E. De Morton and G. M. Leak, Metal Sci. J., 1%7, 1, 166. 49. A. Pinon and C. Wert, Acta Met, 1962, IO, 299. 50. G. K. Mallseva, V. S. Postnikov and V. V. Usanov, Phys. Mer. Metallogr., 1963, 16 (2), 120. 51. B. A. Mynard and G. M. Leak, Phys. Status Solidii, 1970,40 (i), 113. 52. C. Ang, J. Sivertson and C. Wert, Acta Met., 1955, 3. 558. 53. J. R. Cost, Acta Met., 1965, 13 (121 1263. 54. K. Mukherjee, J. appl. Phys., 1966, 37 (4),1941. 55. C. Ang and K. T. Kamber, J . appl. Phys., 1963,34,3405. 56. Choh-Yi Ang and K. T. Kamber, J. appl. Phys., 1963,34 (ll),3405. 57. M.J. Elias and R. Rawling, J, Less-common Metals, 1965, 9 (4),305. 58. J. Lulay and C. Wert, Acta Met., 1956,4,627. 59. J. Enrietto and C. Wert, Acta Mer., 1958,6, 130. 60. R. Karnel and K. Z. Botros, Phys. Status Solidii, 1965, 12 (l),399. 61. G. Mah and C. A. Wert, Trans. met. SOC.AIME, 1968,242 (7).1211. 62. K. P. Belov. G. I. Katayev and R. Z. Levitin, J. appl. Phys., 1960, 31 (Suppl. l), 1535. 63. V. N.Belko, B. M. Darinskiy, V. S . Postnikov and I. M. Sharshakov, Phys. Met. Merallogr, 1969, 27 (I), 140. 64. M. E.Fine, E. S. Greiner and W. C. Ellis, J . Metals. N. Y;, 1951, 191,56. 65. M.E. De Morton, J. appl. Phys., 1962, 33, 2768. 66. M. J. Klein, J . appl. Phys., 1967. 38 (2),819. 67. M.J. Kelin and A. H. Claver, Trans. met. Soc., A I M E , 1965,233 (Il),1771. 68. M.J. Klein, Trans. Met. Sm.,A I M E , 1965, 233 (l), 1943. 69. S. Okuda, J. appl. Phys., 1963, 34 (lo), 3107. 70. D. H. Niblett and J. Wilks, Phil. Mag, 1956, 1, 415. 71. H. S. Sack, Acta Met., 1962, IO, 455. 72. P. Bajons and B. Weiss, Scripta Metall.. 1971,5, 511. 73. B. M. Mecs and A. S. Nowick, Acta Met., 1965, 13 (7),771. 74. M. Koiwa and R. R. Hasiguti, Acta Met., 1963,11, 1215. 75. D. T. Peters, J. C. Bisseliches and J. W. Spretnak, Trans. me?. Sm.A I M E , 1964, 230 (3), 530. 76. M.E. De Morton and G. M. Leak, Acta Met.,1966, 14 (9), 1140. 77. H. Kayano, K. Kamigaki and S. Koda, J. phys. Sm. Japan, 1967,U. (3), 649. 78. C. Y. Li and A. S. Nowick, Phys. Ran., 1956, 103,294. 79. A. A. Karmazin and V. I. Startsev, Phys. Met. Metallogr, 1970,29 (6),191. 80. V. S. Postnikov, S. A. Ammer, A. T. Kosilov and A. M. Belikov, Phys. Met. Mrtallogr., 1966, 21 (5).121. 81. B. N. Dey, Scripta Metall., 1968. 2 (9),501. 82. J. T. A. Roberts and P. Barrand, Scripta Metall, 1969, 3 (I), 29. 83. V. S. Postnikov, I. V. Zolotukhin and I. S. F’ushkh-Phys. Met. Metallogr., 1968, 26 (4). 147. 84. J. T. A. Roberts, Metall. Trans., 1970, 1 (9), 2487. 85. M.G. Coleman and C. A. Wen, Trans.Met. Soc. AIME, 1966,236 (4), 501. 86. A. Ikushima and T. Kaneda, Truns. Japan Inst. Metals, 1968,9 (Suppl). 87. K. J. Marsh, Acta Met., 1954,2, 530.

Damping capacity

15-33

88. R. R. Randall, F. C. Rose and C. Zener, Phys. Reu., 1939, 56, 343. K. M. Shtrakhman, Phys. Met. Metallogr., 1967. 24 (3), 116. T. S. KZ, J . appl. Phys., 1948, 19, 285. L. M. Clareborough, Acta Met., 1957, 5, 413. K. M. Shtrakhman, Yu. S. Logvinenko, V. F. Grishchenko and Yu. V. Piguzov, Soviet Phys. solid Sr.. 1971,

89. 90. 91. 92.

13 (3,1238.

K. M. Shtrakhman, Sooiet Phys. solid St., 1967, 9 (6), 1360. K. Takita and K. Sakamoto, Scripta Metall., 1970, 4 (5). 403. A. I. Surin and M. S. Blanter, Phys. Met. Merallogr., 1970, 29 (I), 199. G. M. Leak, Proc. phys. Soc., Lond., 1961, 78, 1520. J. D e l a p k , J. Hillairet and A. Silvent, C.r. hebd. SPanc. A d . Sci., Pnris, 1966 (c), 262 (4), 319. D. B. Fishbach, Acta Met., 1962, 10. 319. K. Tanaka, J . phys. Sac. Japan, 1971, 30 (2), 404. W.R. Thomas and G. M. Leak, Nature, Lond., 1955,176,29. Y. Hayashi and T. Sugeno, Acta M e t , 1970, 18 (6). 693. C . A. Wert, Phys. Rev., 1950,79, 601. 103. N. Blackwell, Nature, Lond., 1966, 211 (SOSO), 733. 104. P. Barrand and G. M. Leak, Acta Met., 1964, 12 (IO), 1147. 105. K.Kamber, D. Keefer and C. Wert, Acta Met., 1961. 9, 403. 106. A. E Lord and D. N. Besherq Acta Met., 1966, 14 (12), 1659. 107. G. W. Miles and G . M. Leak, Proc. phys. SOC.,Lond., 1961, 78. 1529. 108. T. Maeda, Japan 1. appl. Phys, 1971, 10 (IO), 1299. 109. P. Barrand, Acta Met., 1966, 14 (lo), 1247. 110. P. Barrand, MetaI Sci. J., 1967, 1, 127. 111. P. Barrand, Metal Sei. J., 1967, 1, 54. 112. C. R. Ward and G. M. Leak, Metallurgical, ital., 1970, 62 (8), 302. 113. I. G. Ritchie and R. Rawlings, Acta Met., 1967, 15 (3), 491. 114. 'W.R. Heller, Acta Met., 1961, 9, 600. 115. R. Gibala, Acta Met., 1967, 15 (2), 428. 116. T. S. KZ and C. T. Tsien, Phys. Met. Metallogr., 1957,4 (2). 78. 117. 'V. Kandarpa and J. W . Spretnak, Trans. Met. Soc. AIME, 1969, 245 (7), 1439. Couper and R. Kennedy, J. Iron Steel Inst., 1967, 205 (6). 642. 118. G. .I. 119. E. T. Stephenson, Metall. Trans., 1971, 2 (6), 1613. 120. .1. D. Fast and M. B. Vemjp, J . Iron Steel Inst., 1955, 180, 337. 121. X. S. Lebyedev and V. S. Postnikov, Phys. Met. Metallogr., 1959, 8 (2), 134. 122. D. Siddell and Z. C. Szkopiak, Metall. Trans., 1972, 3 (7), 1907. 123. Yu. V. Grdina, Ye. E. Glikman and Yu. V. Piguzov, Phys. Met. Metallogr., 1966, 21 (4). 90. 124. D. A. Leak, W. R. Thomas and G. M. Leak, Acta .Met., 1955,3, 501. 125. 0.Szab&Miszenti, Acta Met.. 1970, 18 (5), 477. 126. 1. Stanley and C. Wert,J . appl. Phys., 1961, 32, 267. 127. R. M. Jamieson and R. Kennedy, J . Iron Steel Inst., 1966, 204 (2), 1208. 128. H.Sekine, T. Inoue and M.Ogasawara, Japan. J . appl. Phys., 1967. 6 (21), 212. 129. J. D. Fast and J. L. Meijering, Philips Res. Rep., 1953, 8, 1. 130. W . Hermann, Solid State Commun, 1968, 6 (9), 641. 131. C. F. Burdett, Phil Mag., 1968, 18 (154), 745. 132. B. M. Mecs and A. S. Nowick, Appl. Phys. Letters, 1966, 8 (4), 75. 133. A. Zuckerwar and W. Pechhold, Z. Angew. Phys., 1968,m(3), 134. 134. K. Ohori and K. Sumino, Phys. Status Solidii, 1972(a). 9 (l), 151. 135. P. D. Southgate. Proc. phys. Soc. Lond., 1960.76, 385, 398. 136. L. N. Aleksandrov, Yu. N. Golobokov, V. N. Orlov and F. L. 'E&? man. Sooiet Phys. solid St., 1969,lO (9), 93. 94. 95. 96. 97. 98. 99. 100. 101. 102.

137. 138. 139. 140. 141. 142. 143. 144. 145. 146.

147. 148. 149. 150. 151. 152. 153. 154.

2269. F. Cakecchi, P. Gondi and S . Mantovani, J. appl. Phys., 1969, 40 (12). 4798. E. Bisogni and C. Wert, US Air Force, Sci. Res. Rep., 1961, Contract AF49(638)672. T. Alper and G. A. Saunders, Phil. Mag., 1969,20 (164). 225. M. E. De Morton, Phys. Status Solidii, 1968, 126, K73. V. S. Postnikov, I. V. Zolotukhin, V. N. Burmistrov and I. M.Sharshakov, Phys. Met. Metallogr., 1969.28 (4), 210. M.J. Murray, J . Less-common Metals, 1968, 15 (40, 425. T. D. Gulden and J. C. Shyne, J . Inst. Metals, 1968, 96 (9,139. T. D. Gulden and J. C. Shyne, J . Inst. Metals, 1968, 96 (5), 143. D. P. Seraphim and A. S . Nowick, Acta Met., 1961, 9, 85. J. M. Roberts. Trans. Japan Inst. Metals, 1968, 9 (Suppl.), 69. R. T. C. Tsui and H.S. Sack, Acta Met., 1967, 15 (ll), 1715. H.L. Caswell, J . appl. Phys., 1958, 29, 1210. S . Koda, K. Kamigaki and H. Kayano, J . phys. SOC. Japan, 1963, 18 (Suppl. l), 195. A. V. Siefert and F. T. Worrel, J . appl. Phys., 1951, 22, 1257. R. H. Chalmers and J. Schultz, Acta Met., 1962.10.466. 8.Muhlbach, Phys. Status Salidii, 1969, 36 (I), K33. R. Gibala, M. K. Korenko, M.F. Amateau and T. E. Mitchell, J . Phys. Chem. Solids. 1970, 3 (8), 1889. G. Rieu, J. De Fouquet and A. Nadeau, C.r. hebd. Sdanc. Acad. Sci., Paris, 1970 (c), 270 (3), 287.

15-34

Elastic properties, damping capacity and shape memory alloys

155. S. Z.Bokshtein, M. B. Bronfin, et al., Souiet Phys. solid St., 1964. 5 (ll),2253. 156. Yu. V. Piguzov, W. D. Werner and I. Ya. Rzhevskaya, Phys. Met. Metullogr., 1967,24 (3),179. 157. R. H.Schnitzel, Trans. Met. Soc. AIME, 1964, 230 (3), 609. 158. M.J. Murray, Phil. Mag., 1969, 20 (165),561. 159. A. A. Belyakov, V. P. Yelyutin and Ye. I. Mozzhukhin, Phys. Mer. Metallogr., 1967. 23 (2),115. 160. E. J. Kramer and C. L. Bauer, Phys. Rev., 1967, 163 (2). 407. 161. J. Schultz, Bull. A m phys. SOC, 1964, 9, 214. 162. F. M. Manolai and M. Npovo, Solid State Conumm., 1969, 7 (1). 103. 163. J. Filloux, H.Harper and R. H. Chalmers, Bull. Am. phys. Soc., 1964.9, 230. 164. M. W. Stanley and 2. C. Szkopiak, J . Inst. Metals, 1966,94 (2), 79. 165. M. F. Amateau, R. Gibala and T. E. Mitchell, Scripta Mefall., 1968, 2 (2). 123. 166. M. F. Amateau. T. E. Mitchell and R. Gibala, Phys. Status Solidit 1969. 36 ( l k 407. 167. R. A. Hoffman and C. A. Werf J . appL Phys., 1966,37 (l), 237. 168. F. SchlZt, Trans. lapun Inst. Metak, 1968, 9 (SuppL), 64. 169. E. Davenport and G. Mah, Metall. Truns., 1970, I (5). 1452. 170. R. W. Powers and M. V. Doyle, J . Metals, NX, 1957,9, 1285. 171. R. W. Powers and M. V . Doyle. J . appl. Phys., 1959, 30, 514. 172. C.Vercaemer and A. Clauss, C.r. he&. Sianc. Acad. Sci.. Paris 1969 (c). 269 (15). 803. 173. D. H. Boone and C. Wert, J . phys. SOC.Japan, 1963, 18 (Suppl. 1). 141. 174. C. Y. Ang, Acta Mer., 1953,1, 123. 175. D. J. Van Ooijen and A. S. Van Der Goot, Acta Met., 1966,,14 (8), 1008. 176. G. Vidal and H. Bibring, C.r. hebd. SLaanc. Acad. Sci., Paris, 1965,260 (3),857. 177. R. E. Miner, D. F. Gibbons and R. Gibala, Acta Met., 1970,18 (4),419. 178. A. W. Sommers and D. N. Beshers, J . appl. Phys., 1966,37 (13),4603. 179. P. S. Venkatesan and D. N. Beshers, J . appl. Phys., 1970,41 (l),42. 180. A. Seeger, P. Schiller and H. Kronmiiller, Phil.Mag., 1960,5, 853. 181. P.Schiller, H.Kronmiiller and A. Seeger, Actd Met., 1962, 10, 333. 182. J. T.A. Roberts and P. Barrand, Acta Mer., 1967, 15 (ll),1685. 183. 0.I. Datsko and V. A. Pavlov, Phys. Met. Metallogr.. 1958,6 (5). 122. 184. T.S. K8, Acta phys. sin..1955, 11 (5),405. 185. V. N. Gridnev, A. I. Yefimov and N. P. Kushnareva, Phys. Met. Metallogr., 1967,23 (4),142 186. Y. S. Avraamov, L. N. Belyakov and B. G. Livshits, Phys. Met. Metallogi-.. 1958, 6 (I), 104. 187. V. M. Azhazha, N. P. Bondarenko, M. P. Zeydlits and B. I. Shapoval. Phys. Met. Meetallogr., 1970,29 (2), 101. 188. R. R. Arons, J. Bouman, M. Witzenbeek, P. T. A. Klaase, C. Tuyn, G. Leferink and G. De Vries, Acta Met., 1967,15 (I),144. 189. R. R. Arons, C. Tuyn and G. De Vries, Acta Met., 1967, 15 (lo),1673. 190. J. Coremberg and F. M. Mazzolai, Solid State Convnun, 1967. 6 (l), 1. 191. V. 0.Shestopal, Phys. Met. Metullogr., 1968, 26 (6), 176. 192. M. Rosen, G. Erez and S. Shtrikman, J . Phys. Chem. Solids, 1969,30 (5),1063. 193. R. Schnitzel, J . appl. Phys., 1959,30, 2011. 194. L. N. Aleksandrov, M. 1. Zotov, R. S h Ibragimov and F. L.'Edel' man, Souiet Phys. solid St., 1970. I 1 (7), 1494. 195. P.D. Southgate, Proc. phys. Soc. Lond., 1957,70 (B). 804. 196. P. D. Southgate, Proc. phys. Soc. Lond., 196Q76.385.398, 197. B. S . Berry, J . Phys. Chem Solids, 1970, 13 (81, 1827. 198. L. Rotherham, A. D. N. Smith and G. B. Greenough, J. Inst. Metals, 1951,79,439. 199. L. Verdini and L.A. Vienneau, Canud. J . Phys., 1968,46 (23),2715. 200. R. W. Powers and M. V. Doyle, J . appl. Phys., 1957,28, 255. 201. P. Kofstad and R. A. Butera, J . appl. Phys., 1963,34, 1517. 202. R. W. Powers and M. V. Doyle, Acta Met., 1956,4, 233. 203. R. W. Powers and M. V. Doyle, Acta Met., 1955,3, 135. 204. R. W. Powers and M. V. Doyle, Trans. AIMME, 1959, 215, 655. 205. G.Schoek and M. Mondino, J. phys. Soc. Japan, 1963, 18 (Suppl. l), 149. 206. A. A. Sagues and R. Gibala, Scripta Metall., 1971,5 (8), 689. 207,G. Arlt and W. Hermann, Solid Stare Commun., 1969, 7 (l),75. 208. J. Winter and S. Weinig, Trans. AIMME, 1959,215, 74. 209 J. E.Doherty and D. F. Gibbons, Acta Met., 1971,119 (4),275. 210. W. Koster, L. Bangert and M. Evers, Z. Metall., 1956, 47, 564. 211. R. R. Hasiguti and K.Iwasaki, J . appl. Phys., 1968,39 (5),2182. 212 W.J. Bratina, Acta Met., 1962, IO, 332. 213. J. N. Pratt, W.J. Bratina and B. Chalmers, Acta Mee., 1954, 2,203. 214. D. Gupta and S. Weinig, Acta Met., 1962, IO, 292. 215. R. W. Powers and M. V. Doyle, Acta Met., 1958, 6, 643. 216. G. Cannelli and F. M. Mazzolai J . Phys. C h m Solids, 1970,31 (s), 1913. 217. R A. Butera and P. Kofstad, J . appl. Phys., 1963,34,2172. 218. R. W.Powers, Acta Met., 1954,2,604. 219. L N.Aleksandrov and V. S. Mordyuk, Phys. Met. Merallogr., 1 9 6 2 1 (l), 101. 220. R H. Chalmers and J. Schultz, Phys. Reo. Letters, 1%1,6,273. 221. R H.Schnitzel, Trans. Met. Soc. AIME, 1965,233 (l), 186. '

Damping capacity

15-35

L. H. Aleksandrov, Phys. Met. Metallogr., 1962, 13 (4), 143. I. Berlec, Metali. Trans, 1970,l (lo), 2677. V. 0. Shestopal, Phys. Met. Metallogr., 1968, 25 (a), 148. V. P. Yelyutin and A. IL Natanson, Phys. Met. Metallogr., 1963, 15 (5), 89. H. Kayano, J. phys. SOC. Japan, 1969, 26 (3), 733. 6. Roberts, P. Barrand and G. M. Leak, Scripta Metall., 1969, 3 (6), 409. J. E Doherty and D. F. Gibbons, J. appl. Phys.,1971,42 (ll), 4502 I?. L.Gruzin and A. N. Semenikhin, Phys:Met. Metallogr., 1963, 1J (5), 128. W.J. Bratina and W.C. Winegard, J. Metals, N X , 19.548, 186. K. Bungardt and H.Preisendanz, 2.Metall., 1960,51, 280. Y.Y. Ivanov, B. I. Shapoval and V. M. Amonenko, Phys. Met. Metdlogr., 1961,ll (l), 55. P. Boch, J. Petit, C Gasc and I. De Fouquet, C.r. hebd. Sianc. Acad. Sci., Paris, 1968 (c), 266 (9),605. It. L. Brown, P. E. Armstrong and C. P. Kempter, J. Less-common Metals, 1967, 13 (4), 373. J. . L Gacougnolle, S. Sarrazin and J. De Fouquet, C.r. he&. Sianc. Acad. Sci, Paris 1970 (c), 270 (2), 158. C. W. Nelson, D. F. Gibbons and R. F. Hehemann, 1. appl. Phys., 1966, 37 (13), 4677. S. Karashima and K. Saito, J. Jap. Inst. Metals, 1973, 37(3), 326. H. Farman and D. H. Niblett, ‘Proc. 3rd Euro. Cod. Int. Frict’, Manchester, 1980, Pergamon Press, p. 7. H. Schulz, U. Rodrian and M. Maul, ‘Proc. 3rd Euro. Conf. Int. Frict’., Manchester, 1980, Pergamon Press, p. 19. 240. H. E. Schaeffer, H. Schulz and H.P. Stark, ‘Proc. 3rd Euro. Conf. Int. Frict’., Manchester, 1980, Pergamon Press, p. 25. 241. F. Baudraz and R. Gotthardt, ‘Proc. 3rd. Euro. Conf. Int. Frict.’, Manchester, 1980, Pergamon Press, p. 67. 242. S. M. Seyed Reihani, G. Fantozzi, C. Esnouf and G. Revel, Scripta Met., 1979, 13(8), 1011. 243. H.Mizubayashi, S. Okuda and M. Daikubara, Scripta Ma., 1979 13(12), 1131. 244. A De Rooy, P. M. Bronsveld and J. Th M. De Hosson. ‘Proc. 3rd. Euro. Conf. Int. Frict.’, Manchester, 1980, Pergamon Press, p. 149. 245. J. N. Lomer and C. R. A. Sutton. ‘Proc. 3rd Euro. Cod. Int. Frict.’, Manchester, 1980, Pergamon Press, p. 199. 246. M. Weller and J. Diehl, ‘Proc. 3rd Euro. Cod. Int. Frict.’, Manchester, 1980, Pergamon Press, p. 223. 247. R. Schaller and W.Benoit, ‘Proc. 3rd Euro. Conf. Int. Frict.’, Manchester, 1980, Pergamon Press, p. 311. 248. M. Mondino and R. Gugelmeier, ‘Proc. 3rd Euro. Cod. Int. Frict’, Manchester, 1980, Pergamon Press, p. 317. 249. R. Klam, H. Schulz and H. E. Schaeffer, Acta Met., 1979, 278, 205. 250. K. Iwasaki, K. Liicke and G. Sokolowski, Acta Met., 1980,28, 855. 251. B. L. Cheng and T. S. Ke, Phys. Status Solidii, 1988, 107, 177. 252. H. Tczuka et al., J. Nucl. Mater., 1988,159/7A, 340. 253. S. J. Ding, W. B. Li and G. P. Yang, Rare Met. (China), 7,99. 254. K. Kato, 0. Yoshinari and K. Tanaka, Jpn Inst. Met., 1988,29,251. 255. M.Tagami, T. Othani and T. Usami, J . Jap. Inst. Light Met., 1988,38 (2), 107. 256. S. C. Yan and T. S. Ke, Phys. Status Solidii, 1987, 104,715. 257. F.Cosandey et al., Scr@ta Metall., 1988,U. 395. 258. E. D. Zhang, J. Shi and T. S. Ke, Phys. Status Solidii, 1986,98, 151. 259. S. Wang, T. Dai and C. Shi, Acta Metall. Sin., 22, A441. 260. S. Chen, J., S.Zhang and Z . Xu,Acta Met. Sin., 22, 379. 261. T. Enjo and T. Kuroda, Trans. JWRA, 1986,15,41. 262. S . Sinnema et ai., Rapidly Quenched Metals, 1985,1, 719. 263. K. E. Vidal, W. N. Weins and R. A. Winholz, High Strength Powder Metallurgy Aluminium Alloys, If, 1986.255. 264. S.Asano and S. Tamaoka, Scr. Metall, 1986,u), 1151. 265. T. S. Ke and C. M. Su, Phys. Status Solidii, 1986,94, 191. 266. K. Kwasaki, J. Phys. SOC.Jpn, 1986,55, 546. 267. K. Iwasaki, J. Phys. Soc. Jpn, 1986, 55, 845. 268. S. Asano and M. Kasaoka, J. Jpn. Inst. Met., 1986,50, 391. 269. S. Asano and M.Usui, J . Jpn. Inst. Mea., 1985,49, 945. 270. 6. Li, Z. Pan and J. Zhang, Acta Metoll. Sin.,1985, 21, 21. 271. T. Yokoyama, Scr. Metall., 1985,19, 747. 272. P, Cui, Q. Huang, T. S. Ke and S. C. Yan, Phys. Status Solidii, 1984, 86, 593. 273. G. Canelli et al., J . Phys. F: Met. Phys., 1984. 14, 2507. 274. C. Esnouf et al., Acta Metall., 1984, 32, 2175. 275. S. Asano and H. Seki, J . Jpn. Insf. Met., 1984, 48, 694. 276. B. F’umiah and R. Ranganathan, Phil. Mag.A, 1983,47, L23. 277, S. A. Antipov, A. I. Drozhzhin and A. M. Roshchupkin, Fiz. Toerd. Tela, 1983, 25, 1392. 278. C. M.M o and P . Moser, Phys. Status SoNdii (a), 1983,78,201. 279. J. N. Daou, P. Moser and P. Vajda, J. Phys. (Orsay), 1983, 44. 543. 280. S. Asano and K. Oshima, Trans. Jpn. Inst. Mer., 1982, 23, 530. 281. H. Mitani, N. Nakanishi and K. Suruki, J . Jpn. Inst. Met., 1980,4443. 282. V. F. Belostotskii, T. V. Golub and I. G. Polotskii, Metalofzika, 1982, 4, 106. 283. K. Hakomori, N. Igata and K. Miyahara, J. Jpn. Inst. Met., 1980,44,474. 284. P. F. Gobin, J, Merlin and G . Vigier, Ti and Ti Alloys, 1982, 3, 1691. 285, V. E. Bakhrushin, A. V. Novikov and Y. A. Pavlov, Izv. V.U.Z. Chernoya Metall., 1982, 7 , 113. 222. 223. 224. 225. 226. 227. 228. 229. 230. 231. 232. 233. 234. 235. 236. 237. 238. 239.

15-36

Elastic properties, damping capacity and shape memory alloys

H. B. Chen, N.lgata and K. Miyahara, Scr. Metall., 1982,16,1039. N.Igata, M. Masamura and H. Murakami, Mech. Props of B.C.C. Melds, 1982,75. H. Muhlbach, Phys. Statup SolIdi (a), 1982,69,615. H. B. Chen,N. Igata, K.Miyahara and T. Uba, 7thInt. Con8 on Internal Friction and UltrasonicAttenuation in Solids, 1981, Inst. de Genie Atomique, Lausanne, Paper l.B.ll. 290. B. Dubois and M. Lebienvenu, 7th Int. Con5 on Internal Friction and Ultrasonic Attenuation in Solids, 1981, Inst. de Genie Atomique, Lausanne, Paper 7.A.6. 291. G. Haneczok, J. Moron and T. Poloaek, 7th Int. Conf.on Internal Friction and Ultrasonic Attenuation in Solids, 1981, Inst. de Genie Atomique, Lausanne, Paper 6.C.2. 292. J . Du, 7th Int. Con$ on InternalFriction and Ultrasonic Attenuation in Solids,1981, Inst. de Genie Atomique, Lausanne, Paper 6.8.4. 293. K. Agyeman, E. Armbruster, H. Guntherodt and H. U. Kunzi, 7th In?. Conf: on Infernal Friction and UltrasonicAttenuation in Solidp, 1981, Inst. de Genie Atomique, Lausanne, Paper 4.A.6. 294. C. Li, W. Li,Z. Lui and G.Yang, 7th Int. Cog. on InternalFrictionand UltrasonjcAttenuation in Solids, 1981, Inst. de Genie Atomique, Lausanne, Paper 3.C.4. 295. I . G. Ritchie and K.W.SprungmaM, 7th Int. Cog. on InfernalFriction and UlnaronicAttenuation in Solidp, 1981, Inst. de Genie Atomique, Lausanne, Paper 3A.1. 296. K. Sakamoto and M. S h i , 7th Int. Con$ on Internal Friction and Ultrasonic Attenuatwn in Soli&, 1981, Inst. de Genie Atomique. Lausanne, Paper 1A.14. 297. R. Hanada, Scr. Metall., 1981,15, 1121. 298. T. Mori,T. Mura and Mokabe, Phil. Mag. A, 1981,44,1. 299. K. Qing-hu, G. Ting-sui, P. Zheng-bang and W. Zhong-guang, Acta Phys. Sinica, 1980,25, 1180. 300. S. Sat0 and H. Suto, Trans. Jpn. Inst. Met., 1980, 21, 83. 301. W. Bernoit and R. Schaller, Mem. Sei. Reu. Metall., 1979,76, 521. 302. G. Bellessa and J. Y.Duquesne, J. Phys. C: Solid State Phys., 1980, 13, 215. 303. S. Asano, M. Shibata and Tsunoda, Scr. Metall, 1980,14, 377. 304. C. Esnouf, G. Fantozzi,G. Revel and S.M.Seyed-Reihani,3rd European Conf. Internal Friction and Ultrasonic Attenuation in Solids, Manchester, 1979, 1979. 305. C. Dido and M. Mondini, 3rd European Cmf. Internal Friction and Ultrasonic Attenuation in Solids, Manchester, 1979, 1979. 306. R.Gugeheier and M. Mondini, 3rd European Con$ Internal Frictwn and Ultrasonic Attenuation in Sol&, Manchester, 1979, 1979. 307. R. L. Crosby, J. L. Holman and L. A. Nmeier, US.Dept of Interior, Bureau of Mines Rep. Invest. No. 8383,32pp. 308. EA. Hirabayashi, M. h k i and M.Koiwa, 6th Int. Conf.Internal Friction and Ultrasonic Attenuation in Soli&, Tokyo, 1977,659. 309. A. Isore, L. Miyada, K. Tanaka and S. Watanabe,6th Int. Conf.Internal Friction and Ultrasonic Attenuation in Solids, Tokyo, 1977, 605. 310. K. Iwasaki, J . Phys. SOC.Jpn, 1978.45, 1583. 311. I. Brough, K. M. Entwistle and P. Fuller, Acta Met., 1978, 26, 1055. 312. N. Nagai, 1979 (1976), U.S.Patent No. 4, 134, 758.

286. 287. 288. 289.

15.3 Shape memory alloys 15.3.1 Mechanical properties of shape memory alloys

Most shape memory alloys have compositions at which the crystallographic structure can change reversibly and reproducibly from a higher temperature phase to one of lower symmetry by a small change in temperature or by a change in mechanical stress at temperatures just above the transformation temperature at zero stress. In most shape memory alloys (and in all the industrially useful alloys), the change of structure usually OCCUTS over a MITOW range of temperature by means of a self-accommodatingmartensitic transformation, during which a small amount of heat is evolved or absorbed depending on the direction of the temperature change. This usually dves rise to a thermal hysteresis of about 10 to 40°Cover which the parent phase (usuallyreferredto as ‘austenite’) and the martensitecan coexist. If a stressed shape memory alloy is thermally cycled through its martensitic transformation temperature, the strain-temperature relationship will take the form of a closed hysteresis loop similar in shape to the B-H curve of ferromagnetic alloys. If a shape memory alloy is cooled to below its M , temperature, it undergoes little change in shape or volume. If it is then deformed

Shape memory alloys

15-37

plastically to a new shape, it will recover its original undeformed shape on re-heating to a temperature above its A, temperature. The amount of strain which can be recovered in this way is not unlimited but depends on the nature of the alloy. For example, the maximum recoverable strain is about 8% in Ti-Ni alloys and 10-12% in Cu-Zn alloys (although the latter cannot be achieved in industrially useful alloys). On cooling through the transformation to the martensitic state, the temperatures at which the transformation starts and finishes at zero applied stress are denoted by M , and Mf respectively. On reheating, the temperatures at which the reverse transformation to the high temperature takes place are A, and A, respectively. These temperatures can be determined experimentallyby thermal or dilatometric analysis or by changes in electrical resistivity. The M, temperature is raised progressively by applied stress; the M, temperature is the highest temperature at which the transformationcan be induced by stress. Figure 15.1 illustratesthese points." If an alloy is deformed above the Mebut below the M dtemperature, a stress-induced martensitic strain can be obtained. This is completely recovered on unloading (see Figures 15.4 and 15.7). Shape memory does not always appear to depend on the martensitic transformation. Small amounts of shape memory can be obtained in primary solid solutions of alloys of low stacking fault energy.16 Examples are shown in Table 15.9, e.g. Cu-A1 and C u S i primary solid solutions and some stainless steels. Although the latter undergo martensitic transformations to the alpha prime martensite, this is too brittle to deform. Shape memory is only found when the stainless steel is deformed at very low temperatures but above the M, to form both delta and some alpha martensite. 20% deformation may be needed to obtain 1.0-1.5% shape memory strain and it has proved to be of little industrial relevance so far.

TemperotureFigure 15.1

Typicul uniariul dimensional change behuviour for drawn wire. TiAfter W B. Cross et al."

%.Ox Ni-0.070/;C.

15-38

Elastic properties, damping capacity and shape memory alloys

Though most work has concentrated on Ti-Ni and related alloys because of their industrial importance, the shape memory phenomenon has been demonstrated in a wide range of alloys, some of which are listed in Table 15.9. M . temperatures can be varied continuously by changing the composition. Examples include: (i) changing Ni content in Ti-Ni alloys; (ii) partially replacing Ni by Fe, Co or Pd in Ti-NI alloys; and (iii) changing A1 and Zn contents in Cu-AI-Zn alloys or by partially replacing either element by others such as Sn, Mn,etc. Such variations also change the character of the alloys. Table 15.9 shows typical compositions for which data are published but it is possible to derive additional alloys within the ternary and more complex systems. Note that if shape memory alloys are cooled under stress, the M,temperature is raised in direct proportion to stress below M, (see Figure 15.7). Note also that the M,,etc temperatures are not exact in that for a given composition they can be changed by heat-treatment and by cold-working.Figure 15.8 illustrates an example of the extent to which the hysteresis can be widened in a Cu-based alloy.37 Table 15.9

COMPOSITIONS A N D TRANSFORMATION TEMPERATURE OF SHAPE MEMORY ALLOYS

4

M.

Alloy composition wt%'"

Au-28at% Au-47.5% Au-12.9% Au-15.2%

Cu-46 At.% Zn Cd Cu-25.5% Zn Cu-28.0% Zn

temperature at zero

temperature at zero

stress at

stress

"C

"C

- 15

- 118

Au-22.3% C~-31.4% Zn Au-28.7% Cu-31.1% Zn Cu-2.50% AI-31.75% Zn Cu-3.94% A1-25.60% Zn Cu-4.00% A1-26.10% Zn

-64 < -1% - 105 54 24

70

48 23

-so

- 10 50

140 170 250

-70 - 140

-so

75 240 160 100 83 52

13

-.g.b.1.0;1.55 brittle phase

32 32

ditto; Zn too high 2.15 ?; Zn too low 10.25 r2.0 14% (56% reversible) 4.8 4 2.8 3.9 2 1.9 1 6.3 6 2.95 0.95 0.45 0.45

32

5

- 10 300 250 82 N.A. N.A. -20

- 70 -52

Reference 6

60 -100 - 50

Au-16.0% Cu-32.3% Zn

Cu-6.00% A1-22.00% Zn Cu-7.50% A1-17.00% Zn Cu-11.75% Al-6.00% Zn CU-lO.M% Al-7.25% Zn Cu-11.25% Al-4.75% Zn Cu-11.75% Al-2.50% ZU Cu-4.90% Sn-31.25% Zn Cu-1.75% Si-34.50% Zn 0 ~ 2 . 2 5 %Si-31.25% Zn Cu-3.25% Si-27.50% Zn Cu-12.00% A1-2.00% Mn Cu-11.25% A1-4.25% Mn C~-10.75% A1-6.00% Mn Cu-10.40% Al-7.00% Mn Cu-10.60% Al-7.00% Mn Cu-11.00% Al-7.00% Mn Cu-11.10% Al-7.00% M n Cu-12.50% A1-1.00% Fe Cu-12.50% Al-8.00% Fe Cu-13.25% A1-2.75% Ni C~-8.0% A1 Cu-4.0% Si Cu-14.2% Al4.3% Ni Cu-40% Zn Cu-34.7% Zn-3.0% Sn

Maximum shape memory strain %

N.A. N.A. 15 - 120

-

-50

1.75 1.1 2.9 1.05 1.4 4.5

32 32 15 23 20 15 15 15 15 15 15 15 15 15 15 15 15 15 21 21 21 21 15 15 15 16 16 8 8 9

(Po~Ycrystal)

8.5

Fe-15% Cr-15% Nk15% Cn Fe-20% Cr-10% N i l % A1 Fe-20% Mn-3.75% Ti

2.6m) or5.65&

90 90 135 165 95 100 225 240 220 240

140 180 165 220 170 230 255 310 235 290

2.5 4 1.5 2.5 3 8 1 3 1 2

Sandcast Chill cast F

130

180 200

21

Sandcast "5 Chill cast T5

120 170

130 210

Sandcast T6 Chillcast T6 Chill cast T5

120 170 170

Sand cast T6 Chill cast T6 Chill cast T5 Sandcast T6 Chill cast T6

F F

T5 "5

T7 l7 T6 T6 T6 T6

Al-Si-CuMg-Ni

(LM21) Cu Si 4.0 6.0 Mg 0.2 Zn 1.0 Si 23.0 Cu 1.0 (LM29) Mg 1.0 Ni 1.0 (LM28) Si 19.0 Cu 1.5 Mg 1.0 Ni 1.0 Si 11.0 cu 1.0 (LM13) Mg 1.0 Ni 1.0

MPa

-

-

-

(P=5$)

60 60 75 85 65 70 105 105 115 115

-55 75 60 95

so*

-

-

110*

1.5 4.5

-

-

-

-

85 90

--

-

-

-

0.3 0.3

-

120

-

-

-

130 210 190

0.3 0.3 0.5

-

120 120 120

-

120 170

0.5 0.5 1

-

-

130 200 220

120 120 105

--

190 280

200 290

0.5

Ni 2.0 Al-Si-CuMg-Zn

Shear Brinell strength haniness

Fatigue strength (unnotched) Impact Fracture energy t o u g k s s 500MHz MPa J f.MPam'/*)

1

-

-

190

120

115 125

-

85* 100;

-

-

1.4

-

-

-

-

b

Remarks

a Ba

2'

me most widely used general purpose, high-

strength casting alloy

3

$

k

&k Highly stressed cornponents operating at elevated temperatures General engineering applications, particular crankcases

Pistons for high pformance internal combustion engines High performance piston alloy

Low expansion piston alloy

Lo-Ex (LM26) Si 9.0 Cu 3.0 AI-Cu-SiMg-Fe-Ni

Mg 1.0 Ni 0.7 (3L52) Cu 2.0 Si 1.5 Mg 1.0

Sandcast TI Chill cast T7 Chill cast 'I3

140 200 180

150 210 230

1 1 1

Sandcast T6 Chillcast T6

260 305

285 335

1

sandcast T5 Chill cast T5

135 150

170 210

1

Piston alloy

-

120 125

80

-

Aircraft eagine castings for elevated temperature service

Fe 1.0 Ni 1.25 AI-Cu-SiFe-Ni-Mg

(3L51)

Cu 1.5 Si 2.0 Fe 1.0 Ni 1.4 Mg 0.15

*Fatigue Limit for 50 x lo6 cycles.

M = as manufactured. H l l l =annealed.

2

"1)

2.5

Awcraft engine castings

3.5

(1) Spedal temper for maximum stms corrosion resistance (US designation T73). (2) Special hea! treatment for combination of propetties (US designation T736). (3) Special heat treatment for combination of propetties (US designation T61). (4) Special heat treatment for combination of properties (US designation "7351).

intermediatetempers.

H6 H8 = fully hard temper.

a

s2:

22-16

Mechanical properties of metals and alloys

-

Table 22.3 ALUMINIUMAND ALUMINNM ALLOYS MECHANICAL FROPERTIES AT ELEVATEDTEMPERATURES ~

TUne

Material (spec$cation)

Al (1095)

AI-Mn (3103)

Nominal composition

Tmp.

%

Condiiwn

A1 99.95

Rolledrod

Mn 1.25

“C

Wrought Alloys 24 Hlll 93 203 316 427 24 100 148 203 260 316 371 HI4 24 100 148 203 260 3 16 371 H18 24 100 148 203 260 3 16 37 1 Hlll 24 100 148 203 260 316 371 H14 24 100 148 203 260 316 371 HI8 24 H18 24 148 203

260 316 371 AI-Mg (5050)

Mg 1.4

Hlll

24

100 148 203 260 3 16 371

at

0.2%

temp. h

Prmfsiress MPa

Tensile strength MPa

-

-

55 45 25 12

loo00 loo00 1oOOO 10OOO 10OOO 10 OM) 10OOO 10OOO 10 OOO 10000 10 OM) 10000 10ooo 10OM) 10000 1oOOO 1oOOO loo00 loo00 10000 10OOO 10m 1oOOO loo00 10OOO loo00

35 35 30 25 14 11 6 115 105 85 50 17 11 6 150 125 95 30 14 11 6 40 37 34 30 25 17 14 145 130 110 60 30 17 14 185 185 110 60 30 17 14 55 55 55 50 40 30 20

90 75 60 40 30 17 14 125 110 90 65 30 17 14 165 150 125 40 30 17 14 110 90 75 60 40 30 20 150 145 125 95 50 30 20 200 200 155 95 50 30 20 145 145 130 95 60 40 30

1oOOO

10 OOO 1oOOO 1oOOO 1oOOO 1oOOO 1oOOO 1oOOO 1oOOO 10 OOO 10OOO 10OOO 10OOO loo00 10OOO loo00 1oOOO 10OOO 10m 10OOO 10ooo 1oOOO 10OOO

5

Elong. % on 50mm or 5.65a

61 63 80 105 131 45 45 55 65 75 80 85 20 20 22 25 75 80 85 15 15 20 65 75 80 85 40 43 47 60 65 70 70 16 16 16 20 60 70 70 10 10 11 18 60 70 70

-

-

Mechanical properties of aluminium and aluminium alloys

22-17

Table 22.3 A L W N M AM) ALUMINNM ALLOYS - MECHANICAL PROPEGIES AT ELEVATED

-

mmERAm conrinued

Maerial (specij?cation)

%

A1-Mg (cant.)

AI-Mg-Cr

Etne at

Nominal composition

(5052)

Mg 2.25 Cr 0.25

(5 154)

hlg 3.5 Cr 0.25

Condition

Emp. "C

Wrought Alloys 24 H14 100 148 203 260 316 371 24 H18 100 148 203 260 316 371 Hlll 24 100 148 203 260 316 371 24 H14 100 148 203 260 316 317 24 H18 100 148 203 260 316 371 Hlll 24 100 148 203 260 316 371 24 H14 100 148 203 260 316 371 24 H18 100

148 203 260 3 16 371

temp.

h

loo00 loo00 loo00 loo00 loo00 loo00 loo00 loo00 loo00 lOo00 loo00 loo00 loo00 1om loo00 10000 loo00 loo00 lOOa0 loo00 loo00 loo00 loo00 loo00 loo00 loo00 loo00 loo00 loo00 loo00 loo00 loo00 loo00 loo00 loo00 loo00 loo00 loo00 loo00 loo00 loo00 loo00 loo00 loo00 loo00 1oo00 loo00 loo00 loo00 10000 loo00 loo00 loo00 loo00 loo00 loo00

0.2% Proofstress MPa

165 165 150 50 40 35 20 200 200 175 60 40 35 20 90 90 90 75 50 35 20 215 205 185 105 50 35 20 255 255 200 105 50 35 20 125 125 125 95 60 40 30 225 220 195 110 60 40 30 270 255

220 105 60 40 30

Tensile

strength MPa

195 195 165 95 60 40 30 220 215 180 95 60 40 30 195 190 165 125 80 50 35 260 260 215 155 80 50 35 290 285 235 155 80 50 35 240 240 195 145 110 70 40 290 285 235 175 110 70 40 330 310 270 155

110 70 40

Elong. % on5Omm or 5.656

-

-

30 35 50 65 80 100 130 14 16 25 40 80 100 130 8 9 20 40 80 100 130 25 30 40

55 70 100 130 12 16 25 35 70 100

130 8 13 20 35 70 100 130

continued overleaf

22-18

Mechanical propenies of metals and alloys

TaMe 22.3 ALUMNKJM AND AUlMINRlM A!LOYS -MECHANICAL PROPERTIES AT ELEVATED TEhPERATWR!B

- continued

Ti Material (specficariorr)

at Temp. temp. “C h

Nominal composition %

Condition

Al-Mg-Mn (5056A)

Mg 5.0

As extruded F

AI-Mg-Si (6063)

Mg 0.7

Wrought Alloys 20

Mn 0.3

50

T6

Si 0.4

100 150 200 250 300 350 24 100 148

__

201 -

(6082)

T6

Mg 0.6 Si 1.0 Cr 0.25

__

201 -

Mg 1.0 Si 0.6 Cu 0.25 Cr 0.25

AI-&-Mu (2219)

Cu6 Mn 0.25

T6

Forgings

T6

Cu 5.5

T4

AI-CU-Mg-Mn (2017)

CU 4.0 Mg 0.5 Mn 0.5

T4

Pb 0.5 Bi 0.5

cu 4.5 Mg 1.5 Mn 0.6

206 316 371 24 100 148 203 260 3 16 371 20 100

Al-Cu-Pb-Bi (2011)

(2024)

260 316 371 24 I00 148

150 200 250 300 350 400 24 100 148 203 260 316 371 24 100 148 207 . ~

T4

260 316 371 24 100 148 203 260 316 371

Elmg. % on5Omm Proofstress strength or MPa MPa 5.65&

Tensile

0.2%

300 300 300 245 215 130 95 60 240 215 145 fi0 ._ 30 20 17 330 290 185

lo00 145 loo0 145 loo0 145 loo0 135 lo00 111 lo00 75 50 lo00 20 lo00 loo00 215 loo00 195 10000 135 innno - - - . 4s .10000 25 17 10000 14 10000 loo00 230 loo00 270 10000 175 innno .. -.

fis ._

loo00 loo00

35 30

1OooO loo00

275 260 213

loo00

80 ..

50

io000 io?

loo00 35 1Oo00 17 loo00 14 100 230 100 100 220 100 185 100 135 100 110 100 45 100 20 loo00 295 loo00 235 1OooO 130 loo00 75 loo00 30 1OooO 14 loo00 11 loo00 275 loo00 255 loo00 205 loo00 11s~. -~ . . . ~ 1Oo00 65 loo00 35 loo00 25 1OooO 340 loo00 305 loo00 245 loo00 145 1OOOO 65 loo00 35 1Oo00 25

25 21 32 45 56 77 100 140 18 15 2Q 40 75 80 105 17 19 22 40

-

_

45 35 30 3 10 290 235 130 50 30 20 385 365 325 280 205 145 70 30 375 320 195 110 45 25 17 430 385 274 150 ~. . 80 45 30 470 422 295 180 95 50

35

50 50

17 18 20 28 60 85

95 8

-

15 16 25 35 45 90 125 22 18 16 2 8 ~. 45 95 100 19 17 17 22 45 75 100

Mechanical propetties of aluminium and aluminium alloys

22-19

-

Table 22.3 ALUMINNM AND ALUMINIUM ALLOYS MECHANICAL.PROpERTDes AT EEVATED ~ERATuREs-rontinued

Material (specification)

Al-Cu-Mg-SiMn (2014)

Nominal composition %

c u 4.4 Mg 0.4 Si 0.8 Mn 0.8

(2618)

c u 2.2 Mg 1.5 Ni 1.2 Fe 1.0

(2031)

cu

AI -Cu -Mg -Ni

2.2 Mg 1.5 Ni 1.2 Fe 1.0 si 0.8

Al-Si-Cu-MgNl (4032)

Si 12.2 c u 0.9 Mg 1.1 Ni 0.9

Al-Zn-Mg-Cu (7075)

Zn 5.6 Cu 1.6 Mg 2.5 Cr 0.3

Condition

Temp.

lime at temp.

"C

h

Wrought Alloys T6 24 100 148 203 260 316 371 Forgings T6 20 100 150 200 250 300 350 Forgings T6 20 150 200 ~. . 250 300 350 400 Forgings T6 20 100 200 250 300 350 Forgings T6 24 100 148 203 260 316 371 T6 24 100 148 203 260 316 371 cast alloys

Mg 5.0 Mn 0.5

Mg 10.0

Sandcast

T4

400 20 100 150 200 300 400

0.2% PToofstress MPa

Tensile strength MPa

10000 10OOO 10000 10OOO 10o00 10OOO 10OOO 100 100 100 100 100 100 100 100 100 100 100 100 100 100 100 100 100 100 100 100 10OOO 10OOO 10OOO 10000 10OOO 10 Do0 10 OOO 10o00 10OOO 10OOO 10o00 10o00 10OOO 10ooo

415 385 275 80 60 35 25 415* 410 400 260 85 45 35 325* 340 260 170 70 30 20 325* 3 10 255 110

485 455 325 125 75 45 30 480 465 430 295 110 70 50 430 440 300 210 115 50 30 430

lo00 lo00 lo00 1OOO lo00 lo00

95 100 95 55 15 180 205 154 105 40 11

lo00

lo00 loo0 lo00 lo00

45

30 320 305 225 60 35 20 14 505 430 145 80 60 45 30

400 310 155 75 40

Elong. % on50mm or 5.656

13 14 15 35 45 64 20 10

-

-

-

-

8

-

13 --

380 345 255 90 55 35 25 570 455 175 95 75 60 45

9 9 9 30 50 70

160 160 130 95 30 340 350 270 185 90 45

4 3 3 4 4 16 10 0 42 85 100

90

11 15 30 60 65 80 65

continued overleaf

22-20

Mechanical properties of metals and alloys

Table 223 ALUMINIUM AND ALUMINIUM ALLOYS -MECHANICAL PROPERTIES AT ELEVATFD TEMPERATURES continued

-

Material (specification)

Nominal composition %

Si 5.0

Si 12.0

Si 5.0 Cu 3.0 Mn 0.5

A1-Si-Cu (LM 4)

Si 5.0 Mg 0.5

Al-Cu-Mg-Ni (4L 35)

Al-Si-Ni-Cu-Mg (LM 13)

Cu 4.0 Mg 1.5 Ni 2.0 Si 12.0 Ni 2.5 cu 1.0 Mg 1.0

Emp. "C

Condition

Cast Alloys Pressure die F 24 100 cast 148 203 260 Pressure die F 2 4 100 cast 148 206 260 Sand cast F 20 100 200 300 400 Chill cast T6 20 100 200 300 400 Sand cast T6 20 100 200 300 400 Chill cast T6 20 100 200 300 400 Chill cast T6 20 Special 100 200 300 400

lime at temp. h

0.2% Proof stress MPa

Tensile strength MPa

110 110 103 80 40 145 145 125 105 40 95* 140 110

205 175 135 110 55 270 225 185 150 75 155 180 135 60 30 325 290 90 40 25 275 325 135 55 40 285 320 165 60 35 275 250 170 60 35

loo00 loo00 loo00 10o00 loo00 loo00 loo00 loo00 loo00 10o00 lo00 lo00 lo00 lo00 lo00 lo00 lo00 lo00 lo00 lo00 1000 lo00 lo00 lo00 lo00 lo00 lo00 lo00 lo00 lo00 lo00 lo00 lo00 lo00 lo00

40 20 270* 255 60 25 12 200' 255 150 30 15 275* 280 110 30 15 200* 195 110 35 15

Elong. % on50mm

or 5.65&

9 9 10 17 23 2 2(1/2) 3 7 13 2 2 2 12 27 2 2 25 65 65 112

in

112

32 60 1/2 112 112 15 25 1 1 3 15 50

*O.l% Roof stress.

