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    Mechanical Properties of MAX Phases
    Mechanical Properties of MAX Phases
    Mechanical Properties of MAX Phases
    Ebook284 pages1 hour

    Mechanical Properties of MAX Phases

    By David J. Fisher

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    MAX Phase Materials are uniquely structured carbide and nitride materials which combine the rigidity, oxidation-resistance and high-temperature strength of ceramic materials with such metallic properties as good machinability, thermal-shock resistance, damage-tolerance and good transport properties. Potential applications include microelectronic

    LanguageEnglish
    PublisherMaterials Research Forum LLC
    Release dateApr 5, 2021
    ISBN9781644908013
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      Book preview

      Mechanical Properties of MAX Phases - David J. Fisher

      Copyright © 2021 by the author

      Published by Materials Research Forum LLC

      Millersville, PA 17551, USA

      All rights reserved. No part of the contents of this book may be reproduced or transmitted in any form or by any means without the written permission of the publisher.

      Published as part of the book series

      Materials Research Foundations

      Volume 97 (2021)

      ISSN 2471-8890 (Print)

      ISSN 2471-8904 (Online)

      Print ISBN 978-1-64490-126-7

      ePDF ISBN 978-1-64490-127-4

      Print ISBN 978-1-64490-801-3 (e-book)

      This book contains information obtained from authentic and highly regarded sources. Reasonable efforts have been made to publish reliable data and information, but the author and publisher cannot assume responsibility for the validity of all materials or the consequences of their use. The authors and publishers have attempted to trace the copyright holders of all material reproduced in this publication and apologize to copyright holders if permission to publish in this form has not been obtained. If any copyright material has not been acknowledged please write and let us know so we may rectify in any future reprint.

      Distributed worldwide by

      Materials Research Forum LLC

      105 Springdale Lane

      Millersville, PA 17551

      USA

      http://www.mrforum.com

      Printed in the United States of America

      10 9 8 7 6 5 4 3 2 1

      Table of Contents

      Introduction

      Cr2AlC

      Hardness

      Creep

      Elastic constants

      Cr2GeC

      Hardness

      Elastic constants

      (Cr,Ti)3AlC2

      Hardness

      Hf3AIC2

      Hardness

      Hf2InC

      Elastic constants

      Hf2PbC

      Elastic constants

      Hf3PB4

      Hardness

      Ir2YSi

      Hardness

      Lu2SnC

      Hardness

      MoAIB

      Hardness

      Mo2Ga2C

      Hardness

      Mo2GeC

      Elastic constants

      Mo2HoC

      Hardness

      Mo2ScAIC2

      Hardness

      Mo2Ti2AlC3

      Hardness

      Mo2TiAlC2

      Hardness

      Nb2AlC

      Hardness

      Nb4AlC3

      Hardness

      Elastic constants

      Nb2CuC

      Hardness

      Nb2GeC

      Hardness

      Elastic constants

      Nb2PC

      Elastic constants

      Nb4SiC3

      Hardness

      Nb2SnC

      Hardness

      (Nb,Zr)4AlC3

      Hardness

      Sc2InB

      Hardness

      Sc2InC

      Hardness

      Sc3SnB

      Hardness

      ScTaN2

      Hardness

      Ta4AlC3

      Hardness

      Ta2InC

      Elastic constants

      Ti2AlC

      Hardness

      Toughness

      Ti3AlC

      Elastic constants

      Ti3AlC2

      Hardness

      Elastic constants

      Toughness

      Creep

      Ti2Al(C,N)

      Elastic constants

      Ti2AlN

      Creep

      Elastic constants

      Ti4AlN3

      Hardness

      Ti3(Al,Si)C2

      Hardness

      Ti3(Al,Si,Sn)C2

      Hardness

      Ti2(AI,Sn)C

      Hardness

      Ti2AsC

      Elastic constants

      Ti2GeC

      Elastic Constants

      Ti3GeC2

      Hardness

      Elastic constants

      Ti2InB2

      Hardness

      (Ti,Mo)2AlC

      Hardness

      Toughness

      Ti2SC

      Hardness

      Elastic constants

      Ti3(Si,Al)C2

      Hardness

      TiSiC

      Hardness

      Ti3SiC2

      Hardness

      Elastic constants

      Ti2SiN

      Hardness

      Ti3(Sn,Al)C2

      Elastic constants

      Ti2SnC

      Elastic constants

      Ti3SnC2

      Hardness

      (Ti,V)2AlC

      Hardness

      Elastic constants

      V2AlC

      Hardness

      Elastic constants

      V4AlC3

      Hardness

      Elastic constants

      Y5Si2B8

      Elastic constants

      Zr2AlC

      Hardness

      Elastic constants

      Zr3AlC2

      Hardness

      Zr2Al3C5

      Elastic Constants

      Zr2(Al,Bi)C

      Hardness

      (Zr,Nb)2AlC

      Hardness

      (Zr,Ti)3AlC2

      Hardness

      Elastic constants

      About the Author

      Materials Index

      References

      Introduction

      These are materials which generally comprise three principal elements, perhaps with others in solid solution, and have great potential importance in fields ranging from the electronic to the mechanical. The present work is concerned only with the mechanical properties, and the primary attraction here is that these materials exhibit properties which can simultaneously be both metallic and ceramic in nature.