Table 22.4 A L U m I U M AND ALUMINIUM ALLOYS -MECHANICAL PROPERTIES AT LOW TEMF'ERMUREX

Material (speciPcation)

Nominal composi tion %

Condition

0.2% Proof Tensile Elong.% Temp. stress strength on 50"C MPa MPa or50mm ~

A1 99.0 Rolled and 24 drawnrcd H l l l -28 -80 -196 H18 24 -28 -80 -196

34 34 31 43 140 144 141 165

Reduction in Fracture area toughness % MPa m1I2 Reference

~~~

90 95 100 170 155 155 165 225

42.5 43.0 47.5 56 16 152 18.0 35.2

16.4 76.4 77.0 74.4 59.8 59.4 65.3 67.0

-

1

1

Mechanical properties of aluminium and aluminium alloys

22-21

-

TaMe 22.4 ALUMINIUM AND ALuMINNN[ ALLOYS MECHANICAL.PROPERTIES AT LOW

- conrinued

mMpERp;IzTREs

Material Nomina! (specicomposi pcation tion) % Condition AI-Mn (3 103)

0.2% Proof Tensile Elong.% Temp. stress strength on 50mm "C MPa MPa or50mm

Mn 1.25 Rolled and 24 drawn rod H l l l -28 -80 -196 Rolled and 24 dramrod B18 28 -80 -196 Mg2.5 Rolledand 24 AI-Mg Cr 0.25 drawnrod H l l l -28 (5052) -80 -196 H18 24 -28 -80 -196 (5154) Mg3.5 Sheet B l l l 26 Cr 0.25 -28 -80 -196 H18 26 -80 -196 -253 HI11 20 (5056A) Mg5.0 Rate Mn 0.2 -75 -196 Al-Mg- Mg0.7 Exmsion T4 26 Si Si 0.4 -28 -80 (6063) - 196 Extrusion T6 26 -28 -80 - 196 Al-Mg- Mg 0.7 Forging T6 24 Si-Cr Si 1.0 -28 (6151) Cr 0.25 -80 -196 24 AI-Mg- Mg 1.0 Rolled and Si-CuSi 0.6 dram rod T6 -28 Cr cu 0.25 -80 Cr 0.25 -196 24 AI-CU- Cu 4.5 Rolled and Mg-Mn Mg1.S drawnrcd T4 -28 Mn 0.6 -80 (2024) -196 Rolled and 24 drawnrod T8 -28 -80 - 196

40 40

so

60 180 185 195 220 97 99 97 115 235 230 236 215 115 11s 115 135 275 280 325 370 130 130 145 90 105 11s 115 215 220 22s 250 300 3 10 305 330 270 280 290 3 15 300 305 320 400 400 405 415 460

110 11s 130 220 195 20s 21s 290 199 201 210 330 275 280 290 400 240 240 250 350 330 340 455 645 290 290 420 175 190 200 260 240 250 260 330 320 352 330 385 315 330 345 425 480 500 s 10 615 500 502 5 14 605

43.0 44.0 45.0 48.8 15.0 15.0 16.5 32.0 33.2 35.8 40.8 50.0 16.6 18.3 20.6 30.9 28 32 35 42 9 14 30 35 30.5 38.2 50.0 32 33 36 42 16 16 17 21 15.2 12.0 14.9 18.3 21.8 21.5 22.5 26.5 23.3 24.4 25.3 26.7 14.5 12.7 13.3 14.0

Reduction in FTflCZUR area roughness % MPam'f2 Reference 80.6 80.6 19.9 71.2 63.5 64.4 66.5 62.3 72.0 74.2 76.4 69.0 59.1 63.2 64.5 51.4 66 72 73 60

-

32.0 48.2 36.2 78 75 75 73 36 36 38

40 38.8 34.0 38.7 34.7 56.4 52.5 53.7 46.5 31.8 33.1 30.8 26.3 25.8 21.5 22.0 19.7

continued overleaf

22-22

Mechanical propertiis of metals and alloys

-

Table 22.4 A L W I Z T M AND AL.UMlNNM ALLOYS MEcIiANIcALPROpwllEs AT LOW ?EMPERATmEs

- continued

Material (specification)

Nominal composi tion %

Condition

AI-CuSi-MgMn (2014)

CU 4.5 Si 0.8 Mg 0.5 Mn0.8

Rod

(2090) (2091)

Al-ZnMg-Cu (7075)

Cu 2.7 Li 2.3 Zr 0.12 Cu 2.1 Li 2.0 Mg 1.50 Zr 0.1 Zn 5.6 Mg2.5 Cu 1.6

0.2% Reduction Proof Tensile Elong.% in Fracfure Rmp. stress smngth a 50mm area toughness "C MPa MPa o r 5 ~ m m% MParn'l' Reference 290 290 302 380 415 415 420 470 410 460 530 590 535 600 615 440 460 495 550 485 490 505 570

T4

26 -28 -80 -196 Rod T6 26 -28 -80 -196 Forging T6 26 -80 -196 -253 Plate 27 (12.5m) T81 -196 -269 mate 27 T8 (38mm) -73 -196 -269 24 Rolled and -28 drawnrd T6 -80 -196

430 440 440 545 485 485 495 565 465 510 610 715 565 715 820 480 495 565 630 560 570

. . ~

590 670

20 22 22 20 13 13 14 14 12 14 11 7 11 13.5 17.5 6 7 10 7 15.0 ~. .. 15.3 15.3 16.0

28 28 26 20 31 29 28 26 24 24 22 22

-

29.1 26.2 23.6 20.1

~. .~

--

2

34 57 72 24 32 32 32

-

14 14

1

H l l l =Annealed HI8 = FUny hard temper. T4 = Solution treated end m d y aged. T6 = Solution treated and pipitation vmced.

-

Table 22.5 ALUMINIUM ALOYS CREEP DATA

Material (specc$cation)

Nominal composition

A1 (1080)

AI-Mg (50521 (LM 5)

Temp. Condition

%

99.8

Sheet

Hlll

Mg

Sheet

HI11

Mg5.6

Cast

"C

Stress MPa

20 20 80 80 250 250 250 250 80

24.1 27.6 7.0 8.3 1.4 2.1 2.8 4.1 45

100

110

100 100 200 200 200 300 300 300

I15 125 30 45

60 3.90 7.7 15

Minimum creep rate %per lOOOh

Total extension %in lOOOh

0.005 0.045 0.005 0.01 0.005 0.01 0.015 0.055 0.005

0.39 1.28 0.045 0.065 0.047 0.047 0.052 0.152 0.085

0.055 0.17 0.21 0.08 0.20 0.62 0.045 0.12 0.35

0.33 0.57 1.19 0.21 0.39 0.92 0.10 0.25 0.60

Reference

3

Mechanical properties of aluminium and aluminium alloys

22-23

Table 22.5 ALUMINIUM ALLOYS -CREEP DATA -continued

Nominal Material (specgication)

AI-CU

compositwn

Rmp.

Condition

%

cu 4

Cast

cu

Cast

10

Si 13 Ni 1.7

"C

Sandcast (modified)

Mg 1.3

A1-MII (3103)

Mn1.25

Exaudednxl

100 100 100 150 150 200 200 205 205 205 205 315 315 205 205 315 315 315 100 100 200 200 200 300 300 300 200

40 55 75 7.5 15 7.5 15 17 34 51 70 8.90 13.1 34 68 8.90 13.1 17 45 60 15 23 30 3.8 7.7 15

200

31 34.8 38.6 42.5 46 54 7.5 15 90 125

200 200

200 200 200

A1-Cu-Si (2025)

AI-Cu-Mg-Mn (203)

cu 4

Extruded

T4

Si 0.8

Cu 4.5 Mg 1.5 Mn 0.6

Clad sheet

T4

Stress MPa

300 300 150 150 150 200 200 200 250 250 250 35 100 I00 150 150 190 190

15

155

30 45 60 15 23 30 415

344 385 276 327 140 200

Minimwn creep rate %per lO00h

Total extension % in lOOOh Reference

0.013 0.022 0.046 0.126 0.147 0.107 0.273 0.04 0.09 0.14 0.69 0.13 0.29 0.01 0.11 0.12 0.43 0.99 0.016 0.06 0.016 0.054 0.14 0.013 0.047 0.223 0.001 0.022 0.040 0.060 0.13 0.15 0.73 0.007 0.39 0.03 0.045 0.325 0.035 0.1 0.040 0.02 0.07 2.36 10.0 1.0 10.0 1.0 10.0 1.0 10.0

0.126 0.107 0.174 0.413 0.647 0.341 0.658

3

-

5

-

5

0.190 0.675 0.096 0.179 0.432 0.026 0.098 0.428

3

-

-

8

0.340 0.395 0.722 0.107 0.204 0.7W 0.156 0.176

3

-

-

4

~~~

continued overleaf

22-24

Mechanical properties of metals and alloys

Table225 (continued) NOmiMf.

Material (specific&.on)

Temp. "C

CompOSthO?I

A1-Cu-Mg -Mn (2024) (con@

%

Condition

cu 4.5

Cladsheet

T6

Mg 1.5 Mn 0.6

cu4 Mg 1.5 Nl 2.2

Al-Cu-Mg-Ni (2218)

Zn 5.6

A1-Cu -Mg -Zn (7075)

Forged

T4

Cast

T4

Clad sheet

T6

Cu 1.6 Mg 2.5

Al-Mg-Si-Mn (6351)

Mg 0.7

Extru

.od

Si 1.0 Mn 0.6

35 35 100 100 150 150 190 190 100 100 100 200 200 300 300 400 200 200 300 300 400 35 35 35 100 100 100 150 150 150 190 190 190 100 100 100 100 150 150 150 200 2ao

200 200

Srress Mpa

424 430 347 363 242 289 117 193 193 232 270 77 108 7 15 1.5 77 116 7 15 1.50 430 480 495 295 355 370 70 170 245 45 75 125 193 20 1 232 255 93 108 154 31 46 62 17

Minimum creep rate %per 1OOOh

Toral extetLFiMt

%in lWh

---

1.0 10.0

LO 10.0 1.0 10.0 1.0 10.0 0.01 0.02

0.394 0.440 0.835 0.173 0.345 0.078 0.640 0.110 0.153 0.287 0.072 0.15 1 0.132

0.04 0.028 0.16 0.037 0.5 0.05 0.01 0.08 0.018 0.08 0.06 0.1

-

1.o

10.0 0.1 1.0 10.0 0.1 1.o 10.0 0.1 1.0 10.0 0.007 0.010 0.11 1.6 0.0087 0.023 0.22 0,011

Reference 4

3

3

A

-

---

-

-

8

-

-

0.040

-

0.13 0.28

H l l l =Armealed. T4 = Solution mated and namlany aged, will nspnd to PreCipitatioDueatment. T6 = Solution treated and aniliciaUy aged.

Table 22.6

ALUMlNRTM ALOYS -FATIGUE STRENGTH AT VARIOUS TEMPERATURES

Material (spec@cation) A1-Mg (5056)

Nominal composifion

Temp.

5%

Condition

"C

Mg 5.0

Extruded

-65 -35 f20

Endurance (unnorched) MPa 184 164 133

MHz

Remarks

20

Rotatingbeam

Reference

Mechanical properties of aluminium and aluminium alloys

22-25

Table 22.6 (contitwed)

Nominal Material (spec@cm'on)

Endurance

T q . (unnotched)

&ompositio?l 9% conditiar

Mg 7.0

Extruded

rod

"C

MPa

-65 -35

182 178 173 93

+20

Mg 10.0 Si 12.0

Al-cu (2219)

Cu 6.0

Sand cast 20 (oil quenched) 150 200 Sand cast 20 (modified) 100 200 300 Forged T6 20 150 200 250

300 350 Al-Si-Cu (W 22)

Si 4.6 Cu 2.8

AI-Cu -Si-Mn (2014)

cu 4.5

Al-Cu-Mn-Mg (2014) A:.-Cu-Mg-Si-Mn (2014)

Sand cast

Forgings

Al-Ni-cu

57

250

39 39 117 103 65 45 100

203

Mn 0.8 Cu 4.0 Mn 0.5 Mg 0.5

Extruded rod

Cu 4.4

Forghgs

Mg 0.7 Si 0.8 Mu 0.8 Forgings

Al-Cu-Mg-Ni (2218)

200

T6 148

Si 0.8

Cu 4.0 Mg 1.5 Ni 2.0

Ni 2.5 Cu 2.2

40 51 43 35 25 117 65 62 46 39 23

150

200 300

260 25 148 203 260 T4 20 150 200 250 300 T6 20

T4

300 Forged 20 148 203 260 Chillcast T6 20 100 200 300 Forged T6 20

20

Rotatingbeam

30

Rotating bean

9

50

Rotating beam, 24h at temp.

6

120

Reversebending

9

stresses

50

Rotating beam

100

Rotatingbeam

500

Rotating beam, 7 100 days at temp.

120

Reversedbending 9

120

Reversedbending 9

500 100

Rotatingbeam after prolonged heating

100

150

200

70

250

59 39 39

6

100

50

Io5 108 80 113 82

300 350

Reference

77

62 54 60 42 65 45 25 103 93 65 31 119 90 62 54 39 130 79

20

100

MHz Remarks

I20

Rotatingbeam, 24h at temp.

6

Reversedbending 9

continued overleaf

22-26 Table 22.6

Mechanical properties of metals and alloys (cutzrbufed)

Material (specification)

Endurance

Nominal composition

p P . (unnotched) Mpa MHz Remarks C

%

Condition

Al-Si-Cu-Mg-Ni (LM 13)

Si 12.0 CU 1.0 Mg 1.0

Chill cast

20

(Lo-EX)

Al-Zn-Mg-Cu (7075)

Zn 5.6 Mg 2.5 Cu 1.6 Cr 0.2

Plate

100 200 300 T6 24 149 204 260

97 107 97 54 15 1 83 59 48

50

500

Rotatingbeam, 24 h at temp. Reversedbending

Reference

6

-

T4 = Solution tmtcd and naturally aged, will respond to precipitationtreatmfnl T6 = Solution treated and aaiacidly aged

REFERENCES

1. Bogardus, S.W. Steckley and F.M. Howell, N.A.C.A. Technical Note 2082, 1950. 2. ‘A Review of Current Literature of Metals at Very Low Temperatures’. Battelle Memorial Institute; 1961. 3. J. McKeown and R. D. S. Lushey, Metallurgia, 1951, 43, 15. 4. A. E.Hanigan, L. F. Tedsen and J. E. Dom, Trans. Amer. Inst. Min. Met Eng., 1947, t71, 213. 5. R. R. Kennedy, Proc. Am.Soc. Test. Mat., 1935, 33, 218. 6. J. McKeown, D.E. Dineen and L. H. Back, Metallurgica, 1950, 41,393. 7. F.M. Howell and E. S. Howarth, Proc. Am. SOC.Test Mat., 1937,37, 206. 8. N. P. Inglis and E.G. Larke, J. Inst. Mech. Engrs., 1959. 9. P. H.Frith, ‘Propertiesof Wrought and Cast Aluminium and Magnesium Alloys at Atmospheric and Elevated Temperatures’, HMSO, 1956. 10. R. Grimes, T.Davis, H. J. Saxty and J. E. Fearon, ‘4thInternational AI-Li Conference, 10- 12th June, 1987’, J. de Physique, Sept. 1987.48, CoUoque C3, pll. 11. G.Leroy et aL, ibid., C3, p33. 12. M. J. Birt and C. J. Beevers, 5rh IntemationalAL-Li Conference, williamburg, Virginia,March 27-31.1989 (ed. T.H. Sanders and EA. Stake), Materials and Component Engineering Publications Ltd, UK,p983. 13. EL D. Peacock and J. W. Manin, $2,p1013. 14. J. Glazer and I. W. Morris, &id, pI471. 15. G. R D. Shrimpton and H. C. Argus, ibid, p1565. 16. A. F. Smith, ibid, p1587. FURTHER INFORMATION

1. The Properties of Aluminium and its Alloys, The Aluminium Federation (8th Edition). 2. Metals Handbook, Vol. 2, 10th Edition, ASM International, 1990.

22.2 Mechanical properties of copper and copper alloys 22.2.1 Standard specifications United Kingdom BS 1400

- British Standards - BS designation

Copper alloy ingots and copper and copper alloy castings Rolled copper and copper alloys, sheet, strip and coil Copper and copper alloys - t u b s Copper and copper alloys - forgoing stock and forgings Copper and copper alloys - wire Copper and copper alloys - rods and sections Copper and copper alloys - plate International Standards Organization - I S 0 designation ISO/R1190-1 1971 Copper and copper alloys. Parts 1 and 2 2870 2871 2872 2873 2814 2815

Mechanical properties of copper and copper alloys

IS0 426K IS0 426KI IS0 427 IS0 428 IS0 429 IS0 430 IS0 431 IS0 R197 IS0 R1187 IS0 R1190-1 22.2.2

22-27

1973 Wrought copper-zinc alloys. Part 1 1973 Wrought copper-zinc alloys Part 2 1973 Wrought copper-tin alloys 1973 Wrought copper-aluminium alloys 1973 Wrought copper-nickel alloys 1973 Wrought copper-nickel-zinc alloys 1972 Electrolytic tough pitch copper 1961 Classification of coppers 1971 Special wrought copper alloys 1971 Copper and copper alloys. Parts 1 and 2

CEN standards

The international Standards Organization (NO)in Technical Report TR7003 published an International Numbering System for Metals. This has led to the European CEN standards numbering xsystem. CENrC 132 agreed to use C as the first letter to denote copper and copper alloys. The second letter indicates the material state: W for wrought material; B for ingots; C for castings; and M for master alloys. There follows three numbers that uniquely identify the material. The sixth position is a letter that defines the material group. These for copper alloys are as follows: A and B for copper; C for miscellaneous copper alloys ( m a 5% alloying elements); E and F for miscellaneous copper alloys (over 5% alloying elements); G for copper-aluminium alloys; H for copper-nickel alloys; J for copper-nickel-zinc alloys; K for copper-tin alloys; L and M for copper-zinc binary alloys; N and P for copper-zinc-lead alloys; R for copper-zinc alloys complex; and A-S for copper materials not standardized by CEN/TC 133 with letters as appropriate to the material group. Typical examples are as follows: Material Coppers

Wrought Brasses

Other wrought alloys Cast d ~ o y s

Master Alloys

I S 0 Symbols CU-ETP CU-OF cuzn37 CuZn39Pb3 CuZn2OAlAs CuZn40MnlpblAlFeSn CuNiZSi CuAll OFe 1 CuNi30MnlFe CuZn33Pb2-GB CuZn33Pb2-GS CuSnl2-GB CuSnl2-GS C uA150(A)-M CuCr 10-M CuS20-M

CEN Numbers CWOMA CWOO8A CW508L CW6 14N CW702R CW721R CWlllC CW305G CW354H CB750S cc75os CB483K CC483K CM344G CM204E CM220E

Temper designations are also given by CEN TC133. For copper and copper alloys letters are used for mandatory properties as follows: A - elongation, B spring bending limit, G - grain size, H - hardness (Brinell for castings. Vickers for wrought products), M - as manufactured, R - tensile strength, Y - 0.2% proof stress. For further reference to the CEN system for Copper, contact the Copper Development Association or tbeir CD ROM Megabyres on Copper. A s the CEN standard has not yet been adopted in the UK, the IS0 designation has been used in Column 1 of Table 22.7 and the current BS specification numbers have been used in Column 2 of Table 22.7 and in Table 22.8.

-

Table 22.7 COPPER AND COPPER ALLOYS-TYPICAL MECHANICAL PROPERTIES AT ROOM TEMPERATURE Condition of material is expressed in accordance with 3s Nomenclature, uiz: 0 Material in the annealed condition

i7

H EH

ESH, SH) M

The various harder tempers produced by cold rolling For certain of the materials in this schedule, these tempers may be produced by partial annealing

% 5

(b

3.

Spring hard tempers produced by cold rolling of thinner material

k

Material in the ‘as manufactured’condition. In this schedule conlined to hot rdled or extruded material Material which has been solution heat treated and will respond effectively to precipitation treatment

wl wpl

WGH) W(4H) W(W

Material which has been solution heat treated and subsequently cold worked to various harder tempers

Material which has been solution heat treated and precipitation treated W(iW W(4H)P Material which has been solution heat treated, cold worked and then precipitation treated W(H)P British Standards gives strengths in N mm-, -numerically equal to MPa. 1 Nmm-2 E 1 MPa.

n

s,

%

British Standard specification number

Material and composition

Condition

Limit of proportionality

0.2% Proof stress

UTS

Elongation on 5d or 50mm

MPa

MPa

MPa

%

Shear strength

Brinell hardness

Viekers hardness

Modulus of elasticity

kgmn-2

(1Okgf)

GPa

117

MPa Cu 99.95% Oxygen-free highconductivity Cu 99.99% copper

Tough pitch copper

+ +

BS 2870 C 103 BS 3839 C 110

StIiH StridH StripH

15 198 154

48 176 265

216 263 314

48 32 16

162 170 185

42 82 96

51 90 106

BS 2870 C 101

Stlip-0 StridH StnpH

31 116 154

54 176 270

224 263 314

56 29 13

162 170 185

49 74 87

107

0,=0.03%

117 BS 2873 and BS 2874 C 101

Wire and Rod-0 H (Over 5mm dia.) H (Under 5mm dia.)

232

45

370

-

448

-

Be 1.85 Co 0.25 Be 0.5 Co 2.5

--c 112

Cadmium copper Cd 0.8 Sulphur copper

55

ii}

117

232 278

40 15

324 479

232 448 541

60 25 14

-

224 1066 1205

479 1205 1313

47

-

56

SttiStriAH StripH

54 180 263

224 286 316

Rod4

54 232 54

Plate M

31

31

R-H

BS 2870 CB 101

162 178 185

239

BS 2870 C 101

Beryllium copper

56 25 10

54

§ilver-bearing copper Ag 0.05%

BS 2874 CC 102

117

30

Plat-M

Chromium coppe~ Cr 0.6%

54

263

BS 2875 C 107

BS 2874 C 109

50

170

Deoxidized arsenical copper P 0.03% As 0.35%

Te 0.5%

162

58

Tube4H

Tellurium copper

90

239

BS 2875 BS 2871 Pt. 1 C 106

(+ silver)

”}

117

82

54

Phosphorus-deoxidized non-arsenical copper P 0.04

R&W R&WP Rod-W(H)

28 247 309

strip-w strip-WP StripW(H)

7

2

162

54

15

90

100

140 185

49

53 85

150 280

58 124 140

540

-

100 350 363 67 205 215

StripW StripWP StripWH

178 618 772

324 757 810

BS 2873 C 108

W-H

600

649

BS2874C111

ROb-0

54 231

216 263

40

140 185

50

12

27 11 8

220 360 370

80

lZ}

117

-

160

159 380 2 ;) 220

159

G

s2 2

9 6’

350

80

Rod4H

Cap copper c u 95 Zn 5

strip0 Stri&H StripH

39 124 162

92 223 315

263 308 386

45 30 8

192 216 232

65 85 105

z}

124

110

Strip0 StriAH StripH

39 124 173

100 247 324

262 317 386

60 24 8

216 224 247

65 85 100

}:

124

882870 CZ 101

g

B

S 0.35

Gilding metals Cu Zn 10

5! sB

0

110

s NN

tWL

Table 22.7 COPPER AND COPPER ALLOYS-TYPICAL MECHANICAL PROPERTIES AT ROOM TEMPERATURE-continued

N N I

Brinell hardness

Vickers hardness

Modulus of elasticity

kgrnm-'

(10kgf)

GPa

55

224 239 285

65 85 125

130

30 16

230 247 285

65 100 130

140

324 378 463

67 40 20

230 247 254

65 107 132

143

115 278 432

331 388 510

60 35 12

247 263 293

65 110 140

112

150

B

70 170 210

131 285 402

331 402 494

55 28 10

278 293 309

65 110 136

145

-

309

424

20

300

120

62

130

371

40

278

85

-

139

318

75

154

393

55 50

269

-

285

95

93

170

408

35

316

100

17

124

386

40

285

90

95

Limit of proportionality

0.2% Proof stress

UT S

Elongation on 5d or 50mm

Condition

MPa

MPa

MPa

%

Strip0 StrieH Strip-H

39 142 193

108 254 370

293 340

M)

Strip0 StriAH StripH

46 170 216

108 285 402

317 378 479

64

Strip0 StridH StripH

46 154 208

115 270 386

Strip-O StriAH StripH

54 154 208

Strip0 StrieH Strip-H

BS 2874 a 123

Rod4H

BS 2875 CZ 123

Plate-M

Aluminium brass

BS2871 CZllO

Tu-

Cu Zn 22 AI 2

BS 2875 CZ 110

Plate-M

Naval brass

BS2874 CZll2

Rod-M Plate-M

Material and composition

British Standard specijication number

Cu Zn 15

BS 2870 CZ 102

Cu zn 20

Brasses Cu Zn 30 Cu Zn 33

Cu Zn 37

Cu Zn 40

BS 2870 CZ 103

BS 2870 CZ 106

BS 2870 CZ 107

BS 2870 CZ 108

Cu Zn 36 Sn 1

440

28 12

Shear strength MPa

108

102

90 110 100 103

Free cutting brass Cu Zn 39 Pb 3

BS2874 CZ 121

Rod-M

-

201

411

25

309

105

110

96

Hot stamping brass Cu Zn 40 Pb 2

BS 2874 CZ 122

Rod-M

-

224

402

30

316

95

100

96

B

High tensile brass Cu Zn 39 Fe Mn

BS 2874 CZ 115

Rod-EA

93

210

440

30

309

High tensile brass Cu Zn 39 AI Fe Mn

BS 2874 CZ 114

Rod-M

139

290

520

30

340

Nickel silvers

BS 2879 NS 103

StriStridH StripH

62 170 270

100

332 510

340 432 564

65 28 11

280 290 320 290

65

400

210

Cu Ni 10 Zu 27 Cu Ni 12 Zn 24

Cu Ni 15 Zn 21

Cu Ni 18 Zn 20

Cu Ni 25 Zn 18

Phosphor bronzes

BS 2870 NS 104

BS 2870 NS 105

BS 2870 NS 106

BS 2870 NS 109

BS 2870 PB 101

Cu Sn 3 P

CuSn5P

CuSn7P

BS2870 PB 102

BS 2870 PB 103

CuSn8P

Copper-nickel

Cu Ni 5 Fe

BS2871 CN 101

strip0

62

108

340

StripH

309

587

695

60 4

95

66 121 155

150

103

160

103

1 ;:

177

I "1

StripO

77

124 618

355

55

340

695

4

290 400

210

220

strip--o StridH StripH

70 91 123

124 386 525

386 486 610

52 21 7

300 390 430

77 I38 166

l:} 168

Strip0

77

124

386

StripH

309

618

695

50 4

75 201

210

StripO StriAH StripH

54 300 402

124 386 579

324 510 656

50 12 2

247 340 378

70 160 195

StriH StrihH StripH

54 362 479

130 440

618

347 541 710

55 14 2

254 347 386

71 165 205

striw Ste&H StrrpH

77 371 494

139 494 687

356 593 741

60 12 5

260 371 424

175 210

Wire4

424

65

Wire-H

927

309 440

35 40

240

65

201

60

116

316

Plat-EA

93

248

121

124

220

Strip-H

Tube-0

]

70

121

% 121 121

}:l

a 5

s.a

2

4 121

205

1 E' 9

Q l;:}

215

80 l:}

220

70i 65

122

2

Table 22.7 COPPER AND COPPER ALLOYS-NPICAL

Material and composition

British Standard spec$cation number

MECHANICAL PROPERTIES AT ROOM TEMPERATURE -continued

Condition

limit of proportionality

0.2% Proof

stress

UT S

MPa

MPa

MPa

E Elongation on 5d or 50mm %

Shear strength MPa

Cu Ni 30 Fe Mn

BS 2871 CN 102

BS 2871 CN 107

Tube4

BS 2870 CS 101

Cu 96 Si 3 Mn 1

T u b 4

-

170

417

42

309

90

161

355

38

278

90

Plate-M

410

55

-

-

Rod4

362

60

293

-

1 -1

152

378

50

286

90

126

170

417

45

316

90

479

602

12

378

160

170

Rod-H

-

417

757

18

57 1

200

210

strip0

77 371 494

139 494 687

356 593 741

60 5

260 371 424

175 210

424

65

309

-

927

-

440

-

Wire4

BS 2871 CN 101

Ni 10.5 Fe 1.0 Mn 0.75

T u b 4 Plate-M

Bs 2871 CN 102

T u b 4 Plat-M

-

116

316

35

240

65

93

278

40

201

60

-

139

331

38

247

70

108

324

40

240

65

131 117

220 111

-

132 65 135 70

3

6

80

-1

92

Q 103

-

-

12

4

95

RodiH

WieH

Ni 5.5 Fe 1.2 Mn 0.5

85

K’

a,

%

70

StrihH S h p H

Copper-nickels

135

65

Pla-M

-

f

70

240

BS 2875 CA 105

Sn 8 P 0.5

247

40

Cu AI 8 Fe 3

BS 2870 PB 103

GPa

324

Plate-M

Sn 7 P 0.1

38

(10kgf)

108

BS 2870 CA 101

BS 2874 CA 104

331

kgmm-2 -

-

Aluminium bronzes Cu A1 5

Cu A1 10 Ni 5 Fe 4

139

Modulus of elasticity

Plate-M

Pla-M Silicon bronze

-

Vickers hardness

-

~

Cu Ni 10 Fe Mn

Brinell hardness

B

Ni 31.0 Fe 1.0 Mn 1.0

Silicon bronze

BS 2871 CN 107

BS 2870 CS 101

Cu96 Si 3 Mn 1

Aluminium bronzes Cu 95 AI 5

BS2870 CA 101

Cu 92 AI 8 Cu 85.5 AI 9.5 Fe 3.0 Mn 1.0 Ni 1.0

BS 2874 CA 103

Tub-0 Plate-M

-

170 161

417 355

42 38

309 218

90 90

}

152

-

-

410

55

-

Rod-0

77

362

60

293

Plate-M

-

147

378

50

286

85

90

126

Plat+M

-

170

417

45

-

479

602

12

316 378

90 160

95} 170

123

RodiH Rod-H

-

417

757

18

571

200

210

131

Plate-M

-

95) 95

-

-

103

N I W

22-34

Mechanicalproperties of metals and alloys

Table 22.8 CAST COPPER--TYPICAL MECHANICAL PROPERTIES AT ROOM TEMPERATURE (Properties vary, dependent on composition, section size and foundry practice) 0.2%

Elongation on

fiO?f

BS 1400

Composition

designation Material

%

Condition

Cu 64

Sandcast

SCBl

Brass for sand castings

UTS Nmm-2

50mm %

Brinell hardness

77

232

25

45-60

Sand cast Continuouscast

108 124

216 254

56 1.5 1.5 1.5 39.5

Sand cast Centrifugal cast

201 224

494 587

20 22

100-150 100-150

Cu 56 AI 5 Fe 2.5 Mn 2.5 Zn 34

Sand cast Centrifugal cast

386 403

710 757

12 15

150-230 150-230

Nrnm-2

Zn 34 Pb

2

Cu 85 Pb 5 Sn 5 Zn 5

LG2

Leaded gunmetal

HTBl

Hightensilebrasses Cu AI Fe Mn Zn

HTB3

stress

15 20

65-75 75-95

G1

Gunmetal

Cu 8s Sn 10 Zn 2

Sand cast 139 *Continuouscast 147

286 317

18 15

50-70 70-90

LB2

Leaded bronze

Cu 80 Sn 10 Pb 10

Sandcast 108 *Continuouscast 170

247 293

18 20

65-85 80-90

PBl

Phosphor bronze

Cu 90 Sn 10

Sandcast 139 *Centrifugalcast 185

293 370

15 16

70-100 100-150

AB1

Aluminium bronzes Cu 87 AI 10 Fe 3

Sand cast 201 *Centrifugalcast 216

541

571

25 28

90-140 120-160

Cu 80 A1 10 Fe 5 Ni 5

Sand cast 263 *Centrifugalcast 293

649 695

15 15

14c-180

1SO

460

20

90-140

AB2

AB3

Aluminium silicon Cu 95.5 bronze A1 6 Si 2

Sand cast

'Properties of continuously cast and centrifugally cast materials are generally simiiar.

14c-180

22-35

Mechanical properties of copper and copper alloys

Table 22.9 COPPER AND COPPER ALLOYS-TYPICALTENSILE PROPERTIESAT ELEVATED TEMPERATURES Limit of proportionality or proof stress is reported under a code, viz: LP = Limit of proportionality 0.1 =0.1% offset proof stress 0.2 =0.2% offset proof stress 0.5 =0.5% offset proof stress Limit of proportionality or proof stress

Material

Condition Elongation Composi- (see TemOn tion Table perarure Code U T S 50mm % 22.7) "C MPa (seeabove) MPa % Remarks

Oxygen-free Cu high conductivity 99.99 + copper

Reference

Sheet-0

24 100 204

78 77 70

0.2 0.2 0.2

212 190 159

56.3 55.4 56.9

Average 2 grain size 0.045 mm

24 100 204

68 68 67

0.5 0.5 0.5

214 187 157

57.8 51.4 56.9

Average 2 grain size 0.043 mm

24

65

100 204

66 57

0.5 0.5 0.5

210 183 161

53.4 52.5 52.1

Average 2 grain size 0.044mm

Plate-M

20 121 204

93 93 83

0.1 0.1 0.1

219 204 184

57 57 52

Hotrolled 2 plate Average 2 grain size 0.03 mm

Tough-pitch copper

0,0.03

Sheet-0

Phosphorusdeoxidized non-arsenical copper

P-0.04

Sheet-

Deoxidized arsenical copper

As 0.35

Silver-bearing copper

Ag0.05

Sheet-0

20 300 500

48 45 32

0.1 0.1 0.1

221 162 107

53 45 42

Tellurium copper

TeO.5

Rod-H

27 260

350 265

0.2 0.2

361 266

12.8 4.1

Chromium copper

Cr-0.6

Rod-0

20 350

_ _

_ _

259 204 148

44 10

Strafnrate 4 0.1 in min-'

-

-

374 298 210

21 10 3

Strainrate 4 0.1 in min -

-

253 137 59 19

56 9 17 16

-

P 0.03

550

Rod-WP

-

20 350 550

-

-

-

-

_

-

35

2

2

Gilding metals cu Zn 10

CU 90 Zn 10

Rod-0

25 375 635 875

Cu Zn 15

Cu 85 Zn 15

Plate-0

20 121 232

79 79 74

0.1 0.1 0,l

297 259 238

50 45 36

-

Cu Zn 20

CU 80

Rod-H

23 400 850

-

-

557 143 10

13 7 30

Cold worked 30%

Strip0

20 200 300

99 93 88

0.1 0.1 0.1

332 293 238

64 54 32

Grain size 2 0.03 mm

Strip-0

20 200 300

125 120 111

0.1 0.1 0.1

347 317 267

60

Grain size 2 0.035 mm

20 121 204

96 96 105

0.2 0.2 0.2

332 312 297

62 62 62

Zn 20 Brasses Cu Za 30

Cu 70

Cu Zn 37

Cu 63

Zn 30

Zn 37 Cu Zn 40

Cu 60 Zn 40

Plate-0

- _ - - _

- _ _ _

54 39

-

-

2

2

2

22-36

Mechanical properties of metals and alloys

Table 22.9 COPPER AND COPPER ALLOYS-TYPICAL TENSILE PROPERTlES A I ELEVATED TEMPERATURES -continued Limit of proportionality or proof stress

Material

Condition Elongation Ternon Composi- (see tion Table perature Code UTS 50mm % 22.7) "C MPa (seeabove) MPa % Remarks

Reference

Aluminium brass

Cu 76 AI 2 Zn 22

T u b 4

20 200 400

165 134 108

0.2 0.2 0.2

397 317 232

53.8 38.5 13.3

Elongation 2 measured on 11.3Jarea

Naval brass

Cu 62 Sn 1 Zn 37

Plate-0

21 121 204

141 133 134

0.1 0.1 0.1

360 246 326

47 46 38

-

2

Free cutting brass

CU 58 Zn 39

Rod-M

21 482

-

LP

477 76

33.5

-

2

Rod-0

20 200 400 610

364 319 163 34

50.2 42.2 25.4 22.5

Pb Forging brass

Cu 59 Zn 39

Cu 59.32 Rod-0

Zn 35.95 Fe AI Pb

Sn

-

3

Pb 2 High tensile brass

266

2.07 1.21 0.71 0.67

Nickel silver 20% Ni

Cu 75 Ni 20 z n 5

R o d 4

Phosphor bronze

Sn 5 P 0.1

Rod-0

27 232 427

30 316 399

- I

_

-

I

-

207 193

0.5 0.5

479 314 208

13 28 47

LP LP

347 310 272

51.0 28.5 37.0

-

76 86

-

-

-

_

2

Extruded 5 and annealed 816°C for 20 min

17 260 500

-

-

65

0.2 0.2

337 278 141

84

loo

Sn 8 Tube-H P 0.05

20 200 400

441 451 304

0.2 0.2 0.2

559 539 345

47 37 6

Temper 2 hard and stress relieved

Silicon bronze

Si 3 Mn 1

Strip0

20 200 300

104 94 92

0.1 0.1 0.1

371 309 276

66 54 52

Strainrate 2inmin-'

Copper-nickels

Ni 5.5 Fe 1.2 Mn 0.5

Plat-0

20 177 316

158 134 133

0.1 0.1 0.1

301 255 230

40 38 34

-

2

Ni 10.5 TUbe-0 Fe 1.0 Mn 0.75

20 204 400

159

371 329 287

35 28 18

-

2

139

0.1 0.1 0.1

Ni 31.0 Plate-M Fe 1.0 Mn 1.0

20 232 371

114 96 86

0.1 0.1 0.1

369 304 283

50 46 63

Hotrolled 2

Cu 89 A1 8 Fe 3

Rod-M

20 300 500

294 69 10

0.2 0.2 0.2

490 44 1 147

51 31 58

CuAIlOFeSNiS Cu 79.9 Rod-M AI 10.0 Ni 4.8 Fe 4.8 Mn 0.4

20 200 400

556 510 263

0.2 0.2 0.2

848 817 310

17 18 35

Extruded rod elongation measured on 11.3darea Extruded rod elongation measured on 4.5 Jarea

Aluminium bronze

147

-

2

34 6

Table 22.10 COPPER AND COPPER ALLOYS-TYPICAL TENSILE AND IMPACT PROPERTIES AT LOW TEMPERATURES Limit of proportionality or proof stress is reported under a code, Viz: LP =Limit of proportionality 0.1 =O.l% offset proof stress 0.2 -0.2% offset proof stress 0.5 =0.5% offset proof stress impact values are reported either as C=Charpy, V notch test or I=Izod test Proof stress Composition Material

%

Tmperature "C

Condition

MPa

Code (see above)

Impact d u e

Elongation

UTS MPa

on 5Omm Joules

Ya

-

code (see above

-

Reference

~

Oxygen-free high conductivity copper

c u 99.99 t

Tough pitch coppe~

0,0.03

Rod-0

Rod-0

Room

- 78

75 80

-253

90

+20

0.2 0.2 0.2

222 270 418

86.2 84.5 83.0

71.1 77.1 85.8

C C C

2

59 69 79

0.1

48.0 47.0 57.6

58.3 59.6 67.7

I I I

2

0.1

216 266 351

171 201 344

0.1 0.1 0.1

525 598 769

36 38 41

55.5 54.2 54.2

I I I

865 1016 1069

0.1 0.1 0.1

1287 1388 1480

2.1 4.1 4.1

I I I

- 197 -269

66 91 147

0.2 0.2 0.2

265 381 470

56 86 91

+20 -80 -180

194 188 204

0.1 0.1 0.1

352 394 507

49.4 59.5 74.6

88.8 93.5 106.4

I I I

-

397 421 523

51.3 53.0 55.3

41.8 42.0 40.7

C C C

-

549 571 669 559 598 735

19.8 21.0 24.4 27 27 26

80 -180 -

Beryllium copper

c u 97.44

Rod-W

Be 2.56

+ 20 80 -180

-

Rod-WP

+ 20

- 80 -180 Gilding metals

Brasses

Free cutting brass

c u 90

zn 10

Rod4

Cu 70 Zn 30

Rod-0

c u 60 Zn 40

Rod-0

Cu 58 zu 39 Pb 3

+ 22

+ 20 78 -183 -

Rod-H (Cold worked 25% reduction) Rod-H

+ 20 78 -183 20 - 80 - 195 -

+

-

0.1

-

2.6 0.4

3.0 Measured on 4.52 ,/area

151.8 151.8

6

C C

-

-

-

-

2

B $

Table 2210 COPPER AND COPPER ALLOYS-TYPICAL TENSILE AND IMPACT PROPERTID AT LOW TEMPERATURES+ontiwd Limit of proportionality or proof stress is reported under a code, vir LP =Limit of proportionality 0.1 =O.l% offset proof stress 0.2 =0.2% offset proof stress 0.5 =0.5% offset proof stress Impact values are reported either as C=Charpy, V notch test or I=Izod test -

Proof stress Material

Yo

Condition

Tempermure "C

Forging brass

Cu 58 Zn 40 Pb 2

Rod-0

+ 20

CU 95

Sheet-0

Composition

Phosphor bronzes

Sn

9

+ 27

-40 - 73

Sheet-EH

Cu 92 Sn 8

- 78 -183

Rod-H

+ 21

- 40 - 73

+ 24

- 196

-253 Silicon bronze

Nickel silver

Copper-nickels

Rod-H (Cold worked 42% reduction)

- 80

Cu 55.15 Ni 30.5 Zn 14.3

Sheet4

+ 20

Ni 10.5 Fe 1.0 Mn 0.5

Rod4

Ni 31.0

Rod-0

-269

Rod-0

cu

Plate-M


99.9 1178'5' Milled (rolled) lead sheet(*'

4

15- 1816'

f2.9"'

l?b > 99.8

4

17'6'

f2.917)

4-4.5

17"'

+ 3'7'

1085"'

5

17'@

f4.2I9'

801 Alloy B

3116' 6-15 (depending on heat treatment)

Lead pipes (not chemical)

Silver copper lead pipes

P b 99.2599.8 Ag 0.003-0.005 CU 0.003-0.005

C. Lead alloysfor cable sheathing Sb 0.85

Cd 0.075 Sn 0.2 Sb 0.4 Sn 0.2

60215' Comp. I 602'5' Comp. I1

801 Alloy f C 801 Alloy E

f 8.317'

f3.8"7' 6

18.516'

f 6.6"'

Notes: (I) Data from BS 334 Revision-Draft for Public Comment. (2) Rate of testing 0.4 mm mm-l min-'. (3) 20 x lo6 cycles. (4) Although no longer in commercial production in the UK,these materials are included for their scientific interest. (5) This information is correct at time of writing, but the standards listed are shortly due for revision. (6) Testing rate: 0.1-0.25 mm mm-' min-'. (7) 10' cycles. (8) Although not included in the current BS 1178, it is now generally recommended to add 0.02-0.06% copper to improve fatigue properties. (9) 2.5 x io7 cycles.

22-50

Mechanical properties of metals and alloys

Table 2217 IMPORTANT LEAD ALLOYS WITH UNSPECIFIED MECHANICAL PROPERTIES”)

Main application

Nominal composition %

Specification (BS)

Speci@c use

Soldming

Sn 64 or 60

219 Grades A, AP,K, KP 219 Grades G, R, F, KP 219 Grades J, H 219 Grades W, V 219 Grade C 219 Grades D, L AU 90 Nos. Z8A, 30A AU 90 No. 25A AU 90 Nos. 161 9 4 22A AU 90 No. 5AX AU 90 Nos. 3AX 5, lOAX 5

Electrical and electronics

Sn 40,45,50,60 Sn 30,35 Sn 15,20 S,n Sb Sn Sb Sn Sb Sn Sb Sn Sb Sn Sb Sn Sb As

40 2.2 30,32 1.6, 1.8 28,30 1.5, 1.6 25 1.4 16,18,22 25, 1.0, 1.2 5.0 4.0 2.6, 10.2 5.1,4.0 0.5

Sn Sb Sn Sb Sn Sb Sn Sb Sn Sb

2-4 2-5 2-5 10-13 5-10 15 6-13 15-19 13-22 20-28

Can soldering, general engineering Cable sheaths Lamps, low service temperatures Heat exchangers, general dip soldering Plumbing, wiped joints General body soldering Radiator core dipping Body soldering, radiator dipping Hot dip coating, tubular radiator manufacture Body solders for shallow areas

Printing

Electrobacking metal

Slug casting metal Stereotype metal Monotype casting metal Cast type casting metal

Notes: (1) In many uses of lead alloys, the strength, hardness, etc. of the alloy are not of prime importance. In general soldering, for example, the geometry of the joint and the materials being joined, are of greater importance than the strength of the bulk solder. In most applications of type metals, fluidity of the liquid alloy, contraction properties, and wear resistance of the solid alloy, are the most important characteristics in formulating an alloy. See also Chapter 34.

BIBLIOGRAPHY

L. I. Goff and G. Hewish, ‘Creep Resistant Lead Sheet by the D.M. Process’, 3rd Inter. Lead Co&, Venice, 1968, Publ’d. LDA, London. L. I. Goff and R. D. Semmens, ‘Lead Products by Continuous Casting’, 2nd Inter. Lead Conf, Arnhem, 1965, Publ’d. LDA, London. J. N. Greenwood, Met. Rev., 1961,6(23), 279-351. W. Hofmann, ‘Lead and Lead Alloys’, English trans. of 2nd revised German edition, Springer-Verlag, Berlin. ‘Lead Abstracts’, 1962-80. LDA, London. A. Lloyd and E. R. Newson, ‘Dispersion Strengthened Lead Properties and Potentialities in Chemical Plant and some Early Trials.’ Second Inter. Lead Cony., Arnhem, 1965. A. Lloyd and E. R. Newson, ‘Dispersion Strengthened Lead-Developments and Applications in the Chemical Industry, 3rd Inter. Lead Con/., Venice, 1968, Publ’d, LDA, London.

22.4 Mechanical properties of magnesium and magnesium alloys Tnble 22.18 MAGNESIUM AND MAGNESIUM ALLOYS WROUGW -TYPICAL MECHANICAL PROERTES AT ROOM TEMPERATURl3

Spec@caiions

DTD

Nominal* composition Material

%

Form

Mg

Mg 99.9

Mg-Mn

Mn

Sheet, annealed Bar, extruded sheet Btruded bar (1 in dim) Extruded tube Sheet, annealed half hard Extruded bar and sections Forgings Extruded bar and sections Extruded tube Forgings

Mg-Al-Zn

AI Zn Mn Zn Mn AI

3.0 1.0 0.3 6.0 1.0 0.3 8.0

Zn

0.5

Mn Mn

0.3 2.0 1.0

Zn Z r

0.6

Zn

3.0

Zr

0.6

Al

Mg-Zn-Mn

Mg-Zn-Zr

1.5

Zn

1.0

zn 5.5 Zr

0.6

Sheet, annealed half breed Extruded bar sections Sheet Extruded bar and sections Extruded tube Sheet Forgings Extruded bar and sections (1 in d i m ) Bars and sections Heat treated

or BS (Air) BS (Gen. Fag.)

ASTM

Proof stress 0.2% Ekktmn MPa

-

118C 1429 737A

2L513 2L5 12 2L503 88C

509 I 5101

3370-MAGS-101M 3373-MAGE-10 1M 3373-MAG-E- l0lM 3370-MAG-S-1110 3370-MAG-S-l l lM 3373-MAG-E-1 11M 3372-MAG-F-12 1M 3373-MAGE-12 1N 3373-MAG-E-121M

-

M 1A-F, B 107 MlA, B107 AZ31, B90 AZ31, B90 AZ31, B107 AZ61. B91 AZ61, B107 AZ61, B107 AZXOA, B91

AM503 AZ3 1 AZM

-55 zM21

2L514 2L508 2L509 2L504 2L514 2L505

3370-MAW-13 10 3370-MAGS-13 1M 3373-MAG-E-13 1M 3370-MAG-S-141M 3373-MAGE-14 1M 3373-MAG-E-141M 3370-MAG-S-15 1M 3372-NAG-F-15 1M 3373-MAG-E-15 1M

5041A

3373-MAG-E-161TE ZK60A-T5, B 107-70 ZW6

-

Compression

Tension

UTS

MPa

Proof stress Hardness Elong. 0.2% VPN % MPa 30 kg 4 6 6

-

7 6 13 10 11 8 8 8 8

12A

30-35 35-45 35-45 45-55 45-55 50-60 55-70 50-60 60-70 55-70 60-70 65-75

69 100 100 162 154 131 170 162 183 183 170 208

185 232 232 263 247 232 263 255 293 293 278 293

131 170 162 118 208 1Y3 185 224 239

232 263 255 263 293 278 270 309 309

10 11 10 13 7 8 8 18

154 193 213

55-70 60-75 60-75 60-70 60-80 65-75

270

340

10

255

60-80

-

-

100 93 147 147 147 185

13

154 177

-

continued overleaf

-

Table 22.18 MAGNESNM AND MAGNESIUM ALLOYS (WROUGHT) - TYPICAL. MECHANICAL PROFZRTEE AT ROOM TEhWERAWRE continued

Nominaf compositwn

Marerial

%

Mg-Zn-Cu-Mn

Zn

Mg-l'h-Zn-Zr'*

Mn 0.8 "h 0.8

(Creep resistant) Mg-l'h-Mn** (Creep resistant)

Cu

6.5 13

Zn Zr

0.5

'Ih

2.0 0.75 3.0 1.2

Mn

Th Mn

8I

Tension

Speciijccations

Compression

Proof stress

DTD

Proof stress

M

VTS M h

Elong.

Form

BS (Air) BS (anEng.) .

ASTM

Elekrmn

Barsandsections Heattreated

-

ZC71-T6,B107

ZC71

340

360

6

-

-

Extrudedb~~dsectioas 5111 Forgings 5111

-

-

ZQ

147

263

18

-

50-70

147

232

13

-

50-70

Sheet

-

Exuuded bar andsections

-

0.6

-

-

%

0.2% MPa

Hardness VPN 30 kg

0.2% MPa

VI h,

W

$ 2 2

3

5.

-

165

247

9

179

-

3

HM21-T8,B90 HM31-T5

-

227

287

8

185

-

2.f?.

Nuclear alloys: Two wrought magnesium alloys (Magnox ALBO; MgO.75AL-0.005 Be and MN70; Mg0.75 Mn) of interest only for their nudear and Mgh-temperature pmpeaies have nwrm-temperaturetensile pmpetties similar to those of AM503. *It is usual to add 0.2-0.4% Mn to alloys containing aluminium tu impnwe corroeion resistance. M = As manuhreblred 0 = Fully annealed. "E = Predpitalion treawd. **llmium-containing alloys are being replaced by alternativeMg alloys.

2

&

Table 22.19 MAGNESrOM AND MAGNESNM ALLOYS (CAST) TYPICAL MECHANICAL PROPERTIES AT ROOM TeMpERATuRE

Tension

Spectfiations

Nominap cotnpositwn

w

Material Mg-zr Mg-Al-Zn

0.6 6.0 3.0

AI

8.0 0.4

3L124 3L125

TF AC

KIA,E80 AZ63A-F, B8O AZ63A-T4, B80 AZ63A-T6, B8O 2970 MAG 1-M 2970 MAG 1-TB 2970 MAG 3-M 2970 MAG 3-TB 2970 MAG 3-TF

MPa

51 97 97 131

185 199 275 275

82 93 90 124 108 97 97 145 162

MPa

86

158

247 154 232 239 216 165 275 275 263

2.0 5 10 5 4 11 2 6 2 3 2 8 2 6

54 97 97 131 86

Brinell hardnesst VPN 30 kg

40-50 50 55 73 50-60 50-60 55-65 55-65 75 85 60-70 65 63

2L127

2970 MAG 4-"E

ZK5lA-T5. B80

4.0

TE

2L128

2970 MAG 5-TE

ZIiXlA-Ts, B80

150

216

5

139

55-75

RE

1.2 0.7 6.0 2.5 0.7 2.7 2.2 0.7 3.0 2.2 0.7 5.5 1.8 0.7

w

5045

190

295

7

190

70-80

TE

2L126

2970 MAG 6-"E

EZ33A-T5, B8O

95

162

4.5

93

50-60

TB

5005A

2970 MAG 8-TB

HZ32A-T5, B80

93

216

7

93

50-60

TE

5015A

2970 MAG 9-l93

ZH62A-T5, B80

167

210

8

162

65 75

Zr Zn

RE Zr RE Zn

Zr Th

Zn

2r

zn Th

Zr

9.5 0.4 9.0 2.0

TF

--

Die cast AC TB

-

AZ81A-T4, B80 AZ91C-F, B80 AZlC-T4, B8O AZ91C-T6, BRO AZ91B-F, B94 AZ92A. B80

Elektron

%

TI3

AI

Zn

-

TB TF

AC AC TB

ASTM

UTS MPa

4.5 0.7

Zn

Mg -RE Zn-Zr (Creep resistant) to 250°C) Mg-Th-Zn-W* (Creep resistant to 350 "C) Mg-Zn-Th-ZP

TB AC

-3L122 -

Pmf stress 0.2%

Zn Zr Zn

A1

Mg-Zn-RE-Zr

BS (Air) BS (Gen. Eng.)

Compression

Elong.

82 93 90 127 111 97 97 145 161

Zn

Mg -Zn-Zr

or Condition

Zr AI Zn

Pmof stress 0.2%

DTD

-

-

84

65-75

-

continued overleaf

BI

M

W

Table 22.19 MAGNESNM AND MAGNESIUM ALLOYS (CAST) TYPICAL MECHANICAL. F'ROPEKTIES AT ROOM TEMPERATURE - continued Specijications NminaP composition

DTD

Material

%

Conditkm

Mg-Th-ZiC*

3.0 0.7 Ag 2.5 RE 2.0* Zr 0.6 Ag 2.5 RE 2.0* ZR 0.6 RE(D) 2.2 Ag 1.5 Zr 0.6 Cu 0.07

TF

Th

Mg- Ag-RE*-=

Mg- RE(D)-Ag-

zr-cu

Mg-Ag-Th-RE*W*

Mg-Y-RE(A)-Zr

Ag RE Th Y

2.5

Compression Proof Brinell stress 0.2% hardnesst MPa VPN3Okg

%

93

208

5

93

50-60

MSR-A MSR-B

187 204

247 260

5 3

178 193

65-80 65-80

BS (Geu. Eng.)

ASTM

Elekiron

-

-

HK31A-T6,B80

M'lZ

5025A

-

5035A

2970 MAG 12-TF

TF

5055

-

QE22A-T6,BSO

QE22

ux)

2 6 0 4

195

65-80

TF

5055

2970 MAG 13-W

EQ21A-T6,880

EQ2l

195

261

-

75-90

'IF

4

TF

-

-

QH21A-T6, B80

QH21A

210

210

4

200

65-80

Tp

-

-

wE43-T6, B80

-3

185

265

7

-

75-90

TF

-

2970MAG 14-TF

WE54-T6,B80

WE54

205

280

4

-

75-90

TF

-

-

ZC63-T6, B8O

ZC63

158

242

-

55-65

1.0s 1.0

4.0 0.7 RWA) 3.4 Zr 0.6 Y 5.1 W A ) 3.0 Zr 0.6

Zn

6.0

Cu Mn

2.7 0.5

P

$

3.

8 ''!

$;I

B

Zr

Mg-Zn-CU-Mn

Elong. VTS MPa

or BS (Air)

Zr

Tension Proof stress 0.2% MPa

E I

VI

4.5

*It is usual to add 0.2-0.4% Mn IO alloys containing aluminium to improve corrosion resistance. RE = Cerlum mischmetal containing approx. 50% cerium.W ( A ) = Neodymium plus Heavy Rare Farth meuils. ?Brinell tests wilh 500 kg on 10 mm ball for 30 8. RE@) = Neodymium enriched mischmetal. $Fractionated ran eaah metals: MSR-A contains 1.796; MSR-B contains 25%. %alulion heat tregted in an atmosphem of hydrogen AC = Sand cast. ? ' E = Precipitation heat treated. TEI = Solution heal trcafed 'IF = Fully heat treated. 'Tboriumcontaining alloys are being replaced by alternative Mg alloys.

3

Mechanical properties of magnesium and magnesium alloys

22-55

Table 22.20 MAGNESRTM AND MAGNESIUM ALLOYS (EXCLWING HIGH TEhGWtAlURE ALLOYS FOR WHICH SEE TABLE 22.21) -TYPICAL TENSILE PROpERTlEs AT ELEWlEDTEMPERATCTRES

‘Shori-time’ torsion?

Nominal composition* Material

%

Fonn and condition

Mg

Mg 99.95

Forged

Mg-Al-Zn

A1 8.0

Sand cast

Zn 0.4 (A81 Sand cast and solution treated (AZ855)

Forged

A1 9.5 Zn 0.4 W91)

Sand cast

Sand cast and solution treated Sand cast and fully heat treated Mg-Zn-Zr

Zn 4.5 Zr 0.7 (Z5z)

Sand cast and heat treated

Zn 3.0 Zr 0.6 (ZW3)

Extruded

Sheet

Mg-Zn-RE-Zr

Zn 4.0 Re 1.2 Zr 0.7 W5)

Sand cast Sand cast treated

Test temp.

“C

Young‘s modulus GPa

0.2% proofstress MPa

-

-

45 34 32 25

86 76 65 62

20 100 150 200 20 100 150 200 250

45

-

-

20

45 34 33 28

82 13 65 62

100 150

200 250 20 150 200 20 100 150 200 250 20 100 150 200 20 100 150 200 250 20 100 150 200 250 20 100 200 250 20 100 150 200

-

-

45

221 153 102 93

-

45

-

45

-

-

90

-

-

45 40 37 28 19 45 34 28 22 19 45 40 22 12 45 40 33

127 91 17 62 46 161 124 102 79

-

-

250

-

20 20 150 200 250

45 41 40 38 33

-

51

255 162 46 11 195 120 74

-

150 134 120 99 74

UTS MPa

Ehg.

170 128 93 54 158 154 145 100 75 241 202 154 116 85 309 216 154 154 131 122 108 77 232 222 196 139 239 232

5 8 16 43 4 5 11 20 27 11 16 21 25 21 8 25 28 2 2 6 25 34 6 12 26 20 2 6 25 34 30 6 14 20 23 20 18 33 56 7i 10 33 42 51 59 4 6 19 29 35

185

133 103 263 185 145 113 85 309 182 127 100 270 165

116 76 49 216 195 167 131 99

%

continued overleaf

22-56

Mechanical properties of metals and alloys

Table 2220 MAGNESIUM AND MAGNESIUM ALLOYS (EXCL.UDING HIGH TEMPERATURE ALLOYS FOR WHICH SEE TABLE 22.21) - TYPICALTENSILE PROPERTIES AT ELEVAW TEMF"' - conthied

Nominal composition*

Material

%

Mg-Zn-Th-Zr**

Mg-Ag-Re(D)**

T"-"

Form and

Test temp.

Young's modulus

condirion

"C

GPa

Zn 5.5 Th 1.8 Zr 0.7 (TZ6)

Sand cast and heat treated

Ag 2 5 RE@)2.0 Zr 0.6 (QE22)

Sand cast and fully heat treated

20 100 150 200 250 20 100 150 200 250 300

45 34 31 28 26 45 41

Re@) 2.2 Ag 1.5 Zr 0.6 Cu 0.07 (EQ21)

Sand cast and fuIly heat treated

Ag 2.6 RE(D) 1.0 Th 1.0 Zr 0.6 (OH21)

Sand cast and fully heat treated

Y 4.0

Sand cast and fully heat treated

W A ) 3.4

Zr 0.6 (wE43)

Y 5.1

Mg-Zn-Cu-Mn

RE(A) 3.0 Zr 0.6 (WE54)

Sand cast and fully heat treated

Zn 6.0 Cu 2.7 Mn 0.5 (Zc63) Zn 6.5 Cu 1.3 Mn 0.8 (2~71)

Sand cast and fully heat treated Extruded and fully heat treated

20 100 150 200 250 300 20 100 150 200 250 300 20 150 200 250 300 20 100 150 200 250 300 20 100 150 200 20 100 200

40 38 34 31 45 43 42 41 39 35 45 41 40 38 37 33 45 42 39 37 35 45 43 42 41 39 36 45

-

45 40 32

'Short-time' tension? 0.2% proof stress UTS MPa MPa

161 134 110 82 52 201 185 171 154 102 68 195 189 180 170 152 117 210 199 190 183 167 120 185 175 170 160 120 205 197 195 183 175 117 158 141 134 118 325 206 115

270 224 178 130 91 259 232 210 185 142 88 261 230 211 191 169 132 270 242 224 205 185

131 265 250 245 220 160

280 260 255 241 230 184 242 215 179 142 350 259 163

Elong. %

9 22 26 26 25 4 12 16 20 27 59 4 10 16 16 15 10 4 17 20 18 19 20 7 6 11 18

40 4 4.5 5 6.5 9 14.5 4.5 9 14 11 6 16 14

*It is usual to d 03-0.48 Mn to alloys Containing aluminium lo improve condm mistance. f In Bccordana with BSIW. 1943; 1 h at tempcature and strain rate 0.1-0.25 in in-' min-*. $Tested according to BS4A4. RE = Cerium mischmeraI containing 8pprox. 50% Ce. RE?@) = Ne~dymiumenriched mischmetal. RE(A) = Neodymium plus Heavy Rare Eaah merals. **Tborium-mntainingalloys are being replaced by alternative Mg alloys.

Mechanical properties of magnesium and magnesium alloys

22-57

Table 22.21 €UGH lEMPERAlURE MAGNESIUM ALLOYS -TENSILE PR0PEIlTE.S AT IXEWATED T E M P E B A W

Nominal composition* Material

%

Mg -RE-Zn

RE 2.7 Zn 2.2 Zr 0.7 (ZRE1)

Mg-Th-W*

Test temp. "C

Fonn and condition

20 100 150 200 250 300 350 20 100 150 200 250 300 350 20 100 150 200 250 300 350 20 100

Th 3.0

Zr 0.7 (HK31)

wm Mg-Th-Zn-Zr**

Th 3.0 Zn 2.2 Zr 0.7 (ZW

Th 0.8 Zn 0.5 Zr 0.6

150

200 250 300 350

0

Mg-AgRE(D)-Zr

Mg-RE(D)Ag-2k-a

Mg -Y-RE(A) -Zr

Ag 2.5 RE(D) 2.0 Zr 0.6 (QE22) RE(D)2.2 Ag 1.5 Zr 0.6 c u 0.07 (EQ21) Ag 2.5 RE(D) 1.0 Th 1.0 Zr 0.6 (QH21) Y 4.0 RE(A1 3.4 (WE43) Y 5.1 RE(A) 3.0 Zr 0.6

(wE54)

Sand cast and filly heat treated Sand cast and fully heat

Young's modulus GPa 45 40 38 36 33 28 21 45 40 38 38 36 34 29 45 36 34 33 33 31 28 45 41 41 40 40 34 29

'Short-tim' tension* 0.2% proof stress UTS

Elong.

MPa

MPa

%

93 79 76 74 65 48 26

162 150 139 125 107 85 56 208 188 174 162 150 136 103 216 159 131 108 90 76 63 266 224 201 171 134 96 56

4.5 11 19 26 35 51 90

93 88 86 85 83 73 56 93 88 79 65 56 49 45 181 179 176 165 124 13 17

4

10 13 17 20 22 23 9 23 21 33 38 41 34 10 10 11 15 20

21 38

'

treated

Sand cast andfully > heat treated Sand cast and fully ueated Sand cast and fully eat treated

High strengthcast alloys with good elevated tempatme properties- for which see Table 22.20

,

'It is usual to add 0.2-0.4% Mn to alloys containing aluminium to impmve corrosion resistance. tln acsatdancz? wilb BS 1094.1943; 1 h at tempcrahm; main rate 0.1-0.25 in in-' min-'. RE= Cerium mischmaaIcontaining appmx. 50% Ck RE@) =IleOdymiumenrichcd mischmetal. =(A) =Neodymium plus Heavy Rare Earths. **Thorium containing alloys are being replaced by alternative Mg alloys.

22-58

Mechanical properties of metals and alloys

Table 22.22

HIGH-IEMPE6(ATURE MAGNESIUM ALLOYS -LONG-TERM

CREEP RESISTANCE

Stress to produce specifred creep strains%

Nominal composition

FO~WIand

~ m p . ~ i i t0.~5 0.1

Material

%

Condition

“C

h

MPa

MPa

Mg-RE-Zn-Zr

RE 2.7 Zn 2.2 Zr 0.7 (=E 1)

Sand cast and heat treated

200

100 500 lo00

52 41 36

66 54 47

250

100 500 lo00 100 500 lo00 100 500 lo00

23 11

28 19 14 7.4 5.2 4.3 97

32 24 20 8 65 5.6 111 106 103

117 117 116

100 500 lo00 100 500 lo00 100 500 lo00 100 1100

77

86 75 70 43 28 23 12 6.2 5.4 45*

97 88 83 52 37 31 19 8.6 6.9 63* 62*

101 96 91 67 52 43 32 15 12 97* 100*

100 loo0 100 100

-

28*

23 19 17 14 12 10 10

28 21 19 19 13 12 12 9

315 Zn 4.0 RE 1.2 Zr 0.7 (E5)

Sandcast and heat treated

100

150 200 250 Mg-Th-Zr**

Th 3.0 Zr 0.7

(MU

0

Mg-Th-Zn-zr**

Mg-7l-Zn-B’

Th 0.8 Zn 0.5 Zr 0.6

(ZW Th 3.0 Zn 2.2 Zr 0.7 (m1)

Sandcast and fully heat treated

Sheet

Sandcast and heat treated

200

260 315 250

250

100 500 lo00

300

100 500 lo00

325 350 375 Zn 5.5

Th 1.8 Zr 0.7 (‘126)

Sandcast and heat treated

150

200

100

500 Io00 100 500 lo00 100 500 lo00 100 500 lo00 100 500 lo00

5.6 - -

29 22 20 6.2 4.3 3.9 31*

-

-

0.2 MPa

05 MPa

1.0 MPa

71 65 58

-

-

36 30 26

-

-

34 30

-

107 100 97 73 64 53 39 19 15 Ill*

-

43* 65* 29* 45* 9.3* 14* 19* 27* 32* Stress of 46 MPa (3 tonf ine2) produced 0.03% creep strain Stress of 46 MPa (3 tonf in-2) produced 0.03% creep strain 42 50 56 63 66 35 43 51 58 63 56 61 48 31 39

--

--

-

35 25 21 24 16 13 18 10

52 41 36 36 25 20 23 14

-

46 36 32 29 21 15 21 12 9 12 8

8

8

-

11

8

10

13 9

51 36 26

66

82

96

56 51

69

85

63

80

102 94 90

26 15 11

32 22 17

45 26 20

56 40 31

62 49 40

22-59

Mechanical properties of magnesium and magnesium alloys Table 22.22 HIGH-TEMPERATURB MAGNESIUM ALLOYS -LONG-TERM CREEP RESISTANCE

- continued

Stress to pmduce speci@d creep strains% Nominal composition

Form and

Temp.

Material

%

Condition

T

Mg-AgRE(D)-B

2.5 2.0 Zr 0.6 (QE22)

Sandcast and fully

200

&D)

zr-cu

RE(D) 2.2 Ag 1.5 Zr 0.6 CU 0.07 (EQ21)

heat treated

Sandcast andfully heat treated

UN)

Mg-Y-RE(A)-Zr

2.5 RE(D) 1.0 Th 1.0 Zr 0.6 (QH21) Y 4.0 RF!(A)3.4 Zr 0.6 (WE43)

Ag

5.1 -A) 3.0 Zr 0.6 (WE54)

Sandcast and fully heat treated

250

Sandcast andfully

200

200

250

Mg-Zn-Cu-Mn

Zn 6.0 Cu 2.7 Mn 0.5 (ZC63)

Sandcast and fully heat 'ueated

88

-

-

65

82

lo00

46

56

73

89 79

100 500 lo00 100

26 15 10 78 57 48

33 22 16 95 71 62

-

-

28 22 116 88 76

31 26

29 18 14 32 20

36 22 19 39 26 21

42 30 24

-

-

32 26

36 30

148

161 115 96

173 148 139

-

61

-

100 500 lo00 100 500 lo00 100 500

lo00

heat treated

Sandcast and fully heat treated

74 54

100

lo00

250

Y

0.5 MPa

500

250 Mg-Ag-RE@)Th-W*

0.2 MPa

500

250

Mg-RE(D)-Ag-

0.1 MPa

Timet h

150

200

100 500 lo00 100 500 loo0

0.05 MPa 55

-

-

-

44

-

160 120 120

4 6 39 165 140 132

--

-

1.0 MPa

-

-

-

-

-

100 500 lo00 100 500 lo00

61 81 47 43 40 58 32 48 16 9 4 9 9 1 0 4 82 92 98 74 89 95 -

100 500 loo0

60 51 42

*Total strains. 74-6 h heating to tea temperature followed by 16 h soaking at test temperature. RE = Cerium mischmetal containing appmx 50% Ce. XED) = Neodymiurn-enriched mischmetal. RE(A) =Neodymium plus Heavy Rare Earth metals. **Thorium-containingalloys are bemg replaced by alternative Mg aUoys

-

63 55 49

67 61 55

-

22-60

Mechanical properties of metals and alloys

Table 22.23 HIGH-TEMPEFUTUREMAGNESKJM ALLOYS -SHORT-TERM CREEP RESlSTANCE

Stress toproduce specified creep srrains% Material Mg-REZn-Zr

Nominal composition Form and % condition

Re 2.7 Zn 2.2 Zr 0.7 (ZRE1)

Sandcast and heat treated

stress to

Tmp. Ti? 0.05 1.0 2.0 5.0 10.0 "C s MPa MPa MPa Mpa MPa 200

250 315

Zn 4.0 RE 1.2 Zr 0.7 W5)

Sandcast and heat treated

200

250 315

Sandcast and fully heat treated

250

315 Mg-ThZn-W

'Ib 0.8

Sheet

250

Zn 0.5 Zr 0.6

-

-

30 60 600 30 60 600 30 60 600

fracture MPa

-

98 91 96

118 117 116

130 128 125

136 134 129

76 74 73 52 51 42 100 99 86

84 83 82 59 58 49 107 105 99

92 91 89 73 69 56 116 114 103

111 110 108 80 76 62 127 124 114

123 120 114 85 83 68

130 129 125 90 88 13 136 134 125

30 60 600 30 60 600 30 60 600

86 83 71 62 59 48 96 95 94

90 88 76 69 66 53 103 103 102

94 91 81 76 73 59 119 118 117

99 96 86 I9 76 64 138 137 137

30 60 600 30 60 600

80 78 74

88 86 82

103 102 96 110 95

117 116 107 159 157 145

163 160 149

128 127 120 165 162 151

48 40 20

80 67 31 100 96 85

93 82 42 118 114 103

102 98 66 125 123 114

84 81 74 73 72 71 128 124

102 99 86 16 16 14 137 133 1I4

111 107 98 82 80 77

30 60 600

-

-

-

-

-

-

-

-

83 79 61

---

-

116 113 93 86 82 69 145 145 144

(mr)

350 Mg-ThZn-W

Th 3.0

Zn 2.2 Zr 0.7

Sandcast and heat treated

200

30 60 600 30 60 600

20

-18

32 28 15

-

-

58 57 56 55 53 50

65 64 63 60 59 59 113 109 90

-

-

-

-

-

(ZT1) 250 3 15

zn 5.5

'Ib 1.8

Zr 0.7

Sandcast and heat treated

200

30 60 600 30 60 600 30 60

96

600

93 63

30 60 600 30 60 600

70 65 56 54 52 44

71 69 68

64 63 61 120 117 102

I10

144

137 119

W6) 250 315

'f 1 h heating to

lest temperature followed by 1 h soaking at test temperature. RE = cerium mischmetal containing approx. 50%Ce. *Therium-containing alloys IM being replaced by alternative Mg alloys.

77 74 60 59 57

49

85 80 66 64 62 53

96 90 14 70 66 56

99 94 71

74 70

58

107

99 82 76 73 59

Table 22.24 MAGNESIUM AND MAGNESIUM ALLOYS -FATIGUE AND IMPACT STRENGTHS

Impact strength5 for single blow fracture

Fatigue strength? at specified cycles

Nominay

I

compositwn

temp. "C

Material

%

Condirion

State

Mg-Mn

M n 1.5 (AM503) Al 6.0 zn 1.0

extruded

U N U N

20

U N U

20

Mg-AI-&

Extruded

20

lo5

5 x lo5

106

5 x 106

lo7

5 x lo7

MPa

MPa

Mpa

MPa

MPa

MPa

iemp. "C

107 76 161 127

90 90 139 110

88

86 51 125 97

85 50 124 94

83

20

12-14

4-4.5

54 133 103

120 91

20

34-43

7-9.5

108 107 124 108 93 71 114 110 124 103

93 KO 102 86 69 52 91 83 93 82

90 73 97 82 66 48 89 74 93 80

88 66 91 74 59 38 88 68 93 79

88 65 90 73 57 36 86 66 93 79

86 63 90 69 57 31 85 63

20

3-5

1.5-2

20

18-27

4.5-7

117 93 151 124

90 66 137 99

80 66 134 93

79 65 128 91

77 65 127

111 90

86

85

86

85

124 108 97 93

99 93 85 74

97 91 80 69

Est

Unnotched

Notched

J

J

48

(-)

A1 8 Zn 0.4

Sand cast

(A@

Sand cast and solution

N U

Sand cast

U

150 200 20

Sand cast and

N U

20

treated

U A1 9.5 Zn 0.4 (u91)

20

solution treated Sand cast and fully heat treated Extruded

N

U N

20

U

20

N

Mg-Zn-RE-Zr

Zn 4.0 RE 1.2 Zr 0.7 (Rz5)

Sand cast and heat treated

U

Sand cast and heat treated

U N

20

U

150 200

20

N

u

-

- 196

1.5

20

1.5-2.0

1-1.5

20

7-9.5

3-4

77 16

20

3-4

1-1.5

20

23-31

9.5-12

90

65 124 88

82 82

80 80

77 77

20 -196

7-12 0.8

3-4

91 88 73 62

96 86 69 59

94 83 65 54

20

4-5.5 0.7

1-2

- 196

continued overleaf

-

Table 22.21 MAGNESIUM AND MAGNESIUM ALLOYS -FATIGUE AND IMPACT STRENGlHS continued Impact strength5 for single blow fracture

Fatigue strength? at specified cycles NominaC cornpositron

Material

%

Condifion

State

2.2 27 Za 0.7 (ZREl)

Sand cast and heat treated

U N U U

Zn RE

Mg-Ag-RE@)-B

Mg-AgRE@)Th-W*

Mg-Zn-lh-zr**

*

Zn 6 RE 2.5 Zr 0.6 (ZU3)

Sand cast and fully heat treated**

tb)E

Sand cast and fully heat treated

Zr 0.6 (MSR-B) Ag 2.5 Re@) 1.0 Th 1.0 Zr 0.6 (QH21) zn 5.5 Th 1.8 Zr 0.7

U U U N U

temp. "C

m 150 200 250 300 20

20

Sand cast and fully heat treated

N N U U N U

Sand cast and heat mated

U N

20

Sand cast and fully heat treated

U N

20

U

200 250

200 250

m 250

lo5

5 x IO5

106

5 x 106

lo7

5 x lo7

MPa

MPa

Mpa

MPa

MPa

MPa

100 77 69 68 59 49 144 99

82 59 60 59 48 39 131 83

80 54 59 56 45 37 127 79

79 52 57 52 43 37 121 73

77 52 57 51 43 36 119 72

74 51 57 51 42 34 117 71

119 77

103 65

103 63

135 86 108

77 114 72 76

68 111 65

103 62 90 57 109 64 56

102 62 88 54 108 63 55

100 62 86 51 108 62 52

120 100

86 86

85 80

83 77

83 76

82 16

Th

Zr

3.0 0.7

-

74 48 74 63

68

40

65 36 60 54

63 34 59 52

62 32 58 51

(MTZ)

U

Test temp. "C

Unnotched

Notched

J

J

p %

K'

-

-

-

69

(m)

Mg--Ih-Zr**

-

E I a\

80

68 59

20

-196 20

6-7.5

1-2

f?.

h

0.5 12.9-17.6

2.3-2.7

3.

8e

B

20 -1%

8-11 05

1.5-3

Mg-Th-Zn-Zr***

Th Zn Zr

0.1 0.5

Zn

zr

3.0 2.2

U Sand cast and heat treated

0.1

GW Mg-REXD)-AS-

zr-cu

RE@) 2.2 Ag 1.5 cu

0.01

Y

4.0

Sand cast and

RUA) 3.4

fully heat treated Sand cast and fully heat treated Sand cast and fully heat treated

0.6 5.9 RE(A) 3.0 Zr 0.6 Zn 6.0 cu 2.1 Mn 0.5

* It is usual to add 0.2-0.4%

20

-

13

200 250 20

86 $2 14 63 82 59 60 51

83 51 68 59 19

19 49 60 54

56

u

200

U

250

80 91 16 I1 66

U

43

U

325 20

-

46

51 54 43 31

103

94

93

92

U U

150

114 10-7 101 113 118 115

101 91 81

98 94 14 102 90 I8 100 62

94 81 65

U N

I

59

14

16 48 59 52 I1 49

74 46 51 51

68 48

52

51

42 34 91

39 29 90

20

-196

1-8

1.5-3

0.8

fully heat treated

0.6

Y

Mg-Zn-Cu-Mn

Sand cast and

Zr

Zr

U N

u

0.6

(m)

Th

Extruded

U U

u

U

U N

20 250 20 200 250 20

-

Mn to alloys conlaining aluminium lo impmve conosion resistance. **Solution heat mated in an atmosphere of hydrogen. t Wo&r mtating beam tests at 2960 c.pm. t U=Unnotrbed N = Ndmed Semi-UPeular m(ch of 0.12 cm (0.047 in) radius. Stress concenmlion fador 1.8.

104

96 84

-

100

84 61 94 51

93 85

64 99 83 66 92 56

91

83 62 91 82 65 90 55

5 Hounsfield baInnced impacl test, nolched bar values am equivalent to Izod values. RE@)) = Neodymium emicbed mischmetaL ***lhodum-containingalloys are being replaced by allanative Mg alloys. W(A) = Ndymium plus Heavy Rare m.

' s.2

[ 2 2

E-

3

Mechanical properties of metals and alloys

22-64

TaMe 22.2.5 HEAT TRBATMBNTOF MAGNESIUM W O Y CASTINGS Heat tceatment conditions for magnesium sand castings can be vasied de nding on the parti& compeneuts and specific propeaies requid. 'IBe foItowing are examples of the conditions used for each $oy which will give p @ e s meeting current national and international speciEcatwns.

NonriM[*

composition I

Ti

Temperulun?

Material

Condition

h

"C

Mg -4 -Zn

AI

TB

12-24

400-420

TB

16-24

400-420

TF

16-24

TE

8-16 10-20

400-420 Air cool 180-210 170-200

TE

2-4

Zn

Al Zn

Mg -Zn-Zr

Zn Zr

Mg-Zn-RE-Zr

Zn

Mg-Th-28

Mg -Zn

-Ih-Zrt

RE

4.5 0.7 4.0 1.2

Zr

0.7

RE

TE

Zn Zr

2.7 22 0.7

10-20 10-20

Th Zr

3.0 0.7

TF

2-4

Zn Ih Zr Th

5.5 1.8 0.7 3.0 2.2 0.7 25 )2.0 0.6 )2.2 1.5 0.6

TE

2-4

TE

10-20 10-20

Zr Ag

W Zr

W Ag 21 cu Ag

Mg-Zn-Cu-Mn

320-340

Air cool 170-200 170-ux)

560-570

Air cool 10-20

Zn

Mg-Y -RE(A)-Zr

8.0 0.4 9.5 0.4

RE@) Ih Zr Y

Mr

Tp

4-12 WatedOil Quench 8-16 4-12 Wawoil Qucncb 12-16

520-530

4-12 Water/Oil Quench 12-20

520-530

195-205 515-525 195-205

0.07

25 1.0

1.0 0.6 4.0 RE(A) 3.4 Zr 0.6 Y 5.1 RE(A) 3.0

Zr Zn Cu

TF

195- 205 320-340 Air cool 170-200 310-3m

0.6 6.0 27 0.5

TF

TF TF TF

195-205

4-12 520-530 Watcr/oil Quench 12-20 245-255 4.12 520-530 Wakr/Gil QuendAir Cool 12-20 245-255 4-12 435-445 W a r Quench 16-24 180-200

* It is usual to add 02-0.4% Mn to Unys containing aluminium to improve cornsion rwistancc.

RE = ceriom mischmetalcomaimng approximately 50% cerium. TB =Solution heat wed. RE@) = Neodymium-enrifhed mischmetal. TE =Pncipitation heat treated RE(A) = Neodymium plus Heavy Rare Eaah merals. TF = PuUy he& treated. t Mum-aontaining alloys are being replaced by alternative Mg alloys.

No&:- Above 350 "C, furnace atmospheres must be inhibited to prevent oxidation of magnesium alloys. This can be achieved either by: (i) adding 1/2-19S01 gas to the furnace atmosphere; or (5) canying out the heat treatment in an atmosphere of 100% dry COz.

Mechanical pmperties at subnormal temperatures At temperatures down to -200°C tensile properties have approximately linear temperature coefficients: proof stress and UTS increase by 0.1-0.2% of the RT value per "C fall in temperature, and elongation falls at the same rate: modulus of elasticity rises approximately 19 MPa (2800 lbf in-2) per ' C over the range 0" to -100°C. No brittle-ductile transitions have been found. Tests at -70 "C have suggested that the magnesium-zinc-zirconium alloys show the best retention of ductility and notched impact resistance at this temperature.

22.5

Mechanical properties of nickel and nickel alloys

Table 22.26 WROUGHT NICKEL AND HIGH NICKEL ALLOYS, STANDARD SPECEICATIONS*ANDDESIGNATIONS Nominal composition

France AFNOR

Alloy

46

Nickel 200 20 1 Nickel 205 Monel400

Ni

99.6

-

Cu Fe Mn

99.6 min. 30 1.5 1.0

NU 30

Ni Fe Cu

31.0 0.7 Rem

Monel K-500 Cu Al

29 2.8 0.5 16 6

Monel450

'Ii

Inconel600

Cr Fe

Inconel601

Ni

Cr Al Fe

60.5 23.0 1.4 15.1

-

NC 15Fe

-

UK

USA

DIN

WerkstoffNr.

BSandDTD

ASTM

ASME

AMs

AECMA

UNS

17740; Ni 99.2 17750-4

2.406 612.406 0 2.406 U2.406 1 2.406 1 2.436 0 2.436 1

3072-76NAll 3072-76NA12

B160-163 8725, 8730 F1-3, €9 B127 B163-165 B564

SB 160-163

5553

-

NO2200

-

NO2205 NO4400

-

NO5500

-

NO6600

Germany

-

17743: Ni Cu 30 Fe 17750 17751 17752 17753 17754

3M2-76zNA13

-

17743:Ni Cu 30 AI 17752 17754 17742Ni Cr 15 Fe 17750 17751 17752 17753 17754 17742 17750 17751 17752

B111, B122 B151, B171 B359, B395 B432, B466-7 B543.8552 2.437 5

2.481 6

2.485 1

3072-76: NA 18 3072-76 NA 14

-

B163 B166-168 B516 B517 B564 B951

-

5555 SB 127 SB163-165 SB564

4544 4574 4675 4730 4731 7233

SB111, SBl77 SB359, SB395 SN466,SB4467 SB543 4676

Boiler c&

sect.

WI

SB163 SB166-168 SB564

5540 5580 5665 5687 7232

Boiler code VJII

5115 5870

% a

fi'

B

-R-8

' E

NO6601

Table 22.26 WROUGHT NICKEL AND HIGH NICKEL ALLOYS, STANDARD SPECIFICATIONS*AND DESIGNATIONS-continued Alloy

Inconel 617

Inconel 625

Nominal composition France % AFNOR

Ni Cr

-

N

Y

a

UK

USA

DIN

Werkstoff Nr.

BS and DTD

ASTM

ASME

AMS

AECMA

UNS

-

-

-

-

Boiler codes I and VI11

-

-

NO6617

Germany

o\

2

b

Co

55.1 21.5 12.5

Mo

9.0

R'

AI

c

1.2 0.1

3 4

Cr

21.5

Mo Nb

9.0

Ni 52.5 Cr 19.0 Fe 18.8 Nb 5.2 Mo 3.1 Ti 0.9 A1 0.5

Inconel X-750

Cr Fe Ti

Al Nb

17744 17750 17751 17752 17754

2.4856

NC19FeNb

-

2.4668

NC 15Fe-T

-

2.4669

3.6

Inconel 718

15 7 2.5 0.6 0.8

Inconel MA 754

Ni 78.0 Cr 20.0 Fe 1.0 Y20, 0.6

INCO 330

Ni Fe Cr Si

35.5 44.8 18.5 1.2

53

f?.

3072 3074 3076(NA21)

HR 505

B443 B444 B446 B565 B704 B705 B751

sB443 SB444

SB446 SB564

2

5666 5599 5837 5581

3

B637, B670

Boiler codes I and 111

-

PrEN2404 2405,2407 2408,2952 2961,3219

NO7718

8637

SA637

5542 558213 5598 56671819 567011 56819 5747,7246

-

NO7750

NO7754

B511,B512 B535, B536 B546, B710

SB511,SB536 5592 SB710 5716 Boiler codes VIII, IX

-

NO8330

'

B464-4 B468 B472-4 B751

SB462, SB464 SB468 Boiler codes 111, VIII, IX

-

NO8020

2.4619

8581-2 B619,B622 B626, B751

SB581-2 SB619,SB622 SB626 Boiler codes VIII, IX

-

NO6985

17744 17750-17752

2.4819

B574-5 B619,B622 B626,B751

SB57k5 SB619, SB622 SB626 Boiler codes I, 111, VIII, IX

-

2.4665

B435, B572 B619, B622 B626; B751

SB435, SB572 SB619, SB622 SB626 Boiler codes 111,VIII, IX

Pr EN 2182-

INCO 020

Ni 35.0 Fe 38.4 Cr 20.0 cu 3.5 Mo 2.5 Nb 0.6

INCO G-?

Ni Cr

49.0 22.5 Fe 19.5 Mo 7.0 cu 2.0

17744 17750-17752

INCO C-276

Ni 59.0 Mo 16.0 Cr 15.5 Fe 5.5 W 4.0

INCO-HX

Ni 48.3 c r 22.0 Fe 18.5 Mo 9.0 co 1.5 W 0.6 c 0.1

NC22FeD

Incoloy 800 Incoloy 800HT

Fe Cr Ti A1

25 NC35-20

Incoloy 825

30 21 Mo 3 cu 2 Ti 2

WFe32C2ODU 17744 1775C2 17754

Incoloy DS

Fe Cr Si

-

46 21 0.4 0.4

Fe Cr

40 18 2

XI0 Ni Cr AI Ti 3220

HR 6, HR 204

N10276

2185

1.4876

3072-76:NA 15

B163 B407-409 B564 B514-5 B751

SB163 SB407-409 SB564

5766 5871

-

2.4858

3072-76:NA 16

B163 B423-425 B704-5 B751

SB163 SB423-425

-

-

3072-76 :NA 17

-

NO8800 NO8811

3

w

x

21

Table 22.26

WROUGHT NICKEL AND HIGH HICKEL ALLOYS, STANDARD SPECIFICATIONS*AND DESIGNATIONkontinued Nomind composition France

Alloy

AFNOR

% ~

Ni-Span C-902

Ni Fe Cr Ti

Al Hastelloy E 2

Hastelloy C-4

UK

DIN

Werkstoff Nr.

BS and DTD

-

3127

-

-

B333 B335B619 B622

SB333 SB335 SB619 SB662

B574 B575 B619 B662

SB574 SB575 SB619 SB662

M o 25

Mo 16 Cr 16

Mo 9 Cr 21 Fe 15

Nimonic 75

Cr Ti

20 0.4

NC22FeD

NC 20T

LW2.4665

-

HR6 HR204

B435 B572 B619 B622 B626

17742:Ni Cr 20 Ti

2.4951 2.4630

Hr5 HR203 HR403 HR504

2.4631 2.4952

2.4632

LW 2.4630 17750-2

Nimonic 80A

Nimonic 90

Cr Ti AI

20

Cr Ti

20 17 2.4

Al

1.4

Co

ASME

AMS 5210 5221 5223 5225

AECMA

UNS

~

42 Rem. 5.5 2.5 0.5

Hastelloy X

k?

USA ASTM

Germany

NC 20TA

2.0

1.5

NCK 20TA

Ni Cr 20 Ti AI 17742 17754

%

2

NO6455 fi

2;

5536,5587 5754,5588

Ni-P93-HT

NO6002

-

Pr EN 22934 2302 2302402 2411

NO6075

3076: NA 20 HRl HR201 HR401 HR601

B637

hEN2188-91 2396 2397

NO7080

HR2 HR202 HR402 HR501 HR502-3 BS3975-NA19

-

Pr EN 2295-99 2401-2 2412 2669-70

NO7090

5829

% & 5

Nimonic 105

Cr

Nimonic 11s

Cr Co Mo

15 c o 20 Mo 5 AI 5 Ti 1.2

AI Ti

14 13 3 5 4

MK2OCDA

-

2.4634

HR3

NKlOATD

-

2.4636

HR4

Nimonic 263

Cr co

20 20 Mo 6 Ti 2 AI 0.5

NCK20D

-

2.4650

HRlO HR206 HR404

Nimonic 901

Fe 35 Cr 13 Mo 6 Ti 3

Z8NCDT42

-

2.4662

HR53

Nimonic PE16

Fe

32 Cr 16 Mo 3 Ti 1.0 AI 1.0

NWllAC

Nimonic PK33

Cr 18 Co 14 Mo 7 Ti 2.25 AI 2.1

NC19KDuIv -

Astroloy

Ni 54.8 Cr 15.0 Co 17.0 Mo 5.3 AI 4.0 3.5 Ti

-

-

-

Pr EN 2179-81

-

-

Pr EN 2196 2197

5872

Pr EN 21992203 2418

NO7263

5660 5661

Pr EN 21768

NO9901

5n

E$-

-

Hr55 HR207

DTD5057

-

-

-

-

N

w

Table 22.26 WROUGHT NICKEL AND HIGH HICKEL ALLOYS, STANDARD SPECIFICATIONS* AND DESIGNATIONS-continued

UK

Alloy

%

AFNOR

DIN

Werkstoff Nr.

BS and DTD

USA ASTM

ASME

AMS

AECMA

UNS

Rene 41

Ni 55.4 Cr 19.0 Co 11.0 Mo 11.0 A1 1.5 Ti 3.1

__

-

-

-

-

-

-

-

NO7041

Ni Cr

61.5 14.0 co 8.0 Mo 3.5 Nb 3.5 AI 3.5 Ti 2.5

-

Rene 100

Ni 61.8 Cr 9.5 Co 15.0 Mo 3.0 AI 5.5 Ti 4.2 v 1.0

-

Udimet 500

Ni Cr Co Mo A1 Ti

Udimet 700

Ni 55.5 Cr 15.0 Co 17.0 Mo 5.0 AI 4.0 Ti 3.5

-

Waspaloy

Ni 58.7 Cr 19.5 Co 13.5 Mo 4.3 A1 1.3 Ti 3.0

-

Nominal composition France

Rene 95

Germany

tJ I

2

g

8.

-

P

2 %

7. 2

3

~~

NO7500

53.7 18.0 18.5 4.0 2.9 2.9

* Spcciticmon constantly under review, check lor latest issue. t AssoLialion EurupCcnnc des Consrmcwurs de MalCnel Ahsparial

NO7001

Meckmical properiies of nickel and nickel alloys

22-71

Table 22.27 WROUGHT NICKEL AND HIGH NICKEL ALLOYS,MECHANICAL PROPERTIES1'AT ROOM TEMPERATURES

0.2%

Nominal composition

proof

~lioy(~)

%

Condition

Nickel-pure

Ni 99.9

Annealed

Nickel--comc.

Ni 99.0

Annealed Hot rolled Cold drawn

Elonga-

UTS MPa

I24

tion %

Brinell hardness 85

60

310

150 200 480

400 500 660

40 40

100

40 25

120 190

impact

J 160 160 160

90

345

45

80

-

Annealed Hot rolled Cold drawn

240 490 570

550

620 700

40 35 25

125 150 190

140 140 110

Nickel 205

Ni 99.6min. Annealed

Monel") 400

Cu 31.5 Fe 1.5 Mn 1.0

stress MPa

Monel450

Ni 31.0 Fe 0.7 Cu Rem.

Annealed

165

385

46

90

-

M o d K-500

Cu 29

Annealed and aged Hot rolled and aged Cold drawn and aged

790

1100

30

290

-

880

1110

25

310

-

850

1110

20

310

-

Annealed Cold drawn

200 450

400 590

45 20

-

-

A1 Ti

2.8 0.5

C~pro-nickel'~)

cu

Inconel"' 600

Cr 15.5 Fe 8

Annealed Cold drawn

310 700

655

880

45 20

150 200

Ni 60.5

Annealed

210-340

550-790

7040

110-150

160 110 -

Inconel 601

55

-

Cr 23.0 AI 1.4 Fe 15.1 Inconel 617

Ni 55.7 Cr 21.5 Co 12.5 Mo 9.0 A1 1.2 c 0.1

Annealed

350

760

58

I73

-

Inconel625

cr

22 Nb 4 Mo 9

Annealed Solution treated

520

930 810

45 50

186 157

-

352

Inconel718

Ni Cr Fe Nb Mo Ti A1

Precipitation hardened

1180

1350

17

382

-

Inconel X-750

Cr 15

900

1240

20

382

-

270

590

47

150

-

Fe Ti AI

Nb Inconel MA 754

52.5 19.0 18.8 5.2 3.1 0.9 0.5 7 2.5 0.6 0.8

Fully heat treated

-

Ni 78.0 Cr 20.0 Fe

1.0

Y,O, 0.6 INCO 330

Ni 35.5 Fe 44.8 Cr 18.5 Si 1.2

22-72

Mechanical properties of metals and alloys

TsbIe 22.27

WROUGHT NICKEL AND HIGH NICKEL ALLOYS, MECHANICAL PROPERTIES"' AT ROOM TEMPERANRES-confinued 02%

Nominal

Proof

composition

stress

Elonga-

fzod

tion %

Brinell

impact

hardness

J

~120y")

Ye

Condition

MPa

UTS MPa

INCO 020

Ni 35.0 Fe 38.4 Cr 20.0 cu 3.5 Mo 2.5 Nb 0.6

Annealed

310

620

40

183

INCO G-3

Ni Cr Fe Mo

Annealed

320

690

50

146

-

Annealed

415

790

50

184

-

Annealed

340

790

45

184

-

cu

INCO C-276

Ni Mo Cr Fe

W INCO-HX

Ni Cr Fe

Mo co

W

c

49.0 22.5 19.5 7.0 2.0 59.0 16.0 15.5 5.5 4.0 48.3 22.0 18.5 9.0 1.5 0.6 0.1

Incoloy(I' 800

Fe 46 c r 21 Ti 0.4 AI 0.4

Annealed Cold drawn

310 700

590 880

45 20

180 250

160 110

Incoloy 825

Fe Cr Mo cu Ti

Annealed

340

650

40

150

160

Incoloy DS

Fe 40 Cr 18 Si 2

Annealed Cold drawn

220 850

600 1000

61 10

190 300

140 110

Ni-Span") C-902

Fe 47 Cr 5.5 Ti 2.5 AI. 0.5

Fully heat treated

770

1200

25

300

-

Hastelloy B-2

Mo 28

Solution treated

526

955

53

235

Hastelloy C-4

Mo 16 Cr 16

Solution treated

416

768

52

184

Hastelloy C-276

Mo 16 Cr 15 w 4 Fe 5 c 0.02 Mo 9 Cr 21 Fe 18 Cr 20 1 Si Cr 20 Ti 0.4 Cr 20 Ti 2.0 AI 1.5

Solution treated

360

790

60

200

Solution treated

350

800

45

175

Annealed

330

760

40

160

-

Annealed

240

750

40

170

110

Fully heat treated

780

1 220

30

370

70

Hastelloy X

Brightvay C Nimonic") 75 Nimonic 80A

32 21 3 2 1

75

Mechanical properties of nickel and nickel a!loyr

22-73

Table 22.27 WROUGHT NICKEL AND HIGH NICKEL ALLOYS, MECHANICAL PROPERTIES1’ AT ROOM TEMPERATURES-continued

~rioy’3’

Nominal composition %

0.2% proof

Condition

MPa

UTS MPa

stress

Elongation

izod

%

Brinell hardness

impact J

Nimonic 90

Cr 20 Co 17 Ti 2.4 Al 1.4

Fully heat treated

750

1175

30

380

70

Nimonic 105

Cr co Mo A1 Ti

15 20 5 5 1.2

Fully heat treated

780

1140

22

380

16

Nimonic 115

Cr Co Mo AI T i

14 13 3 5 4

Fully heat treated

865

1240

27

400

-

cr

20 20 6 2 0.5 35 13

Fully heat treated

580

970

39

320

-

Fully heat treated

900

1220

15

-

-

Fe 32 Cr 16 Mo 3 Ti 1.0 A1 1.0

Fully heat treated

460

850

30

280

-

cr

Fully heat treated

790

1170

Nimonic 263

Nimonic 901

Nimonic PE16

Nimonic PK 33

co Mo Ti AI Fe Cr Mo Ti

Co Mo Ti A1

6

3

18 14 7 2.2 2.1

Astroloy

Ni 54.8 Cr 15.0 Co 17.0 Mo 5.3 AI 4.0 Ti 3.5

Precipitation hardened

1050

1415

Rene 41

Ni Cr co Mo

55.4 19.0 11.0 11.0 Al 1.5 Ti 3.1

Precipitation hardened

1 060

1420

Rene 95

Ni 61.5 Cr 14.0 c o 8.0 Mo 3.5 Nb 3.5 AI 3.5 Ti 2.5 Ni 53.7 Cr 18.0 co 18.5 Mo 4.0 A1 2.9 Ti 2.9

Precipitation hardened

1310

1620

Precipitation hardened

840

1310

Udimet 500

22-14

Mechanical properties of metals and alloys

Table 27.27 WROUGHT NICKEL A N D HIGH NICKEL ALLOYS, MECHANICAL PROPERTIEP AT ROOM TEMPERATLJREhontinued Nominal composition %

Alloy'3'

Udimet 700

Ni 55.5 Cr 15.0

0.2% Proof UTS MPa

stress

Condition

MPa

Izod

Elongatwn %

Brinell

impact

hardness

J

-

-

Precipitation hardened

965

1410

17

-

Precipitation hardened

795

1275

25

-

Co 17.0

Mo 5.0 4.0 Ti 3.5 Ni 58.5 Cr 19.5 Co 13.5 Mo 4.3 Al 1.3 Ti 3.0

Al

Waspaloy

(1) Registered Trade Mark. ( 2 ) All values in the tables in this section are representative and not to be consided as minima or maxima not to be used for specification purposes. Conversion figures have all heen rounded off and are not to be taken as precise equivalents. (3) Where trade marks apply to the name ofan aUoy there may be materials of similar composition available from other producm who may os may not use the same suffix along with th& own trade names. The suffix alone, e.g. Alloy 800 is sometimes used

as a descriptive term for the type of alloy but trade marks can be used only by the registered user of the mark. (4) Other copper-nickel alloys, cupro-nickels, will be found listed under copper base alloys. ( 5 ) Fully heat-treated usually implies a solution treatment followed by some form of precipitation hardening cycle. The precise heat-treatment and the associated properties may be vaned to suit particular applicationsor according to the form of the alloy

as forging, bar,sheet or welded fabrication. (6) l k e are m a n y oickd chromium alloys with and without iron used for electrical rsistanCe heating and for general high-temperatureapplications in furnaces and heat-treatment plant. This alloy is typical.