      Their name arises from the designations of the three elements, with M being a transition metal, A usually being another metal or metalloid (cadmium, aluminium, tin, lead, gallium, indium, thallium, silicon, germanium, phosphorus, arsenic, sulfur) and X being carbon or nitrogen. In recent years, a similar class of materials has attracted interest. In these, the third element is boron. These are known as MAB phases, and a number of them are included in the present work, for comparison purposes. The M, A and X elements are present in simple numerical ratios, and the various types of MAX phases are conveniently designated by that ratio. The 211-type phases are of the form, M2AX. This is one of the largest groups and these phases possess a nanolaminate structure within which blocs of a M2X, carbide or nitride, are separated by monatomic layers of A. Due to a high crystal symmetry, the structure is conveniently defined merely by the a and c lattice constants and the interplanar separation of the M and X layers. As well as the layering of the structure, the nature of the bonding, covalent or ionic or metallic, is important. Another useful feature is that the chemistry of a MAX phase can be easily changed without affecting the structure.

      These nanolaminates generally consist of hexagonal carbide or nitride blocs and planar A atomic sheets with a zig-zag stacking along the z-axis. It is this layered structure which imparts to the phases an unusual combination of ceramic and metallic properties. Among the ceramic properties are rigidity, oxidation-resistance and high-temperature strength. Among the metallic properties are machinability, thermal-shock resistance, damage-tolerance and good transport properties. The MAX phases are relatively soft and the Vickers hardness values of polycrystalline samples tend to range from 2 to 8GPa, making them generally softer than structural ceramics but harder than metals.

      The essentially two-dimensional nature of these phases means that the dislocations also tend to be confined to the two dimensions of the basal planes upon which the dislocations glide. This facilitates the general understanding of their deformation. Knowledge of the fundamental elastic constants, rather than of specific properties, is instead found be of especial interest because they closely govern a wide spectrum of properties which range from machinability to tribology. Various simple criteria can be applied to the values of the elastic constants in order to predict possibly useful mechanical properties. The machinability, for example, is quite closely correlated with the ratio of the bulk modulus to the C44 elastic constant, while ductility is related to the value of the so-called Pugh ratio of the bulk modulus to the shear modulus. In what follows, these considerations are explored for a wide selection of representative MAX phases, with priority being given to the most recent theoretical and experimental results complete to early 2021.

      Figure 1. Structure of Cr2AlC grey: carbon, red: chromium, blue: aluminium (a = 2.86Å, c = 12.8Å,, theoretical density = 5.24g/cm³)

      Cr2AlC

      Hardness

      Thin (1.2μm) crystalline films of this phase (figure 1), first reported in 1963¹, were deposited² layer-by-layer, using magnetron sputtering of elemental targets, onto polished Inconel 718 substrates at 853K. The hardness was about 15GPa and the Young's modulus was about 260GPa. The films did not delaminate, and exhibited ductile behaviour during nanoscratching. Nanolamellar coatings with a columnar structure and nanocrystalline sub-structure were direct-current magnetron sputter-deposited³ onto Inconel 718 superalloy or (100) silicon wafers and the properties were measured by nano-indentation. The deposition rate increased with sputtering power and the coatings comprised Cr2AlC AlCr2 and Cr7C3 carbide phases, while there was a change in the preferred growth orientation. The hardness ranged from 11 to 14GPa, and increased slightly with sputtering power. The mechanical properties (figures 2 and 3) of high-density pure samples at up to 980C were determined⁴ by nano-indentation before and after oxidation at 1200C for over 29h. There was only a slight reduction in hardness and modulus at up to 980C; implying that there was no change in the deformation mechanism. In further work⁵, the film thickness decreased from 8.95 to 6.98μm with increasing bias voltage. Coatings which were deposited at 90V exhibited the least (33nm) roughness and grain-size (76nm), combined with the greatest (15.9GPa) hardness.

      Figure 2. Indentation hardness of Cr2AlC as a function of temperature

      Figure 3. Young’s modulus of Cr2AlC as a function of temperature

      The effect of the aluminium content upon the mechanical properties was investigated⁶ in vacuum-annealed Cr-Al-C coatings which had been deposited by the co-sputtering of Cr2Al and aluminium targets in a CH4/Ar atmosphere. Following vacuum-annealing (750C, 1.5h), the coatings comprised Cr2AlC, Al8Cr5 and Cr7C3. With increasing aluminium content, the hardness and modulus of the coatings increased from 10.17 to 19.00GPa and from 198.43 to 267.62GPa, respectively. The toughness clearly decreased. The excess aluminium led to Al8Cr5 and aluminium segregation at grain boundaries and to deterioration of the mechanical properties. When Cr2AlC coatings were prepared on high-speed steel substrates by direct-current magnetron sputtering, combined with subsequent heat-treatment⁷, their formation was suppressed by

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