Table 22.28

WROUGHT NICKEL AND HIGH NICKEL ALLOYS, SHORT-TIME HIGH-TEMPERATURE TENSILE

PROPERTIES

Alloy

Nominal composition %

Condition

Nickel

Ni 99.0

Hot rolled

0.2% Proof

Test temperature

stress

"C

MPa

20 200 400 600 800

170

150 140 110

-

UTS MPa

Elongation %

490 540 540 250

50 50 50 60

170

60

Nickel 205

Ni 99.6min.

Annealed

20

90

345

45

Monel* 400

Cu 30 Fe 1.5 Mn 1.0

Hot rolled

20 200 400 600 800

230 200 220 120 77

560 540 460 260 120

45 50 52 30 54

Monel450

Ni 31.0 Fe 0.7

Annealed

385 300 290 150 58

46 55 42 40

680 650 600 460 185

45 40 30 5 30

Cu

Monel* K-Mo

Rem.

Cu 29

Al

2.8

Ti

0.5

Fully heat treated

20

165

200

120

400 600 800

100

20 200 400

340 290 260 290

600 800 *Registered trade mark.

75 28

-

19

Mechanical properties of nickel and nickel alloys

22-15

Table 22.28 WROUGHT NICKEL AND HIGH NICKEL ALLOYS, SHORT-TIME HIGH-TEMPERATURE TENSILE PROPERTIES-continued

Alloy

Inconel* 600

Nominal composition %

Cr 16 Fe 6

Condition

Hot rolled

Test temperuture "C

20 400 600 800 1000

0.2% Proof stress MPa 250 185 150 95 -

UTS MPa

Elongation %

590 560 530 250 1IO

50 50 10 20 50

Incooel 601

Ni 60.5 Cr 23.0 A1 1.4 Fe 15.1

Annealed

20 200 400 600 800 870

440 410 380 325 170 100

760 750 740 575 205 160

43 38 38 32 92 122

Inconel 617

Ni Cr Co Mo AI

Solution Annealed

20 200 400 600 800 1000

330 260 230 220 230 80

720 640 600 580 410 160

63 70 72 58 65 92

c

55.7 21.5 12.5 9.0 1.2 0.1

Inconel 718

Ni Cr Fe Nb Mo

52.5 19.0 18.8 5.2 3.1 Ti 0.9 A1 0.5

Precipitation hardened

20 200 400 600 800

1180 1100 1080 960 720

1350 1280 1240 1160 760

17 16 13 16 8

Inconel X-750

Cr 15 Fe 7 Ti 2.5 AI 0.6 Nb 0.8

Fully heat treated

20 400 650 800 800

620 590 280 310 100

1110 1100 830 370 170

24 2x 9 22 90

Inconel MA 754

Ni 78.0 Cr 20.0 Fe 1.0 Y203 0.6

Annealed

20 200 400 600 800 1000

560 560 540 500 230 120

940 910 860 640 250 160

20 18 16 18 30 16

20 200 400 600 800 980

280 220 200 165 120 70

580 520 500 430 170 80

48 45

Ni 35.5 Fe 44.8 Cr 18.5 Si 1.2

Annealed

INCO 020

Ni Fe Cr cu Mo Nb

35.0 38.4 20.0 3.5 2.5 0.6

Annealed

30 200 400 600 800 870

300 280 250 185 150 140

620 575 560 505 275 220

40 40 39 41 59 12

INCO G-3

Ni Cr Fe Mo cu

49.0 22.5 19.5 7.0 2.0

Solution Annealed

20 200 400 600

320 235 190 175 170 75

690 590 555 500 355 140

50 62

INCO 330

800

lo00 Registered trade marlk.

44 49 68 74

68

73 66 76

Mechanical properties of metals and alloys

22-16

Table 22.28 WROUGHT NICKEL AND HIGH NICKEL ALLOYS, SHORT-TIME HIGH-TEMPERATURE TENSILE PROPERTIES-wntinued

Nominal

composition %

Alloy

0.2% proof stress MPa

UTS MPa

tion %

Elonga-

59.0 16.0 15.5 5.5 4.0

Annealed

20 200 400 540

415 285 240 220

790 690 660 610

50 56 64 60

48.3 22.0 18.5 9.0 1.5 W 0.6 c 0.1

Solution Annealed

20 200

340 300 225 220 180

790 745 700 600 370 110

45 40 48 46 48 56

Fe 45 Cr 21 Ti 0.4 A1 0.4

Annealed

300 210

600 440

45 40

Fe 40 Cr 18 Si 2

Annealed

300

700 460 150 75

45 50 90 100

Hastelloy* B-2

Mo 28

Solution treated

200 320 430

451 426 418

885 864 866

50 49 51

Hastelloy C-4

Mo 16 Cr 16

Solution-treated

200 320 430

403 371 320

706 675 656

49 52 64

Hastelloy X

Mo 9 Cr 21 Fe 18

Solution treated

20 600 800 lo00

360 280 230 110

790 620 410 160

45 40 37 45

Nimonic* 75

Cr 20 Ti 0.4

Annealed

20 400 600 800 lo00

420 400 310 110 50

800 740 590 220 90

35 30 30 80 58

NhoniC* 80A

Cr 20 Ti 2.0 AI 1.5

Fully heat treated

20 400 600 800 lo00

740 680 620 490 70

1240 1150 lo80 620 120

24 26 20 24 120

Nimonic 90

Cr 20 Co 17 Ti 2.4 AI 1.4

Fully heat treated

20 600 800 lo00

750 680 530 48

1175 1030 900 76

30 26 18 130

Nimonic 105

cr co Mo A1 Ti

Fully heat treated

20

780 720 680 150

1140 1040 810 175

22 25 25 42

INCO C-276

Ni Mo Cr Fe

Condition

Test temperature "C

W

-

INC0 HX

Incoloy* 800

Incoloy DS

Ni Cr Fe Mo co

*Registered trade mark.

15 20 5 5 1.2

400 600 800 lo00 20 600

20 600 800 lo00

600

800 lo00

40

-

Mechanical properties of nickel and nickel alloys

22-11

Tabb 22.28 WROUGHT NICKEL AND HIGH NICKEL ALLOYS, SHORT-TIME HlGH-TEMPERATURE TEXSILE PROPERnES-continued

0.2% Nominal composition

Test temperature “C

MPa

lion %

860 790 760 200

1230 1100 1 020 420

27 20 19 26

970 790 560 110

40 41 20 65

1000

490 450 290 46

880 730 390 92

37 27 53 100

?4Q

Condition

Nimonic 115

Cr 14 Co 13 Mo 3

Fully heat treated

20 600 800 1 000

A1

5 4

ElongnUTS MPa

Alloy

Ti

proof

stress

0.1% PS 570 460 390 60

Nimonic 263

Cr 20 c o 20 Mo 6 Ti 2 Al 0.5

Fully heat treated

20 600 800 loo0

NimonicPE 16

Cr 16 Fe 32 Mo 3 Ti 1.0 AI 1.0

FuUy heat treated

20 600 800

Astroloy

Ni Cr Co Mo

54.8 15.0 17.0 5.3 A1 4.0 Ti 3.5

Precipitation hardened

20 540 650 760 870

1050 965 965 910 690

1410 1240 1310 1160 770

16 16 18 21 25

Rene 41

Ni 55.4

Precipitation hardened

21 540 650 760 870

1060 1010 lo00 940 550

1 420

1400 1340 1100 620

14 14 14 11 19

Precipitation hardened

21 540 650 760

1310 1250 1 220 1100

1620 1540 1460 1170

15 12 14 15

21 650 760 870

840 765 760 730 495

1310 1240 1210 1 040 640

32 28 28 39 20

21 540 650 760 870

965 895 855 825 635

1410 1 240 1030 690

17 16 16 20 27

21 540 650 760 870

795 725 690 675 515

1280 1170 1120 795 525

25 23 34 28 35

Cr co Mo AI

19.0 11.0 11.0 1.5 Ti 3.1

Rene 95

Ni 61.5 Cr 14.0 Co 8.0

Mo 3.5 Nb 3.5 A1 3.5 Udimet 500

Udimet 700

Waspaloy

Ti

2.5

Ni Cr Co Mo A1 Ti

53.7 18.0 18.5 4.0 2.9 2.9

Precipitation hardened

Ni Cr Co Mo

55.5 15.0 17.0 5.0 A1 4.0 Ti 3.5

Precipitation hardened

Ni 58.7 Cr 19.5

Precipitation hardened

Co 13.5 Mo 4.3 AI 1.3 Ti 3.0 *Registered trade mark.

540

1280

22-78

Mechanical properties of metals and alloys

Table 22.29 WROUGHT NICKEL AND HIGH NICKEL ALLOYS. CRYOGENIC PROPERTIES Nominal composition ailoy

%

Condition

Nickel

Ni 99.0

Annealed

Test temp. "C

0.2% Proof stress MPa

MPa

160 170 230

20

-75

-200 Monel** 400

Cu 30 Fe 1.5 Mn 1.0

20

Annealed

- 180

M o d * * K-500 Cu 29 AI 2.8 Ti 0.5

Fully heat treated

Inconel** 600 Cr 16 Fe 6

Annealed

Inconel718

Fully heat treated

20

-80

-200 -255

Cr Nb Mo Ti A1

19 5

3 0.9 0.5

Inconel X-750 Cr 15 Fe 7 Ti 2.5 A1 0.6 Nb 0.8

Fully heat treated

Ni-Span** c-902

Fully heat treated

Fe 47 Cr 5.5 Ti 2.5 A1 0.5

* IO6 cycles Kt=3.1.

20

-80 - 190

230 230 230

-

220 340

540 800

52 50

260 240

-

670 740 830 940

1060 1 140 1260 1380

22 24 30 28

74 68

-

-

300 330 330

120 140

650 730

37 40

240 210 190

280 280 300

1400 1400 1600

1500 1600 1800

-

-

-

-

-

-

700 790 810 900

1200 1290 1440 1450

24 23 19 16

-

-

760 860 1000

1210 1410 1690

30 28 25

-200 -255

-255

48 58 54

UTS

-

20

20

500 560 710

230 290

-15

- 130

Charpy impact J

-

20

-80 - 190

Notched fatigue strength* MPa

Elongation %

-

24 23 23

410 440 460 320 310 390

-

**Registered trade mark.

Table 22.30 WROUGHT NICKEL AND HIGH NICKEL ALLOYS, FATIGUE PROPERTIES

Alloy

Nominal composition %

Nickel

Ni 99.0

Annealed Cold drawn

20 20

230 340

Monel** 400

Cu 30 Fe 1.5 Mn 1.0

Annealed Cold drawn*

20 20

230 300

Monel K-500

Cu 29

Annealed Cold drawn and aged Annealed

20 20

260 320

20 850

270 180 75

29 421 538 649 760

460 450 425 390 310

Inconel** 600

Inconel 625

A1 2.8 Ti 0.5 Cr 16 Fe 6 Cr 21.5 Mo 9.0 Nb 3.6

Condition

Test temperature "C

650

Hot rolled

Average endurance limit Rotating beam tests IO8 cycles MPa

Mechanical properties of nickel and nickel alloys

Table 22.30

22-79

WROUGHT NICKEL AND HIGH NICKEL ALLOYS, FATIGUE PROPERTIES-continued Nominal composition

Alloy

Yo

Condition

Test temperature "C

Inconel 718

Cr 19

Fully heat treated

20 650

620 500

Fully heat

20 700

280 340

20 500 850

290 260 95

Nb 5 Mo 3 Ti 0.9 AI Inconel X-750

MPa

0.5

c r 15 Fe 7

Ti

Average endurance limit Rotating beam tests 10' cycles

treated

2.5

A1 0.6 Nb 0.8 Incoloy** 800

Fe 45 Cr 21

Ti

Annealed

0.4

0 f stress. For lives of

Nimonic** 75 Nimonic 90

Nimonic 105

Cr 20 Ti 0.4

Annealed

Cr 20 Co 17 Ti 2.4

Fully heat treated

MPa

h

20 750

260 190

750

260 240 140 110

65 300 300 1000 300 1 000 50 500 50 500 50 500 50 500

870

Al 1.4 Cr 15

Fully heat treated

c o 20

20

350 250 260 250 240 190 170 124

750

Mo 5 5 1.2

AI Ti

870 980

*Stress equalized 3 h at 26O'C.

cycies 10 x 106

10 x 106 36 x lo6 120x 106 36 x lo6 120x 106 3 x 107 3 x 10' 3 x 107 3 x 10' 3 x 107 3 x 106 3 x 107 3 x 108

**Registemi trade marks.

'Table 22.31 WROUGHT NICKEL AND HIGH NICKEL ALLOYS, CREEP PROPERTIES-continued Stress MPa for creep extension of

0.1% Alloy

Nominal composition % Condition

Nickel

Ni 99.0

Colddrawn

400

Monel* 400

Cu 30 Fe 1.5

Hot rolled

400

-

400

-

Mn 1.0 Monel K-500 Cu 29 Colddrawn A1 2.8 and aged Ti 0.5 Inconel* 600 Cr 16 Hot rolled Fe 6 Inconel601 Ni 60.5 Annealed Cr 23.0 AI 1.4 Fe 15.1

0.2%

1%

Rupture

Test temp.

"C

300 h

400 600 650 195 760 63 870 30 980 14 1095 7

1000 10000 h h

lo00 10000 1OOW h h h

300 h

1000 loo00 h h

-

7

220

-

-

-

140

-

-

-

215

-

-

-

35s

-

-

-

-

-

-

-

340 3 8

-

-

-

-

_

_ -

-

-

_ - - - _ - - _ - _ _ _ _

-

_ _ _ _ _

_ -

-

7

-

-

-

-

-

-

I1 -

-

22-80

Mechanical properties of metals and alloys

Table 2231 WROUGHT NICKEL AND HIGH NICKEL ALLOYS,CREEP PROPERTIES Stress MPa for creep extension of

Nominal composition Alloy

%

Inconel 617

Ni Cr Co Mo A1

Condition

320 150 58 25 10

-

Precbitation hard&d

595

760

-

Incoloy*800H Fe 45 Cr 21 T1 0.4 A1 0.4

Solution treated

650 870 980

-

115 24 7

Inconel X-750

Cr 15 Fe 7 Ti 2.5 A1 0.6 Nb 0.8

Fully heat treated

595

-

InconelMA754 Ni 78.0 Cr 20.0 Fe 1.0 Y203 0.6

Annealed

-

INCO 330

Ni 35.5 Fe 44.8 Cr 18.5 Si 1.2

Annealed

760 870 980 1095

INCO-HX

Ni 48.3 Cr 22.0 Fe 18.5 Mo 9.0 Co 1.5 W 0.6 c 0.1

Solution Annealed

760 815 870 925 980

Cr 20 Ti 0.4

Annealed

Inconel718

Ni Cr Fe

Nb Mo Ti A1

Nimonic' 75

Nimonic 80A

Nimonic 90

Solution Annealed

-

650 760 870 980 1095

c

55.7 21.5 12.5 9.0 1.2 0.1 52.5 19.0 18.8 5.2 3.1 0.9 0.5

0.1% 0.2% 1% Rupture Test temp. 300 1000 10000 300 lo00 loo00 loo00 lo00 loo00 "C h h h h h h h h h

Cr 20 Ti 2.0 A1 1.5

Fully heat treated

Cr 20 Co 17 Ti 2.4 A1 1.4

Fully heat treated

650 730 815 870 650 256 760 199 870 158 980 129 1095 94 1150 78 48 21 8.6 5.4 110 72 45 26 15

56 650 750 25 815 870 925 980 650 390 705 750 170 815 93 650 400 705 750 185 815 85 870 49

-

-

-

-

-

-

-

-

-

90 20 3.8

-

I

-

-

-

-

-

-

-

-

_

-

-

-

-

-

-

121 24 8.3

-

-

-

-

-

110

-

-

630 470 260 110 50

-

-

-

170 50 24 15 10 8

-

260

280

66 26

90 29 325

500 350 220 110

- 420 - - _ -

-

-

-

-

-

-

-

-

-

-

-

-

-

-

- - _ - - - - _ -

185

460

-

-

120 58

200 108 450

150 73

348

-

-

-

-

62 29

-

_

390

400

-

-

-

137 57 29

220 108 60

175 71 37

51

25 -

-

-

310

-

85 31 17

-

-

-

-

110 38 18

455 360 240 150 75

280

-

85 34 340

-

135 54 28

Mechanical properties of nickel and nickel alloys

22-81

Table 22.31 WROUGHT NICKEL AND HIGH NICKEL ALLOYS, CREEP PROPERTlES-continued Stress MPa for creep extension of

0.1% Nominal

Test tap.

composition

Alloy

Ya

Condition

Nimonic 105

Cr 15

Fully heat treated

Nimonic 115

co 20 Mo 5 AI 5 Ti 1.2 Cr 14 Co 13 Mo 3 AI 5 Ti 4

Astroioy

Rene 41

R a e 95

Udimet 5001

Udimet 700

Waspaloy

"C

750 815 870 940 980 Fully heat 750 treated 815 850 870 950 925 980 1000 Ni 54.8 Precipitation 650 Cr 15.0 hardened 760 Co 17.0 870 Mo 5.3 980 A1 4.0 Ti 3.5 Ni 55.4 Precipitation 650 Cr 19.0 hardened 760 co 11.0 870 Mo 11.0 A1 1.5 Ti 3.1 Ni 61.5 Precipitation 650 Cr 14.0 hardened Co 8.0 Mo 3.5 Nb 3.5 AI 3.5 Ti 2.5 Ni 53.7 Precipitation 650 Cr 18.0 hardened 760 Co 18.5 870 Mo 4.0 A1 2.9 Ti 2.9 Ni 55.5 Precipitation 650 Cr 15.0 hardened 760 Co 17.0 870 980 Mo 5.0 A: 4.0 Ti 3.5 Ni 58.7 Precipitation 650 Cr 19.5 hardened 760 870 Co 13.5 Mo 4.3 A1

Ti

300 h

0.2% lo00 loo00 300 h

h

h

1%

Rupture

lo00 10000 10000 lo00 1 0 m h h h h h

-

285 162 86 31

-

355

154

-

51

22 770 425 170 55 705 345 115

860

760 325 125

705 425 200

55

615 290 110

1.3 3.0

'Registered trade mark.

BIBLIOGRAPHY 'Nickel and Its Alloys', US Department of Commerce NBS Monograph 106,Washington, USA; 1968. W. Betteridge and J. Heslop, The Nimonic Alloys', Edward Arnold, London; 1974. For more detailed information, see: INCO Alloys International Ltd., Product Handbook, 1990. G.W. Meetham (ed.), The Developmentof &Turbine Materiak',AppliedScience Pubiishers Ltd,Barking, Essex, 1981. Metals Handbook, 9th Edition, Vol. 3, American Society for Metals, 1Y80. Merals Handbook, loth Edition, Vol. 1, ASM International, 1990.

Mechanicai properties of metals and alloys

22-82

22.6

Mechanical properties of titanium and titanium alloys

UK British srandmdr

IMI designation

IMI 115 IMI 125

IMI 130

IMI 155 IMI 160

IMIm IMI 315 IMI 317 IMI 318

AECMA

(Aerospace seriesJ andMin. ofD$ DTD seties*

Frunce AIR-9182, 9183,9184

Germany BWB series?

recorn

USA

USA

mendations

AMs series*

ASTM gerie8

BS TA 1, DlD 5013 BS TA 2,3,4,5

T-35

3.7024

limI

T-40

3.7034

li-PO2

DTD 5023,5273, 5283,5293 BSTA6

T-50

Bs TA 7.89 BS TA 21,22, 23.24, BS TA 52-5558 DTD 5043 BS TA 14,15, 16, 17 BS TA 10, 11, 12, 13, 28, 56

T-60

3.7064

T-U2

3.7124

T-A5E T-A6V

AMs 4902,4941,4942, 4951 AMS 4900

ASTM grade 2 ASTM grade 3

AMs 4901 AMs 4921

Tip1 1

li-F'65 3.7164

ASTM grade 1

'Ii-P63

AMS 4909,4910,4926, 4924,4953,4966 AMS 4911,4928,4934, 4935,4954,4965,4967

ASTM grade 5

IMI 318 ELI (exfra low AMS 4907, 4930,4931 AMS 4943 4944

interstitial)

IMI 325 IMI 550 IMI 551 IMI 624

3.7194

Bs TA 45-51,57 BS TA 39-42

-

T-A4DE

3.7184

T-A6Zr4 DE

3.7144

IMI646 IMI662 M I 679 IMI 680 MI 685 IMI 811 IMI 834

BS TA 18-25, 25-27 DTD 5213 BS TA 43,44

-

-

T-El IDA T-A6ZD T-A8DV T-A6E Zr4Nb

li&8

3.7174

--

3.7154

li-P67

-

ASTM grade 3, E. 136. ASTM grade 9

AMs 4919, 4975,49l6 AMs 4981 AMs 4918, 4971,4978, 4979 AMS 4974

AMS 4915, 4916

*UKBS 3531 Part 1 (Metal Implants in Bone Surgery), and D& British StandardforLining of Vessels and Equipment for Chemical Pmcsses. Part 9, also refer. t(;ermany DIN 17850.17860,17862,17863, 17864 (3.7025/35/55/65), and "V 230-1-68 Gmup I, E,III and N also %fer. $USA MIGT9011,9046,9047.14577.46038,46077, MI0737 and ASTM B265-69, B33865.8348-59T, B367-61T. B381-61T. B382-61T also =fez

Table 22.33

PURE m A N N M , TYPICAL MECHANICAL PROPERTIES AT ROOM TEMPERATURE

Designalion*

Grade

Iodide IMI 115

h e , 6 0 HV Commercially pure

Condition

Commercially pure

IMI 12s

Commercially pure.

MI 130

Commercially pure Commercially pure

IMI 155 IM1 160

*MI Nomenclature.

0.2% p.wfsmss MPa

Annealed sheet Annealed rod Annealed W-iie +Annealed sheet Annealed rod Annealed tube Annealed sheet Annealed rod Annealed wire Harddrawn wire Annealed sheet Annealed rod Annealed wire

103 255 220 340 305 325 420 360 540

500

Elongation %

Red

shvngth

OR

MPa

50 nun

on5D

arm 40

241

55

40

70

28

57

24

48

23

46

Tolsile

in

Mod.of

Mod.of

~ 1 . 8 3mm

~ 3 . 2 5mm

elasticity GPa

rigidity GPa

It

2t

lit

2t

2t+

24t 105

38

80

33

370 370 390

Specimion bend &ius 180 bend

38 30

460 460 480 540 540 550 700 640 670 690

35 25

24 11.5 24

24 t

3t

24

tup to 16.3 mm.

Table 22.34 TIXWlWM ALLOYS TYPICAL. MECHANICAL F'ROPERTES AT ROOM TEMPFBATURE

Nominal composition Designation*

%

MI 230

cu

IMI 260 IMI 261 IMI 315 IMI 317

Pd Pd A1 Mn A1 Sn

0.2%

Tensile

proofsmss

smgth

MPa

MPa

on50 mm

Annealedsheet 520 Aged sheet 670 500 Annealedrod Aged rod 580 Similar to commercially Pure TItanium 115 Similiar to commercially Pure 'IItanium 125 Annealedrcd 590

620 770 630 740

24

Annealed sheet

820

860

Annealedrod

930

1 0

Condition 6.0

0.2 0.2 2.0 2.0 5.0

Elongation %

20

720

Red inarea

on5D

%

27 22

45 41

21

50

Modof elasticily GPa

2t(0.5-3 mm) 2t(typical)

125

Modof rigidily GPa

125

120 4t(99.9% purity Crystal bar, Impurities in cold rolled ppm by wt and vacuum 0,65, N,15, annealed 2 h H,12, Hf 35, at 750°C Ni 20

Zr 299.6% purity (ex sponge) Impurities in ppm by wt 0,1300, N,80, HZ20,Hf 400, Ni 40 Zircaloy 2 Sn 1.2-1.7% Fe 0.0742% Cr 0.05415% Ni 0.03-0.08% Zr-remainder Zirconium Cu 0.46466% 30* Mo 0.50-0.60% Zr-remainder Zrf29h Nb 2.55% Nb Impurities in ppm by wt 021050,N,2O, H210, Hf 70

N0 Ni alley 1.2:; Mn followed by 0.6% Si followed by 0.03% Mg Can degas with N, or dry air

Cast-irons

Deoxidation not required

Acid cupola: Limestone 28-32 kg tonne-' providing (a) Standard cupola practice (b) Coke ash content-lO"/, (c) CaCO, is 96% of limestone Energized' flux for increased efficiency 21 kg tonne-' (14 kg limestone + 7 kg CaF,) Basic cupola 80 to 90 kg tonne-' of flux made up as Limestone 30-40':,, coke wt Dolomite IO",, coke wt * Fluorspar 25"" uf limestone

*Can replxe fluorspar by 50:SO fluorspqsoda ash

Patterns-crucibles-fluxing

26-19

Special purpose fluxes and inoculants

Grain refinement not usually beneficial with these alloys-encourages ‘layer porosity’-although has been achieved with 0.03% Zr 0.02% B, Ti, Co

+

Grain refinement of manganese bronzes by iron

Fe in alloy acts as a grain-refiner

Some grain refinement with Mn

-

Anhydrous soda ash or calcium carbide for desulphurization of acid cupola metal Calcium silicide: ’Meehanite iron’ for grain size control (eutectic cells) Ferro-silicon ( + 1-2% AI and up to 1% Ca), zirconium etc., and reduction of ‘chill depth’ 75% FeSi (A1 and Ca free) and 1-4% Sr

.1

{

elimination of ‘pinholing’ in green sand moulds Nodularization (spheroidization): sulphur 5 0.02% Magnesium for hypo- and hypereutectic irons introduced as: Mg impregnated coke Mg-Ni(Si) alloys Mg-FeSi alloys Mg-Si alloys Cerium for hypereutectic irons introduced as mischmetal

26.3 Aluminium casting alloys Table 26.22 ALUMWRIM-SILICON ALLOYS

r:

Specirnfion BS 1490 1988 Related British SpeciJccatwns

b

LM6M(Ge) BS L33

Composition (%) (single figure indicates maximum) 0.1 Copper Magnesium 0.1 Silicon 10.0- 13.0 Iron 0.6 Manganese 0.5 Nickel 0.1 Zinc 0.1 Lead 0.1 Tin 0.05 lltanium 0.2 Other Pmperlies of material Suitability for: Sand casting E Chill casting (gravity die) E Die casting (press die) G P Strength at elevated temperature E Corrosion resistance E Pressure tightness E Fluidity Resistance to hot shortness E Machinability F Melting range, "C 565-575 Casting temperature range, "C 710-740 Specific gravity 2.65

-

Q

LM2OM(Ge)

0.4 0.2-0.6 10.0-13.0 1.0

LM9M(SP)

.

LM9TE(SP)

LM9TE(SP)

LM13TE(SP)

LM13TF(SP)

0.1 0.2 0.1 0.1 0.2

0.1 0.2 10.0- 13.0 0.6 0.3-0.7 0.1 0.1 0.1 0.05 0.2

0.7-1.5 0.8-1.5 10.0- 12.0 1.o 0.5 1.5 0.5 0.1 0.1 0.2

E* E G P G E E E F 565-575 680-740 2.68

G E G* G E G G E F 550-575 690-740 2.68

G G

0.5

-

-

LM13TF7(SP)

,.!

,

-

P E G F G E F 525-560 680-760 2.70

Rs

8 I

N

%

3

Table 26.22 ALUMINIUM-SILICON W O Y S -continued Speci@ation BS 1490: 1988 Related British Specijlcations

B

LM18M(SP)

Composition Z (Single figure indicates maximum) 0.1 Copper 0.1 Magnesium Silicon 4.5-6.0 0.6 Iron Manganese 0.5 Nickel 0.1 Zinc 0.1 Lead 0.1 Tin 0.05 Xtanium 0.2 Other Pmpenies of material Suitability for: Sand casting G Chill casting (gravity die) G G* Die casting (press die) P Strength at elevated temperature E Corrosion resistance E Pressure tightness G Fluidity E Resistance to hot shortness F Machinability 565-625 Melting range, C Casting temperature range, "C 700-740 Specisc gravity 2.69

LM25M(Ge)

LM25WGe)

LM25TEi7(Ge)

LM25TF(Ge)

LM29TE(SP)

LM29W(SP)

,

\

0.8-1.3 0.8-1.3 22 25 0.7 0.6 0.8-1.3 0.2 0.1 0.1 0.2 Cr 0.6; Co 0.5, P§

G E G* GS

P F U G G G F

E

G G G F 550-6 15 680-740 2.68

3

I

0.20 0.20-0.60 6.5-7.0 0.5 0.3 0.1 0.1 0.1 0.95 0.2f

-

R

-

E P 520-770 At least 830 2.65

8 B

Heat tmarment Solution temperature, "C Solution time,h Quench Precipitation temperature, "C Precipitation time, h

-

Stabilization temperature, "C Stabilization time, h

--

-

-

155-175 8-12

I

Special properties

525-545 525-545 4-12 4-12 Water, 70-80 "C Water, 70-80 "C 155-175 8- 12

-

250 2-4 General purpose high-strength casting alloy

Readily welded

- SI units (Imperial units in brackets)

Mechanical properties - sand cast Tensile stress min., MPa (tonf in-') Elongation min. % Expected 0.2% proof stress, MPa (tonf in-2) Mechanical properties - chill cast Tensile stress min., MPa (tonf inp2) Elongation, min. % Expected 0.2% proof stress, MPa (tonf in-')

120(7.8) 3 55-60(3.6-3.9)

130(8.4) 2 80- lOO(5.2-6.5)

SI units (Imperial units in brackets) 140(9.1) 160(10.4) 4 3 60-70(3.9-4.5) 80-100(5.2-6.5)

-

495-505

4 Air blast 185

185 To uroduce HB 8 requirement

-

-

-

More suited to chill (grav. die) casting Piston alloy

15N9.7) 1 120-15q7.8-9.7)

160(10.4) 2.5 80-llO(5.2-6.5)

230(149) 0-2 200-250(12.9-16.2)

120(7.8) 0.3 120(7.8) HB 100-140

120(7.8) 0.3 120(7.8) HB 100-140

190(12.3) 2 130-2W8.4-12.9)

230114.9) 5

28q18.1) 2 220-26q14.2-16.8)

lgO(12.3) 0.3 170(11.0) HB 100-140

190(12.3) 0.3 170- 190(1 1.O- 12.3) HB 100-140

90-llO(5.8-7.1) ~~~~~

* Not normally used in ibis form. t If Ti alone is used for glain refinement then Ti # 0.05%.

* Fully

heat-treated.

8 Refine with phosphorus

- subject lo examination under microscope.

Note &Excellent, F-Fair,G-Good, P-Poor, U-Unsuitable. (GeGeneral purpose alloy; SP-Special purpose alloy as per BS: 1490: 1988.

** Or for such time to give required BHN.

s:

I w N

26-24

Carting alloys and foundry data

Table 26.23 ALUMINIUM-SILICON-COPPW ALLOYS Specification BS 14W1988 Related British Specifications

LM2M(Ge)

Composition % (Single indicate maximum) Copper 0.7-2.5 Magnesium 0.30 Silicon 9.0- 11.5 Iron 1.0 Manganeae 0.5 Nickel 0.5 Zinc 2.0 Lead 0.3 Tin 0.2 litanium 0.2 Properties of material Suitability for: Gt Sand casting Gt Chill casting (gravity die) Die casting (press die) E GS Strength at elevated temp. Corrosion resistance G Pressure tightness G Fluidity G Resistance to bot sholtness E Machinability F Melting mge, "C 525 570 Casting temperature range, 'C Specific gravity 2.74 Heat treatmnf Solution tempemture, "C Solution time, h Quench

-

-

-

-

Tensile stress min. MPa (tonf in+) Elongation min. % Expected 0.2%proof stress. m a (tonf in-2)

--

LM16W (SP) 3L78

1.0-1.5 0.4-0.6 4.5-5.5 0.6 0.5 0.25 0.1 0.1 0.05 0.2'

G G G G G G G G G 525-625 700-760 2.73

LM21M(SP)

-

3.0-5.0 0.1 -0.3 5.0-7.0 1.o 0.2-0.6 0.3 2.0 0.2 0.1 0.2

G G

Ft G G G G G G 550-620 690-760 270

-

505 520 6-16 water at 70-80 "C 150-170 6-18

Alloy for pressure die castings

Mechanical properties sand c a t

LM16TB (SP)

2.0-4.0 0.15 4.0-6.0 0.8 0.2-0.6 0.3 0.5 0.1 0.1 0.2

--

-

LM4MTF (Ge)

'

-

--

Precipitation temperature, "C Precipitation time, h Special properties

LM4M(Ge)

General engineering alloy Can tolerate relatively high static loading in W condition SI umts (Imperial units in brackets) 140(9.1) 2

230(14.9)

70-110 (4.5-7.1)

2M) 250

-

-

(12.9-16.2)

520-530 12 (min) Water at 70-80 "C

-

G G Gt G G G G G G 520-615 680-760 2.8 1

520-530 12 (min) Water at 70-80 'C 160-170 8-10

Pressure tight. High strength alloy in 'IF condition

170(11.0) 2

230(14.9)

-

1

120-140 (7.8-9.1)

220-280 (14.2-18.1)

80-140 (5.2-9.1)

150(9.7)

Mechanical properties -chill cost - SI units (Imperial units in bmkets)

Tensile strength min. MPa (tonf in+) Elongation min. %. Expected 0.2% proof stress, MPa (tonf in-2)

150(9.7) 1

160(10.4) 2

280(18.1) 1

230(14.9) 3

280(18.1)

-

170(11.0) 1

90-130 (5.8-8.4)

80-110 (5.2-7.1)

2G0-300 (129-19.4)

140-150 (9.1-9.7)

250-300 (16.2-19.4)

80-140 (5.2-9.1)

* 0.05% min. if li alone used for grain refinement. t Not normally used in this fonn.

Z Tne use of die castings is usually restricted to only moderately elevated temperatures

Aluminium casting alloys

26-25

-

Table 26-23 ALUMIN~-SLICON-COPPElZW O K S continued

Specijccation BS 114901988 Related British Specifications

LM22TB (SP)

LM24M (Gel

Composition 5% (Single figures indicate maximum) Copper 2.8-3.8 3.0-4.0 Magnesium 0.05 0.1 Silicon 4.0-6.0 7.5-9.5 Iron 0.6 1.3 Manganese 0.2-0.6 0.5 Nickel 0.15 0.5 zinc 0.15 3.0 Lead 0.1 0.3 Tin 0.05 0.2 Titanium 0.2 0.2 Properties of material Suitability for: Sand casting Gt Ft Chill casting (gravity die) G Ft Die casting (press die) Gt E Strength at elevated temp. G GS Corrosion resistance G G Pressure tightness G G Fluidity G G Resistance to hot shormess G G Machinability G F 525-625 520-580 Melting range, "C Casting temperature range, "C 700-740 Specific gravity 2.77 2.19 Heat treatment Solution temperature, "C 515-530 Solution time, h 6-9 Quench Water at 70-80 "C Precipitation temperame, "C Precipitation time, h Special Properties

LM26lT (SP)

LM27M (Ge)

2.0-4.0 0.5-1.5 8.5-10.5 1.2 0.5 1.0 1.o 0.2 0.1 0.2

1.5-2.5 0.3 6.0-8.0 0.8 0.2-0.6 0.3 1.0 0.2 0.1 0.2

G G

G

~

3

(SP)

4.0-5.0 0.4-0.1 16-18 1.; 0.3 0.1

0.2 0.1 0.1 0.2

Ft E

E Gt G

U F G G

G

G

G

F

G

F

G

G G G 525-605 680-740 2.75

G

F F 520-580 670-740 2.76

-

-

~0 ~ ~ 3 0 ~ s [SP)

F P 505-650 Well above 650°C 2.73

--

Stress relief I75-225 200-210 8(rninimum) 7-9 Chill casting Alloy for piston alloy, Excellent Alloy for pressure die castability casting autombile engine retains alloy (grav. pressure cylinder blocks die) die castings strength and hardness at elevated temps.

Mechanical pmpenies - sand cast - SI units (Imperial units in brackets) Tensile stress min., MPa (tonf in-2) Elongation min. 46 Expected 0.2% prcmf stress, MPa (tonf in-2) Mechanical pmperties - chill cast - SI units (Imperial units in brackets) HB = 90-120 Tensile strength min. MPa (tonf in-2) 245(15.9) 180(11.7) 210(13.6) Elongation min. % 8 1.5 1 Expected 0.2% proof smss, MPa (tonf in-*) 110-120 100-120 160-190 (7.1-7.8) (6.7-7.7) (10.4-12.3) Notes &Excellent, F-Fair, GGmd, P-Poor, U-Unsuitable. Numerical putpose alloy; SpSpecial purpose alloy as per BS 1490: 1970)

140(9.1) 1 80-90 (5.2-5.8)

160(10.4) 15W9.7) 2 0.5 90- 110 (5.8-7.1)

150-200 (9.7-12.9)

160(10.4) 0.5 160-200 (10.4-12.9)

KI OI h,

ka.

s

Table 26.24 ALUMINRIM-COPPER ALLOYS

Specification BS 14901988 Aemspace BSL series DTD series

LM12M(SP)

LM 12TF(SP)*

[LM14-WP]t

[LMll-W]

[LMll-WP]

-

-

4L35

2L9 1

2L92

-

.

-

Composition % (Single figures indicate maximum)

copper Magnesium Silicon Iron Manganese Nickel Zinc Lead Tin ntanium Other

Pmperties of material Suitability for: Sand casting Chill casting (gravity die) Die casting (press die) Strength at elevated temperature Corrosion resistance Pressure tightness Fluidity Resistance to hot shormess Machinability Melting range, "C Casting temperature range, OC Specific gravity

-

,

-

-

-

361B

741A

3.5-4.5 1.2-2.5 0.5 0.5 0.1 0.1 0.1 0.1 0.05

1

9.0-11.0 0.2-0.4 2.5 1.0 0.6 0.5 0.8 0.1 0.1 0.2

3.5-4.5 1.2-1.7 0.6$ 0.6$ 0.6 1.8-2.3 0.1 0.05 0.05 0.25

4.0-5.0 0.10 0.25 0.25 0.10 0.10 0.10 0.05 0.05 0.25

4.0-5.0 0.10 0.25 0.25 0.10 0.10 0.10 0.05 0.05

F

F G U

F P

F P

-

G U G

P

-

E F

G F

G E 525-625 700-760 2.94

G 530-640 700-750 2.82

-

U F F P F P G 545-640 680-700 2.80

'E

-

+ Nb 0.05-0.30

-

CO0.5 - 1.O Nb 0.05-0.3

F

-

G

F

F F G G G 530-640 710-725 2.80

P

F P G 540-640 675-750 2.80

-

&!

3

B

2

J

%.

Heat ireammt Solution temp., "C Solution time, h

-

515-520 6

500-520 6

525-545 12-16

525-545 12- 16

525-545 16 (minimum)

495-505 10

(minimum)tt Quench Precipitation temperature, "C Precipitation time, h Special properties

-

-

Water at 70-80 "C 175- 180 2 (minimum)

Piston alloy, now superseded by LM13 and LM26. Excellent machinability

Mechanical properties - sand cast - SI units (Imperial units in brackets) Tensile stress min., MPa (tonf in-2) Elongation % Expected 0.2% proof stress, min., MPa (tonf in-2) Mechanical properties - chill cast - SI units (Imperial units in brackets) Tensile stress min., MPa (tonf in-*) 170 278 (18.0) Elongation 5% Expected 0.2% proof stress, min., MPa 140- P O 139- 170 (tonf in-21 (9.0- 11.0) HB 100-150 I

* Not included i o BS 14901988. t[ ] signifies obsolete specification:

Water at 70-80 "C 120- 140 1-2 Good shock resistance

Water at 70-80 "C 120-170 12-14

Water or oil 160-70 8- 16 High strength alloy

Oil at 80-90 "C

220 (14.2)

220 (14.2) 7 165-200 (10.7- 12.9)

280 (18.1) 4 200-240 (12.9-15.5)

324 (21.0)

263 (17.0)

310 (20.1)

250 (16.2)

265 (17.1) 13 165-200 (10.7- 12.9)

310 (20.1) 9 200-240 (12.5-15.5)

402 (26.0) 4 360 (23.3)

340 (22.0)

-

210-240 (13.6-15.5) 280 (18.1)

-

230-260 (14.9-16.8) HB 100-130

Note: E-Excellent. F-Fair. G-Good. P-Poor. U-Unsuitable. (GeGeneml purpose alloy; SPSpecial p q s e alloy as per BS 1490:1988).

$ S i f Fe 1.0 max.

5 Or 5 days ageing at mom temp.

** Can substitute stabilizing treatment at 200-250 tt Allow to cool to 480 "C before quench.

Boiling water 95-1035 2** Excellent props. at elevated temperatures Grav. die alloy

"C if used for pslons.

-

195-205 4-2

-

-

260 (16.8)

26-28

Casting alloys and foundry data

Table 26.25 MISCELIA~OUSALUMMIUM ALLOYS

Specipatwn BS 1400:1988 Aerospace BSL series DTD series

LM5M(SP)

-

LMlOTB(SP)

-

-

-

4L53

-

L99

5018A 0.2 7.4-7.9 0.25 0.35 0.1-0.3 0.1 0.9-1.4 0.05 0.05 0.25

0.1 9.5- 11.0 0.25 0.35 0.10 0.10 0.10 0.05 0.05 0.21.

0.1 0.20-0.45 6.5 -7.5 0.20 0.10 0.10 0.10 0.05 0.05 0.20

F F -

F

G

Composition % (Single figures indicate maximum) copper 0.1 Magnesium 3.0-6.0 Silicon 0.3 Iron 0.6 Manganese 0.3-0.7 Nickel 0.1 Zinc 0.1 Lead 0.05 Tin 0.1 Titanium 0.2 Other Properties of material Suitability for: F Sand casting F Chill casting (gravity die) Die casting (press die) FS F Strength at elevated temp. E Corrosion resistance P Pressure tightness Fluidity F Resistance to hot shortness F Machinability G Melting range 'C 580-642 Casting temperature range, "C 680-740 Specific gravity 2.65 Heat treatment Solution temperature, "C Solution time, h Quench -

-

Precipitation temp., "C Precipitation time,h Special properties

Goodcorrosion resistance in marine atmospheres

-

-

-

F E P

-

F

E

F*

F*

-

680-720 2.64

F E P F G G 450-620 680-720 2.57

425 -4359

425 435

8

8

Oil at 160 Y!** or boiling water

Oil at no more??

F G G

-

E

G G G F 550-615 680-740 2.67

-

than 160 "C

-

-

-

150-160 4 Excellent castability with good mech. FOPS.

Good shock resistance and high corrosion resistance

***

Mechanical properties -sand cast - SI units (Imperial units in brackets) Tensile stress min, MPa (tonf in-') 140 (9.1) 278 280 (18.0) Elongation 7 '0 3 3 8 Expected 0.2% proof stress, min MPa (tonf in-2) 90-110 (5.8-7.1) 170 (11.0) 170-190 (11.0- 12.3) Mechanical properties - chill cast - SI units (Imperial units in brackets) Tensile stress min, ma (tonf in-2) 170 (11.0) 309 (20.0) 310 (20.1) 5 10 12 Elongation % Expected 0.2% proof stress, 90-120 (5.8-7.8) 170 (11.0) 170-200 min MPa (tonf in-2) (11.0- 12.9) ~

*

[

~~~~

535-545 12 Water at 65 "C min

~~~

I obsolete.

t 0.05%mi- if li alone used for e n refinement. $ Not normally ustd in th~sform. 0 Or 8h 435-445 ' C then raise lo 490-500 ' C for fuaber 8 h and quench a8 in table. ** Do 1l0t main castings in oil for more than Ih.

*** Not genedly recommended since occapional brittleness can develop over long periods.

230 (14.9) 2 185 (12.0)

280 (18.1) 5 200 (12.9) ~

Aluminium casting alloys Table 26.25 -

26-29

MISCELLANEOUS ALUMlNlIJM W O Y S - continued

Spec@cafionBS 140031988 Aerospace BSL series DTD sen'es

LMZ&TE(SP)

--

--

Composition 8 (Single figures indicate maximum) copper Magnesium silicon Imn Manganese Nickel zim: Lead liR litanium Other Propenies of materid Suitability for. Sand casting Chill casting (gravity die) Die casting (press die) Strength at elwated temp. Corrosion resistance Pnssure tightness

Fluidity Resistance to hot shomess Machinability Melting range "C Casting temperature range, "C Sp%ilic gravity Heal treatmenl SoMion temperature, 'C Solution time,h Quench

LM28TF(SP)

1.3-1 .E 0.8 1.5 17-20 0.7 0.6 0.8 1.5 0.2 0.1

-

-

0.1 0.2

Cr 0.6 Co 0.5

P F

-

F G F F G P 520-675 jt735 2.68

--

495-505 4 Air blast

Ptedpitation temp., "IC

185

185

Prcdpitation time, h

Toproduce

8

KMlnrp]*

3L51

-

3L52

0.8-2.0 0.05-0.2 1.5-28 0.8-1.4 0.1 0.8-1.7 0.1 0.05 0.05 0.25

1.3-3.0 0.5-1.7 0.6-2.0 0.8 - 1.4 0.1 0.5-2.0 0.1 0.05 0.05 0.25

0.1 0.5-0.75 0.25 0.5 0.1 0.1 4.8-5.7 0.1 0.05 0.15-0.25 Cr 0.4-0.6

G G G$ G

F

G U

F P

-

G

-

5008B

-

ut F E

E

F

G F F

G G 545-635 680-750 2.77

G G 600 645 685-755 2.75

G

--

150-175

F

-

520-540 4 Water at 80-100 "C Oil or air blast 150-180 (195-205)

8-24

8-24 (2-5)

Aimaft engine

High mechanical

castings

pmps. at elevated temps.

requited HB

Piston alloy

Special properrics

-

Mechanicd properties sand cast Tensile stress min, (uonf in-2) Elongation % Expected 0.2% p m f stress, min ma (tonfin-2)

-

KM23Pl*

- SI units (Imperial units in brackets) 120 (7.8) 160 (10.4) 2 125 (8.1)

F P

G 572-615 730-770 2.81

175-185tt (at least 24 h after cast) 10 (at least 24h atkr cast) Good strength wahout heat treatment See$*

280 (18.1)

-

216 (14.0) 4

245 (15.9)

150 (9.7)

325 (21.0)

-

232 (13.0) 5

295 (19.1)

180 (11.7)

HB 100-140

-

-

Mechanical properties chill casf SI units (Imperial units in brackets) Tensile stress min, Mpa (tonf in+) 170 (11.0) 190 (12.3) 200 (13.0) Elongation 8 3 Expected 0.2% p m f stress, min Mpa (tad in-*) 160-190 140 (19.1) HB 90-130 (10.4-12.3) HB 100-140

-

-

* Can be furnace mole4 to 385-395 ' C before quench. Do not retain in oil for more than 1h. Fuaher quench in water or air. Alternative mom temp. age-harden for 3 w&.

-

Note: E-Excellent, F-Fair. G c o o d . P-Poor. U-Unsuitable. &-General purpose alloy; SP-Special purpose alloy as per BS 14901988).

Table %.%a

KO1

European Designation A1 Assoc (USA) designation

cu

Mg Si Fe Mn Ni Zn Sn Ti Ag Others each Others total

3a

HIGH STRENGTH CAST AI ALLOYS BASED ON AI-4.5 Cu

4

E *$

A-U5GT

a

201.0 4.0-5.2 0.15-0.55 0.10 0.15 0.20-0.50

201.2 4.0-5.2 0.20-0.55 0.10 0.10 0.2M.50

A201.0 4.0-5.0 0.15-0.35 0.05 0.10 0.20-0.40

A201.2 4.0-5.0 0.20-0.35 0.05 0.07 0.20-0.40

-

-

-

-

0.15-0.35 0.40-1.0 0.05 0.10

0.154.35 0.40-1 .O 0.05 0.10

0.15-0.35 0.40-1.0 0.03 0.10

0.15-0.35 0.40-1 .O 0.03 0.10

A206.0 4.2-5.0 0.15-0.35 0.05 0.10 0.2M.50 0.05 0.10 0.05 0.15-0.30

-

-

A206.2 4.2-5.0 0.20-0.35 0.05 0.07 0.20-0.50 0.03 0.05 0.05 0.15-0.25

0.05 0.15

0.05 0.15

0.05 0.15

204.0 4.2-5.0 0.15-0.35 0.20 0.35 0.10 0.05 0.10 0.05 0.15-0.30

204.2 4.2-4.9 0.20-0.35 0.15 0.1w.20 0.05 0.03 0.05 0.05 0.15-0.25

0.15-0.3

206.2 4.2-5.0 0.20-0.35 0.10 0.10 0.20-0.50 0.03 0.05 0.05 0.15-0.25

0.05 0.15

0.05 0.15

0.05 0.15

-

-

206.0 4.2-5.0 0.15-0.35 0.10 0.15 0.20-0.50 0.05 0.10 0.05

-

-

E

Aluminium casting alloys Table 26.26b Alloy

201.0 204.0

26-31

MINIMUM REQUIREMENTS FOR SEPARATELY CAST TEST BARS

SandlDie

Sand Sand Sand Die

Treatment*

T6 T7 T4 T4

U TS MPa

0.2PS MPa

E1 % in 50mm or 4 x diarn

414 414 311 331

345 345 194 220

5.0 3.0 6.0 8.0

Typical

HB 500 kgf 10 mm 110-140 130 95

*For temper designations see Table 29.13

Table 26.26c TYPICAL PROPERTIES OF SEPARATELY CAST TEST BARS Alloy

SandlDie

Treatment*

U TS MPa

0.2PS MPa

E1 % in 50mm or 4 x diam

201.0

Sand

T4 T43 T6 T7 T7

Temp. 0.5-100 h lOOOh loo00 h 0.5 h 100 h lOOOh 10000 h 0.5 h 100 h 1OOOh 0.5 h 100 h lOOOh 1OOOO h

365 414 448485 46M69 380 360 315 325 285 250 185 195 150 125 140 85 70 60

215 255 380-435 415 360 345 275 310 270 230 150 185 140 110 130 75 60 55

20 17 7-8 4.5-5.5 6-8.5

2oc 12oC 175C

436 384 333

347 316 302

11.7 14.0 17.7

Sand Sand

Room 15oC* 205C

26oC 315C

A206.0

Sard

T4 T7

* Elevated temperature properties.

Typical HB 500 kgf 10 mm

95 135 130

8 7 9 10 9 14 14 17 18 39 43 118 HV 137 HV

26-32

26.4

Casting alloys and foundry data

Copper base casting alloys

Table 26.27

GUNMETALS

Alloy Specijkation BS 14001969 Alloy groupingt

Gunmetal 88/10/2

Nickel gunmetal (as cast)

Nickel gunmetal* (fully heat treated)

G1

G3

C

C

G3WP C

Composition % (Single figures indicate maximum) Tin 9.5-10.5 1.75-2.15 Zinc Lead 1.5 1.0 Nickel 0.02 Silicon Bismuth 0.03 Aluminium 0.01 0.20 iron +arsenic antimony Manganese Total impurities 0.50

+

Properties of material Suitability for: Sand casting Chill casting Die casting (gravity) Centrifugal Continuous Pressure tightness for sand castings: Thin sections Thick sections Machining Resistance to corrosion

Fluidity

Hot shortness Bearing properties Density (g Casting temperature range, "C Under 13mm section 13-39mm section Over 40mm section

6.5-7.5 1.5-3.0 0.104.50 5.25-5.15 0.01 0.02 0.01 0.20

0.20 0.50

2 3 3 2

1

1 2** 2 1 2% 2 All these alloys withstand atmospheric natural water and sea water corrosion to a degree depending largely upon the tin content (88jlOj2 best) Addition of phosphorus in amounts of order of 0.05% for deoxidation gives high fluidity in all cases All alloys are very hot short All alloys suitable for bearing applications-choice dependent on conditions 8.8 8.8 1080-1 200

Mechanical p r o p e r t i e s 4 1 units (Imperial units in brackets) in order sand cast,chill cast, continuously cast, centrifugally casttt (Bs 1400) Tensile stress min, MPa 270, 230, 300,250 280, -, 340, 430, -, 430,(tonf in-*) (17.5, 14.9, 19.4, 16.2) (18.1, -, 22.0, -) (27.8, -, 27.8, -) 0.2% proof stress min MPa 130, 130, 140, 130 140, -, 170, 280, -, 280, (tonf in-*) (8.4, 8.4, 9.1, 8.4) (9.1, -, 11.0, -) (18.1, -, 18.1, -) Elongation 5.65JSO9,, 13, 3.9, 5 16. -, 18. 3, 3, HB 160min 1

* Heat treatment 2 h

at 790

10 'C air cool plus 6 h at 320 2 IO "C air cool.

t Group A alloys in common use; group B special purpose alloys; group C alloys in limited production. iTin +$ Nickel cnnteut 7.O-S.Ox. 8 Grading 1=Excellent.

**

tt

2 =Satisiac%ory. 3=Possible with special techniques. 4=Unsuitabk. 5 =Not applicable. Grading l=Suitable 2= Less suitable. 3 =Unsuitable. Values apply to samples cut from centrifugal castings made in metallic moulds. Min.props. of centrifugal castings made in sand moulds same as for other sand castings.

Copper base casting alloys

26-33

Table 26.27 GUNMETALS-continued Alloy

Leaded gunmetal 83131915

Leaded gunmetal 85151515

Leaded gunmetal 87171313

LGl B

LG2 A

LG4 A

Leaded semi-red brass 76/3/6115

~~~~

Spec8cation BS 1400:1969 Alloy grouping+

Composirion %(Single figures indicate maximum) 4.0-6.0 Tin 2.0-3.5 4.04.0 7.0-9.5 Zinc 4.04.0 4.0-6.0 Lead 2.0 2.0 Nickel 0.02 0.02 Silicon 0.05 0.10 Bismuth 0.01 0.01 Aluminium Iron +arsenic+ 0.50 0.75 antimony Manganese 0.80 1.o Total impurities

Properties of material Suitability for: Sand casting Chill casting Die casting (gravity) Centrifugal Continuous Pressure tightness for sand castings: Thin sections Thick sections Machining Resistance to corrosion Fluidity Hot shortness Bearing properties Density (g ~ r n - ~ ) Casting temperature range "C Under 13mm section 13-39mm section Over 4Omm section Mechanical properties-SI cast77 (BS 1400) Tensile stress min MPa (tonf i n - 3 0.2% proof stress min, MPa

(tonf in-') Elongation 5.65JSJ;

6.0-8.0:

1.5-3.0 2.5-3.5 2.0f

0.01 0.05 0.01

~

A

2.5-3.5 13.0-17.0 5.25-6.75 1.0 0.01 -

0.40

0.55

-

-

0.70

I 1 2 2 2 2 1 2 1 1 1 2 All these alloys withstand atmospheric natural water and sea water corrosion to a degree depending largely upon the tin content (8S/l0/2 best) Addition of phosphorus in amounts of order of 0.057; for deoxidation gives high fluidity in all cases All alloys are very hot short All alloys suitable for bearing applications-choice dependent on conditions 8.77 8.8 8.8 8.8 1 200 1150 1120

1180 1140 1100

1 200 1160 1120

1 150-1 260 1110-1,220 1066-1 177

units (Imperial units in brackets) in order sand cast, chill cast, continuously cast, centrifugally 180, 180, -, (11.7, 11.7, -,

so, -,

-1

-, -

-.

(5.2, -, -) 11.2, -, -

ZOO, 200, 270,220 250,250, 300,250 (13.0, 13.0, 17.5, 13.0) (16.2, 16.2, 19.4, 16.2)

Sand cast 172 (Sandcast 11.6)

100, 110, 100, 110

130, 130, 130, 130

(6.5, 7.1, 6.5, 7.1) 13, 6, 13, 8

(8.4, 8.4, 8.4, 8.4) 16, 5, 13, 6

0.59; proof stress sand cast 83 (Sand cast 5.4) Sand cast 15 (50.8mm GL)

Grading 1 =Excellent 2=Good 3=Satisfactory with special techniques.

(Comparisonbetween copper alloys rather than with other metals)

Table 26.28 BEARING BRONZES

Allov

Phosphor bronze

Specification BS 1400: 1985 Allov arouvinat

PB1 B

Phosphor bronze for qear blanks

PB2

B

Composition % (Single figures indicate maximum unless otherwise stated) 10.0 min 11.0-13.0 Tin Phosphorus 0.50 rnin 0.15 min 0.25 0.50 Lead Zinc 0.05 0.30 Nickel 0.10 0.50 Iron 0.10 0.15 Silicon 0.02 0.02 Aluminium 0.01 0.01 Total impurities 0.60 0.20 Copper REM REM

Phosphor bronze

Phosphor bronze

Leaded vhosvhor bronze

CT1 B

PB4

A

LPBl A

9.0-1 1.0 0.15 max 0.25 0.05 0.25

9.5 min 0.40 min 0.75 0.50 0.50

6.5-8.5 0.30 rnin

2.0-5.0 2.0 1.0

a F

-5

-

-

-

0.80 REM

0.50 REM

0.50 REM

a Properties of'material Suitability for: Sand casting Chill casting Die casting (gravity) Centrifugal Continuous Pressure tight sand castings Thin sections Thick sections Machining Corrosion resistance Fluidity Hot shortness Density (g ~ m - ~ ) Casting temperature range, "C Under 13mm section 13-39 mm section Over 40 mm section Mechanical properties-SI Tensile stress (min) MPa (tonf in-') 0.2% proof stress (min) MPa (tonf in-') Elongation on 5.65&,%

n-

2$ 1 3 1

1

2 1

3 1 1

36 3 3 3 291: 2 All alloys are resistant to natural and sea water Good Good All alloys are very hot short 8.8 8.8 1120 1100 1 040

1170 1120 1070

2

1

2 1 3 1

1

1

1

2 3 2

3 3 2

2 2 1

Good

Good

Good

8.8

8.8

8.8

1100 1070 1040

1120 1100 1 060

1130 1050 1030

2 1 3

1

3 L

units (Imperial units in brackets) in order sand cast, chill Last, continuously cast, centrifugally cast** BS 1400

210, 310, 360, 320 (13.6, 20.1, 23.3, 21.4)

220, 270, 310, 280 (14.2, 17.5, 20.1, 18.1)

230, 270, 310, 280 (14.9, 17.5, 20.1, 18.1)

190, 270, 330, 280 (12.3, 17.5, 21.4, 18.1)

190, 220, 270, 230 (12.3, 14.2, 17.5, 14.9)

130, 170, 170, 170 (8.4, 11.0, 11.0, 11.0) 3, 2, 6, 4

130, 170, 170, 170 (8.4, 11.0, 11.0, 11.0) 5, 3, 5, 3

130, 140, 160, 140 (8.4, 9.1, 10.4, 9.1) 6, 5, 9, 6

100, 140, 160, 140 (6.5, 9.1, 10.4, 9.1) 3, 2, 7, 4

80, 130, 130, 130 (5.2, 8.4, 8.4, 8.4) 3, 2, 5, 4

Specijcation B.S. 1400: 1985 Alloy groupingt

LB1 C

LB2 A

LB4 A ~~

Composrtion ”/, (Single figures indicate maximum unless otherwise stated) Tin 8,O-10.0 9.0-11.0 0.10 0.10 Phosphorus 13.0-17.0 8.5-1 1.0 Lead 1.0 Zinc 1.o 2.0 Nickel 2.0 Iron Sb 0.50 Sb 0.50 Fe 0.15 Silicon 0.02 0.02 0.01 Aluminium Total impurities 0.30 0.50 Copper REM REM Properties of material Suitability for: Sand casting Chill casting Die casting (gravity) Centrifugal Continuous Pressure tight sand castings Thin sections Thick sections Machining Corrosion resistance Fluidity Hot shortness Density (g cm-’) Casting temperature range, “C Under 13 mm section 13-39 mm section Over 40 mm section Mechanical properties-SI Tensile stress (min) MPa (tonf in-*) 0.2% proof stress (min) MPa (tonf in-’) Elongation OR 5.65JS,%

* This

LB5 B ~

4.0-6.0 0.10 8.0-10.0 2.0 2.0 Sb 0.50 0.02

~~

4.0-6.0 0.10 18.0-23.0 1.0 2.0 Sb 0.50 0.01

-

-

0.50 REM

0.30 REM

2

3 2 4 3 3

1

4 2 1

2 3

1 1 All alloys are resistant to natural and sea water Good Good All alloys are very hot short 9.1 9.0

2 2 1

Good

Good

9.0

9.2

1110 1030 1010

1110 1070 1040

1 090 1030 1010

2 3

2 2

1130 1080 1030

1

units (Imperial units in brackets) in order sand cast, chill cast, continually cast, centrifugally cast** BS 1400

f2. =a

170, 200, 230, 220 (11.0, 13.0, 14.9, 14.2)

190, 220, 280, 230

(12.3, 14.2, 18.1, 14.9)

160, 200, 230, 220 (10.4, 13.0, 14.9, 14.2)

160, 170, 190, 190 (10.4, 11.1, 12.3, 12.3)

80, 130, 130, 130 (5.2, 8.4,8.4, 8.4) 4, 3, 9, 4

80, 140, 160, 140 (5.2, 9.1, 10.4, 9.1) 5, 3, 6, 5

60, 80, 130, 80 (3.9, 5.2, 8.4, 5.2) 7 , 5, 9, 6

60, 80, 100, 80 (3.9, 5.2, 6.5, 5.2) 5, 5, 8, 7

bronze is now primarily intcnded for shaped castings rather than

hearings. t See footnote t to Table 26.27. 1: See footnote 5 to Table 26.21. 5 See footnote** to Table 26.27.

0

** See

footnote tt to Table 26.21.

$1See footnote §$ to Table 26.21.

9 b

‘E

T W

v,

26-36

Casting alloys and foundry data

Table 26.29 BRASSES

Alloy

Brass sand cast

Brass sand cast

Naval brass sand cast

Specifration BS 1400: 1985 Alloy grouping

SCBl A

SCB3 A

SCB4 C

Composition % (Single figures indicate maximum unless otherwise stated) Copper 70.0-80.0 63.0-70.0 60.0-63.0 Lead 2.0-5.0 1.0-3.0 0.5 Tin 1.0-3.0 1.5 1.0-1.5 Iron 0.75 0.75 Nickel 1.o 1.0 Aluminium 0.01 0.1 0.01 Others Total impurities 1.0 1.0 0.75 Zinc REM REM REM Properties of material Suitability for: Sand casting 1% 1 1 Chill casting 5 5 5 Die casting (gravity) 5 5 5 Centrifugal 3 3 3 Continuous 5 2 2 Pressure tight castings (sand) Thin sections 15 Ill 1 Thick sections 1 17 1 Machining 1% 1 2 Corrosion resistance Generally excellent in natural waters, DCBI, DCB3, PCB1, SCB1, SCB3 undergo dezincification in sea water Hot shortness Alpha brasses tend to be hot short. Alphabeta brasses relatively good Density (g ~ m - ~ ) 8.5 8.4 8.3 Casting temperature range, “C Under 13 mm section 1150 1100 1100 13-39 mm section 1100 1050 1050 Over 40 mm section 1070 1020 1020 Mechanical properties-SI units (Imperial units in brackets)-sand cast props.** for alloys SCBl, 3, 4, 6chill cast$$ for DCBl and 3 and PCBl Tensile stress (typical) MPa 170-200 190-220 250-310 (tonf in- ’) (11.0-13.0) (12.3-14.2) (16.2-20.1) 0.2% proof stress (typical) 70-110 70-110 MPa 80-1 10 (tonf in-*) (5.2-7.1) (4.5-7.1) (4.5-7.1) 11-30 18-40 Elongation on 5.65JS,% (typical) 18-40

* 0.1% Pb if required.

** On separately cast

t Nickel to be counted as copper.

tt

’7

{ See footnotes 5 and ** to Table 26.27.

test bars. Values based on 15-40 mm thick sections from castings. Values based on 15-40 m m sections for DCB1, DCB3 and

PCBI.

For pressure tight castings AlsO.U2”,,.

I See footnote

to Table ?h.27. ~~~~~

Alloy

Brass hrarable castings

Specification BS 1400:1969 Alloy grouping

SCB6 A

lh then oil at room temperature,or air

-

-

Boiling water

-

-

Single figures am minimum tims at tempratwe for average castings and may have to be incnased for particular castings. Hot water means water at 70-8WC unless otherwise stated. The exact number of hours depends on the mechanical propetties required. The castings m a y be allowed to cool to 385495°C in the furnace before quenching. The castim shall be allowed to stay in the oil for not more than 1h and m a y then be quenched in water or oooled in air. ?The duration of the treatment shall he such as will produce the s@ed Brinell hardness io the castings. *For Iempr designation see Table 29.13.

Aluminium alloys

29-19

Table 29.12 TYPICAL HEAT TREATMENT DATA FOR WROUGHT ALUMINIUM ALLOYSo Times and tempemhues within the limits shown. Some specifications give tighter Limits Solution treatment Timeat temperature temperature "C h Ageing

Material Alloy a'e~gnation type

Temperature Quench "C mediumt

Ternpet$

2011

Al Cu5.5 Pb Bi

2014A

Al Cu4 Si Mg

2024

Al Cu4 Mgl

2031 2117 2618A 6061

Al Cu2 Nil Mg Fe Si Al Cu2 Mg Al Cu2 Mgl.5 Fel Nil Al Mgl Si Cu

6063

A1 Mg Si

Water Water Water Water Water Water Water Water Water Water or oil Water Water Water Water Water

525f 5 530 f 10 530 f 10 525f15 525 f 5 525 f 5 525 f 5 525f5 475 10 475 f 10

Water Water Water Water Water Water Water Water Water Water 172+3* or 120k3 followed hy 17253 Water 172f3* Water 85°Cor oil 135f5 Water or oil 135f 5 Water 135f 5 Water 135f5 Water (6040°C) 110k5 or 12055 followed by 177f5 Water 11055 177f 5 followed by Water 70°C 110f5 12055 OI 17755 followed by

-

6082

Al Si1 Mg Mn

6101A

A1 Mg Si

6463

AlMgsi

7010

Al Zn6 Mg2 Cu2

7014

A1 2115.5 Mg2 Cu Mn

7075

Al Zn6 Mg Cu

*

465+10 460k 10 46Of 10 46Of10 460f 10 465 5 465f5 465+5

-

Heatiog to temperature at not more than ZO"C/h. Water below 40°C unkss otherwise stated. $For temper designations see Table 29.13.

Table 29.13 ALUMINIUM ALLOY TEMPER DESIGNATIONS Symbol -~

Condition ~____

~~

~

~~

Cestiog rlloys Bs 1490

M

As Cast

TB m7 TE TF TF7

Solution treated and naturally aged Solution treated and stabilized Artificially aged Solution treated and artificially aged Solution treated, artificially aged and stabilized Thermally stress relieved

TS

Room 155-165 Room Room 155-190 155-190 Room Room Room 155-205 Room 160-200 Room 165- 195 Room 160-180 160-180 Room 175-185 165-195 Room 170f 10 Room 170f 10

510f5 510f5 50555 505 f 5 505 f 5 505f5 495 f 5 495 f 5 495 5 5 525 f 10 495 f 5 530 k5 525 f 15 525 f 15 5255 5

48 12 48 48 5-20 5-20 48

48 48 2-20 96 16-24

-

3-12

-

5-15 5-15 120 7-12 312 120 120 5-15

-

6-15 24 6-15 10-24 12 12 12 12 6-24 20-30 6-10

6-24 5-12 6-24 20-30 6-10

29-20

Heattreamtent

Table 29.l3

-

ALXMNWM ALLOY lEMpER DESIGNATIONS conaimwl

condition Cooled from elevated temperature shaping process and naturally aged to stable. condition As T 1 but cold worked after cooling from elevated temperature Solution treated, cold worked and naturally aged to stable condition Solution treated and naturally aged to stable condition Cooled from elevated temperatureshaping process and artilicially aged Solution treated and artificially aged Solution treated and stabilized (averaged) Solution treated, cold worked and then artificially aged Solution treated, artificially aged and then cold worked Cooled from elevated temperature shaping process, aaificiaUy aged and thm cold worked

29.6

Copper and copper base alloys

29.6.1

Environmentsfor copper base heat treatments

to copper and both are used on an industrial scale. The forma has the disadvantage of giving rise to water staining, while the latter is less economical. Burnt hydrocarbon gas is used extensively for bright annealing copper, but the metal is very susceptible to staining by hydrogen sulphide. Organic sulphur and sulphur dioxide do not attack copper but may be converted to hydrogen sulphide so that complete desulphurization of the controlled atmosphere is advisable. Sulphur compounds are much r e d u d if the gas is fully bumt rather than partially burnt Cracked and burnt ammonia are suitable for copper annealing and are sulphw free, but the former is little used for economic reasons. Tough pitch copper contains oxygen and hydrogen in the contmlled atmosphere must be less than 1%. Burnt ammonia or burnt hydrocarbon gas can be used, however, embrittlement can OCCUT due to reaction of steam with iron in the furnace producing hydrogen. An open flame furnace in which the preferably desulplnuized gas is fully burnt can be used in bright annealing. Copper-tin and copper-nickel alloys can be bright annealed as above but desulphurlzation must be absolutely complete. For alloys containing more readily oxidized elements, the range of suitable atmospheres is restricted to ammonia or dry burnt ammonia. Copper-zinc alloys. A successful industrial process11 has been developed for the full annealing of brass with zinc content up to at least 37%. CO, C02 and water vapour must be minimal and the atmosphere should contain some hydrogen. Qpical composition is 25% H/Nwith max 0 2 1 vpm, COz 20 vpm and de point -70°C. Zinc has a considerablevapour pressure at annealing temperatures and this may affect the colour and surface finish. Temperatures and soak times should be chosen with care. Where finish is less critical, 'flash' annealing may be applied to light gauge material with good results where rapid heating and cooling may be applied. Commercial annealing is often carried out in the cheaper types of controlled atmospheres which produce a light oxide film sufficient to restrict excessive zinc loss. Gilding metal contains low zinc concentration and can be bright annealed readily in atmospheres used for the annealing of copper, especially when in the form of coiled strip. Stream and carbon dioxide are virtually inactive

29.6.2

Temperatures for annealing and stress relief

'Ihese are are set out in 'pdble 29.14. For more details on copper base alloys reference should be made to Copper Development Association data sheets.

Magnesium alloys

2!4-21

Table 29.14 ANNEALING A N D STRESS RELIEVING OF COPPERS AND BRASSFST IS0 alloy designation

Annealing range ("C)

Stress reIhing range ("C)

Cu Cd3 and Cu Cd Sn Cu Si3 Mnl

200-650* 225-650* 200-650 225-600 250-650 375-650 350-650* 400-650 425-650* 500-700 475-700

150-200. 175-225* 170-200 175-225 200-250 225-275 225-275* 225-275 225-275* 250-350 250-380

Brasses c u zn5-20 Cu Zn28-30 Cu 21133-40 Cu Zn9 Pb2 Cu Zn34 Pb2 Cu Zn34-40 Pbl-3 Cu Zn43 Pb2 Cu Zn20 A12 Cu Zn28 Snl Cu Zn38 Snl Cu Ni10-12 Zn24-27 Cu Nils-18 Zn21-20 Cu Nil8 Zn27 Cu Nil0 Zn42 Pb2 Cu Nil8 Zn19 Pbl

425-600 450680 450-650 425-600 450-620 450-650 425-550 450-650 450-650 450-600 600-750 625-775 650-800 600-700 625-775

200-300 250-350 250-350 200-320 250-350 250-350 250-350 250-350 250-3.50 225-325 250-350 250-350 250-350 300-400 300-400

Coppers CU-ETPand Cu-FRH Cu-FRTP Cu-OF Cu-DEP Cu-DHI? CU-DPA Cu-LSTP a d Cu-OFS CuS

Cu Te

* Embrittlemeat will occur if heated in atmosphere containing ex-

of hydrogen.

For more details see Copper Development Association data TN 26 and 27.

29.7 Magnesium alloys B.7.1 Safety reqnirernentd2

A potential fire hazard exists in the heat treatment of magnesium alloys. Overheating and direct access to radiation from heating elements must be avoided and the furnace must be provided with a safety cutout which will turn off heating and blowers if the temperature goes more than 6°C above the maximum permitted. In a gastight furnace a magnesium fire can be extinguished by introducing boron trifluoride gas through a small opening in the closed furnace after the blowers have been shut down. 29.7.2

Environment

For temperatures over 4OO"C,surfaceoxidation takes place in air. This can be suppressedby addition of sufticient sulphur dioxide, carbon dioxide or other suitable oxidation inhibitor. In the case of castings to MEL ZE63A and related specifications,solution treatment should be carried out in an atmosphere of hydrogen and quenching of castings from solution treatment temperature of MEL QE22 is to be done in hot water. If microscopic examination reveals eutectic melting or high temperature oxidation, rectification cannot be achieved by reheat-treatment. Quench from solution treatment should be rapid, either forced air or water quench. From ageing treatment, air cool.

29-22

Heat treatment

29.73 Conditiom for heat treatment of magaesiUm d o y castiagS These are shown in Table 19.15 and for some wrought magnesium alloys in Table 19.16. Stress relief treatments are given in Table 19.17.

Table 29.15 HEAT TREATMENT OF MAGNESIUM C A m G ALLOYS Specifications

Composition

Temperature CC) MEL ZREl BS 2L126 BS 2970 MAG 6 ASTM EZ33A UNS M12330 MEL RZ5 BS 2L128 BS 2970 MAG 5 ASTM ZE41A UNS MI6410 MEL ZE63A DTD 5045 ASTM ZE63A

Aselrs

Solution treatment

Zn2.5 ZrO.6

Tim (h) quench

Temperature CC)

Time @) quench

-

250

16 AC

330 170-180

2 AC 10-16AC

RE3.5

Zn4.2 ZrO.7 RE1.3

-

-

Zn5.8 ZrO.7

480*

10-72WQ

140

48 AC

315

16 AC

330 170-180

2 AC 10-16AC

+

RE2.5

MELZTl DTD 5005A BS 2970 MAG 8 ASTM HZ32A

2112.2 ZrO.7 Th3.0

-

MEL TZ6 DTD 5015A BS 2970 MAG 9 ASTM ZH62A UNS M16620

Zn5.5 ZrO.7 Th1.8

-

MEL EQ21A

Ag1.5 ZrO.7 (30.07 Nd(RE)2.0

520

8WQ

200

12-16 AC

MEL MSR-B DTD 5035A

Ag2.5 ZrO.6 Nd(RE)2.5

520-530

4-8WQ

200

8-16 AC

MEL QE22 (MSR) DTD 5055 ASTM QE22A UNS M18220

Ag2.5 ZrO.6 Nd(RE)z.O

520-530

4-8WQ Hot WQ

200

8-16 AC

MEL .___ A8 .~ BS 3L122 BS 2970 MAGI ASTM AZ8lA UNS M11818

A18.0 ZnO.5 Mn0.3

380-390 410-420

8 AC 16 AC

MEL AZ91 (ST) BS 3L124 BS 2970 MAG 3

A19.0 ZnO.5 Mn0.3 BeQ.0015

380-390 410-420

8 AC 16 AC

ASTM AZ91C (STCPT) A19.0 ZnO.5 UNS M11914 Mn0.3 Be0.0015

380-390 410-420

MEL MAG 7 (ST) BS 2970 MAG 7

A17.519.5 Zn0.3/1.5 Mn0.15

MEL MAG 7 (ST&PT)

A17.5/9.5 Zn0.3/1.5 Mn0.15

*In hydrogen.Max 490°C.

+

-

-

8 AC 16 AC

200

10 AC

380-390 410-420

8 AC 16 AC

-

-

380-390 410-420

8 AC 16 AC

200

10 AC

Nickel and cobalt alloys

29-23

Table 29.16 HEAT TRF$ATMENTOF MAGNESIUM WROUGHT ALLOYS Specifications

Composition

Form

Solution treatment Temperature CC)

Time (h) FCh

Temperature CC)

Time@) quench

Ex

-

-

177

16 AC

F

400 -

2-4 WQ

177

16-24 AC

-

232

16 AC

500 500

2 WQ 2 WQ

-

-

150

24 AC

MEL AZ80 ASTM AZSOA UNS M11800

A18.5 Zn0.5

ASTM HM31A UNS 13310

Th2.5-4.0 Zn0.3 m.4-1.0

Ex

ASTM 60A WNS 16600

zn5.5

FT6 FT4 FT5

Mn0.12

-

24 AC

150

-

Nom: Ex-extrwions, F-fmgiags, T4-solution treated, T5--cooled and d i c i a l l y aged, T&SOlution treated and &Qdy aged, A G a i r cool, WQ-water quench. T.bk 29-97 STRESS RELIEF TREATMENTS FOR WROUGHT MAGNESIUM ALLOYS

Specifications

Composition

Form

Temperature CC)

MEL AZM ASTM AZ61A UNS 11610

A16.0 Znl.0 Mn0.3

Ex&F SH SA

260 204 343

MEL AZ84 ASTlM A280 UNS 11811

4 8 . 5 Zn0.5

260

MnO.12min

ExtF Ex&F*

MEL AZ31 ASTM AZ31B UNS 11311

A13.0 Znl.0 Mn0.3

Ex&F SH

260 149 343

Time (min) 15

60

im

15 60

204

SA

15 60

im

Notes: Ex-ext~sims, F-forgbw, S H 4 e e t hard rolled, SA-sheet annealed, *-cooled and a r t i l i i l y aged.

29.8

Nickel and cobalt alloys

For bright annealing of nickel alloys, ammonia, burnt ammonia or hydrogen atmospheres can be used but the dew point should be below -50°C. All traces of sulphur gases should be excluded from atmospheres in which nickel alloys are heat treated. The heat treatments of some nickel alloys are given in Table 29.18 and some cobalt alloys in Table 29.19. These alloys are normally used by name and therefore these tables do not give the alloy type. The UNS number (see Chapter 1)is given when available. Table 29.18 HEAT TREATMENT OF NICKEL ALLOYS Annealing

Alloy

UNS

Temp. CC)

(bs)

Time

Astroloy

-

1135

HasteUoy B HasteUoyB2 HastelloyC4 Hastelloy C276

NlOOOl N10665 NO6455 N10226

1175 1215

Stress relief Temp. W)

(hs)

Time

4

f

f

1

f

f

1

f

f

Sohttion treatment Temp. Cc)

1175 lo80 1175 1065 1065 1120

Time (h)

4AC 4AC 0.5 SQ 0.5 WQ 0.5 WQ 0.5 WQ

Ageins Temp. CC)

Time (h)

845 760

24AC 16AC

AS

-

-

Noles: FC=fumaa cool. AC=air cool, h=hours, hs=hou$iich ofsection, WQ=water quench, AS=ageing during acrviCe, k u s c full anneal, SQ=qmch M o w 540°C rapidly enough to prevent precipitation.

29-24

Heat treatment

Table 29.18 HEAT TREATMENT OF NICKEL AuOY%-continued Annealing

HastelloyN Hastelloy S Hastelloy C Hastelloy W HastelloyX Inconel 901 Inconel 600 Inconel 601 Inconel 625 Inconel 617 Inconel 706

Stress relief

N10003

-

NlMK)4 No6002

-

No6600 NO6601 NO6625

-

1175 1175 1095 1010 980 980

1 1 2 0.25

f f f 900

f f f 1

I

1

870

1

f

Inconel 718

NO7718

955

1

InconelX750 AMS 5667 AMS 5668 Nimonic8OA Nimonic 90 Rene 41 Unimet 500 Unimet 700

NO7750

1035

0.5

880

NO7080 No7090 NO7041 NO7500

-

1080 1080 1080 1080 1135

2 2 2 4 4

f f f f f

NO7001

1010

4

f

Waspalloy

f f

f f f f

Solution treatment

1175 lo65 1220 1175 1175 1095 1120 1150 1150 1175 925-1010

0.5 WQ 0.5 WQ 1SQ 1SQ 1SQ 2WQ 2AC 1AC ZSQ 2SQ

980

1AC

855 1150

24AC 2AC

1080 1080 1065 1080 1175 1080 1080

SAC 8AC 0.5AC 4AC 4AC 4AC 4AC

Ageing

AS AS

-

790

2AC

845 720 620 720 620 705 845

3AC 8FC SAC 8FC 8AC MAC 24AC

705 705 760 845 845 760 845 760

16AC 16AC 16AC 24AC 24AC 16AC 24AC 16AC

Nora: FC=fumacc cool, AC=& cool, h=hours, hs=hours/iach of section, WQ=water quench, &=ageing during service, few full &, SQ=quench Wow 540°C rapidly enough to prevent precipitation.

Table 29.19 HEAT TRWTMENT OF COBALT ALLOYS Annealing Time

Stress relkf

Solution treatment (h)

Temp. (“C)

1230

lRAC

AS

1175 1175 1175 1230

0.5RAC 0.5RAC 1SQ 1AC

-

Temp.

Alloy

UNS

Temp. CC)

(hs)

Temp.(T) Time&)

ec,

Hayes25 L-605 Hayes 188 Hayes566 S816 Stellite 6B

R30605

1230

1

f

R30188

-

R30816

-

1205

1

f

Time

Ageing

760

-

Time (h)

12 AC

Notes: RAC=rapid air cool, AC=& cool, h=hours, hs=hours/inch of d o n , AS=ageing during Service, f=wfull anneal, @=quench balm W C rapidly enough to prevent precipitation.

REFERENCES

1. I. Jenkins, ‘Controlled Atmospheres for the Heat Treatment of Metals’, London, 1946. 2. C. E. Peck, Metah and Alloys, 1944,19, 593; 1945,22,85.

3. B. Lustman, Mefal Progress, 1946,51, 850. 4. L. Fairbank and L. G.W. Palethorpe,‘Controlled Atmospheresfor the Heat Treatment ofMetals’, ISI, Special Report No. 95, 1966, p. 52. 5. 0.Kubaschewski and C. B. Alcock, ‘Metallurgical Thermochemistry’, 5th edn, F’ergamon, Oxford, 1979.

Refeences

29-25

6. ‘Cassel Manual of Heat Treatment and Case Hardening’, 7th edn, Sections 1.2.3 and 1.2.4, Cassel, London, 1966. 7. K. J. Irving, Low Alloy High Strength Steel Symposium,Nuremberg, 1970. 8. R. A. Harding, ‘FerrousMaterials for Geam-A Review’, BCIRA Report No.1578,1984. 9. P.A. Blackmore, ‘High Strength Nodular Irons’, BCIRA Report No. 1581,1984. 10. “The Properties of Aluminium and Its Alloys’, 8th edn, Aluminium Federation, Birmingham, 1983. 11. P.H. Elner and J. B. Carcol, Heat Treatment of Metals, 1978,4, 83. 12. ‘Standard Practice for Heat Treatment of Magnesium Alloys’, ASTM 661-87. 13. K.H. Habig, Materia& in Engineering, 1980,2,83. 14. ASTM B637, ‘Heat Resisting Alloys’.

30 Laser metalworking 30.1 Introduction Laser radiation, in contrast to that from black body sources, can offer a high degree of spatial coherence. This means that it can transmit as a well-directed, often near-parallel beam which may then be focused to spot diameters comparable with the wavelength of the radiation. Illustratively, beams of kilowatt power may be transmitted through air and then focused to intensities in excess of lo6W cm-2 which, when applied appropriately to a metal workpiece, permit the carrying out of processes such as drilling, cutting and welding. Importantly, because these processes are carried out at intensities much greater than those of conventional sources, heating is localized and there is usually a related reduction in phenomena such as distortion, shrinkageand heat-affected-zones. As a result the need for post-processmachining may be eliminated so that components go into use directly; this can, of course, be an important factor in the overall economics. Thus the unique combination of high focused power density, coupled with the facility for beam delivery and flexible use at ambient pressure, has resulted in a continuing growth in industrial applications in laser metal working.

30.2 Lasers 30.2.1

Basic principles

The three essential components of a laser are the laser medium, the excitation source and the optical resonator (Figure 30.1). The excitation source drives the atoms, ions or molecules of the laser medium to a situation where there is an excess of those at high energy level over those at a low level. This inversion of the normal thermodynamic population distribution leads to laser actioc:

Optical resonoto

t t t t t Excito tion source

Figgre 30.1 Essentiak of a laser

3&2

hers

an excited member of the medium undergoing a transition from high to low energy will emit a photon, which in turn stimulates further emission, perfectly in phase, and at the same wavelength, from the other excited members of the medium. The radiation is thus rapidly amplified; the role of the optical resonator is to direct and control the radiation by allowing an appropriate fraction to be bled off as a near-parallel beam while the remainder is circulated within the cavity to maintain laser action. The output is monochromatic, usually with high spatial and temporal coherence. At present, metal working applications involve use of predominantly two laser types, carbon dioxide (CO,) and neodymium YAG (Nd:YAG). The salient features of the two types are summarized in Table 30.1 and they are discussed in turn below. 30.2.2

C 0 2 lasers

In these lasers, the laser action results from electric discharge excitation of a low pressure gas mixture containing carbon dioxide. The beam is invisible, having a wavelength 1 lying in a far intrared at L=10.6pm. Industrial units are available with powers up to lOkW and above. Whilst early CO, lasers were almost exclusively of continuous wave (CW) operation, many low to medium power units now offer kilohertz pulsing capabilities. Since the pulse power may be ten times the average power, such operation can give better coupling of the beam into reflective metal surfaces. Additionally, pulsing may permit improved control of energy delivery to the work and this can be important, for example in the processing of thin sections. Current trends in laser development have resulted in the use of radio frequency (RF) excitation of the discharge in some designs. In general, research and development continues on the building of ever higher power CO, lasers. Motivated by the promise of increased single-pass weld penetration, work is underway on the design of improved 25 kW units.

30.2.3 Nd:YAG lasers Here the laser action results from the excitation of a solid rod of yttrium aluminium garnet, doped with neodymium, by intense white light from a lamp which may be pulsed or continuous. As in the CO, laser, the beam is invisible but here it is in the near infrared at 1=1.06pm. Currently, most metal-working Nd:YAG lasers have average powers in the region of several hundred watts, and have an output which is pulsed. A pulse may deliver tens of joules of optical energy in a millisecond, so that power at the workpiece may be tens of kilowatts. As a result, Nd:YAG lasers are well suited to drilling. They are also used very successfully for cutting and, with less intense pulses, for welding and surface treatment. Present trends in laser development have led to the availability of powers of 1 kW and above, and to the increasing appearance of cw units. Replacement of rod geometry by that of slabs is claimed to ease cooling problems, reduce distortion and improve beam quality. Because high beam power is more readily achievable, and available, in CO, lasers than in Nd:YAG lasers, the latter have been mainly associated with fine-scale applications whereas CO, lasers tend to be used for larger-scale application. However, with Nd:YAG units now offering beam powers of 1 kW and above, there is a greater overlap of capabilities in the cutting and welding of metal thicknesses which represent a significant part of engineering production. 30.2.4 Resonators The beam-metal interaction process is strongly affected by the intensity distribution of the beam, . which in turn is influenced by the design of the optical resonator (or cavity). These fall into two categories: stable and unstable. The terms refer to a mathematical description of the resonator which will not be attempted here. Figure 30.2 compares practical realizations of a stable and unstable cavity. The stable cavity is particularly suited to long lasers of low aperture, and in a well-designed system only the lowest-order mode (TEM,,) will be sustained, yielding an output beam which has a Gaussian radial intensity distribution [=l,e-'/" where I=intensity (as a function of radius), /,=on-axis intensity, r =radial position, w = 'spot radius' at which the intensity falls to l/e of axial value. This distribution has a strong central peak, steep sides and low wings; it is obtained also in the beam spot after focusing and it appears to correspond to excellent metal penetration capabilities.

Lasers

30-3

c+ Figure 30.2 (a) Stable and (b) unstable cavity resonators

On the other hand, a stable cavity can be arranged to sustain higher-order transverse modes so that instead of there being a lone spike of high intensity, additional rings appear around it (the TEM,,* mode gives the first ring alone). The redistribution of power results in a broader, flatter distribution in both the output beam and the focused spot. Although such multimode beams do not appear to be particularly well suited to creation of deep, narrow cuts and welds, they may be preferable for surface treatment processes requiring an extended uniform distribution. If the laser gain medium tends towards a geometry of short length and high aperture, an unstable resonator must normally be used to ensure good mode control and focusability. As seen in Figure 30.2(b), the output beam is annular. This distribution (which should not be confused with the much less focusable TEM,,*) yields, after focusing, an Airey pattern distribution which is strongly peaked on axis but with some power in concentric rings. For lasers with high gain where the central hoie in the annulus is small (high magnification cavity), the power after focusing is predominantly in the central spike, giving generally very acceptable cutting and welding performance. One special merit of the unstable resonator is that the out-of-focus annular distribution is well suited to metal surface treatment operations.

30.2.5 Beam delivery The beam emerging from the laser is only near-parallel; if it is transmitted a significant distance before use, the growth in diameter may need to be taken into account in choosing the diameter of beam lines and focus units. Consider the case of a laser having TEM,, mode: the beam envelope

Figure 30.3 Laser beam focusing typically consists of a waist region (diameter wl, left-hand side of Figure 30.3) and a region bounded by straight lines of divergence a. Then

4 1

G(,

=- 77 0 1

It is seen at once that for a given beam diameter, a short wavelength laser will have less divergence than one with long I; for a given wavelength, a large diameter beam will have less divergence than one with small diameter. If the beam is now focused on to the workpiece by a lens of focal length F (right-hand side of Figure 30.3),the near field distribution at waist w , is transformed to the far field distribution at waist 0 2 .Further lenses can effect further transformations, the product w l a l =w2Ct2=w,Ct,

being a constant. It can be shown that the diameter of the focused spot is

41 02%-

nu2

4°F %-A-

n d

4

4 -1. (flnumber)

n

where d is the diameter of the beam at the lens and the lens f/number=F/d. If depth of focus is

W

Processing considerations

defined by a distance z from focus at which the axial power density has fallen by 10% from that at focus, then

It is seen that short wavelength gives smaller spots and greater depth of focus than long, and that short focal length lenses will give smaller spots and more shallow depth of focus than long (provided that aberrations do not dominate). In practice, f/3 focusing might be chosen for high speed cutting of thin sheet where depth of focus is less important, whilstf/lO tof/l5 focusing might be chosen for high power welding of 15-nun thick steel where a broad depth offocus is desirable. As an alternative to beam transmission through air, optical fibres may be used for Nd:YAG lasers; quaxtz fibres offer good transmission at 1.06pm and are capable of operation with kilowatt power levels. On the other hand, suitable low-loss optical materials capable of transmitting high power 10.6pm radiation have not yet been developed. Nevertheless, flexible beam delivery systems for CO, lasers do exist based on line of sight transmission between suitably articulated mirrors.

TABLE 30.1

CHARACTERISTICS OF NdYAG AND CO, LASERS

Relevant energy levels Laser wavelength Laser medium

Nd:YAG

a

Electron orbits of neodymium ion in host lattice of yttrium aluminium garnet (Y,AI,O,,)

Stretching of CO, molecule

1.06W

1 0 . 6 ~

Solid rod of NdYAG

Gaseous CO, (usually with He and N,, total pressure 50 mbar) Collisional excitation by electrons of glow discharge operated in gas mixture. power supply may be D C or AC up to R F (i) Operate dischargein glass tubes and water cool tube walls (ii) Blow gas through discharge and then cool in heat exchanger $ 5 kW cw and RF, pulsable up to several kHz. 1&20 kW mainly cw

Excitation

White light excitation from flash tubes beside rod

Waste heat removal

Water cool rod

Typical operating conditions, including pulsing

cw pulse lamp Q switch

Overall efficiency Resonator Mirrors Lenses Part ofeye most at risk from accidental exposure

2

6IkW 20 Hz, 20j per pulse 20 kHz 150W mean

64% Stable or unstable Dielectric Glass, as for visible light Retina

-

6 10% Stable or unstable Metal e.g. ZnSe, KCI Cornea

30.3 Processing considerations 30.3.1 Role of intensity Each of the categories of laser metal-processing (drilling, welding, surface cladding, transformation hardening) can be characterized approximately by the beam intensity (beam power divided by beam spot-area) applied to the work, and by illustrative metal surface temperatures. In drilling steel for example it is desirable to use very high intensity ( 2lo7W/cm') so that super-heating occurs (temperatures > 3000"C),leading to explosive ejection of liquid and solid material, thereby yielding very efficient machining. In deep penetration welding, where the creation of the welding capillary involves melting and carefully controlled vaporization, intensities of lo6W/cmZ and a little above are normally employed. Surface cladding requires good melting with negligible vaporization, Le. t < 3000°C and intensities of 104-105W/cm2 are used. In transformation hardening, surface melting must not occur, Le. temperature must be held below 1500°C for steel, and typical intensities are > lo3w/cm2.

Processing considerations

30-5

30.3.2 Beam coupling Clean, smooth metal surfaces are good reflectors of infrared radiation although they are more absorbing at the Nd:YAG wavelength than that of the CO, laser. Indeed, ‘perfect’ metal surfaces may have reflectances in the range 60-90%. However, reflectivity decreases with increasing temperature, presence of oxides, onset of surface melting, and capillary formation. The result is that in most practical applications even the CO, laser beam is efficiently coupled to the metal. In drilling, cutting and welding, the focus intensity is sufficiently high (particularly in the case of pulsed beams) to initiate melting, surface disruption and capillary formation which yields efficient beam trapping. In CO, laser welding, plasma formation associatedwith the capillary also contributes by absorbing beam energy and redistributing it to the metal by conduction. In cutting, the assist gas jet keeps the cut slot (kerf) relatively clear so that the beam couples directly to the kerf leading edge and sides. It is found that better coupling occurs in CO, laser cutting for a plane polarized beam having the electric vector lying along the cut (Brewster effect). The overall result is that the machining processes exhibit a very highly efficient utilization of the beam. However, CO, lasers are not suited to the processing of gold, and they require good beam quality for processing of copper and aluminium. Surface melting, cladding and alloying can be carried out with high efficiency using Nd:YAG lasers, and with acceptable efficiency using C 0 2 . Because there is no strong capillary feature in these processes, some CO, beam reflection does occur. However, when powders are being fused into metal surfaces, their delivery into the interaction region can provide a surface with good absorptivity, and typical overall beam utilization efficiencies may be better than 30%. The implementation of efficient transformation hardening by CO, laser relies on the presence of an absorbing coating. This may be an oxide layer grown during processing,but it is more normal to employ a pre-applied thin layer of colloidal graphite. Such coatings can present greater than 80% absorptivity. As in the case of cutting, the Brewster effect may be used to give better coupling when the beam has to be inclined to the surface: the beam should be plane polarized with the electric vector lying in the plane of incidence-reflection.

3033 Processing depths and rates Cutting and welding

In these processes, prediction from first principles of the depth of penetration achievable with a given laser beam is at present not a practical proposition. This is a consequence of the complexity of the beam interaction processes occurring in the kerf and keyhole. Nevertheless,a simple energy balance may give a qualitative guide to the scaling of penetration with process speed. Consider full penetration taking place using beam power p in a plate of thickness d at speed u. A parallel sided kerf and melt region occur in the case of cutting and welding respectively. Let these have widths w, and respectively. A significant fraction of the applied power p is deposited in the metal, the remainder being lost by reflection and through transmission. Of the power deposited, a fraction (perhaps of order corresponds to that required to heat and melt the volume of metal of interest, whilst the remainder is conducted into the work. It should be noted that the weld region can become a cut kerf with the application of an assist gas jet; use of a reactive gas has the effect of increasing the power deposited in the kerf. Therefore the approximation can be made that the volume of melt produced per unit time is proportional to the beam power applied. That is

a)

P =k,vdw, p = k,vdw, whiere k,, k , are the constants of proportionality which contain contributions from reflectivity. specific enthalpy for melting, etc. Consider now two special cases: In cutting, the width of the kerf may be comparable with the beam spot diameter and furthermore may remain substantially constant over a (limited) speed range. Thus from the above equation at constant powe: vd=constant, i.e. vcclfd

A ?lot of speed against thickness at threshold of cutting penetration will therefore have the form shown in Figure 30.4(a). In welding, over part of the speed range, the aspect ratio of the melt, d / o , may tend to be maintained, i.e. w,Kd and from the above equation, at constant power ud2=constant, Le. uccl/d2

30-6

Processing considerations

r

1I Thickness d (/inearscule, orb.uniW

Figme 30.4 Characteristic relationships between process speed and workpiece thickness based on simple energy balance and ( a ) kerfwidth independent of speed, (b) kerf aspect ratio (thicknesslwidth) independent of speed

A plot of speed against thickness at threshold of weld penetration may have the form also shown in Figure 30.4(b). In practical application, processing may fall between these two special cases. Nevertheless, the energy balance approach permits some understanding of the characteristicshapes of plots of speed and thickness which are observed, and it provides a guide to extrapolating performance.

Su$ace transformation hardening Here, a defocused beam is scanned over steel or cast iron, austenitizing a surface layer which then quenches by conduction into the bulk to give a martensitic layer. It is possible to make relatively simple and accurate predictions regarding process depths and speeds because the laser energy is deposited on the metal surface and is conducted, according to classical heat flow, into the meal. Because the depth heated is small compared with the extent of the heating spot, it is quite appropriate to use a one-dimensional heat flow model which considers a heating flux P deposited for a time z in the surface of a semi-infinite body. The dwell time z corresponds to a beam spot, moving over a workpiece at speed u, and having length 1 in the travel direction where ~ = l / u .At the end of the heating pulse, the surface temperature T as a function of depth z is given by (Carslaw H.S. and Jaeger J.C., 'Conduction of Heat in Solids', 2nd edn, Clarendon Press, Oxford, 1959,p75). 2F K

erfc x=l-erfx

1 and ierfc x=-e-x2-xerfc

fi

x

and the surface temperature T, by

where K =thermal conductivity, k =thermal diffusivity =K/pc, p =workpiece density, c =workpiece specific heat. In laser transformation hardening, it is usual to take the surface close to (but not above) the , melting point. Thus in hardening steel, where T,= 1500"C, K = 0 . 3 5 W ~ m - ~ ~ " C - 'and k = 7 . 3 x 10-2cm2s-1,the last equation gives F A < 1722w crn-2s1/*

Cutting

3&7

if surface melting is to be avoided. Typically absorbed intensities of 3 kW/cmz and 6 kW/cmz might be used so that interaction times of g0.33 s and G0.083 s should be chosen respectively. The resulting case depth can be estimated from the model by assuming that this is the same as the depth raised above austenitizing temperature. The temperature as a function of depth can be rewritten in terms of a surface temperature T,

If hardening takes place down to a depth z' where T =850"C, then since T,= 1500°C z'

ierfc -w0.3

2Jj;; i.e.

z'x0.164

For the two casesconsideredabove where T =0.33 s and0.083 s, z' x 1mm and 0.5 mm respectively. I[t is important to note from the foregoing that the process operates by the surface being heated very close to melting point. Thus a high degree of uniformity is required in the beam spot, otherwise melt strips may occur. Furthermore, a move towards greater case depth implies use of lower intensities in order to provide sufficient heat diffusion time. In practice, laser hardening is best suited to depths < 1mm; beyond that self-quenching may become problematic and distortion may become noticeable. Also, in practice depth can be reduced by increasing processingspeed-however there is a strong sensitivity in the interrelationship, and care is required.

30.4

Catting

The cutting process is based on location of beam focus at the surface of the (moving) workpiece, so that it melts the metal, and on provision of a jet of gas, usually coaxial with the laser beam,

which displacesthe molten material. This gas jet, if containing oxygen, may promote an exothermic reaction with the workpiece which enhances speed or penetration. For a well-optimized process, the resulting kerf can be narrow and parallel sided, the cut faces smooth (exhibiting striations of limited amplitude), the rear edges of the cut substantially free of adherent dross, and the heat affected zone (HAZ) narrow. Laser cutting currently occupies a niche which overlaps to some extent (depending on laser and workpiece) with electro-discharge machining, plasma cutting and abrasive water jet cutting. It is now believed that the following factors contribute crucially to the achievement of good cut quality. The radial intensity distribution of the beam should be narrow, steep sided and with little power in the wings; a Gaussian distribution appears suitable. The gas jet must be accurately centred on the beam interaction point and it should deliver high pressure into the kerf to promote efficient removal of material; however, care is required in the use of very high pressures since adverse supersonic shock structures may be present (and, particularly for lower laser powder, high gas flows may cause a deleterious chilling). Furthermore, an excess of oxygen can lead to too much burning of the material with a concomitant decrease in edge quality. For preference, the beam should be circularly polarized so that cutting performance is the same in all directions. The overall system (beam, jet, workpiece traverse) should be stable, smooth and free of jitter. However, the use of a pulsed laser beam may have advantages; it enables better control of energy input for the cutting of thin sections and fine details, and indeed it is claimed that careful matching of pulse frequency to cutting speed permits achievement of very smooth cut edges. There is a growing body of data on cutting performancefrom laser manufacturers and researchers using a range of lasers and a wide variety of materials. Some care should be exercised in the use of such data because of the process dependencesjust described. For present purposes it is convenient to discuss performance by material type. Steels

The vast majority of laser metal cutting is applied to steel, much of which is mild steel. Figure 30.5 provides a guide to cutting performance trends with oxygen assist; it shows illustrative data for both 1Vd:YAG and CO, lasers, bearing in mind that at present the former cover the range up to 1kW and the latter up to 5 kW and above. Generally speaking, edge quality improves for the cleaner, more highly alloyed compositions; thus tool steel gives a better edge finish than mild steel.

30-8

Cutting

m

-

h

100

80 60

h: 40

20

in

0.6 0.8

7

2 Thickness mm

4

6

8 1 0

Fiure 30.5 Illustrative performance in oxygen-assisted laser cutting of mild steel; note that edge quality depends sensitively on processing conditions

The cutting of stainless steel is more difficult because it resists formation of slag so that the dross is metallic rather than a friable oxide and it tends to adhere strongly to the rear edges. Indeed it is currently claimed that best edge quality on stainless steel is obtained with the use of N, assist gas at pressures up to 15 bar. In broad terms, the speeds of Figure 30.5 should be reduced by approximately 50% for stainless steel cutting. Nickel alloys

Nickel alloys also exhibit a tendency to form a tenacious dross when laser cut. Again the cutting speeds of Figure 30.5 should be reduced by approximately 50%. Titanium

Titanium is highly reactive, and therefore can be cut with considerable exothermic enhancement if oxygen is used. However, care is required. Not surprisingly, the cut edges are then highly oxidized. It is probably more relevant to utilize inert gas assist, e.g. argon, in which case oxide-free edges can result although the speeds of Figure 30.5 are again reduced by approximately 50%. Aluminium

Aluminium is a good reflector, particularly at the CO, wavelength. For low average power CO, lasers, good focus spot quality is required, and pulsed operation is preferred. Speed is enhanced by use of oxygen. In all but the thinnest sections,the formation of a tenaciousrearsidedross occurs. Laser metal cutting is well established industrially for a wide variety of applications. These range from two-limensional profile cutting of sheet components to the three-dimensional trimming of pressings for the automobile industry. The process economics are best suited to prototype and medium batch production where the alternativeof manufacturing blanking dies would be expensive. A wide range of proprietary cutting equipment is now available. For very high precision, thin-section work this may consist of a Nd:YAG laser with le& focusing and a CNC X-Y table

Dri&q and engrauing

30-9

to move the work. For thicker sections,where a COzlaser is more appropriate, a similar arrangement may be used or alternatively moving optics may be employed so that the focus head moves in X-Y over the fixed workpiece. Movements over several metres are now commonplace. For three dimensional cutting, the moving optics concept may be extended by the addition of a z axis together with one or two axes of rotation at the focus head. Five, or even six, axes are employed because it is desirable to cut with the beam normal to the workpiece surface. As an alternative to moving optics based on the foregoing Cartesian system, robot arm systems are also available where the beam is conducted along the side of the arm, or even inside it. One of the claimed advantages of Nd:YAG lasers is that their use with fibre optics considerably simplifies beam delivery.

30.5

Drilling and engraving

The majority of drilling and engraving operations on metals are at present performed by pulsed Nd:YAG laser (although Nd:glass units may be used for drilling if lower repetition rates are acceptable). This is because the solid state lasers offer good coupling into metal surfaces, as well as pulse power densities which are higher than those obtainable from most industrial COz units. The high focal intensities lead to vigorous material expulsion in drilling and, in engraving, legible symbols may be generated by surface evaporation and the creation of a very thin, slightly disrupted melt layer. 30.5.1 Drilling

The process arrangements for metal drilling are somewhat similar to those for cutting, i.e. the beam is focused on or close to the workpiece surface and a jet of assist gas is provided to aid expulsion of material. The laser is normally operated in free-running, pulsed-lamp mode (typical beam pulse length approximately 1ms) and pulse energies up to 50 J may be employed. Empirical process optimization can be used to choose between the regimes of high repetition rate/low pulse energy and the converse. Two drilling techniques may be distinguished: percussion and trepanning. In the former the beam is kept fixed with respect to the workpiece, and the hole diameter is determined largely by spot diameter, values ranging from approximately 0.1 mm to 1.5 mm. Use of larger spots leads to an unacceptable reduction of focal intensity and larger holes are therefore. drilled by the trepanning technique. The repetitively pulsing beam is then caused to describe on the work a circular trajectory, the diameter of which determines the diameter of the resultant hole. In principle, trepanned holes of arbitrarily large size can be drilled but in practice the method is best suited to diameters up to approximately 3mm since thereafter mechanical drilling may offer a more cost-effective alternative. Currently, laser drilling in metal can give hole depths in excess of 20mm. Under particular circumstances, depth to diameter aspect ratios may approach 509. The trepanning technique results in excellent axial symmetry. Holes are substantially parallel sided, although some degree of taper may be present, particularly in thicker workpieces. However, holes can be drilled having minimal heat-affected zones and recast layers as well as absence of microcracking. Furthermore, it is possible to drill holes which are inclined far off-normal to the workpiece surface. Typical production applications include the drilling of metering and lubrication holes for the automotive industry and, most importantly, the large-scale drilling of cooling holes in nickel-alloy gas-turbine components for the aerospace industry.

30.53 Engraving The engraving of uncoated metal requires localized application of the focused laser beam to the workpiece surface. A typical beam delivery system therefore incorporates a pair of galvanometer-type mirror units which permit steering of the beam over the work. Alphanumeric characters can then be created either via a dot-matrix array, or by tracing out the characters with a quasi-continuous beam. In the former, the laser is normally operated in free-running pulsed mode, synchronized with the line scanning system so that a dot may be produced at each co-ordinate oi the array; the beam may then be switched on or off to write the required characters. In the latter, the laser is operated in Q-switched mode (tens of kilohertz) so that for typical mirror deflection speeds the written character is effectively continuous. The advantages of laser engraving of metals include the contactless nature of the marking, the minimized metallurgical and mechanical damage and the ability to engrave through glass. A range of commercially-available equipment is available. Production applications include engraving of stock metal, engineering components and medical implants.

30-10

Welding

30.6

Welding

Laser welding now spans a significant thickness range, from submillimetre to greater than 10mm. For thin section work, Nd:YAG lasers are generally preferred because of better beam coupling and the good control associated with pulsed operation (although rapid quenching between pulses may induce cracking in sensitive materials). For sections of one or two millimetres and upwards, CO, lasers are normally used but this range is becoming accessible to Nd:YAG with the advent of kilowatt power levels. Although conduction-limited laser welding (carried out using beam intensities of around 5 x lo5W/cm2) may be of interest in some applications, it is more usual to exploit the deep penetration capability of the beam by employing focused power densities of lo6W/cmZ or greater. The workpiece surface then undergoes melting and vaporization which is sufficiently intense to disrupt the melt to form a capillary or keyhole, thereby enabling the beam to penetrate relatively deeply into the material. Using a pulsed or CW laser, and by suitably moving the work or beam, the keyhole translates along the join line, metal melting ahead and flowing round to solidify behind. The process, like that of electron beam welding but without the vacuum requirement, thus produces welds which are energy efficient, of low shrinkage (because they are narrow) and of low distortion (because they are parallel-sided). Laser welding is particularly suited to autogenous welding, close fit-up of the parts being normally required, although filler material can be added if a gap exists; filler may be used to improve weld properties. At higher CO, laser beam powers, plasma formation at the workpiece becomes important since it can be responsible for the broadening of the weld beads, a reduction in workpiece penetration and (more desirably)a smoothing of both weld surfaces. The plasma is frequently controlled by directing at it a jet of helium (which serves also to prevent oxidation). As in the case of cutting, the best penetration is obtained with good-quality, tightly focused beam spots. However, it should be noted that, particularly with pulsed lasers, it is possible to apply to the work power densities which are too high so that excessive evaporation and weld disruption occur. Figure 30.6 provides a guide to weld penetration trends in the welding of alloys of iron, nickel and titanium. Care should be exercised in the use of the figure because of the sensitivity of values to conditions such as spot quality, plasma control, etc; in any case, it is often

0.6 0.8 1

2

4

6

8

10

20

Thicknessmm Figure 30.6 Illustrative performance in laser welding of steel. Note: welding speeds slower than penetration-threshold values are required in order to create acceptable weld profiles; penetration at very slow welding speeds depends sensitively on pulsing and plasma effects

Welding

I

30-11

+ Lap

Buff

I Tee

Corner

1 Sake

Sandwich

I

7

Figure 30.7 Laser weld configurations necessary to reduce speed significantly below that at threshold of penetration, in order to achieve desirable weld geometry. However, the capability of the laser to carry out keyhole welding at ambient pressure can permit a novel approach to component fabrication. Indeed it is likely that the best exploitation of laser welding follows from a rethink of component design to match the process. Figure 30.7 shows a selection of possible joint configurations. Laser welding is being applied to a wide range of materials. This has involved exploration of a new regime of welding, for although it may be argued that the process is similar to that of the electron beam, laser welding speeds are normally higher and cooling rates are faster so that different weld properties may result. Indeed there is no doubt much to be learned yet about process techniques such as the use of beam pulsing and spinning. Similarly, there is scope for more work to better understand the fine-scale scattered microporosity often seen in laser welding. At higher power levels more attention is required to the overlapping and ramping out of circumferential welds. Nevertheless, laser welding is now exploited in production to achieve high-integrity joints in a wide range of products. There follow comments on the weldability of a number of materials types. Steels Successful laser welding of mild steels requires choice of cleaner, low-carbon compositions which are not too rich in oxygen, sulphur or phosphorus otherwise weld disruption, porosity and solidification cracking may occur. If such effects are problematic, reduced welding speeds or use of appropriate fillers may help. Steels which have carbon equivalent greater than approximately 0.3% are difficult to weld without cracking because they have high hardenability and insufficient ductility to resist the shrinkage stresses encountered in many joint geometries. Thus the welding of planetary joints in gear assemblies may require shrink-fit assembly. Interest in the use of

30-12

Transformation hardening

multikilowatt power levels for deep penetration welding has led to studies in the joining of high-strength low alloy steels such as those used in pipelines and marine applications. The indications here are that low-carbon casts are greatly to be preferred for the achievement of restricted hardness and acceptable impact properties, although the use of appropriate filler may help. There is some evidence that flux-cored filler promotes in the weld an acicular ferrite microstructure have excellent impact properties. Most austenitic stainless steels weld extremely well by laser. The welding of ferritic stainless, which is difficult by most processes because of grain growth and embrittlement, may benefit from the use of lasers because of reduced energy input. Non-ferrous alloys Titanium and nickel, and many of their alloys, exhibit good weldability by laser. On the other hand, the laser welding of aluminium and its alloys can require considerable care. This is partly because of high reflectivity (in the case of the CO, laser) but more importantly because in those alloys containing Mg and Zn selective evaporation of these elements can lead to porosity and weld disruption. The problem is greatly reduced when the alloying element is mainly copper.

30.7 Transformation hardening By use of a diffuse beam, the surface hardening of carbon steels and irons can be achieved by martensitic transformation. The laser can be distinguished from alternative surface hardening techniques by one or more of the following attributes: 1 . It characteristically operates as a rapidly moving source so that overall heat input (and therefore distortion) is minimized, and adequate quenching rates are obtained solely by conduction into the substrate. 2. The beam can be manipulated and directed into bores and conventionally inaccessible regions without the hindrance of supply cables and pipes. 3. Its heating patterns may be altered to suit the application.

The power densities (usually 103-104W/cmz) and speeds (or beam dwell times) are chosen to austenitize a relatively shallow case depth (usually < 1 mm) while avoiding surface melting. The workpiece surface may be given a prior coating of colloidal graphite to ensure efficient COz laser energy absorption at the surface. As noted in Section 30.3.2., if access demands the use of an inclined CO, beam, it should be plane polarized to enable exploitation of the Brewster effect. Illustratively, for a 0.5 mm case depth, coverage per kilowatt is approximately 65 mmz/s for cast iron and 135 mm2/s for steel. Preferred materials for laser hardening are those in which the carbon is wiformly distributed, i.e. steels in quenched and tempered conditions, and cast irons having pearlitic matrices. In such materials, despite the brief thermal cycle, austenitization occurs quite quite uniformly with depth and a relatively flat hardness profile results. Nevertheless, adequate hardness may be obtained in steels having a coarse normalized structure, or in ferritic irons. This is because the near-surface layer experiences temperatures close to melting and sufficient carbon diffusion may occur to yield a useful martensite. Process conditions should be biased towards low intensities and long interaction times to aid diffusion. However, such cases generally exhibit a strong decrease of hardness with distance from the surface. One of the key elements in laser hardening equipment is the means for achieving an extended, uniform heating pattern. A number of possible CO, laser beam techniques have been developed to varying degrees. These include: high-speed spot-rastering systems, beam scrambling based on faceted mirrors; and light pipes featuring multiple internal reflections. In some applications multi-mode operation of the laser resonator may yield a beam distribution which is adequately flat-topped to avoid causing melt strips. For treatment of components with special profiles, the use of tailored beam distributions may be required: for example the treatment of internal corners requires enhanced intensity there because of the increased heat-sinking; the converse is true of external corners and knife edges. The use of on-line surface temperature monitoring by optical pyrometry and with associated feedback control of the process parameters has been demonstrated as a useful adjunct to hardening equipment. The production implementation of laser hardening is at present much less established than say laser cutting. Many of the reported applications relate to the automotive field and these include hardening of piston ring grooves and cylinder bores. In the latter application, the use of discrete spiral tracks seems preferred to overall hardening.

Surface cladding and alloying

30-13

30.8 Surface cladding and alloying These are surface treatment processes which involve substrate melting in conjunction with the addition of material to improve wear or corrosion resistance. In cladding, the additive is fused and then solidifies as a coating which is metallurgically bonded via the melting of only a very thin layer of the substrate; the composition of the final surface is close to that of the additive since it experiences little dilution by the substrate. On the other hand, in alloying there is significant mixing of molten substrate and additive and the resulting surface has composition and properties determined by contributions from the two. The attractions of using a laser for these processes concern localization of treatment, low cladding dilution, good geometrical control, efficient additive utilization and useful microstructures resulting from rapid cooling rates. Although there is research and development activity on fine-scale treatments relevant to the electronics sector (including use of Nd:YAG lasers) the current major effort is concerned with treatments for the automotive and power sectors performed mainly, but not exclusively, with CO, lasers. The additive may be in two forms: solid or gas. In the former it is preferable to use fhe material in powder form (cf. rod or wire for example) because not only are the deposit width and thickness more readily varied, but the powder promotes better coupling of the beam for CO, lasers. Normally the powder is supplied from a hopper via a delivery tube to the interaction point. Transport through the tube may be under gravity or via an inert gas stream. Alloying may also be carried out by arranging an appropriate gas atmosphere above the irradiated, molten surface; in this case it is usually adequate to direct at the interaction point a laminar flow of the gas and to avoid entrainment of air. The beam intensities used for cladding and alloying lie in the range 104-105 W/cm2. There is a natural tendency for cladding, rather than alloying, to occur when the additive has a lower melting point than the substrate. For example, a typically cobalt-based alloy (melting point 1340°C) can be clad on to steel (melting point 1SOOT) under conditions of minimal substrate melting. Conversely alloying tends to occur when the additive has a higher melting point that the substrate; for example, in the alloying of silicon (melting point 1410°C) into aluminium (melting point 660°C)significant melting of the substrate and mixing with the silicon occur. It should be noted that all surface melting processes, including those carried out by laser, tend to result in tensile stress in the as-treated layer. This is because the recast surface, as it solidifies and cools, tries to contract but is prevented from doing so by a relatively massive cold substrate. The effect is reduced by preheating the substrate and by heat-treatment after laser processing. -Production-line exploitation of laser cladding and alloying is still relatively limited. Most work appears to involve the cladding of cobalt-based hard-facing alloys on process plant components and on the interlock region of gas-turbine blading. Research and development effort is being directed towards alloying processes for titanium and aluminium. In the former, gas phase alloying using nitrogen results in a structure containing TiN and offering hardness up to 1OOOHV and more. Alternatively, the introduction of carbides also leads to a surface offering high hardness. In the case of aluminium, alloying with silicon can be carried out very controllably to yield strengthened microstructures having hardnesses double that of the parent alloy.

30.9 Safety In general, some of the basic requirements and guidelines for the safe handling of laser power supplies and laser beams are well established in existing safety standards such as BS480331983 in the UK. Whilst high power laser installations for metals working and materials processing are not addressed explicitly by such standards, nevertheless these installations usually come under Class 1 of the five classes identified in it. (More exceptionally, they may come under Class 4 operation in which, for example during beam alignment, an operator has to work without having the protection of a beam-tight protective enclosure around the equipment; in this case, reliance has to be placed largely on strict administrative controls.) However, in Class 1 operation, the installation is regarded as a laser system contained within a protective enclosure from which personnel are excluded and which does not permit the escape of radiation above the ‘Accessible Emission Limit’ (AEL). For example, in the case of CW Nd:YAG or C O , lasers, it is prescribed that an operator must not encounter access to greater than 0.6 to 0.8mW of beam power. Since the enclosed laser may have power of many kilowatts, it can be appreciated that much of the emphasis on safety provisions must centre on the engineering of the system so that there is a minimal risk that the beam can become errant and impinge on the enclosure and that, if it does, it is not permitted to penetrate the enclosure. The best current approaches tend to embrace a range of fail-safe design features which may include the following: Optical components in the beamline must be selected, mounted and maintained with care to

30-14

Bibliography

that they do not fail and allow the beam to become errant. The workpiece must be presented in such a way that the beam couples to it and is not excessively reflected in a way to cause damage. The enclosure must be capable of containing an errant beam: at lower laser powers, it may be adequate simply to select materials such as brick or copper; at high powers, such constructions may need to be augmented by, for example, heat-sensitive scanners which can register beam impingement on the enclosure and then shut down the laser before penetration occurs. Preferably the processing should be continuously monitored: in some cases this may be done visually by a remote operators holding a dead-man’s handle switch which they release if they see something amiss; alternatively for example a simple photo-sensitive detector can register light from the normal beam-workpiece interaction and enable continued operations (loss of light would imply that the beam had become errant so that the laser would then be shut down). Where one laser can be used with several workstations, a carefully designed system of beam switching, beam isolation and door interlocks must be employed to permit safe operator access for setting-up in one workstation whilst processing takes place in another. It is important to note that, although the foregoing discussion has been concerned with safety issues to do with the laser beam, in a materials processing installation all due care must also be taken with associated hazards including: high voltage power supplies; moving manipulators and robots; toxic fume from welding and cutting; fire due to hot spatter as well as impingment of the transmitted or rdected beam; ultraviolet radiation from the welding plasma plume.

30.10 Bibliography Books 1. ‘An Introduction to Lasers and Masers’ A. E. Siegman, McGraw-Hill, 1971. 2. ‘Lasers in Industry’ ed. S. S. Charschan, Van-Nostrand-Reinhold, Princeton, New Jersey, 1972. 3. ‘Industrial Applications of Lasers’ J. F. Ready, Academic Press, New York, 1978. 4. ‘Laser and Electron Beam Processing of Materials’ ed. C. W. White and P. S. Peercy, Academic Press, New York, 1980. 5. ‘Materials Processing, Theory and Practice, Vol. 3 Laser Materials Processing’, ed. M. Bass, North-Holland, 1983. 6. ‘Laser Treatment of Materials’, ed. B. L. Mordike, DGM Informationsgellschaft, 1987.

Industrial laser publications 7. Lasers and Optronics, published monthly, Gordon Elsevier Business Press. (Annual Buying Guide also published). 8. Laser Foeus World, published monthly, Pennwell Publishing. (Annual Buyers’ Guide also published). 9. ‘The Industrial Laser Annual Handbook‘, eds D. Belforte and M.Levitt, F’ennwell Books.

Laser beam principles 10. I. J. Spalding, ‘Characteristics of Laser Beams for Machining’, in ‘Physical Processes in Laser Materials Interactions’, ed. M. Bertolotti, Plenum, 1983. 11. J. T. Luxon, ‘Optics for Materials Processing’, in the 1986 ‘Industrial Laser Annual Handbook’, eds D. Belforte and M. Levitt, Pennwell Books, 1986, pp38-48. 12. L. Marshall, ‘Applications a la Mode’, Laser Focus, April 1971, pp26-28. Cutting and drilling

13. D. Schuocker, ‘Laser Cutting’, 1986 ‘Industrial Laser Annual Handbook’, eds D. Belforte and M. Levitt, Pennwell, pp87-107. 14. J. Fieret et a[., ‘Overview of Flow Dynamics in Gas-Assisted Laser Cutting’, Proc. Conf. High Power Lasers, 30 March-3 April, 1987, The Hague, SPIE Vol. 801, pp243-250. 15. G. Brodh and H.-0. Ketting. ‘Influence of the Purity of Cutting Oxygen in Laser Beam Flame Cutting’, Schweissen and Schneiden, August 1989, DVS ppE124-126. 16. J. M. Weick and W.Bartel, ‘Laser Cutting without Oxygen and its Benefits for Cutting Stainless Steel’, Proc. Vi Int. Conf. Lasers in Manufacturing, 10-11 May 1989,ed. W.M. Steen,IFS/Springer-Verlag, 1989,pp81-89. 17. A. Thompson, ‘CO, Laser Cutting of Highly Reflective Materials’, 1989 ‘Industrial Laser Annual Handbook‘, eds D. Belforte and M.Levitt, Pennwell, 1989, pp149-153. 18. A. G. Corfe, ‘Laser Drilling of Aero-Engine Components’, Roc. 1st Int. Conf. Lasers in Manufactwing, 1-3 Nov 1982, Brighton, IFS/North-Holland, pp31-40

Bibliography

30-15

Marking 19. L. Rosescrans, ‘Effects of Laser Marking on Fatigue Strength of Selected Space Shuttle Main Engine Materials’, Proc. ICALEO ‘86,eds C. M. Banas and G. L. Whitney, IFS/Springer-Verlag, 1987,ppU3-230. Welding 20. D. T. Swift-Hook and A. E. F. Gick, ‘Penetration Welding with Lasers’, Welding Journal Research Supplement 52 (11) 492499s. 21. P. G. Klemens, ‘Heat Balance and Flow Conditions for Electron Beam and Laser Welding’, J . App. Phys., May 1976,41 ( 9 , pp2165-2174. 22. M. Davis et al. ‘Modelling the Fluid Flow in Laser Beam Welding’, Welding Journal, July 1986,167s-174s. 23. A. P. Hoult, ‘Welding, - Cutting and Drilling with the 1kW Solid-state Oscillator-AmplifierLaser’, Ibid ref. 16, pp23-30. 24. J. Heyden et al., ‘Laser Welding of Zinc Coated Steel‘, Zbid ref. 16, pp93-104. 25. V. Ram et al., ‘C8, Laser Beam Weldability of Zircalloy 2’, Welding Journal, July 1986, pp33-37. 26. M. N. Watson, ‘Laser Welding of 6A1-4V Titanium Alloy’, The Welding Institute Research Bulletin, November 1986, ~~381-385. 27. T. Zacharia et al., ‘Weld Pool Development during GTA and Laser Beam Welding of Type 304 Stainless Steel’, Parts I and II, Welding Journal Research Supplement, December 1989, ~ ~ 4 9 9 ~ 5 1 9 s . 28. J. H. P.C. Megaw et al., ‘Girth Welding of X-60Pipeline with a lOkW Laser’, Proc. SPIE/ANRT Conf. High Power Lasers and Their Industrial Applications, Innsbruck, April 15-18, 1986. 29. I. J. Stares et al., ‘Improved Microstructure and Impact Toughness of Laser Welds in a Pressure Vessel Steel’, Metal Construction, March 1987 19. (3), pp123-126. 30. M. Sasaki et al., ‘CO, Laser Welding for Steel Strip Production Process, Proc. 3rd Int. Coll. on Welding and Melting by Electron and Laser Beams (CISFFEL) Lyon 5-9 September 1983. pp705-711. Surface treatment 31. W. M. Steen, ‘Surface Engineering with a Laser’, Metals and Materials, December 1985, pp730-736. 32. D. N. H. Trafford et al., Laser Treatment of Grey Iron’, Proc. Heat Treatment ’79, The Metals Society, 1980, pp32-38. 33. A. S. Bransden et ~ l . ‘Laser , Hardening of Ring Grooves in Medium Speed Diesel Engine Pistons’, Surface Engineering, 1986, 2 (2), pp107-113. 34. J. H. P. C. Megaw et d.,‘Surface Cladding by Multikilowatt Laser’, Ibid ref. 30, pp26S277. 35. R. M. Macintyre, ‘Laser Hard-surfacing of Turbine Blade Shroud Interlocks’, in ‘Lasers in Mate& Processing’.ed. E. A. Metzbower, ASM 1983, pp230-239. Safety 36. ‘BS4803: 1983 Radiation Safety of Laser Products and Systems’, British Standards Institution 1983. 37. ‘IEC825, Radiation Safety of Laser Products, Equipment Classification, Requirements and UserB Guide’, European Laser Safety Regulations. (Note that this standard is being redrafted to include recommendations on workstation enclosuredesign, and it is intended that in due course BS4803: 1983will be aligned with this). 38. R. D. Ball et a!., ’The Assessment and Control of Hazardous By-products from Materials Processing with CO, Lasers’, [bid ref. 17, pp154-162.

1

uide to corrosion control

31.1 Introduction Metals may be chosen specifically for their resistance to a corrosive environment but in industry, where economic considerations affect the selection of materials, it may be less costly to choose a metal that has a comparatively short life, and carry out regular maintenance or replacement rather than a high initial capital investment in a resistant metal or alloy that will withstand the conditions of corrosion during the lifetime of the plant. There are many examples where either of these two extremes has been the more economic choice, and therefore a wide choice of materials is required. It may be that the most economical decision would be to use coatings (see Chapter 35), cathodic protection or control of the environment (inhibitors, etc.). Resistant materials will be listed, where these are available, followed by the less resistant metals and alloys where shorter lifetimes may be tolerated.

31.1.1 Types of corrosion Corrosion damage to a metal or alloy can be (a) general or uniform corrosion, (b) Localized or pitting corrosion, and may be caused or enhanced by one or more of the following broad classifications: bimetallic coupling (and dealloying), crevice corrosion, erosion corrosion, stress corrosion cracking, corrosion fatigue (and fretting corrosion), Cydrogen embrittlement.

31.1.2 Environments which cause corrosion These may be broadly classified into three main groups: 1. Natural Atmosphere Water Soil Storage 2. Chemicals Acids Alkalis Feirtilizers Closed circulating systems Manufacture

- Humid,

polluted condensation. condensation.

- Sea water, river, potable, - Buried structures.

-Possible

corrosion during storage, transit or erection.

- Sulphuric.

hydrochloric, nitric, phosphoric. -Sodium and calcium hydroxides. -Nitrogen compounds, ammonia, organic acids. -Concentration

of river, well or sea water.

Of

chemicals

- 1000+varieties.

31-1

31-2

Guide to corrosion control

Process chemistry High temperatures Wet flue gases 3. Contact Wood Polymers

-Treatment;

e.g. dyeing, pickling, food processing, paper-making.

- Oxidation of metals, exhaust fumes, flue gases. -Combustion -Some - Some

systems where gases can condense, i.e. dew point corrosion.

vapours from wood are aggressive. polymers, in contact with metals can cause corrosion.

31.1.3 Accelerating factors Corrosion rates may be drastically changed when temperature, flow rates, pressures and concentrations of chemicals are varied; corrosion of metals from these parameters can therefore be regarded as an ‘add on’ factor and under certain conditions of temperature, pressure and flow the corrosion rates may then become excessive. There are many anomalies, e.g. mild steel is not attacked by very high concentrations of H,SO, but rapidly at concentrations below 70% w/v. Copper can withstand sea water but is attacked when the flow rate is excessive. 31.1.4 Measurement of corrosion damage Corrosion attack is not often uniform and it can be misleading to apply much of the published data which convert weight loss into penetration rate (mmyr-I). For instance, mild steel in sea water corrodes at approximately O.lmmyr-’, but pitting can occur up to 0.4mmyr-’ over a relatively small area of the total surface. In the case of intergranular attack at the metal grain boundaries a relatively small rate of attack can cause deep penetration so that whole grains drop out. Corrosion rates must also be accompanied by the type of attack and in the case of pitting by the probability of finding the deepest pit at a certain depth. In the case of high temperature oxidation and also for atmospheric corrosion, adherent corrosion products may be produced. The measurement of weight gain is then recorded. Corrosion damage, although not excessive, can be very undesirable or even dangerous. When metals are under tensile or cyclic stresses a small amount of pitting could give rise to stress concentrations that lead ultimately to failure by cracking. Formation of corrosion products in a confined space can lead to ‘oxidejacking’ where the expansion suffered by the components can cause bursting and distortion. This has been widespread in some forms of concrete reinforcement where relatively mild corrosion can give rise to serious cracking of the nearby concrete. 31.1.5 Chemicals For data on particular systems the following bibliography may be helpful. SOURCES OF CORROSION RATE DATA

Three main sources of information: 1. data books; 2. national and international standards; 3. scientific journals and abstract literature. I . Data books

‘Corrosion Guide’. E. Rabald, VDI, Diisseldorf, 1969. ‘Corrosion Data Survey’, G . A. Nelson, NACE, Houston, 1967. ‘Werkstoffetabelle’, DECHEMA, Frankfurt am Main, 1980. ‘Materials Selector’, The Elsevier/Elsevier Science Publishers, London, 1991. 2. See ‘Corrosion Prevention Directory’ HMSO, for extensive list.

Bimetallic corrosion

31-3

3. Abstract literature Metal Abstracts, ASM, Met. SOC.,London. Corrosion Abstracts, NACE, Houston, Texas. Corrosion Profile (Chem. Abstracts), UKCIS, University of Nottingham.

31.2 Bimetallic corrosion Designers require structures and machines to have metals and alloys of differing mechanical properties in close proximity, e.g. mild steel backed copper bearing surfaces, lightweight aluminium structure on a mild steel base, and many fasteners, rivets, screws etc. Table 31.1 CORROSION RATE IN mm yr-'

FOR BIMETALLIC COUPLING IN SEA WATER O F COM-

MON STRUCTURAL MATERIALS'*

Cathodic memb'er M

M:AI*

Carbon Carbon (Vs H30) Carbon (Vs NS4) Lead Silicon bronze 10% ,41 bronze NiAl bronze (Vs H30)

HY80 Ni-Resist Ni AI bronze Tin CN30 EN57 Monel Mild steel (Vs H30) Mild steel LG4 gunmetal Lead TitaniuM EN58J Tin Aluminium Copper

*

M:Zinc*

M:Mild steel*

101

I:1

1:lO

101

1:1

1:lO

101

1:l

1:lQ

39 32 49 0.5 2.0 2.4 2.8 1.6 0.7 2.4 2.2 1.7 2.7 2.2 3.0 1.7

2-10 2-10 2-10 0.15 0.6 0.6 0.7 0.3 0.06 0.15 0.14 0. I 0.15 0.12 0.16 0.07

0.4 0.5

7.5

2-8

-

60

33

9

1.7

2.2

1.3

1.0

2.5 1.6 3.3

0.6 0.5 7.4

2.2

2.8 2.0 2.2 2.7 2.8

1.8 1.4 0.6 0.3 0.35

0.04

4.2

1.6

6.7

0.3

0.12

1.2 14.5

0.3 0.5

0.2 0.09

0.66

4.5

1.4

0.04 0.06

0.05

0.27

Includes effect of anode/cathode area ratio,

** Based on BS PD6484 (1979).

Table 31.2 CORROSION RATE (mm yr-') FOR CATHODIC MATERIALS CARBON, TITANIUM AND COPPER 'COUPLED TO VARIOUS ALLOYS

Anodic member M

10:l

1:l

EN57 HYXCI Ferralium 40V Ni-Resist Tin 2% A! brass Si Al bronze Monel Silicon bronze Lead Naval brass

0.5 10 0.007 5.5 4 0.4 0.26 0.02 1.2 0.5 0.5

Carbon:M*

Titanium:M* 1:lO

1O:I

I:1

0.3 2-7 0.01 2

0.08

0.003

0.3

0.25

0.05

0.02 0.004

0.005 0.002

0.1 0.16 0.02 0.3 0.16 0.22

Copper:M" 130

101

1:1

1:lO

0.1

0.01 0.2

0.002

1.4

0.14

0.85

0.27

0.04

4.9

0.35

0.19

1.5

0.46

0.06

0.002

0.01

*Includes the effect of varying the anodejcathode area

31-4

Guide to corrosion control

In these cases, providing the environment is sufficiently conducting, serious acceleration of corrosion may occur. However, compatibility can be achieved. Table 31.1 gives the accelerating effect on coupling various materials with sea water as the conducting electrolyte. Comparable results may occur with other conducting chemical solutions. For electronic materials with thin metallic coatings in humid conditions, corrosion products may affect performance.

31.2.1 Bimetallic coupling associated with electronic materials Various noble metals are used to provide good conducting, tarnish-free contacts which are reliable over the life-time of the equipment. These metals are used generally as very thin films (1-5 pm) are usually porous. They are therefore likely to act as a good cathode and induce corrosion even under slightly humid conditions. Thus, the connector can become covered with a thin film of corrosion products which can reduce the performance of the electronic device. Frequently this corrosion effect occurs in handling and in storage. It can also arise with unsatisfactory packaging, and the bimetallic coupling encourages attack. Table 31.3 contains the combinations which have given satisfactory service and those that have been known to cause corrosion should the environment permit. Table 31.3 SEVERITY OF GALVANIC CORROSION FROM METALLIC COMBINATIONS Coatings are shown in brackets: (Ni)Cu = nickel-plated copper; (r.Sn)Cu =reflowed tinned copper; (s.d.)Cu = solderdipped copper. Completely satisfactory

Satisfactory slight corrosion

Borderline moderate corrosion

Unsatisfactory seuere corrosion

Cu-(Ni)Cu Cu-(Au) Cu (Sn)Cu-A1 (Sn)Cu-(Ni)Cu (Sn)Cu-(s.d.)Cu (Sn)Brass-AI (s.d.)Cu-(Ni)Cu (Ni)Cu-(Ao)Cu (Ni)Cu-( Ag)Cu (Au)Cu-(Ag)Cu AI-(Sn)Al*

Cu-(Ag)Cu (s.d.)Cu-(Sn)Al Cu+Sn)Cu Cu-(s.d.)Cu Cu-(r.Sn)Cu (Ag)Cu-(Sn)Cu (Ag)Cu-(s.d.)Cu (Au)Cu-(Sn)Cu AI-(Sn)AI**

(Au)Cu-(s.d.)Cu (Sn)Al-(Ni)Cu Al-(s.d.)Al

AI-Brass AI-CU (%)AI-Cu Al-(Ni)Cu AI-(Ni)Brass AI-(Ag)Cu (Sn)Al-(Ag)Cu AI-(Au)Cu (Sn)AI-(Au) Cu

' No copper undercoat.

** Zincate process

31.2.2 Dealloying-selective dissolution as a form of bimetallic corrosion A special case of bimetallic corrosion occurs for certain alloys where the base metal can be preferentially dissolved. Copper-zinc alloys are prone to this corrosion, and dezincification can be a serious corrosion problem resulting from the chemical composition of some natural waters. In particular, high chlorides and high temperatures lead to corrosion of the zinc alloying element leaving the copper as a porous mass. The component may keep its shape but has weak mechanical properties. Information about these water supplies may be obtained from the British Non-Ferrous Metal Association. The standard test, I S 0 6509, for susceptibility to dezincification requires the immersion of a sample of the alloy in 1% copper chloride at 75°C for 24 h. The corrosion can be reduced by a 1 % alloy addition of Sn or by 0.02-0.06% of Sb or P. Copper alloys with resistance to dezincification are given in Table 31.4. Table 31.4 SINGLE AND TWO PHASE COPPER-ZINC ALLOYS AND THEIR SUSCEPTIBILITY TO DEZINCIFICATION

Alloy type

Dezinciflcation

Alloy addition to reduce rate

Copper 85% and above Copper 70-85% Copper 60-70%

No Susceptible Susceptible

Arsenic up to 0.1% Tin up to 1.0% with arsenic 0.1%

Crevice corrosion

31.3

31-5

Crevice corrosion

Many engineering designs place metals together for joining, or create narrow slots or pockets where liquids could be retained. Such crevices include screw threads, nuts, washers, gaskets, some weldments, heat exchanger rolled in tubes, valve packings, etc. In neutral aerated waters there is the strong possibility of corrosion within these crevices, particularly with strongly passive metals in chloride solutions such as sea water. Practically all metals can suffer from this form of attack and the usual remedy is to remove the crevice by careful design of the fit of the components, or by sealing or coating. Table 31.5 gives an order of resistance to crevice corrosion which shows that some metals show good resistance. It is interesting to note that many of the popular stainless steels can bse affected to a serious extent by crevice corrosion.

Table 31.5

RESISTANCE TO CREVICE CORROSION

Metal

Very resistant

+

Mild steel Low alloy steel

Moderate corrosion

-+

Severe corrosion

Sea water

Cupro nickel Cu I O N 1.5Fe

Sea water

Cu and Cu/Zn

J

Titanium and T,I alloys

J (ambient temp)

95°C

321

316

304

302

13:< Cr

316

321

302

304

16% Cr

Stainless steel 107i H,SO, RT 10% H,SO,+NaCl Fe l8Cr 13Ni 3Mo 2Si NNG Fe 18Cr 14Ni 2Mo NiTi Fe l8Cr 24Ni 3Mo 2Cu Fe 20Cr 25Ni 5Mo 1.5Cu Fe l8Cr lONi 2.5Mo 2.5Si Fe 25Cr 2Mo(duplex) Fe 25Cr 6.5Ni 3Mo(duplex) 0.3 W

Neutral solutions Halide' and sulphate s o h

$ $

3J

Nickel alloys Hastalloy 'C'

0.02% increases time to failure Fully killed steels very susceptible Semi-killed steels slightly susceptible Low C rimming steels very resistant to SCC Temperature increase reduces time to failure. The higher the temperature the lower the concentration at which cracking occurs. Plastic deformation increases SCC. Annealing prevents SCC unless deformation is beyond yield stress

High strength steels (yield > 1000 MPa)

Below 1000 MPa yield stress hardenable steels are generally immune from SCC Above 1000 MPa yieldChloride solutions: Increase above 0.25% NaCl has little effect on time to fracture by SCC. Temperature has little effect in range 15-80°C. pH has little effect but above pH 10 susceptibility is reduced. Hydrogen embrittlement and cathodic protection can increase susceptibility to SCC

Stress corrosion cracking 31-9 Table 31.12 CONDITIONS FOR STRESS CORROSION CRACKING IN STAINLESS STEELS Environment for SCC:

Chloride solutions

H,S with or without chlorides

Caustic solutions

Polythionic acid

Susceptible allojs:

Types 304,316 martensitics

Martensitics ferritics ferritic-austenities

Types 304,316

Types 304,3 16

> 70 10 p.p.m. temp. dependent

120

Ambient

-

-

> 2.0 At lower pH general corrosion for susceptible alloys

pH atTects threshold stress

> 12

-

-

Temperature "C Chloride content PH

Stress level

Moderate

High

Moderate

LOW

Metallurgical condition

All

All

All

Sensitized

Talk 31.13 STAINLESS STEEL GRADE SELECTION IN ENVIRONMENTS WITH RISK OF STRESS CORROSION

Solution

Conditions Temp. Chloride "C content

Chloride

S 70

LOW

5 70

High

2 70

> 70 > 300

Low High Low

304 or 316 depending on risk of pitting 2RE 65,") high pitting resistance 2RE 60'" 2RE 65") SANICRO 3d3)

>60

None

316

>60 160 ’ oy

where X is a factor dependent on the crack geometry, upis the yield stress, C is maximum allowable crack length if crack growth is to be avoided. Note: If KISCC is in MPa milZ and rry in MPa, then C is in metres. For stress intensity greater than KISCC a crack will grow to the critical crack size usually at a constant crack velocity, the magnitude of which depends on the chemical environment. If the crack velocity is sufficiently low. the structure may be safe within its design life. Temperature also affects the magnitude of the crack velocity. See also Chapter 21, ‘Mechanical Testing’. Table 31.15 KIC AND KISCC VALUES Assume critical crack size C = 200 (K/U)’, where u in mm.

= yield

Alloy

in air C KIC MPam’I2 mm

Environment which induces stress corrosion

Copper alloys Cu-30% Zn

200

NH,OHpH7

13

stress, in MPa; C = crack length,

KISCC MPam1I2 1

C mm

0.003

Ultra high strength steels virtually independent of composition variation, P and S have little effecton KIC and KISCC.

Fracture toughness under corrosive conditions Tabk 31.15 KIC AND KISCC VALUES-continued

Alloy

Iron-steel alloys Mild steel 0.2 c 0.8 Mn High strength sreels Steel reinforcing bar

Martensite steel 0.47 C 1.14Cr 0.82 Mn 0.6 Ni 1.0 Mo Fe rem

in air C KIC MPamLf2 mm

Environment which induces stress corrosion

120

10 M NaOH (boiling)

36 31 31 42

KISCC MPam"*

1

Distilled water Ca(OH), (sat.)+NaC1 pH 120 above but coupled to Mg above but stress relieve at 430°C

C mm

0.001

20 22 18

25

yield stress 1400 MPa -100

Natural sea water 3.3% NaCl Distilled water

12-20

Hydrazine inhibitor 2%

2s

0.015-0.04

(D6-AC)

High carbon steel 0.84 C 0.26 Si 0.86 Mn

71

Tensile strength 1500 MPa Distilled water 600 ppm C1' + 1300 ppm

so:

High strength alloy steel 4340 steel 0.3 C. 0.63 Mn 0.87Cr, 0.39M0, 2.29 Ni Stainless steels 13% Cr steel (0.2:; C )

18%Cr, 8% Ni,

66

60 200

Stainless steels-cont. 15;i Cr, 4;< Ni, 4% Cu, Mn, 1%Si, Nb-Ti-0.3%, 187 0.07%C. 124

(17-PH alloy)

Cathodic protection 3.5% NaCI, 20°C Heat treatment to 1420 MPa 1000 MPa H,S gas 0.5 MPa pressure} 0.35 MPa

Distilled water 23 "C 3.5% NaCl 42% MgCI,-boiling

48

0.2

48 42

0.2 0.16

20 94 33 30

0.05 1.0

17 12 10

-

-

0.008 0.18

3.5% NaCl tempered at 1150 "C

140

tempered at 900 "C Cathodic protection by coupling with Zn (900'C with AI temper) with Mg

87

33 60 29

-

High alloy steels iS%Mn, 5%Ni

145

Hot aqueous halide solutions

8

0.01

13%Co, lO%Ni,

140

3.5% NaCl at 20°C at 0.2% proof 1660 MPa 19 stress 1440 MPa 33

0.03

1%Mo, 0.15%C. Prec. hardened

{

0.10

31-11

31-12

Guide to corrosion control

Table 31.15 KIC A N D KISCC VALUES-continued

Alloy

in air KIC MPaml

C

mm

Encironmenr xAich induces scress corrosion

KISCC MPaml”

C mm

High-alloy steels-continued

9%Ni, 476 Co, 0.45%C Aluminium ulbys Type 2024 Type 2219 Type 7075 Ag-3Mg-7 Zn Titunium alloys Ti-6Al-ZNb 1% Ta+0.8”/, M o Ti-6A1-1V Ti-3AI-SV

67 100

13 25 22 22 24 20 25

150 138 60 35

0.4 1.0

P

I

-

m

I

-

9 6 1.1 0.2

Martensitic yield at 1650 MPa 15 18 Bainitic, yield at 1500 MPa 3.5% NaC1+0.2 M Na,Cr,O, +0.07 M Na acetate, +acetic acid to pH 4.0 14 Resistant temper T854 12 Susceptible, temper T351 22 Resistant, temper T37 12 Susceptible. temper T37 20 Resistant, temper T 7351 4 Susceptible, temper T651 5 Aqueous halides at 20°C NaCl solutions Heat treated to 700 MPa Heat treated to 800 MPd 0.6 M KCI Methyl alcohol-HCI

116 44

20 6

0.02 0.04

-

-

I

m

0.04

5

0.6 0.12 0.006

REFERENCES TO TABLE 31.15. H. L. Craig (Ed.), ‘Stress corrosion-new approaches‘, ASTM-STP 610, Philadelphia (1975). R. W. Staehle et al., ‘Stress corrosion cracking and hydrogm embrittlement of iron-based alloys’, NACE, 5 (1973).

31.10 Atmospheric corrosion Table 31.16 UNIFORM CORROSION* IN INDUSTRIAL ATMOSPHERE Alloy

Uniform rate of corrosion mm yr-‘

Mild steel Wrought iron Wrought iron Copper-bearing mild steel Fe, IS/, Cr, 0.5:; Cu Aluminium Zinc Copper 70/30 brass Nickel 80Ni 20Cr 18 Cr 8 Ni stainless steel

0.125 0.200 (f; SitO.l>;) 0.100 (% Si>O.3%) 0.100 0.075 0.005 0.006 0.007 0.020 0.010 0.004 0.001

*

Pitting may take place and penetration can be 2-5 times uniform values.

Table 31.17 UNIFORM CORROSION* IN SPECIAL ATMOSPHERES

Environment

Rate of unijorm corrosion for mild steel mm yr-’

Domestic kitchens and bathrooms Laundry Sulphuric acid plant Paper mill Pickling sheet steel

0.0025-0.001 0.0075 0.048 0.068 > 0.45

* Pitting may occur and penetration may be 2-5 times uniform rate.

Contact corrosion

31-13

31.11 High temperature oxidation resistance Oxidation of metals in air produces a relatively thick oxide scale dependent on temperature. Above certain high temperatures the scale becomes excessive and will spa11 away to give wastage. For close fitting components, such as bolts, values etc. this could cause seizure and cracking.

Table 31.18 HIGH TEMPERATURE OXIDATION OF STEELS

Steel

Temperature "C for oxidation 20.127 mm y r - I

Plain carbon Fe 0.5% Mo Fe 0.5% Cr, 0.5% Mi0 Fe 2.25% Cr, l:< Mo Fe 5.0:/, Cr, OS:/, Mo Fe 9% Cr, 17; Mo

580 600 600 613 607 670

Table 31.19 RECOMMENDED TEMPERATURE LIMIT FOR OXIDATION OF VARIOUS ALLOYS IN AIR

Metal

Temperature limit "C

Carbon steel 2$%Si, l%Al, 1%Mo steel* )%Mo steel PhMo, 1%Cr steel $%Mo, 5%Cr steel 1% Mo, 9%Cr steel 12%Cr, Mo, V steel 18%Cr, 8% Ni stainless steel 12%Cr, 8%Ni, 1% Nb steel 19% Cr, 11%Ni, 2%Si steel 23%Cr, 14%Ni steel 23%Cr, 30%Ni steel 80%Ni, 20%Cr 60%Ni, 20%Cr, 2O%Co, Al, Ti 55%Ni, 15%Cr, 2O%Co, 5%Mo, 5%A1 and Ti

450 700-900 500 550 550 550 575 650 650 1000 1000 1100 900 900 1100

* E. A. Brandes, Fulmer Research Institute, Special Report No.2, 1956.

31.12 Contact corrosion Contact corrosion can be a serious problem in packaging and in electronics. As miniaturization and sophistication of electronic devices have increased, the hazard presented by corrosion is often the limiting factor inhibiting the attainment of expected levels of reliability. Semiconducting devices, switches and miniaturized VHF circuits are all particularly sensitive to the slightest reaction on critical surfaces, and in devices calling for the highest levels of reliability even the most inert of the phenolic, epoxide and silicone resins are not considered to be fully acceptable; corrosion of electronic assemblies may often be enhanced by migration of ions to sensitive areas under applied potentials, and by local heating effects associated with current flows. For more information see: P. D. Donavan in L. L. Shreir, 'Corrosion', Vol. 2, Butterworths, London, 1976 and W. H. Abbott, 'Corrosion of Electrical Contacts', Brit. Corr. J., 1989,24, NO.2.

31-14

Guide to corrosion control

Table 31.20

CONTACT CORROSION DANGERS: POLYMERS ETC.

Material Rubbers, elastomers and adhesives 1. Natural rubber ( a ) Non-vulcanized

(b) Vulcanized 2. ( a ) Synthetic tubbers

( b ) Polysulphide rubbers (cold curing)

Severity of corrosion*

Volatiles evolued and remarks

Slightly corrosive on prolonged exposure Slight1y-moderately corrosive

Formic and acetic acid evolved Hydrogen sulphide and sulphur dioxide evolved

Non-corrosive at ambient condition-most are corrosive above IOO'C

Many are chlorinated and evolve HC1 on heating; Hypalon may also emit sulphur dioxide Formic acid; the catalysts used are peroxides

Moderately corrosivevery corrosive

3. Silicone polymers

Non-corrosivevery corrosive

Acetic and formic acids. Some single-pack silicone sealants cure by hydrolysis of acetoxy groups releasing acetic acid and are very corrosive; some two-pack formulations evolve formic acid and are corrosive, and others are reputed to be among the most inert polymers

4. Phenol and ureaformaldehyde glues

Slightly corrosive-very corrosive

Formaldehyde, phenol, ammonia and HCI may be evolved. Various acids and salts that yield acids (e.g. formic acid and hydrochloric acid) are used in cold-set formulations. Volatiles evolved during cure may be absorbed by the materials being bonded

Non-corrosive at ambient temperature (but see column 3); moderatelyvery corrosive at 70°C

Hydrogen chloride (HCI). May become corrosive at ambient temperature if irradiated with UV radiation or in the presence of certain contaminants, e.g. zinc ions

2. Fluorinated thermoplastics (e.g. PTFE)

Non-corrosive at ambient and moderate temperatures; very corrosive above about 350°C

Decompose to release H F and F,

3. Nitrocellulose

Slightly-very corrosive

Oxides of nitrogen may be evolved progressively with ageing

4. Nylons (a) Nylon 6

Corrosive

Acetic acid; formulations frequently contain acetic acid additions as molecular weight regulators

Thermoplastics 1. Polyvinyl chloride (PVC) (and other chlorinated thermoplastics)

(b) Nylon 66

Non-corrosive

5. PVA (polyvinyl acetates and alcohols)

Non-corrosive-very corrosive

Acetic acid released; corrosivity dependent on conditions and formulation (degree of hydrolysis and presence of stabilizers and inhibitors)

6. Cellulose acetate

Slightly corrosive

Acetic acid may be released

Contact corrosioM

31-15

Table 31.20 CONTACT CORROSION DANGERS: POLYMERS ETC.-continued

Mareriul

Sereriij of corrosion*

Voluriles evolsed

Slightly corrosive at ambient temperature, more corrosive above 40°C Usually non-corrosive at ambient temperatures, corrosive above 45‘C

Acetic acid and formic acid evolved (acetic acid may be used as an end-stopper) Formic acid evolved (if arduous moulding conditions have been used, the polymer may be corrosive at ambient temperatures)

and remarks

7. Polyacetals ( a ) Homopolymer

( b ) Copolymer (formaldehyde and 10;; ethylene oxide)

8. Polyolefines, polyesters, polycarbonates, polystyrene, polysulphone, polyphenylene oxide and polymethylmethacrylate

Non-corrosive at ambient temperatures

Therinosetting resiras 1. Cross-linked polyesters (I) Cold cured polyesters

MEKP catalyst and cobalt naphthenate accelerator-very corrosive. Other peroxide catalyst systems slightlymoderately corrosive. Irradiation or non-oxidizing corrosive catalyst Non-corrosivemoderately corrosive

In-

(41) Hot cured polyesters

Formic and acetic acids evolved. Corrosivity is determined largely by the catalyst used, but is also affected by the formulation, in particular diethylene glycol gives more corrosive resins than does propylene glycol

.

* Refers directly io Zn,

Mg and steel.

Defence Guides, DG-3A, ‘Prevention ofcorrosion of zinc and cadmium coatings by vapours from organic materials’. HMSO. Table 31.21

CORROSION BY CONTACT WITH WOOD

Wood

Clnssificution

Typical pH Ldues

O dk

Most corrosive Most corrosive Moderately corrosive Moderately corrosive Moderately corrosive Moderately corrosive Moderately corrosive Moderately corrosive Least corrosive Least corrosive Least corrosive Least corrosive Least corrosive Least corrosive Least corrosive Least corrosive

3.35, 3.45, 3.85, 3.9 3.4, 3.45, 3.65 3.85, 4.2 4.85, 5.05, 5.35 3.45, 3.55, 4.15, 4.2 4.2, 4.45, 5.05, 5.2 4.65, 5.45 3.45 5.2 to 8.8 4.0, 4.45 6.45, 7.15 5.1, 5.4, 5.55. 6.65 4.4, 4.55, 4.85, 5.2 5.4, 6.2, 1.25 5.25, 5.35 4.15, 6.75

Sweet chestnut Steamed European beech Birch Douglas fir Gahoon Teak Western red cedar Parana pine Spruce Elm African mahogany Walnut Iroko Ramin Obeche REFERENCE TO TABLE 31.21

V. R. Gray, J . Inst. Wood Sei., 1958,1, 58.

2 Eleetroplating and metal finishing

The processes and solutions described in this section are intended to give a general guide to surface finishing procedures. To operate these systems on an industrial scale would normally require recourse to one of the Chemical Supply Houses which retail properietary solutions. This particularly applies to electroplating baths containing brighteners.

32.8 Polishing compositions The following abrasive powders are used for polishing metal. ALOXITE

Aluminium oxide made by fusing bauxite. Used for cutting down in the same way as emery. ALUMINA

Certain grades of alumina are used for polishing stainless steel and chromium. The material is generally used in the form of a composition in which the powder is mixed with stearines or other fats. EMERY POWDER

Used principally in cutting down and for preliminary operations. It is applied to the mop by means of an adhesive, usually glue. Emery powder is an impure aluminium oxide containing about 50-60% A1,0,, 3040% magnetite and small amounts of ferric oxide, silica, chromium, etc. Emery powder should never be used on magnesium or aluminium components because af the adverse effect on corrosion resistance. TRIPOLI

A calcined diatomaceous earth used for polishing brass, steel and aluminium. It is used generally in tbe intermediate stages, and is usually compounded with stearines and paraffin wax to make a

polishing composition which can be used directly on a mop. CROCUS POWDER

A polishing composition consisting essentially of ferric oxide, of coarser grade than rouge, used for polishing iron and steel. and also, tin. Usually compounded with stearine and used with a mop or fibre brush.

32-1

32-2

Electroplating and metal finishing

ROUGE A high-grade ferric oxide supplied in various degrees of fineness. It can be used in the form of a paste directly on to a soft mop or can be made into a composition with stearine. It is used essentially for finishing to obtain a very high polish on gold, silver, brass, aluminium, etc. BLACK ROUGE

This consists of black oxide of iron and is sometimes used for finishing operations, GREEN ROUGE

Chromic oxide used for polishing chromium and stainless steel and can be used either in the form of a composition mixed with stearine or as a paste applied directly to the mop. VIENNA LIME

Used for making the white finish for polishing nickel, etc. It consists of a calcined dolomite and contains about 60% calcium oxide and 40% magnesia. CARBORUNDUM

Silicon carbide used for low tensile strength materials, e.g. brass, copper, aluminium, etc. and also brittle metals, such as hard alloys and cast irons.

32.2 Cleaning and pickling processes VAPOUR DEGREASING

Used to remove excess oil and grease. Components are suspended in a solvent vapour, such as trior tetrachloroethylene. Note: Both vapours are toxic and care should be taken to ensure efficient condensation or extraction of vapours. EMULSION CLEANING

An emulsion cleaner suitable for most metals can be prepared by diluting the mixture given below with a mixture of equal parts of white spirit and solvent naphtha. Pine oil Oleic acid Triethanolamine Ethylene glycol-monobutyl ether

62 g 10.8 g 1.2 g 20 g

This is used at room temperature and should be followed by thorough swilling. Table 32.1 ALKALINE CLEANING SOLUTIONS Composition of solution Metal to be cleaned

All common metals other than aluminium and zinc, but including magnesium

Sodium hydroxide (NaOH) Sodium carbonate (Na,CO,) Tribasic sodium phosphate (Na,PO, . 12H,O) Wetting agent

Temperature

ozgal-'

gl-'

"F

"C

Remarks

6

37.5

180-200

80-90

For heavy duty

4

25.0 6.2 1.5

CIeuning and pickling processes

32-3

Table 32.1 ALKALINE CLEANING SOLUTIONS-continued Composition of solution Metal to be cleaned Sodium hydroxide Sodium carbonate Tribasic sodium phosphate Sodium metasilicate (PJa,SiO,. 5H,O) Wetting agent Tribasic sodium phosphate Sodium metasilicate Wetting agent Aluminium and zinc

Most common metals

Most common metals

Tribasic sodium phosphate Sodium metasilicate Wetting agent Sodium carbonate Tribasic sodium phosphate

Temperature

ozgal-I

gl-'

"F

"C

Remarks

2 4

12.5 25.0

180-200

80-90

For medium duty

2

12.5

2

12.5 0.75 25.0 25.0 0.75

180-200

80-90

For light duty

180-200

80-90

8

12.5 25.0 0.75

2

12.5

180-200

80-90

4

25.0

Electrolytic cleaner, 6 V Current density l00/A ft-' (1O/A drn-') Article to be cleaned may be made cathode or anode or both alternately

Room

Room

May be used electrolytically

1 -

8

4 4 1 8

2 4 1 -

Wetting agent

1

*

1.5

Sodium carbonate Sodium hydroxide Tribasic sodium phosphate Sodium cyanide (NaCN) Sodium metasilicate Wetting agent

6 1

37.5 6.25

2

12.5

2 1

12.5 6.25 0.75

8

Table 32.2 PICKLING SOLUTIONS Composition of solution Metal to be pickled Aluminium (wrought)

For etching Sodium hydroxide (NaOH)

Temperature

ozgal-I

gl-'

"F

"C

Remarks

8

56

104-176

40-80

Articles dipped until they gas freely, then swilled, and dipped in nitric acid 1 part by vol. to of water (room temperature) I

Aluminium (cast and wrought)

Nitric acid, s.g. 1.42 Hydrofluoric acid (52%) Water

1 gal 1gal

11 11

8gal

81

Room

Room

Articles first cleaned in solvent degreaser. Use polytheile or PVC tanks

Note-: It is almost universal practi- to use an inhibitor in the pickling bath. This ensures dissolution of the scale with practically no attack on the metal. inhibitors are usually of the long chain amine type and often proprietary materiais. Examples are Galvene and Stannine made by ICI.

32-4

Electroplating and metal ,finishing

Table 32.2 PICKLING SOLUTIONS-continued Composition of solution Metal to be pickled Bright dip Chromic acid Ammonium bifluoride Cane syrup Copper nitrate Nitric acid (s.g. 1.4) Water (distilled) to

Temperature

ozgal-'

gl-'

"F

"C

Remarks

0.84 oz 0.72 oz 0.68 oz 0.04oz 4.8 oz

5.2g 4.5 g 4.2g 0.25 g

195

90

Immerse for 15 min. Solution has limited life. AR chemicals and deionized or distilled water should be used

1 gal

11

30 ml

Aluminium and other nonferrous metals

Bright dip Phosphoric acid (s.g. 1.69) Nitric acid (s.g. 1.37)

8.4gal 0.6gal

9.41 0.61

195

90

Immerse for several min. Agitate work and solution. Good ventilation necessary. Addition of acetic acid useful with some alloys

Copper and copper alloys

To remove scale Sulphuric acid* Water

1 gal

11 41

150-170

65-75

4 gal

After pickling articles can he dipped in sodium cyanide: 40zgal-' (25gl-') to remove tarnish

70-175

20-75

This solution leaves a slight passive film which helps to prevent tarnish

Iron and steel

Or Sulphuric acid' Sodium dichromate (Na,Cr,O, .2H,O) Water

1 gal 12 02

11 75 g

4 gal

41

Bright dip Sulphuric acid* Nitric acid Water Hydrochloric acid

2 gal 1 gal 1 gal 0.5 oz

21 11 11 25 ml

Room

Room

If any scale first dip in spent bright dip. Remove stains by dipping in sodium cyanide 4 oz gal(25g 1-I)

Matt dip Sulphuric acid* Nitric acid (s.g. 1.42) Zinc oxide (ZnO)

1 gal 1 gal 2 lb

11 11 2mg

160-180

70-80

If the finish is too fine add nitric acid. If too coarse add sulphuric acid

Semi-matt dip Sodium dichromate Sulphuric acid* Water

3 02 18 oz 1 gal

19 g 114 g 11

Room

Room

2 Yo

-

Room

Room

0.25%

Leave for several hours or overnight

10%

-

120-180

50-80

Or hydrochloric acid

Slow pickle to loosen heavy scale Sulphuric acid' Glue To remove scale Sulphuric acid*

10-20%

* Sulphuric acid, pure cornel. grade, s.g.

1.84. Note: It is almost universal practice to use an inhibitor in the pickling bath. This ensures dissolution ofthe scale with practically no attack on the metal. Inhibitors are usually of the long chain amine type and oftenproprietary materials. Examples are Galvene and Stannine made by ICI.

Cleaning and pickling processes

32-5

TabUe 32.2 PICKLING SOLUTIONS--continued Composition of solution Metal $0 be pickled

Iron and steel conrinued

Bright dip Oxalic acid crystals Hydrogen peroxide (100 vol.) Sulphuric acid (10%) Water to Anode etching Sulphuric acid* Water

Magnesium and magnesium alloys

Temperature

ozgal-'

gl-'

"F

"C

Remarks

4 oz 2 oz

25g 13 g

Room

Room

This solution has so far only been used on an experimental basis

0.02 oz 1 gal

0.1 g 11

1 gal 2 gal

11 21

Not above

Not above

75

25

Current density: 200AK2 (20Adm-')

-

Not above 75

Not above 25

Density must not fall 01 below 1.61 g work will he etched

100-

200

Up to b.p.

Up to b.p.

For removal of oxide films, corrosion products, etc. Should not be used on oily or painted material Should be used on rough castings or heavy sheet only. Removes approx. 0.002 in. in 20-30 s

For polished work Sulphuric acid*

-

General cleaner Chromic acid

16-32

Sulphuric acid pickle Sulphuric acid*

3Yo

-

Room

Room

Nitro-sulphuric pickle Nitric acid Sulphuric acid*

8% 2Yo

-

Room

Room

150

Room

Room

Room

Room

Bright pickle for wrought products Chromic acid Sodium nitrate Calcium or magnesium Iluoride

23 4

__

25

Lustrous appearance. Involves metal removal

1 -

3

314 3:

235 20

1

6.2

Acetic acid

8 approx.

50 Room approx.

Room

Special purpose pickles

Citric acid

8

50

Room

Room

approx.

approx.

Special purpose pickles

Brightpicklefor castings Chromic acid Concentrated nitric acid (70%) Hydrofluoric acid (50%)

A

* Sulphuric acid, pure comcl. grade, s.g. 1.84. Note: It is almost universal practice to use an inhibitor in the pickling bath. This ensures dissolution of the scale with practically no attack on the metal. Inhibitors are usually of the long chain amine type and often proprietary materials. Examples are Galvene and Stannine made by ICI.

32-6

Electroplating and metal jnishing

Table 32.2 PICKLING SOLUTIONScontinued Composition of solution Metal to be pickled

Stainless steel

ozgal-'

gl-'

"F

"C

Remarks

To loosen scale Sulphuric acid* Hydrochloric acid (s.g. 1.16)

13-30 6-20

80-180 40-120

130-160

60-70

Use prior to scale removal treatment, for heavy scales

To remove scale Nitric acid (s.g. 1.4) Hydrofluoric acid (52% HF)

32 6

200 40

130-150

55-65

10 10 10

60 60 60

Room

Room

40

250

140-160

60-70

3

22

13

80

160-180

70-80

5-15 min

6

40

40 3

250 19

Room

Room

5-30 s. If yellow film persists after rinsing dip in sulphuric acid: 1 floz per gal (6 ml1-I) and rinse again

Or Sulphuric acid* Hydrofluoric acid Chromic acid (CrO,) Bright pickle Hydrochloric acid (s.g. 1.16) Nitric acid (s.g. 1.4) White matt finish Ferric sulphate [Fex(so4),1 Hydrofluoric acid (52% HF)

Zinc and zinc alloys

Temperature

Bright dip Chromic acid (CrO,) Sodium sulphate (NaW4)

* Sulphuric acid, pure comcl. grade, s.g. 1.84. Nore: It is almost universal practice to use an inhibitor in the pickling bath. This ensures dissolution of the scale with practically

no attack on the metal. Inhibitors are usually of the long chain amine type and often proprietary materials. Examples are Galvene and Stannine made by ICI.

Anodizing and plating processes

32-7

32.3 Anodizing and plating processes Table 32.3 ANODIZING PROCESSES FOR ALUMINIUM Good ventilation above the bath and agitation of the bath is advisable in all cases. COmpOSiliOfl of SOhtiOn

Temprrature

02

gal-'g I - '

"F

-

"C

Current density Time ampft-2 and (A dm-2) voltage

Hangers Remarks

Chromic acid (CrO,), chloride content must not exceed 0.2 g I-', sulphate less than 0.5 g 1-' (After BengoughStuart)

5-16 30-100 103- 38108 42

Sulphuric acid (sg. 1.84)

32

200

6075

15- 10-20 12-18V 24 (1-2) d.c. 20-40 min

AlumLead inium or lined lead pla- steel tes (tank if lead lined)

Pure

32

200

2341

-5-

Lead

Lead lined steel

Aluminium

Agitation required. or Gives coating titanium 1-3 thou. thick

12.8 80

70

20

10-20 50 V (1- 2) d.c. 30-60 min

Vat lining

Lead lined steel

Aluminium or titanium

12.8 80

7595

2535

20-30 20-60 (2-3) a s . V 4060 min

Vat lining

Lead lined steel

Aluminium

Hard anodizing Hardas process Sul?huric acid

Elosui G X process Oxalic acid (COOH),.2H20

Eloxal WX process Oxalic acid

+5

Current controlled by voltage. Average 3-4 (0.34.4) d.c.

25-400 (2.540) d.c.

tl-10 min 040 V increased in steps of 5 V 5-35 min Maintain at 40 V 3-5 min Increase gradually to 50 V 4-5 min Maintain at 50 V

Cathodes Vat

40120V

Tank or Steel stain(exless hausted) steel

Pure ahminium or titanium

Slight agitation is required This process cannot be used with alloys containing more than 5% copper

The current alumin- must not ium or exceed 0.2 titanium A l - ' of electrolyte

Oxalic acid processes are more expensive than sulphuric acid anodizing; but coatings are thicker and are coloured.

or titanium

Integral colour Anodizing Kalcoior process Sulphuric acid 0.8 Sulphosalicylic acid 16

t Period according

to

5 100

72

22

30 (3) d.c.

25-60 V 2M5 min

degree of protection. Complete cycle normally 40 min

Lead

Lead lined steel

Aluminium level in solution must be or maintained between titanium 1.5 and 3 gl-'

Aluminium

32-8

Electroplating and metal ,finishing

Table 32.4 ANODIZING PROCESSES FOR MAGNESIUM ALLOYS Composition of solution

Temperature

02

HAE process Potassium hydroxide Aluminium Potassium fluoride Trisodium phosphate Potassium manganite

Dow 17 process Ammonium bifluoride Sodium dichromate Phosphoric acid 85% H,PO, Cr 22 process Chromic acid Hydrofluoric acid

(G%,

Time and voltage

Cathodes Vat

Hangers Remarks

gal-' g I-'

"F

19.2 120

160

0.35 0.7

2 3 69 4 5 66

380-520

1150 2000 1800 160

0.9 0.5

6 7

0.4

65

>600

8 9 10 61

A1-33Cu AldCu-O.5Zr A1-2.59C~2.26LA.l6Zr(U)90) Al-4.4QCu-O.70Mg4.8OSi0.75Mn(2014)+ 15%SiC Al-25-33C11-7-11Mg A!-Ga-Ti AMGe AM.4Li-2.OCu-0.70Mg0.08Zr18091 A1-2.5Li-1.2Cu4.6MgO.lZr(8090) A1-2.4Li-1 .~CU-(P.@IM~0.12Zr[8090) Al-1 S6Mg-5.6Zn Alr3Mg-6Zn AM.93Mg-10.72Zn-0.42Zr

-

4Oc-500

450480 450480 420-480

-

64

RT

-

0.72 0.3-0.5

400-500 490-550

230 1350

0.6

52C-530

660-1 200 0.65

62

>lo00

0.68

63

500 400 1550

0.7 0.35 0.9

11

-

530

530 3W360 550

-

36-1

12

11

Remarks

Euratom alloy Optimum 500°C at 4.16 x Alcan 08050

Mer 25% pre-deformation at 510°C

n supral Optimum 520"Cat 5 x Elong% 350% at 5.25 MPa hydrostatic pressure

Optimum 530°C at iO-3-10-4 2-3 mm sheet at 2-5 x 2mm sheet at5 x and 5-10 micron grain size

TI BA 480

362 TaMe 36.1

Superplasticity NON-FERROUS

SYSTEMS SHOWING SUPERPLASTICITY-continued. Maximum Temperature elongation range"C X

Alloy sysrem

A1-5.8Mg-O.37Zr + others A1-4.89Mg-1.19Cr A1-8.OMg-1 .OLi-O.lSZr

A1-5.70Zn-2.30Mg-1.5OCu-

+

0.22Cr(7475) 1S%SiC

520 482-520 300 495-515

-

>800 >loo0 >loo0 97

m

References

Remarks

0.6

13 67

Optimum 520°C at 1.6 x lo-*

0.43

65 68

Elong% 310% at 5.25 MPa hydrostatic pressure Optimum 530°C at 2.8 x

530

1300

Be

6OC-700

130

0.9

14

Bi-44.5Pb Bi-3 1Pb-17% Bi43Sn

20 20 20

600 600 1950

0.42 0.45

-

15 15 15

Cd-17.5Zn Cd-27Zn

20 20-30

400

0.5

350

0.5

16 16

co-1oAl

1200

450

0.47

17

Cr-3OCo

1 200

160

-

18

Cu-9.8A1 Cu-9.5AI-14Fe Cu-1OAl-3Fe Cu-1OAMFe Cu-2.8A1-1.8Si4.4Co Cu-10-20Mg cu-7P cu Cu-9.8Zn Cu-4OZn Cu-48Zn Cu-38.5Zn-3Fe Cu-38Zn-15Ni-O.2Mn

540-700 800 800 750 500-600 700 410-600 450 163 627

0.7 0.7 0.6 0.6 0.5

450-565

700 > 800 7 200.6 lo00 320 250 > 600 > 300 570 > 525 450 330 200

-

19 19 20 21 22 23 24 25 26 27 28 25 29

In-34Bi

20

450

0.76

30

Eutectic

Mg-?;3Al Mg-9Li Mg-9Li Mg-9Li Mg-4.3A1-3Zn-0.5Mn Mg-30.7Cd Mg-5.5Zn-0.5Zr Mg-O.5Zr

350-400 180 200 250

2 100 460 445 310

0.8 0.52 0.47 0.44

250 1000 150

-

Eutectic 6.1 micron grain size At 3 x 7.1 micron grain size At 1 x At 1 x lo-"; 14.2 micron grain size Russian MA 15

450 270-310 500

31 70 70 70 32 23 33 34

Ni Nichrome* Ni-20Cr

800 1 000 800-900 810-1 070

180 190 200 1 000

0.5 e5

795-855 810-980 810-980 800- 1000

20 25-100 25 55 246 20-80 20

Al-5.70Zn-2.30Mg-1.5OCu0.22Cr(7475)

Ni-15Co-9.5Cr-5.5AI-STi3Mo Ni-34.9Cr-26.2Fe0.58Ti Ni-38Cr-14Fe-1.75Ti-lAl Ni-39Cr-lOFe-1.75Ti-lAl

Ni-16Cr-8.3Cc-3.4Ti-3.4Al-

500-800 500-800

-

0.5 0.45 0.4-0.5 0.75 0.9 0.53

0.6 0.3

CDA619 CDA 638 Solder, temporary superplasticity 1n836

ZK 60

0.5

35 35 36 37

IN 100

> 1000 1000 1000 500

0.5 0.5 0.5 0.4

38 38 38 39

IN 738

-

0.35 0.6 0.35

40 41 41 42 43

0.5 0.5

44

-

2.6W-1.78Ta-1.75Mo 0.9Nb-0.1 Zr-O.17C-O.O1B Pb-5Cd Pb-17.4Cd Pb-30Cd Pb4OIn PF11Sb Pb-19Sn Pb-7.9Tl Regstered Trade Mark.

> 350 >900 215 1 200

-

400

-

45

Eutectic Eutectic

Superplasticity

36-3

Table 36.1 NON-FERROUS SYSTEMS SHOWING SUPERPLASnCITY-continued

Alloy system

Sn Sn-1Bi

Maximum Temperature elongation range"C %

Sn-SCcl Sn-2Pb Sn-38Pb Sn-32Pb18Cd Sn-3 1.1Pb3.4Zn Sn-2-6Sb Sn-9.8Zn

20 22 20 25 20-80 20-170 25-70 25-70 140-210 20-180

Ti (commercial) Ti4A1-0.250z Ti-5AI-2.5Sn Ti-6Al-4V

900 950-1 050 900-1 100 750-1 MH)

Ti-6Al-5Zr-4Mo-lCu-0.25Si Ti-8Mn Ti-15Mo Ti-1 1.311-5Zr-2.25AI-1 Mo0.25% Zn (Commerciai) Zn-0.2Al Zn-O.4Al Zn4.9A1 Zn-l8Al Zn-22Al Zn-36AI Zn-40Al Zn-5OAl Zn-22A1-0.1Cu Zn-22A14u Zn-22A1-0.2Mn Zn-O.lNi-0.04Mg

Sn-5Bi

References

500 1000 350 600 >4850

-

0.5 0.48 0.68 0.32 0.5 0.7 0.55

500

0.55

570

0.4 0.5

44 46 47 48 44 44 49 49 50 26

-

-

450

0.8 0.6 0.72

1000

0.85

800 580-900 580-900 800

300 140 450 500

-

20-70 23 20 200-360 22-350 20-300

409 465 650 300

22-350 250-300 250-300 250 20-250 20-250 100-250

-

627-827 Zr-1.2-1.7Sn-0.07-O.2Fe-0.05- 800-1 050 0.15Cr-0.03-0.08Ni Zr-1.2-1.7Sn-0.12-0.18Fe0.05- 800-1050 0.15Cr-0.007Ni

Zr-2.5Nb

W-15-50Re

m

2000

37 37 37 37

Remarks

Eutectic

Eutectic RC 70 Commercial alloy used throughout world IMI 700

-

23 28 28 23

0.2 0.8 0.5 0.68 0.6 0.7

51 52 51 53 54 54 54

loo0 lo00 > 980

0.5 0.65 0.3 0.65 0.5 0.5 0.51

55 55 56 57 57 58

430 2 500

0.6 0.57

59 60

Zircalop 2 +O,

2 500

0.57

60

Zircaloy 4 + 0,

260

0.8

17

-

2 900 1 300

loo0

-

0.95 0.6

IMI 679

Eutectic Eutectoid; main commercial alloy, i.e. SPZ

REFERENCES TO TABLE 36.1

H. E. Cine and D. Lee, Acta Met., 1970, IS, 315. V. A. Likhachec, M. M. Myshlyaev, S. S. Olevskii and T. N. Chuchman. Acta Met., 1974, 22, 829. G. Piatti. G. Pellegrini and R. Trippodo, J . M a t . Sci., 1976, 11, 186. D. M. Moore and L. R. Morris, Mat. Sci. Eng.;1980, 43. 85. J. R. Cahhoon, Met. Sei., 1975, 9, 346. 6. G. Rai and N. J. Grant. Metall. Trans., 1975, 6A, 385. 7. R. Grimes, M. J. Stowell and B. M. Watts. Met. Technol., 1976, 3, 154. 8. R. Horiuchi, A. B. El-Sebai and M. Otsuka, Scripta Met., 1973. 7 , 1101. 9. S. K. Marya and G. Wyon, J. Phys. (Paris), 1975, 36, (10 Suppl.), c4.309*4.313. 10. R. 1. Kuznetsova and N. N. Zhukov, Phys. Met. Metallography. 1977. 44 (6), 134. 11. K. Matsuki and M. Yamada, J. Jap. Inst. Met., 1973, 37, 448. 12. R. H. Bricknell and J. W. Edington, Metall. Trans., 1976, 7A, 153. 13. K. Matsuki, Y. Uetani, M. Yamada and Y. Murakami, Met. Sci., 1976, 10, 235. 14. C. R. Heiple, Metall. Trans., 1973, 4, 585. 15. A. M. S. Guthrie, D. E. Newbury and P. M. Hazzledine, Scripta Met., 1972,6,841. 16. C. M. H. Jenkins, J. Inst. Met., 1928. 40,41. 17. H. E. Cline, Trans. Met. Soc. AIME, 1967, 239, 1906. 18. J. R. Stephens, and W. D. Klopp, Trans. Met. Soc. A I M E , 1966, 236, 1637. 1. 2. 3. 4. 5.

364

Superplasticity

19. 20. 21. 22. 23. 24. 25. 26. 27. 28. 29. 30.

D. M. R. Taplin and S. Sagat, Mat. Sci. Eng., 1972,9,53. D. Oelschlaegel and V. Weiss, Trans. Am. SOC Met., 1966.59, 143. M. W. A. Bright and D. M. R. Taplin, Copper Dev. Assn Pubn, 061/2, 1972. R. G. Fleck and C. J. Beevers and D. M. R. Taplin, J. Mat. Sn'., 1974,9, 1737. R. Pearce and C. J. Swanson, Sheet Metal 2nd.. 1970,4?, 599. G. Herriot, M. Suery and B. Baudelet, Scripta Mer., 1972, 6, 657. J. W. Edington. K. N. Melton and C. P. Cutler, Prog. Mat Sei., 1976, 21, 61. R. J. Prematta, P. S. Venkatesan and A. Pense, Met. Trans., 1976, 7A, 1235. M. Suery and B. Baudelet, J . Mat. Sci., 1973, 8, 363. P. Griffiths and C. Hammond, Acta Met., 1972, 20, 935. R. D. Schelleng and G. H. Reynolds, Met. Trans., 1973, 4, 2199. C. Dasarathy, 2. Metallk., 1971, 62, 612. 31. D. Lee and E. W. Hart. Mer. Trans., 1971, 2, 1245. 32. Yu, V. Gusev, Tekhnol. Legk. Splauou, 1978 (l), 9. 33. A. Karim and W. A. Backofen, Mat. Sei. Eng., 1968-69, 3, 306. 34. D. A. Woodford, J. Inst. Metals, 1968, 96, 371. 35. 0. A. Kaibyshev and A. A. Markelov, Phys. Mer. Metallog., 1976, 41 (l), 165. 36. I. V. Doronin, Fiz. Khim. Obrub. Mat., 1976 (6), 147. 37. D. Lee and W. A. Backofen, Trans. Met. Soc. AIME, 1967, 239, 1034. 38. H. W. Hayden and J. H.Brophy, Trans. Am. Soc. Met., 1968,61, 542. 39. D. A. Woodford, Met. Trans., 1976, IA, 1244. 40. T. H. Alden, Trans. Am. SOC. Met., 1968,61, 559. 41. S. Srinivasa Rao, 0. Sivakesavan, S. H. Ghude and R. V. Tamhankar, Trans. Ind. Inst. Met., 1970,23 (4), 44. 42. J. C. Wei and W. D. Nix, Scripta Met., 1979, 13, 1017. 43. J. Gryziecki and J. Jarominek, Rudy Met. Niezelaz, 1975, 20 (6), 316. 44. H. E. Cline and T. H. Alden, Trans. Met. Soc. AIME, 1967, 239, 710. 45. R. C. Gikins, J . Inst. Met., 1967, 95, 373. 46. M. A. Clark and T. H. Alden, Acta Met., 1973, 21, 1195. 47. T. H. Alden, Acta Met., 1967, 15, 469. 48. V. S. Darekar and R. D. Chaudhari, Trans. Ind. Inst. Mer., 1970, 23 (3), 56. 49. M. D. C. Moles and G. J. Davies, Met. Sci., 1976, 10, 314. 50. S. B. Agarwal and M. L. Vaidya, Scripta Met., 1975, 9, 447. 51. G. R. Edwards, J. C. Shyne and 0. D. Sherby, Met. Trans., 1971, 2, 2955. 5 2 R. C. Cook and N. R. Risebrough, Scripta Met., 1968, 2, 487. 53. J. C. Marshall, T. J. Stewart and T. C. Babcock, Met. Eng. Quart., 1973, 13 (4), 12 54. T. H. Alden and H. W. Schadler, Trans. Met. Soc. AIME, 1968,242,825. 55. K. N. Melton and J. W. Edington, Scripta Met., 1975, 9, 559. 56. H. Naziri and R. Pearce, Int. J. Mech. Sci., 1970, 12, 513. 57. K. Nuttall, J . Inst. Met., 1973, 101, 329. 58. J. D. Lee and P . Niessen, J. Mar. Sci., 1974, 9, 1467. 59. K. Nuttall, Scripta Met., 1976, 10, 835. 60. A. M. Garde, H.-M. Chung and T. F. Kaussner, Acta Met., 1978, 26, 153. 61. C. Gandhi, C. Bampton, A. K. Ghosh and C. E. Anton, 51h Inlernational AI-Li Conference, Williamsburg, Virginia, March 27-31, 1989 (ed. T. H. Sanders and E. A. Starke), Materials and Component Engineering Publications Ltd, UK,pp. 141-150. 62. R. Amich and N. Ridley, Ibid., pp. 159-167. 63. R. A. Ricks and N. C. Parson, Ibid., pp. 169-178. 64. E. Y. Ting, B. Ward and T. Williams, Ibid., pp. 189-199. 65. J. Pilling, Scripta Metall. 1989, 23, 1375. 66. G.A. Nassef, M. Suery and A. El-Ashram, Metals Tech., 1982, 9, 355. 67. Dong Hyuk Shin, J . Mal. Sci. Letrers, 1989, 8, 1412. 68. Dong Hyuk Shin and Sun Chae Maeng, J. Mar. Sci. Letters, 1989,8,1380. 69. G. Piatti, J. Mat. Sci., 1983, 18, 2471. 70. P. Metenier er al., Mat. Sei. mdEng., 1990, A125, 195. 71. S. J. Hales, T. R. McNelIey and I. G.Munro, Scripta Mer., 1989, 23, 967.

Table 36.2

IRON AND STEEL SYSTEMS SHOWING SUPERPLASTTCITY

Alloy system

Maximum Temperature elongation range "C

m

References

Remarks

Cast iron Fe-2.13C-1.41 Mn Fe-2.36C-1.48Mn

650 650

526 29 1

0.5 0.5

1 1

White White

827

-

0.9

2

C. steels

Fe-O.lC

Superplasticity

36-5

Table 36.2 IRON AND STEEL SYSTEMSSHOWING SUPERPLASTICITY-lcontinued

Maximum Alloy system

Temperature elongation % range"C

Fe-O.4C Fe-0.9C Fe-0.8C Fe-1.3C Fe-1.3C Fe-1.6C Fe-!.6C Fe-1.9C Fe-1.9C

827 loo0 750-860 540-650 630 540-650 630 540-650 650

Alloy sfeels Fe-0.3C-2Al Fe-0.34C-2AM.47Mn Fe-l.W-1.5Cr Fe0.14C-1.93Mn FeO.44C-2Mn Fe-2C-30Mn Fe-C-Mn steels+ V, Nb, AI and Ti

1040 900-950 650 727-800 700-800 770-950 800-1 OOO

[email protected] 1000 Fe-O.15C-1.2Mn-0.04Nb Fe-O.15C-I .3Mn-0.3Si Fe-0.2C-0.6Mn-0.2Si-lCr Fe-0.3C-0.6Mn-0.2Si-lCr

790 780 770 740 Fe-00.2C-0.8Mn-0.3Si-1Cr 760 Fe-O.9C-1.2Mn-0.5Cr-0.5W-0.5V 650 FA.75C-0.3Mn-1.3CP 650 Fe-1.2C-0.3Mn 700 800 Fe-lG1.5Si-32Mn-llAl Fe-0.07C-0.91 M11-0.5P-0.1v 800-950 Fe-0.14C-1.16Mn-0.5P-O.lIV 800-950 Fe-0.16C-l.54Mn-1.98P-0.13V 900 Fe-0.18C-1.54Mn-0.9P-O.llV 900 Fe-0.42C-1.87Mn-0.24Si 727 Fe-0.91C-0.45Mn-0.12Si 710-915 Fe-O.13C-l.llMn-O.IlV 700-900 Fe-0.03-0.1C-3.9Ni-3M1o-1.58Ti850-1 000 Fe-0.01C-6.4Ni4l.35Nb 700-800 Fe-0.2C-3.1Ni-0.29Nb 700-800 Fe-0.12C-1.97Si 800-950 Fe-l.5Cr-lP 800

Stainless steeis Fe-13Cr-16Mn Fe-C-1213r-lONi

m

References

>300

0.6

100 500 700 500 760 500 380

0.35 0.4

2 16 3 4 16 4 16 4 16

372 1220

-

460 250 184 184 738 640 600 500 845 1200 840 780 > 500 169 270 376 320 460 142 310 820

-

150 400

-

-

0.45

0.5

0.37 0.48

-

0.6 0.8

-

0.7

-

I

0.31 0.57 0.55 0.55 0.65 0.42 0.45 0.67 0.4 0.56 0.26

5 6 7 2 2 8 9

16 16 16 16 16 16 16 16 16 16 6 6 6 6 2

-

6 11 12 12 6 16

-

228

-

16 13

Fe-C-12Cr-lONi+Ti+Al

9W50

-

-

13

Fe-C-13Cr-INi

900-950

-

-

13

990-1 020 lo00 800 921 927 982 982 982 982 982 982 982 982 982

195 270 527 500 200 460 260 160 520 >lo00 480 >740

0.3-0.5

Fe-0.08C-20Cr-9Ni-7Mn Fe20Cr-lONi-0.7N Fe-2OCr-lONi4.7N Fe-25Cr-6.5Ni-0.6Ti Fe-30Cr-S.ONi-0.6Ti Fc34Cr-lONi-0.6Ti Fe-28Cr- 19Ni-0.6Ti Fe-28Cr-22Ni-0.6Ti Fe-36Cr-26Ni-0.6Ti Fe4lCr-22.5Ni-0.6Ti Fe-46Cr-16Ni-0.6Ti Fe-43Cr-33Ni-0.6Ti Fe-55Cr-35N1-0.6Ti . Fe-39Cr-52Ni-0.6Ti

+Ti

400

740

-

-

-

At 2.5 x At 1.3 x IOW4 At 1.3 x At 1.7 x loW4

AISI 52160 AIS1 340

At 1.7 x At 1.7 x At 1.7 x At 1.7 x At 1.7 x At 1.7 x At 1.6 x At 2.5 x At 0.7 x lo-& At 0.7x

AISI 1340

10

750 900-950

+Ti

Remarks

14 16 16 16 16 16 16 16 16 16 16 16 16 16

At -lo-'' At 0.4 x Martensitic Russian Khl2Ni 1OT Martensitic Russian Khl2NilOTYu Martensitic Russian OKh13N7 Russian 08Kh20N9G7T At 0.8 x At 0.8 x At 2.6 x At 2.6 x At 2.6 x At 2.6 x lod3 At 2.6 x ~t 2.6x 10-3 At 2.6 x At 2.6 x At 2.6 x At 2.6 x lo-' At 2.6 x

36-6

Superplasticity

Table 36.2 IRON AND STEEL SYSTEMS SHOWING SUPERPLASTICIlYJC~tlmcod Maximum Temperature elongation % range "C

Alloy system

982 982 927 871 960 950 1050 1000 1000 950 1 000 700-1 020

m

>loo0 720 600 300 1050 2 500 >2000 >3000 765 750 >loo0 >loo0

Rgterences

Remarks

16 16 16 16 16 16

At 2.6 x At 2.6 x At 4.4 x At 4.4 x At 3.2 x lop4 At 2 x

16 16 16 16 15

At 4 x At 2 x IO+ At 8 x IN 744

Table 363 POWDERED MATERIAL SYSTEMS SHOWING SUPERPLASTW'N Maximum Temperature elongation range "C %

Alloy system Al-4.89Mg-1.19Cr Fe-3C-1.50 Fe3C Fe2.4C Fe-23 ACr-5Ni-l.5Mc-1

482-520 700 700 700 Cu-O.15N 1 070

Fe-26Cr6.5Ni-3Md.llN Fe-21AI-4B Fe-5OCu

950

871 800 Ni-0.125C-6Al-6Cr4Mc-2.5Nb- 980 8Ta4W ~-0.15C-18.5Co-15Cr-4.2A1- 1020 5.2Mo-3.5Ti Ni-5.4A1-0.015B-0.14C-7.5Co- 1090 6Cr-2Mc-OSNb-9Ta-lTi-6WHf-Re-Zr Ni-5.5-6.5A1-1.8-2.8Nfj12-14Cr1090 3.8-5.2Mo up to 2.5Fe-0.5-1Ti

References

Remarks

>lo00 1410 940 480 500

18 16 16 16 16

>lo00

16

Optimum520'Cat 1 . 6 ~ 1 0 - ~ At 1.7 x At 1.7 x lod4 At 1 . 7 ~ RS ribbonhot At 2 x ext. RS ribbonhot At 1.7 x ext.

281

16 16 17

At NASA-TAaa

17

u700

> 300

17

NASA-TRW-VIA

230

17

IN 713

300 >600 1 000

0.42

REFERENCES TO TABLES 36.2 AND 36.3 IRON AND STEEL

J. Wadsworth, L. E. Eiselstein and 0. D. Sherby, Materials Eng. Appl., 1979, 1 (3), 143. R. W. Schadler, Trans. Met. SOC. AIME, 1968, 242, 1281. A. R. Marder. Trans. Met. SOC.AIME, 1969, 245, 1337. 0. D. Sherby, B. Walser, C. M. Young and E. M. Cady, Scripta Met., 1975, 9, 569. E. Snape and N. L. Church, J. Metals, 1972, 24 (I), 23. W. B. Morrison, Trans. Am. Soc. Met., 1968, 61, 423. J. Wadsworth and 0. D. Sherby. J. Mat. Sci., 1978. 13, 2645. S. I. Bulat and A. L. Molochnikova, Mer. Sci Heat Treat., 1979,21 (a), 420. M. J. Stewart, Met. Trans., 1976,7A, 399. 10. G. R. Yoder and V. Weiss, Met. Trans, 1972,3,675. 11. C. W. Humphries and N. Ridley, J. Mat. Sci., 1974, 9,1429. 12. T. Hirano, M. Yamaguchi, and T. Yamane, Met. Trans., 1974,5. 1245. 1. 2. 3. 4. 5. 6. 7. 8. 9.

Superplasticity 13. 14. 15. 16.

I. N. Bogachev, L. I. Lspekhina and A. A. Kovaleva, Phys. Met. Metallog., 1977, 44 (6), 138. Ya. M. Okrimenko, Nauchn. Trud. Moskov. Inst. Stali Splavov, 1976 (94), 75. H. Hildebrand, 6.Michalzik and B. Simmon, Met. Tech., 1977. 4, 32. Y . Maehara and T. G. Langdon, Mar. Sei. and Eng., 1990. A l a , 1.

COMPACTED METAL POWDERS 17. J. W. Edington, K. N. Melton and C. P. Cutler, Prog. Mat. Sro., 1976, 21.61. 18. Dong Hyuk Shin, J. Mat. Sci. Letters, 1989, 8, 1412.

36-7

37 Metal-matrix composites Metal-matrix composites are engineered materials comprising reinforceants of high elastic modulus and high strength in a matrix of a more ductile and tougher metal of lower elastic modulus and strength. The metal-matrix composite has a better combination of prope~esthan can be achieved by either component material by itself. The objective of adding the reinforceant is to transfer the load from the matrix to the reinforceant so that the strength and elastic modulus of the composite are increased in proportion to the strength, modulus and volume fraction of the added material. The reinforcement can take one of several forms. The least expensive and most readily available on the market are the particulates. These can be round but are usually irregular particles of ceramics, of which Sic and A1203 are most frequently used. Composites reinforced by particulates are isotropic in properties but do not make best use of the reinforceant. Fine fibres are much more effective though usually more costly to use. Most effective in load transfer are long parallel continuous fibres. Somewhat less effective are short parallel fibres. Long fibres give high axial strength and stiffness, low coefficients of thermal expansion and, in appropriate matrices, high creep strength. These properties are very anisotropic and thecomposites can be weak and brittle in directions normal to that of the fibres. Where high two-dimensional properties are needed, cross-ply or interwoven fibres can be used. Short or long randomly oriented fibres provide lower efficiencies in strengthening(but are still more effective than.particulates). These are most frequently available as Sic whiskers or as short random alumina (‘Saffil’) fibres or alumino-silicatematts. Long continuous fibres include drawn metallic wires, mono-filaments depositedby CVD or multifilaments made by pyrolysis of polymers. The properties of some typical fibres are compared in Table 37.1. The relative prices are given as a very approximate guide. Because most composites are engineered materials, the matrix and the reinforceant are not in thermodynamic equilibrium and so at a high enough temperature, reaction will occur between them which can degrade the properties of the.fibre in particular and reduce smngth and more especially fatigue resistance. As many composites are manufactured by infiltration of the liquid metal matrix into the pack of fibres, reaction may occur at this stage. Some typical examples of interaction 8re listed in Table 37.2. In order to obtain load transfer in service, it is essential to ensure that the reinforceant is fully wetted by the matrix during manufacture. In many cases,this requires that the fibre is coated with a thin interlayer which is compatible with both fibre and matrix. In many cases, this also has the advantage of preventing deleterious interdiffusion between the two component materials. The data on most coatings are proprietary knowledge. However, it is well known that silicon carbide is used as an interlayer on boron and on carbon fibres to aid wetting by aluminium alloys. The routes for manufacturing composites are still being developed but the most successful and lowest cost so far is by mixing particulates in molten metal and casting to either foundry imgot or as billets for extrusion or rolling. This is applied commercially to aluminium alloy composites. Anotha practicable route is co-spraying in which Sic particles are injected into an atomized stream of aluminium alloy and both are collected on a substrate as a co-deposited billet which can then be processed conventionally. This is a development of the Osprey process and can be applied more widely to aluminium and other alloys. Other routes involve the infiltration of molten metal into fibre pre-forms of the required shape often contained within a mould to ensure the correct final shape. ’ K i s can be done by squeeze casting or by inliltrating semi-solid alloys to minimize interaction between the fibre and metal. Fibres can also be drawn through a melt to coat them and then be consolidated by hot-pressing. To reduce interaction, solid state methods can be used, e.g. cold isostatic pressing (CP)and 37- 1

Y N

n

Table 37.1 PROPERTlES OF REINFORCING FIBRES AT ROOM TEMPERATURE (BASED ON REFERENCE 9) Fracture stress MPa

Elastic modulus GPa

400

3

2.6 3.2 3.9 3.5 2.0 1.9 3.0

2500 2500 3500 3800 2500 10000 1500 2000 3000 4200 850

Diameter pm

Density gm-3

10-500 10-250 150 1so 10-15 0.1-2.0 15-25 2-4 10

19.2

Fibre

Form

Preparation route

Tungsten Steel Boron Sic Sic Sic -A1,0, A1,03 C(high modulus) C(med. strength) Alumino-silicate Glass(27% SiO,) Alumino-silicate Glass(47% SO,) S-Glass

Wire Wire Cont. mono-filament Cant. mono-filament Cont. multi-filament Whisker (random, short) Multi-filament Random short fibres Cont. multi-filament Cont. multi-filament Random short fibres

Drawn Drawn Chemical vapour depos. Chemical vapour depos. Polymer fibre pyrolysis Polymer fibre pyrolysis Oxide/salt fibre pyrolysis Polymer fibre pyrolysis Polymer fibre pyrolysis Polymer fibre pyrolysis

Random short fibres

Drawn from melt

3

2.7

Cont. multi-filament

Drawn from melt

3-20

2.5

N

8

7.8 2.6 3.4

210 400 450 200

700 380 300 600

Coegicient of tliermal expansion K-' x lo6 5.0 15.0 8.0 4.5 4.5 4.5

7.0 7.0

Price relutiue to glassfibre 1000-50 30-1 250 500 100 150 100 25

0 0

lo00

150

-

100 20

1750

105

-

1

4OOo

90

300

3.0

P B. 5

m

2.5

Metal-matrix composites

37-3

Table 37.2 TYPICAL INTERACTIONS IN SOME FIBRE-MATRIX SYSTEMS Temperature System

Potential interaction

of signpicant interaction "C

AI-C

Formation of AI,C, at interface. Degradation of C fibre properties.

550 -495

Al-AlZQ,

No significant reaction at normal fabrication temperatures

Al-oxide (AI,O,-Si0,-B,O,)

B,O, reacts with AI to form borides.

770

10

AI-B

Boride formation: interlayer of Sic needed.

500

9

References 9 9

Al/LMl,O,

Interfacial layer of LiAl,O, on liquid infiltration.

-

650

13

AI-Sic

No significant reaction below melting point. AI,C, and Si can form in liquid Ai.

m.p. 660 > 700

9 12

Al-steel

Formation of iron aluminides.

500

9

C-TaC

Directionally solidified eutectic; dissolution and re-precipitation.

1200

9

cu-w

No interaction up to melting point.

1083

9

Fe-W

Formation of Fe,W6: dissolution of fibre.

1000

9

Mg(AZ9 1FC

No significant reaction at m.p. of alloy provided 0 and N avoided during infiltration.

Ni-AI,O,

Slight reaction to pit fibre. NiAI,O, spinel forms in air.

1100 1100

NiC(1)

Ni activates recrystallization of fibre.

1150-1300

Ni-(11) Ni-Sic

Ni activates recrystallization of fibre. Formation of nickel silicides. Recrystallization of fibre. Degradation of creep properties.

Ni-W Ti-B Ti-Sic

Formation of TiB,. Formation of Tic, TiSi, and Ti&.

11,14 9

800 800

lo00 900 750

9

700

9

sinteringor hot isostaticpressing (HIP) of metal powders mixed with short fibres. Diffusion-bonding laminates of layers of fibres and metal foil is also effective. The properties which can be achieved in composites include higher strength, higher stiffness, improved high-temperature properties, lower or matched coefficients of thermal expansion and improved wear resistance. This is usually at the expense of conventional ductility but in most cases improved fracture toughness can be obtained. The following tables illustratewhat has been achieved in aluminium, magnesium, titanium and zinc alloys. The improvement in strength is often larger in the weaker alloys with less benefit being realized in the stronger alloys, e.g. see Table 37.3. All alloys show an improvement in elastic modulus when reinforced.

Y

A

Table 37.3 MECHANICAL PROPERTIES OF ALUMINIUM ALLOY COMPOSITES AT ROOM TEMPERATURE

Base Alloy

Nominal composition

606 1

Mg Si cu Cr

2014A

1.0 0.6 0.2 0.25

c u 4.4

Form

Heat treatment

% particulate

0.2% proof stress MPa

Extrusion

T6

Nil 10% A1,0, 15% A1,0, 20% AI,O, 13% Sic 20% Sic 30% Sic

276 297 317 359 317 440 570

Nil 10% A1,0, 15% A1,0, 20% A1,0, 10% SIC

414 483 476 483 457

Extrusion

T6

Mg 0.7 Si 0.8 Mn 0.75

Tensile stress MPa

Elongation %

Elastic modulus GPa

Fracture toughness MPam-’”

3 10 338 359 379 356 585 795

20.0 7.6 5.4 2.1 4.9 4.0 2.0

69.9 81.4 87.6 98.6 89.5 120.0 140.0

29.7 24.1 22 21.5 17.9

483 517 503 503 508

13.0 3.3 2.3 0.9 1.8

73.1 84.1 91.7 101.4 91.2

Sheet

T6

8.2% Sic

448

516

4.5

82.5

2219

Cu 6.0 Mn 0.3 v 0.1

Extrusion

T6

Nil 15% A1,0, 20% A1,0,

290 359 359

414 428 421

10.0 3.8 3.1

73.1 88.3 91.7

2618

cu Mg Si Fe Ni

T6 T6 T6

-10% Sic Nil 13% Sic

396 320 333

468 400 450

3.3 -

0.9 0.9 1.0

Sheet Extrusion Extrusion

6.0

93.6 75.0 89.0

Zn Mg Cu Cr Li Cu Mg Zr

5.6 2.2 1.5 0.2 2.5 1.3 0.95 0.1

Extrusion

T6

Nil 12% Sic

617 597

659 646

11.3 2.6

71.1 92.2

Extrusion (18mm)

T6 T6

Nil 12% Sic

480 486

550 529

5.0 2.6

79.5 100.1

7075

8090

2.0 1.5

-

25.3 18.0 18.8

% 2

E

Density

gem-,

References

2.71 2.81 2.86 2.94

1,2 1,2

-

-

2.80 2.92 2.97 2.98

17.7

-

6 6 1,6 1,6

I

2

$

-

Table 37.4 MECHANICAL PROPERTIES OF ALUMINIUM ALLOY COMPOSITES AT ELEVATED TEMPERATURES Base Alloy

Nominal composition

6061

Mg Si cu Cr

cu Mg Si Mn

2014A

Form

Heur treatment

% purticulure

1.0 0.6 0.2 0.25

Extrusion

T6

15% A1,0, 15% A1,03 15% A1,03 15% A1,03 15% A1,03 15% A1,0, 15% A1,0,

4.4 0.7

Extrusion

15% A&O, 15% A1,03 15% A1,0, 15% A1,03 15% A1,03 15% A1,03 15% A1,0,

T6

0.8 0.75

0.2%

Tensile

proof stress MPa

strength MPa

References

204 260 316 371

317 290 269 241 172 110 62

359 331 303 262 179 117 69

1 1 1 1 1 1 1

22 93 150 204 260 316 371

476 (413) 455 (393) 407 (352) 317 (283) 200 (1 59) 103(62) 55 (35)

503 (483) 490 (434) 434 (379) 338 (310) 214(172) llO(76) 55(41)

1 1 1 1 1

Temprutitre "C 22 93 150

1 1

Figures in parentheses are for basic alloy without particulate.

Table 37.5 MECHANICAL PROPERTIES OF MAGNESIUM ALLOY COMPOSITES AT ROOM TEMPERATURE

Base Alloy

0.2% proof

Nomind composition

Form

reinforcement

stress MPa

Mg-5.5Zn-0.5Zr

Extruded rod

Nil 15% SiC(partic.) 20% SiC(partic.) 15% SiC(whisker) 20% B,C(partic.)

260 330 370 450 405

%

Tensile strength MPa

Elongation %

Elustic modulus GPa

R References

~

ZK60A

MG-l2Li

Squeeze infiltration Squeeze infiltration Squeeze infiltration

Extruded rod Extruded rod

Nil 12% Al,O,(fibre) 24% Al;Oj(fibre) Nil 20% SiC(whisker)

325 420 455 570 490 80 200 280 15

338

15.0 4.7 3.9 2.0 2.0 8.0 3.5 2.0 10.0 0.8

44

68 74 83 83 -

45 112

5 5 5 5 5 7 7 7 7 7

3 4w

j;.

n a

3

T (

12.

5

? VI

Table 37.6 MECHANICAL PROPERTIES OF TITANIUM ALLOY COMPOSITES Base Alloy

YO Form

particulate ~

TidAI4V

~~~

~

10% T i c 10%TIC 10% Tic 10% T i c 10% B,C

Forging

~~~

Temperature “C

~

Figures in pawtheses are for basic alloy without particulate.

0.2% proof stress MPa

Tensile strength MPa

800 476 (393) 414 (359) 369 (221)

806 524(510) 455 (441) 317(310) 1055 (890)

Elongation %

Elastic modulus GPa

References

~~

21 427 538 649 21

-

1.13 1.70(1 1.6) 2.40 (8.5) 2.90 (4.2)

-

106-120 __

205

4 4 4 4 5

Metal-matrix composites

37-7

Table 37.7 MECHANICAL PROPERTIES OF ZINC ALLOY COMPOSITES AT ROOM TEMPERATUE

ZA-12

Elongation

Elastic modulus

Zn-I2%Al

Form

MPa

%

GPa

Nil Nil 10% Sic 20% Sic Nil 20% A1,0,

300 350 323 373 313 532

5 22

87

8

115

0

119

8 8

0

129 102 120

8

73 92

8 8 8 8

composition

Ascast As rolled

Nil

410 396 330 310 393 370 349 340 382 466 3 14 382

Extruded ZA-27

Tensile strength

Nominal

Base ANoy

Zn-27%AI

As cast

10% Sic 20% Sic 50% Sic

As rolled Extruded

Nil 10% S i c 20% Sic Nil 12% Sic 16% Sic Nil 20% A1,0,

2

0 0 0 16 3

110 220 85

0

102

-

89 83 105 130 78 100

Refmences

8 8

8 8

8 8 8 8 8 8

References 1. Private communication, Alcan Aerospace, 1989. 2. C. Baker, Alcan International, 1990. 3. F. H. Froes, Materials Edge. May/June, 1989, 17. 4. S. Abkowitz and P. Weihrauch, Adc. Mat. and Proc., 1989 (7), 31. 5. F. H. Froes and J. Wadsworth, BNF 7th Int. Conf., 1990. Paper 1. 6. J. White et a[., in ‘Adv. Mat. Tech. Int.’. ed. G. B. Brook, publ. Sterling Publ. Ltd, 1990. 96. 7. J. F. Mason et al., J . Mat.Sci., 1989, 24, 3934. 8. J. A. Cornie et al., ASM Conf. on Cast Metal Matrix Composites, Chicago, Sept. 1988. 155.

9. R. Warren, in ‘Adv. Mat. Tech. Int.’, ed. G. B. Brook, Publ. Sterling Publ. Ltd. 1990, 1KJ. 10. J. Yang and D.D. L. Chung. J. Mar. Sci., 1989. 24, 3605. 11. T. Iseki, T. Kameda and T. Maruyama, J. Mal. Sci.. 1984,19, 1692 12. S. P.Rawal. L. F. Allard and M. S. Misra. in ‘Interfaces in Metal- Matrix Composites’, Proc. Symp. AIME, New Orleans, March, 1986 (ed. A. K. Dhinga and S. G. Fishman), 211. 13. A. R. Champion et al., Proc. Int. Conf. on Composite Mat., AIME, ICCM, 1978. 883. 14. M. H. Richman, A. P. Levitt and E. S . DiCesare, Metallography, 1973, 6. 497.

Index

Alkaline oxidation processes, 32-25 Alloy steels heat treatment, 29-16, 29-17 Alloying with lasers, 30-13 Alnico alloys, 20-7 Alumina composites, 37-2 to 37-5,37-7 Aluminium alloy composites, 374437-5 Aluminium alloys: cast, high strength, 26-30, 26-31 creep properties, 22-22 to 22-24 colour etches, 10-19 designation, 22-1, 22-2 elevated temperature properties, 22-16 to 22-20

fatigue strengths, 22-24 to 22-26 fluxing and inoculation, 26-16 hardness value conversions, 21-5,216 heat treatment, 2P-17 to 29-19 KISCC values, 31-12 low temperature properties, 22-20 to 22-22 mechanical properties, 22-3 to 22-15 mechanically alloyed, 23-13 metallography, 10-22 to 10-27 physical properties, 14-14 to 14-16 soldering, 3 4 4 superplasticity, 36-1 temper designation, 22-2,29-19,29-20 Aluminium bronze welding, 33-3 1 Aluminium casting alloys, 26-20 to 26-29 Aluminium: castings, welding, 33-28 electrical resistivity, 14-1, 19-1 fusion welding, 33-27 ore, 7-2 physical properties, 14-1, 14-3, 14-7, 14-10, 14-14

pickling, 32-3 plating, 32-9 related specifications, 1-7 resistance welding, 33-6 spot welding, 33-6 welding dissimilar alloys, 33-28, 33-30 Aluminizing steels, 29-16 American specifications, 1-1 to 1-9 Amorphous alloys, 20-16 Anelastic damping, 15-10 to 15-31 Annealing aluminium alloys, 29-17

Anodizing and plating processes, 32-7 to 32-8 Antimony: metallography, 10-28 ores, 7-2 physical properties, 14-1, 14-3, 14-8, 14-12 plating, 32-9 Arsenic: ores, 7-2 physical properties, 14-1, 34-7, 14-10 Atomic and ionic radii, 441, 4 4 2 Atomic weights and numbers, 3-1 Auger emission, 18-7 Austenite retained in steel, 4-17, 4-18 Autocatalytic plating, 32-19 Barium, physical properties, 14-1, 14-7,14-10 Bearing alloys, mechanical properties, 22-162 to 22-164 Bearing bronzes, 2634,2633 Bearing metals, metallography, 10-60,10-6? Bearings, oil containin,g 23-13 Becquerel, 2-2 unit of radiation activity, 4-47 Beryllium: metallography, 10-28, 10-29 ores, 7-2 physical properties, 14-1,143, 14-7,1410 superplasticity, 36-2 Binary diagrams, 11-7 to 11485 acknowledgements, 11-486 index, 11-1 to 11-6 Bismuth: metallography, 10-28 ore, 7-2 physical properties, 141,143, 14-7,14-10 Bismuth alloys, superplasticity, 36-2 Blast furnace operation, 28-26 Blueing steels, 29-16 Boiling point elements, 8-1 to 8-3 Borides: heat capacities, 8-45 heats of formation and entropies, 8-22 Brass: annealing, 29-21 castings compositions and properties, 26-36 1-1

1-2

Index

Brass (cont.), fluxing and inoculation, 26-1 8 hardness value conversions, 21-6 high tensile, 2637,2638 physical properties, 14-17 plating, 32-9 welding, 33-6, 33-34 Brazability, 34-14 Brazing, 34-9 to 34-21 alloy systems BS1723, 34-15 bibliography, 34-14 British Standards, 34-2 definition, 34-1 electric resistance, 34-13 filler compositions and meltingpoints, 34-16 furnace, 34-12 induction, 34-13 joint clearances, 34-10 joint design, 34-9 parent/filler combinations, 34-17 to 34-21 positioning of fillers, 34-12 precleaning, 34-12 salt bath, 34-13 torch, 34-12 vacuum, 34-21 Brinell hardness, 21-1 Bronze: fluxing and inoculation, 26-18 imitation plating, 32-9 plating, 32-10 welding, 33-33 BTU conversions, 2-1 Carburizing steels, 29-12, 29-13 Cadmium: alloys, superplasticity, 36-2 metallography, 10-29 ore, 7-2 physical properties, 14-1, 14-3, 14-7, 14-10 plate, soldering fluxes, 34-4 plating, 32-10 Caesium,physicalproperties,14-1,14-7,1411 Calcium, physical properties, 14-1,14-7,14-10 Calculus, 2-23 Calorific value, 2-4 fuels, 28-3 liquid fuels, 28-18 Carbide composites, relative wear, 25-18 Carbides: chemical vapour deposition, 35-12 heat capacities, 8 4 6 I S 0 classification, 23-32, 23-33 physical vapour deposition, 35-1 1 thermochemical data, 8-23 Carbon dioxide process moulding, 26-5 Carbon equivalent: cast irons, 26-74 welding formulae, 33-17 Carbon fibre composites, 37-2,37-3 Case hardening, 29-8 to 29-10 of sintered steel, 23-14

Cast iron: alloy, 26-88 austenitic, 26-87 carbon equivalent, 26-74 chilling tendency, 26-75, 26-76 classification and properties, 2674,2675, 2689 colour etches, 10-19 compacted graphite, 26-83 to 26-86 corrosion resistant, 26-89 to 26-91 fluidity/density/hardness, 26-79 fluxing and innoculation, 26-18 grey, typical analyses, 26-74 heat treatments, 29-17 losses of alloying elements, 26-78 magnetic properties, 20-5 metallography, 10-36 to 1041 non-magnetic, 20-18 to 20-20 relative wear rates, 25-16 scrap compositions, 26-77 soldering fluxes, 34-4 special purpose, 26-89 to 26-91 standard test pieces, 21-9, 21-10 structural effects of alloying, 26-78 superplasticity, 36-4, 36-5 thickness effect, 26-75 welding, 33-27 Casting techniques, 26-1 Cavitation, 31-6 Cements, aluminous, 27-7 Centrifugal cast tubes, 26-69 Centrifugal casting, 26-3 Ceramic coating, 32-19 Ceramic mould casting, 26-2 Ceramics: castable/mouldable/ramming/gunning, 27-12,27-13 properties, 27-1 pure, properties, 27-1 to 27-6 relative wear rates, 25-17 Cerium: ores, 7-3 physical properties, 14-1, 14-7,1610 Cerium-hydrogen system, 12-8 Charpy test pieces, 21-11,21-12 Chemical vapour deposition, 3 5 2 , 3 5 4 to 35-9 applications, 3 5 4 , 3 5 5 carbides, 35-12 elements, 354 to 35-7 nitrides, 35-10, 35-11 processes, 3 5 2 , 3 5 4 references, 35-6, 35-7 Chromating, 32-23 Chrome-constantan thermocouple tables, 16-7 Chromel-alumel thermocouple tables, 16-8 Chromium: metallography, 10-29, 10-30 ores, 7-3 physical properties, I k f , 14-3,147, 14-10 plating, 32-10 Chromium alloys, superplasticity, 36-2

Index

Chromizing steels, 2 F 1 6 Cladding with lasers, 30-13 Coal: analysis, 28-1 classification,28-5 Coating processes, 32-19 Cobalt: metallography, 10-30 ores, 1-3 physical properties, 14-1, 14-3, 14-7, 14-10 Cobalt alloys: heat treatment, 29-24 superplasticity,36-2 Coercivity magnetic definition, 20-22 Cok-: analysis, 28-9 blast furnace, 28-13 formed, 28-14 foundry, 28-13 metallurgical, 28-12 Colouring of metals, 32-23 Compacted graphite irons, 2 6 8 3 to 26-86 Composite materials, 37-1 to 37-7 Continuous casting, 26-3 Controlled atmospheres: fos brazing, 34-13 gases, 29-5 in heat treatment, 29-1 to 29-5 Conversion coating processes, 32-22 Conversion factors, 2-1, 2-4 to 2-8 Co-ordination number elements, 4-41,4-43 Copper: ores, 7-3 physical properties, 14-1,14-3, 14-7,1411 pickling, 3 2 4 plating, 32-1 1 related specifications, 1-8 Copper alloys, 22-26 to 22-27 cast, 26-32 cast mechanical properties, 22-34 compositions, 2 6 3 9 , 2 6 4 1 creep properties, 2 2 4 2 to 2 2 4 7 dezincification,3 1 4 elevated temperature properties, 22-33,22-36 fatigue properties, 22-39 to 2 2 4 1 fluxing and inoculation, 26-18 heat treatment, 29-20,29-21 impact properties, 22-41 KISCC values, 31-10 low temperature properties, 22-37, 22-38 mechanical properties, 22-28 to 22-33 metallography, 10-31 to 10-35 physical properties, 14-16 to 14-18 resistance welding, 33-7 sintered, 23-21 standard specifications,22-26,22-27 superplasticity, 36-2 welding, 33-30 to 33-32 Copper-constantan thermocouple tables, 1 6 8 Copper-nickel : eIectrical resistivity, 19-6 welding, 33-32

1-3

Copper-silver alloys, mechanical properties, 2'2-47, 22-48

Core bonding processes. 26-8 to 26-1 1 Core making materials, 26-4 Corrosion: accelerating factors, 31-2 atmospheric, 31-12 bimetallic, 31-3 contact, 31-13 to 31-15 crevice, 31-5 environments, 31-1 fatigue, 31-7 intercrystalline, 33-22 measurement, 31-2 rates, 31-3 to 31-6 resistant cast irons, 26-89 to 26-91 resistant materials, 31-5 in sea water, 31-6, 31-7 of soldered joints, 34-5 types, 31-5 Coulomb, 2-2 Creep: aluminium alloys, 22-22 to 22-24 copper alloys, 22-42 to 2 2 4 7 magnesium alloys, 22-58 to 22-61 nickel alloys, 22-79 to 22-81 steels, 22-143 to 22-145 titanium alloys, 22-89 Critical fields, superconducting alloys, 19-8 Crucibles, 26-15 Crystal: chemistry, 6-1 to 6-71 geometry, 4-24 to 4-26 glide and fracture planes, 4-36 lattices, 5-2 structure: metals/metalloids/compounds,6-1 to 6-3 5 translation groups, 5-1 symmetry groups, 5-2 Crystallography, 5-1 Curie point, definition, 20-22 Cutting with lasers, 30-7 to 30-9 CVD, see Chemical vapour deposition Damping, anelastic, 15-10 to 15-31 Damping capacity, 15-8, 15-9 magnesium alloys, 14-19 to 14-21 Density: aluminium alloys, 14-1, 14-14, 14-15 ceramics, 27-1 coke, 28-14 copper alloys, 14-16 to 14-18 inorganic compounds, 9-19 magnesium alloys, 14-19 to 14-21 molten salts, 9-1 to 9-18 nickel alloys, 14-22 to 14-24 petroleums, 28-17 pure metals, 14-1, 14-2, 14-7 to 14-10 steels, 14-27 to 14-41 titanium alloys, 14-25

1-4

Index

Density (cont.), units, 2-4 zinc alloys, 14-26 zirconium alloys, 14-26 Die casting, 26-3 Diffusion: arrhenius equation, 13-7 bonding, 33-10 to 33-12 chemical, coefficients, 13-2, 13-70 to 13-102 chemical, diagrams, 13-102 to 13-1 16 homogeneous alloys, 13-40 to 13-70 Matano-Boltzmann method, 13-5 measuring methods, 13-4 to 13-7 mechanisms, 13-7 in metals, 13-1 to 13-119 self, grain boundry, 13-116 to 13-119 self, in solid elements, 13-9 to 13-15 thin layer, 13-3, 13-6 tracer coefficients, 13-3, 13-15 to 1340 Dislocations, etching for, 10-20,10-21 Dissociation pressures: metal oxides, 29-2 phosphides, 8-38 sulphides, 8-39 Drilling with lasers, 30-9 Dysprosium, physical properties, 14-1 Elastic compliances and stiffness - single crystals, 1 5 4 to 15-8 Elastic constants, polycrystalline metals, 15-2 to 1 5 4 Elastic properties, metals, 1 5 1 to 15-8 Electrical conductivity: copper alloys, 14-16 to 14-18 molten salt systems, 9-28 to 9-55 pure molten salts, 9-20 to 9-27 Electrical resistance: international ann. copper standard, 14-18 international copper standard, 14-18 Electrical restivity: alloys, 19-3 to 19-5 aluminium alloys, 14-14 to 14-16 magnesium alloys, 14-19 to 14-21 nickel alloys, 14-22 to 14-24 pure metals, 19-1,19-2 steels, 14-27 to 14-41 titanium alloys, 14-25 Electrochemical potentials, 34-5 Electrodeposits, textures, 4-39 Electron metallography, 10-62 to 10-69 Electron microscopy, 10-69 Electron emission, 18-1 auger, 18-7, 18-8 field, 18-9 secondary, 18-5 to 18-7 Electrophoretic processes, 32-19 Electroplating: non-conducting surfaces, 32-20,32-21 parameters, 18-18 processes, 32-9, to 32-16 Electropolishing, 10-8to 10-13

Electrostatic painting, 32-19 Elements, mechanical properties, 22-159 to 22-161 Elements, vapour pressures, 8-54 Emissivity: definition, 17-1 oxidized metals, 17-11 oxidized spectral metals, 17-9 spectral metals, 17-6 to 17-9 total, metals, 17-10 Energy: conservation, 28-31 heating processes, 28-29 iron making, 28-27 Energy product, magnetic, definition, 20-22 Engraving with lasers, 30-9 Entropy: borides, 8-22 carbides, 8-23 double oxides, 8-35 halides, e29 liquid systems, 8-17 nitrides, 8-23 oxides, 8-25 phosphides, 8-37 selenides and tellurides, 8-12 silicates and carbides, 8-34 silicides, 8-24 sulphides, 8-28 Equilibrium diagrams, 11-7 to 11-485 acknowledgements,11-486 index, 11-1 to 11-6 Erbium, physical properties, 14-1 Erosion resistant materials, 31-5 Etches, macro examination, 10-2 to 10-5,see also Metallography and specific metals Etching for dislocations, 10-20, 10-21 Evaporation coatings, 35-1 Expansions, thermal, in brazing, 34-10,JQ-ll Fatigue data: aluminium alloys, 22-24 to 22-26 copper alloys, 22-39,2240 magnesium alloys, 22-60 to 22-63 nickel alloys, 22-78 to 22-79 steels, 22-140 to 22-142 titanium alloys, 22-70 to 22-73 Ferrites, 20-7, 20-8, 20-14, 20-15 Ferroalloy additions to cast iron, 26-77 Fibre - matrix interactions, 37-3 Fibre reinforced materials, 37-2,37-3 Fick’s Laws, 13-1, 13-6,13-7 Field emission, 18-9 Fixed points of ITS-90temperatures,163,164 Flash points, liquid fuels, 28-19 Fluid sand moulding process, 26-5 Fluxing, 26-15 to 2619 Foundry data, acknowledgements,2691 Fracture toughness: calculations, 21-16 recording results, 21-17

Index Fracture toughness (cont.), under corrosion, 31-10 to 31-12 French specifications, 1-1 to 1-9 Fretting wear, 2515 Friction: boundry, 25-6 definition, 25-1 laws, 251 lubricated, 25-6 static and sliding, 25-2 to 25-5 welding, 33-10,33-11 Fuels: coal, 28-1 coal tar, 28-16 coke, 28-9 energy data, 28-24 flame temperatures, 28-24 gaseous, 28-19 inflammability, 28-23 liquid, 2115 manufactured, 28-22 metallurgical coke, 28-12 non-ferrous melting, 28-28 petroleum, 28-16 solid, analysis, 28-10 Full mould casting, 26-1 Furnaces: ferrous heat treatment, 2%6 non-ferrous heat treatment, 29-7 Gadolinium, physical properties, 14-1,14-11 Gallium: ores, 7-4 physical properties, 14-1,14-7, 14-11 Garnets, 20-15 Gas-metal systems, 12-1 Gaseous fuels, properties, 28-19 German specifications,1-1 to 1-9 Germanium: ores, 7-4 physical properties, 14-1, 14-7, 14-11 Gibbs-Duhem relation, 13-3 Gold: metallography, 10-35,10-36 ores, 7-4 physical properties, 14-1,14-7,14-10 plating, 32-12 soldering fluxes, 34-3 Goldschmidt atomic radii, 4-41 to 4-43 Gravitational constant, 3-2 Gravity die casting, 26-3 Gray unit of absorbed dose, 446 Greases, 24-8 to 24-10 Hafnium: hydrogen solubility, 12-7 ores, 7-4 physical properties, 14-1,14-3,167, 14-1 1 Halides: heat capacities, 8-51 to 8-54

1-5

thermochemical data, 8-29 to 8-34 vapour pressiues, 8-56 to 8 6 3 Hard metals, 23-28 to 23-34 hardness conversions, 21-7 metallography, 10-61,10-62 Hardenability of sintered steel, 23-14 Hardening induction, 29-7 Hardening steels, 29-8,29-9 Hardness: testing, 21-1 to 21-7 value conversions: aluminium alloys, 21-5, 21-6 brass, 21-6 hard metals, 21-7 nickel alloys, 21-7 steels, 21-4, 21-5 HAZ, see Heat affected zone Heat affectedzone, in welding, 33-25 Heat capacities, 8-41 to 8-54 borides, 8-45 carbides, 8-46 intermetallic compounds, 8-43 oxides, 8-48 to 8-50 silicides, 8-47 sulphides-tellurides-selenides,8-50 to 8-5 1 Heat treatment: aluminium castings, 26-20 to 26-29 cast irons, 29-17 cobalt alloys, 29-24 controlled atmospheres, 29-1 to 29-5 copper alloys, 29-20,29-21 equipment, 29-5 to 29-7 furnaces, 29-6,29-7 magnesium alloys, 22-64,29-21 to 29-23 magnesium casting alloys, 26-48 to 26-55 nickel alloys, 29-23,29-24 of sintered steel, 23-14 of steel castings, 26-62 to 26-67 references, 29-24, 29-25 tool steels, 22-156 to 22-158 Heats of formations: binary systems, 8-17 borides, 8-22 carbides, 8-23 double oxides, 8-35 to 8-37 halides, 8-29 to 8-34 nitrides, 8-23 oxides, &25 to 8-27 phosphides, 8-37 to 8-39 silicates and carbonates, 8-34 silicides, 8-24 sulphides, 8-28 Heats of solution, 8-20 Hermann-Mauguin point and space group notation, 5-3 HIP (Hot Isostatic Pressing), 37-3 Holmium, physical properties, 14-1, 14-11 Hybrides, solubility in alkali and alkali earth metals, 12-6 Hydrogen: embrittlement, 31-9 solubility in metals, 12-2 to 12-7

1-6

index

Hydrogen (cont.), solubility in uranium, 12-7 Hydrogen-metal systems, 12-8 to 12-13 Hysteresis, magnetic definition, 20-22 IACS international ann. copper standard, 14-18 Impact testing, 21-10 to 21-12 Indium: metallography, 10-36 ores, 7-5 physical properties, 14-1, 14-7, 14-11 plating, 32-12 Induction melting, 28-7 Injection moulding metals, 23-27 Intermetallic compounds: entropies, 8-9 heat capacities, 8 4 3 heats of formation, 8-9 latent heats of transition, 84 transition temperatures, 84 Intermetallic phases, entropies/free energies and heats of formation, 8-14 to 8-16 Investment casting, 26-1 steels, 26-70 to 2673 Ion cleaning, 35-2 Iron making, materials used, 28-26 Iron: ores, 7-5 physical properties, 14-1,14-4,14-7,14-11 plating, 32-12 Iron-constantan thermocouple tables, 16-7, 16-8 Iron-nickel electrical resistivity, 19-6 Japanese specifications,1-1,l-9 Kelvin unit, 16-1 KISCC values, 31-10 to 31-12 Lanthanum, physical properties, 14-1, 14-7, 14-1 1 Lasers: alloying with, 30-13 beam delivery and focusing, 30-3,'30-4 carbon dioxide, 30-2,304 cladding with, 30-13 cutting and welding, 30-5 to 30-12 metal working, 304 to 3&15 Nd/YAG, 30-2,304 principles, 30-1 processing, 30-4 to 30-7 resonators, 30-2 safety, 30-13, 30-14 Latent heats : elements, 8-1 to 8-3 intermetallic compounds, 8-3.8-4 metallurgically important compounds 8-5 to 8-8 Lattice constants, 6-2, to 6-35

Lead: ores, 7-5 physical properties, 14-1,14-4,14-8,14-12 plating, 32-13 Lead alloys: mechanical properties, 22-48 to 22-50 soldering fluxes, 3 4 4 superplasticity, 36-2 welding, 33-34 Liquid metals, physical properties, 14-6 to 14-13 Lithium: ores, 7-5 physical properties, 14-1, 14-7, 14-11 Low temperature, physical properties, steels, 1442,1443 Lubricants: metal working, 24-1 1 to 24-13 oils, 24-1 1 to 24-10 water based, 24-6 Lubrication : boundry, 24-1 hydrodynamic, 24-1 Lutetium, physical properties, 14-1 Magnesite, fired: mechanical properties, 27-14 properties, 27-14 Magnesium: metallography, 10-43 to 10-46 physical properties, 14-1, 144, 14-7, 14-12 pickling, 32-5 plating processes, 32-17 related specifications,1-9 sources, 7-5 Magnesium alloy composites, 37-5 Magnesium alloys: creep properties, 22-58 to 22-61 elevated temperatureproperties,22-55,22-56 fatigue and creep properties, 22-60 to 22-63 fluxing and inoculation, 26-16, 26-17 heat treatment, 29-21 to 29-23 heat treatment castings, 22-64 high temperature properties, 22-57,2240 mechanical properties, room temperature, 22-51 to 22-54 physical properties, 14-19 to 14-21 soldering fluxes, 3 4 4 superplasticity,36-2 welding, 33-7,33-34 Magnesium casting alloys, 26-48 to 26-59 Magnesium melting, crucibles for, 26-15 Magnetic constant, definition, 20-21 Magnetic dipoles, definition, 20-20 Magnetic field strength, definition, 20-20 Magnetic flux density, definition, 20-21 Magnetic flux, Weber definition, 20-21 Magnetic materials, 20-1, 20-2 Magnetic moment, definition, 20-20 Magnetic polarization, J definition, 2&21 Magnetic poles, definition, 20-20

Index Magnetic powder cores, 20-17,20-18 Magnetic saturation, definition, 20-21 Magnetic susceptibility, definition, 20-21 Magnetic temperature compensating materials, 20-17 Magnetic units: cgs to SI conversions, 20-22 definitions, 20-20 to 20-22 Magnetically soft materials, 20-9 to 20-16 Magnetization : definition, 20-21 unit mass definition, 20-21 Magnetostriction, definition. 20-22 Magnes: constant permeability, 20-17 permanent, 20-2 to 20-10 Malleable cast iron, 26-80 to 26-83 Manganese: ores, 7-5 physical properties, 14-1, 14-7, 14-12 Mass absorbtion coefficients elements, 4-30 to 4-3 5 Matano-Boltzmann, diffusion equation, 13-5 Mathematical formulae, 2-12 to 2-22 Mechanical alloying, 23-2, 23-24 to 23-26 Mechanical plating, 32-20 Mechanical properties : aluminium castings, 26-20 to 26-29 of butt welds, 33-12 composites, 37-2 to 37-7 copper alloy castings, 26-32,26-33 nickel alloy castings, 2646,26-47 steel castings, 24-62 to 26-68 see also Metals Mechanical testing: Brinell hardness, 21-1 cast iron test pieces, 21-9,21-10 fracture toughness, 21-12 to 21-19 hardness conversions, 214 to 21-7 hardness testing, 21-1 to 21-7 impact testing, 21-10 to 21-12 micro-hardness, 214 tensile testing, 21-8 to 21-10 Melting point: ceramics, 27-1 copper alloys, 14-16 to 14-18 elements, 8-1 to 8-3 intermetallic compounds, 8-3, 8-4 magnesium alloys, 14-18 to 14-21 metallurgically important compounds, 8-5 10 8-8 pure metds, 8-1 to 8-3,14-1,14-2 Melting volume change elements, 8-1 to 8-3 Memory alloys: compositions and transformations, 15-36 to 15-44

mechanical properties, 15-36 titanium-nickel, 15-40 to 1 5 4 3 Mercury: ore, 7-5 physical properties, 14-1, 14-7,1611 Metallizing vacuum, 32-21

1-7

Metalloids, 6-1 to 6-35 Metallography: chemical polishing, 1&13 to 10-15 dark field illumination, 10-16 electrolytic polishing, 10-8 to 10-13 etching, 10-16 to 10-21 grinding, 10-7 interference microscopy, 1&16 mechanical polishing, 10-7, 10-8, 10-22 mounting, 10-6,10-7,10-22 phase contrast, 10-16 polarized light, 10-17 preparation/washing/drying, 10-1 8 specific metals, 10-22 to 10-62 MIM (metal injection moulding), see Injection moulding Minerals, metallurgical, 7-1 Modulus bulk, 15-2, 15-3 Molten salts: binary systems, 9-7 electrical conductivity, 9-28 density, 9-1 inorganic compounds, 9-19 electrical conductivity, 9-20 surface tension, 9-42,9-45 viscosity, 9-51,9-52 Molybdenum: metallography, 10-46, 10-47 ores, 7-5 physical properties, 14-2,14-4,14-7,1412 Moments of inertia, 3-3 Monel spot welding, 33-6 Mould dressings and coatings, 2643,2644 Moulding materials, 26-4 Moulding sands, 2 6 4 to 26-7 Nee1 point, definition, 20-22 Neodymium, physical properties, 14-2, 14-7, 14-12 Neodymium-hydrogen system, 12-9 Neodymium-iron-boron magnets, 20-8,20-9 Nickel: casting alloys, 26-42 ores, 7-6 physical properties, 14-2,14-4,14-7,14-12 plating, 32-13,32-14 Nickel alloys, 33-6, 33-8 cryogenic properties, 22-78 fatigue properties, 22-78,22-79 heat treatment, 29-23, 29-24 high temperature properties, 22-74 to 22-77 metallography, 10-47 to 10-49 physical properties, 14-22 to 14-24 soldering fluxes, 34-4 specifications, 22-65 to 22-70 superplasticity, 36-2 wrought: creep properties, 22-79 to 22-8 1 mechanical properties, 22-71 to 22-74 Nickel-copper electrical resistivity, 19-6 Nickel-iron electrical resistivity, 19-6

1-8

Index

Nimonic alloys, 33-6 Niobium: metallography, 1 0 4 9 ores, 7-6 physical properties, 14-2, 14-4, 14-7, 14-12 Niobium-hydrogen-nitrogen-oxygen systems, 12-8,12-17, 12-20 Nitrides : chemical vapour deposition, 35-10 heat capacities, 8-46 physical vapour deposition, 35-9 solubility in iron and chromium 12-16 thermochemical data, 8-23 Nitriding steels, 29-11, 29-14 Nitrogen, solubility in metals, 12-13 to 12-17 Noble gases, solubility in metals, 12-21, 12-22 Nodular cast iron, 2 6 8 1 , 26-82,26-84,2646 Normalizing steels, 29-7, 29-8

ODs, see Oxide dispersion strengthening Oil additives, 24-10 Oils: cutting, 2 6 1 1 lubricating, 24-1 to 24-4 mineral, 24-3, 24-5 synthetic, 24-6 to 24-8 Ore preparation sinter, 28-25 ORS, 7-2 Osmium, physical properties, 14-2, 14-7 Oxidation by water or carbon dioxide, 29-2 Oxidation resistance, 31-13 Oxide dispersion strengthening, 23-3, 23-23 aluminium, 23-26 copper, 23-24 lead, 23-25 superalloys, 23-23 Oxides: chemical vapour deposition, 35-8 double, thermochemical data, 8-35 heat capacities, 8-48 physical vapour deposition, 35-7 thermochemical data, 8-25 vapour pressures, 8-56 Oxygen solubility in metals, 12-18 to 12-20 Oxygen-niobium-tantalum systems, 12-20, 12-21 Palladium: physical properties, 14-2, 14-4, 14-8 plating, 32-14 Palladium-hydrogen system, 12-9 Parting materials in moulding, 26-13 Patterns: casting weights from, 26-12 contraction allowances, 26-10, 26-1 1 machining allowances, 26-13 materials, 26-12 standard colours, 26-12 Pearson to Struktur Bericht comparison, 6-63 to 6-46

Pearson symbols, 6-2 Permanent mould casting, 26-3 Permeability, magnetic definition, 20-21 Phase identification by x-rays, 4-14 Phosphating, 32-22 Phosphides: dissociation pressures, 8-38 thermochemical data, 8-37 Photoelectric emission, 18-4, 18-5 Physical constants, 3-2 Physical properties: composites, 37-2 liquid metals, 14-6 and 14-13 pure metals: elevated temperatures, 14-3 to 14-6 room temperature, 14-1,14-2 Physical vapour deposition, 35-1,353,354 applications, 35-3 carbides, 35-11 to 35-13 elements, 35-3 nitrides, 35-9 to 35-11 oxides, 35-7 to 35-9 Pickling and cleaning processes, 32-2 to 32-6 Pig irons, analyses, 26-76 Plaster mould casting, 26-2 Plating: autocatalytic, 32-19 non-conducting surfaces, 32-20,32-21 Platinum: emissivity, 17-3 physical properties, 14-2,144, 14-8, 14-12 plating, 32-14 Platinum group metals, metallography, 10-50 Platinium group sources, 7-6 Platinum-platinum/rhodium thermocouple tables, 1 6 6 , 16-7 Plutonium, physical properties, 14-2, 144, 14-8,1612 PM, see Powder metallurgy Poisson’s ratio, 15-2, 15-3 Polishing: chemical, 10-13 to 10-18 compositions, 32-1 Polonium, physical properties, 14-2, 14-12 Potassium: physical properties, 14-2, 14-7, 14-11 sources, 7-6 Powder coating, 32-20 Powder compacts, testing, 23-4, 23-6 Powder components: aluminium, 23-11, 23-13 copper, 23-7,23-11,23-13 ferrous, 23-7, to 23-10, 23-14 to 23-22 mechanical properties, 22-10 Powder manufacture, 23-2 Powder metal: particle size, 23-3, 2 3 4 properties, 23-3, 2 3 4 Powder metallurgy: process products, 23-1 processes, 23-1 Praseodymium, physical properties, 14-2,1612

Index Praseodymium-hydrogen system, 12-10 Preferred orientation, 4-22 Pressing, lubricants for, 24-12 Producer gas analysis, 28-21 PVD, see Physical vapour deposition Quantitative image analysis, 10-69 Radiating properties, emissivity/reflectivity, 17-1 Radiation screening, 4-44 to 4-48 Radium, physical properties, 14-2, 14-12 Rare earth magnets, 20-8 Reactive evaporation, 3 5 1 Refractories, unshaped, properties, 27-1 1 Refractory bricks: properties, 27-8,27-9 unfired properties, 27-10,27-11 Refractory linings, 27-12 Refractory standards, 27-14 to 27-17 Remanence, magnetic, definition, 20-22 Reserves, of metals, 7-2 to 7-8 Residual stress measurement, 4-18 Resistance welding, 33-5 to 33-7 Resistivity, pure metals, 14-1 to 14-6, 14-10 to 14-13,19-1, 19-2 Rhenium: physical properties, 14-2, 14-4,14-8, 14-12 source, 7-6 Rhodium: physical properties, 14-2, 144, 14-8 plating, 32-14 soldering fluxes, 34-3 Rigidity modulus polycrystalline metals, 15-2, 15-3 Rockwell hardness, 21-1 to 21-3 Rolling: oils for, 24-12 textures, 4-38,4-39 Rubidium, physical properties, 14-2, 14-8, 14-12 Russian specifications, 1-1 to 1-9 Ruthenium, physical properties, 1 4 2 , 1 4 1 2

Samarium, physical properties, 14-2, 14-12 Sampling fuels, 28-1 Sand casting, 26-2,26-6,26-7 Scandium, physical properties, 14-2,14-12 Scanning electron microscopy, 10-68 Scattering factors mean atomic, 4-26 to 4-29 Schaeffler diagram, 32-25 Schoeflies point and space group notating, %3,5-4 Screening radiation, 4 4 l to 4-48 Seizure loads, 25-8 Selenides: heat capacities, 8-50 heats of formation, 8-12

1-9

selenium: physical properties, 14-2, 14-8, 14-12 source, 7-6 Selfdiffusionhomogeneous alloys, 1Mto 13-70 Shape memory alloys, 15-36 to 15-44 Shell mould casting, 26-2 Sheradizing steels, 29-16 SI units, 2-2 to 2-3 Sieve: mesh numbers, 2-1 1 sizes, standard comparisons, 23-5 Sievert unit of dose equivalent, 4 4 6 Silicates: heat capacities, 8-47 thermochemical data, 8-24 Silicides: heat capacities, 8-47 thermochemical data, 8-24 Silicon: metallography, 10-50,10-51 physical properties, 14-2,148, 14-12 source, 7-7 Siliconizing steels, 2%16 Silver : metallography, 10-51, 10-52 ores, 7-7 plating, 32-14, 32-20 welding, 33-38 Silver alloys, soldering fluxes, 34-3 Sintered materials, 23-1 to 23-34 metallography, 10-62 Sintering, 23-4 Sodium: physical properties, 14-2, 1 4 7 , 1 4 1 2 sources, 7-6 Sodium silicate, properties for carbon dioxide processes, 26-5 Solder formulations, 34-6, 34-7 Soldered joints product assurance, 34-8 Soldering, 34-1 to 34-9 bibliography, 34-14 British Standards, 34-2 fluxes, 34-2 to 34-4 Solders: intermediate and high temperatures, 34-8 mechanical properties, 22-97 to 22-98 metallography, 10-60,10-61 physical properties, 22-97 Space groups. 5-3 Specific heat: cokes, 28-14 liquid fuels, 28-18 magnesium alloys, 14-20, 14-21 nickel alloys, 14-22 to 14-24 pure metals, 14-1, 14-2 steels, 14-27 to 14-41 titanium alloys, 14-25 see also Heat capacities Specifications,related, 1-1 to 1-10 Spheroidal graphite iron, 26-81,26-82, 26-84, 26-86

1-10

Index

Spot welding, 33-9 Spray forming, 23-26 Sputter plating, 35-1, 35-2 Stabilizing aluminium alloys, 29-17 Stainless steel: corrosion, 31-9 pickling, 32-6 powders and products, 23-20 Stamping, lubricants for, 24-12 Standards refractories, 27-9 to 27-17 Steels: alloy, heat treatment, 29-16, 29-17 alloy, superplasticity, 36-5 austenitic-ferritic,mechanical properties, 22-124 austenitis, mechanical properties, 22-118 to 22-123 carbon, mechanicai properties, 22-100 to 22-1 03 carbonitriding, 29-1 1 carburizing, 29-11 to 29-13 carburizing, mechanical properties, 22-1 12 to 22-114 case hardening, 29-8, 29-9 cast welding, 33-26 castings, 26-62 to 26-73 castings - aerospace series, 26-70 castings for pressure purposes, 26-68 colour etching, 10-19 creep data, 22-143 to 22145 fatigue properties, 22-140 to 22142 ferritic welding, 33-16 forged and rolled, mechanical properties, 22-1 32 hardening, 29-8,29-9 hardness conversions, 21-4,21-5 high alloy, mechanical properties, 22-1 14, 22-115,22.128,22-129 hot tensile properties, 22-134 to 22-139 investment cast, 26-70 to 26-73 KISCC values, 31-11 low alloy, mechanical properties, 22-103 to 2 2 112 low alloy welding, 33-15 magnetic properties, 20-4,2&5, 20-13 making, 28-28 maraging, mechanical properties, 22-127, 22-128 martensitic, mechanical properties, 22115 to 22-117 mechanical properties, 22100 to 22-132 metallography, 10-36 to 1 0 4 1 microalloyed, mechanical properties, 22-133 mild welding, 33-13 to 33-15 nitriding, 29-1 1, 29-14 non-magnetic, 20-18 to 20-20 normalizing, 29-7, 29-8 physical properties, 14-27 to 1443 pickling, 3 2 4 related specifications, 1-1 to 1-7 relative wear rates, 25-16 resistance welding, 33-5

retained austenite, 4-17,4-18 semi-austenitic, mechanical properties, 22125 to 22-127 sintered, 23-14 spring, mechanicalproperties, 22-1 30,22-131 stainless, mechanical properties, 22-1 14 to 22-127 stainless welding, 33-21 to 33-25 stainless superplasticity, 36-5 sub-zero mechanical properties, 22-146 to 22- 149 superplasticity, 3 6 4 surface hardening, 29-9,29-15, 29-16 tool, compositionand use, 22-150 to 22-154 tool, heat treatment, 22-156 to 22-158 valve, mechanical properties, 22-1 24,22-125 welding, 33-6,33-13 to 33-27 Stress corrosion cracking, 31-8 Stripping electroplate, 32-21 Strontium, physical properties, 14-2, 14-8, 14-13 Struktur Bericht: details, 6-36 to 6-63 to Pearson comparison, 6-63 to 6-66 types, 6-2 to 6-35 Sulphides: dissociation pressures, 8-39 thermochemical data, 8-28 Sulphides-selenides-tellurides, heat capacities, 8-50 Superalloys, mechanically alloyed, 2 S 2 4 to 23-26 Superconductivity,19-7 transition temperatures, 19-8 Superplasticity,36-1 to 36-7 powdered metals, 36-6 Surface tension : liquid metals, 14-6 to 14-10 molten salts, 9 4 2 to 9-50 Surface treatment, steels, 29-9, 29-16 Susceptibilities,elements, 2&3 Susceptibility, magnetic, definition, 2&21 Swedish specifications, 1-1 to 1-9 Symmetry, point groups, 5-1 Tantalum: metallography, 10-52,10-53 physical properties, 14-2, 14-5, 14-8, 14-13 sources, 7-7 Tantalum alloys, welding, 33-39 Tantalum-hydrogen system, 12-11 Tantalum-nitrogen system, 12-17 Tantalum-oxygen system, 12-21 Taper sectioning ,10-22 Tellurides: heat capacities, 8-50 heats of formation and entropies, 8-12 Tellurium: physical properties, 14-2, 14-8, 14-13 sources, 7-7 Temperature: conversions ITS-90,2-2,2-12

index

Temperature (cont.), fixed points, 1 6 3 , 1 6 4 of flames, 28-24 measurement, 16-1, to 16-4 scale (ITS-90). 16-1 scales, 16-1 to 1 6 3 thermodynamic, 14-1 Temperature measurement, emissivity effect, 17-4,17-5 Terbium, physical properties, 14-2,14-8,1413 Ternary diagrams, 11496 Textures, 4-38 to 4-40 Thallium: physical properties, 14-2, 14-5, 14-8, 14-13 sources, 7-7 Thermal conductivity: aluminium alloys, 14-14 to 14-16 ceramics, 27-1 to 27-6 copper alloys, 14-16 to 14-18 liquid fuels, 28-1 8 magnesium alloys, 14-9 to 14-21 nickel alloys, 14-22 to 14-24 pure metals, 14-1 to 14-6 refractory bricks, 27-8, 27-9 steels, 14-27 to 1 4 4 3 titanium alloys, 14-25 zinc alloys, 14-26 zirconium alloys, 14-26 Thermal electromotive force., 1 6 4 , 1 6 5 Thermal expansion : aluminium alloys, 14-14 to 14-16 in brazing, 34-10,34-11 copper alloys, 14-16 to 14-18 magnesium alloys, 14-19 to 14-21 nickel alloys, 14-22 to 14-24 pure metals, 1 4 1 , 1 4 2 steels, 14-27 to 14-23 titanium alloys, 14-25 zinc alloys, 14-26 zirconium alloys, 14-26 Thermionic emission, cathodes, 18-3 Thermionic properties, 18-1, 18-2 Thermochemical data: alloy phases, 8-43 borides, 8-22 carbides, 8-23 double oxides, 8-35 elements, 8-1 to 8-3,8-8 halides, 8-29 heat capacities, 8-41 intermetallic compounds, 8-3,8-4, 8-9 intermetallic phases, 8-14 liquid and solid binary systems, 8-20 liquid binary systems, 8-17 metallurgically important compounds, 8-5 nitrides, 8-23 phosphides, 8-37 to 8-39 selenides and tellurides, 8-12 to 8-14 silicates and carbonates, 8-34 silicides, 8-24 sulphides, 8-28 Thermocouple reference tables, 16-6 to 1 6 9

1-11

Thermoelectric force, platinum absolute, 16-5 Thorium: ores, 7-7 physical properties, 14-2, 14-8 Thorium-hydrogen system, 12-1 1 Thulium, physical properties, 14-2, 14-13 Tin : mechanical properties, 22-96 ore, 7-7 physical properties, 14-2. 14-5, 14-8, 14-12, 14-26 plating, 3 2 1 5 Tin alloys: mechanical properties, 22-99 metallography, 1@53,10-54 superplasticity, 36-3 Tin-lead plating, 32-15 Tin-nickel plating. 32-15 Titanium: ores, 7-8 physical properties, 14-2, 14-5, 14-8, 14-13 soldering fluxes, 34-3 Titanium alloys: composites, 37-6 creep properties, 22-89 to 22-90 elevated temperature properties, 22-86 to 22-88 fatigue properties, 22-90 to 22-93 impact properties, 22-93 mechanical properties, 22-83,22-84 metallography, 10-54,10-55 physical properties, 14-25 specifications, 22-82 superplasticity, 36-3 welding, 33-39 Titanium alloys, KISCC values, 31-12 Titanium sheet, mechanical properties, 22-85 Titanium-hydrogen system, 12-12 Transformation hardening with lasers, 30-12 Triple points, fixed, 16-3 Tungsten : ores, 7-8 physical properties, 14-2,165, 14-8, 14-13 spectral emissivity, 17-2,17-3 Tungsten alloys: metallography, 10-55, 10-56 superplasticity, 36-3 Twinning elements, 4-37

UNS designations, 1-1 Uranium: hydrogen solubility, 12-7 physical properties, 14-2, 14-5, 14-8, 14-13 welding, 33-39 Uranium alloys, metallography, 10-57 to l e 5 9 Vacuum brazing. 34-21 Vanadium, physical properties, 14-2, 14-5, 14-8,14-13 Vanadium-hydrogen system 12-12

1-12

Index

Vapour deposition coatings, 35-1 to 35-13 Vapour pressures: elements, 8-54 halides and oxides, 8-56 Vickers hardness, definition, 21-3 Viscosity: liquid fuels, 28-18 liquid metals, 14-7 to 14-10 molten salts, 9-51, 9-52 Wear: abrasive/adhesive/erosive, 25-9 to 25-1 1 coated and uncoated ferrous materials, 25-20 to 25-21 fretting, 25-15 resistance, 25-23, 25-24 resistance erosion, 25-15, 25-23 resistant materials, 25-12 to 25-14 Wear rates, 25-18 engineering materials, 25-18 ferrous materials, 25-16, 25-17 unlubricated, 25-22 Weld decay, stainless steel, 33-25 Weldability, magnesium alloys, 14-19 to 14-21 Weldable chromium-nickel steel tubes, 26-69 Welding: aluminium alloys, 33-27 to 33-30 bibliography, 33-42 to 3344 British standards, 3 3 4 0 to 3 3 4 2 cast irons, 33-27 cast steels, 33-26 clad steels, 33-26 copper alloys, 33-30 to 33-34 diffusion bonding, 33-10 to 33-13 dissimilar alloys, 33-39 electrodes, cast steels, 33-23 ferritic steels, 33-22 friction, 33-10 fusion, 33-13 to 33-38 gold, 33-38 high alloy steels, 33-21 to 33-25 with lasers, 30-9 lead alloys, 33-34 magnesium alloys, 33-34, 33-35 martensitic steels, 33-22 nickel alloys, 33-35 to 33-38

platinum alloys, 33-38 resistance, 334 silver, 33-38 terms, 33-1 to 334 zinc alloys, 33-39 X-ray: crystal chemistry, 6-1 to 6-71 crystallography, 5 1 to 5-1 1 excitation, 4-1 to 4-10 fluorescence, 3-42 to 4 4 4 techniques, 4-11 to 4-23 wave lengths, 4-2 to 4-4 Young’s modulus: aluminium alloys, 14-14 to 14-16 ceramics, 27-1 polycrystalline metals, 15-2, 15-3 Ytterbium, physical properties, 14-2, 14-8, 14-13 Yttrium, physical properties, 14-2, 14-13 Zinc: casting alloys, compositions, 26-60 casting alloys, properties, 26-61 equivalents, 26-37 physical properties, 14-2, 14-5, 14-8, 14-13 plating, 32-16 soldering fluxes, 34-4 Zinc alloys: composites, 37-7 mechanical properties, 22-94,22-95 metallography, 10-57 to 10-59 physical properties, 14-26 superplasticity, 36-3 Zirconium physical properties, 14-2, 14-8, 14-13 Zirconium alloys, 14-26 mechanical properties, 22-94, 22-95 metallography, 10-59, 10-60 superplasticity, 36-3 welding, 33-39 Zirconium-hydrogen system, 12-1 3

Reference Book