Plastic Deformation and Diffusionless Phase Changes in Metals — the Gold-Cadmium Beta Phase

Chang, L. C.; Read, T. A.

doi:10.1007/bf03398954

Cited by 139 publications

(116 citation statements)

References 4 publications

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“…Bifurcation points are represented by hollow circles, whereas turning points are represented by solid circles. The B2 austenite phase (red line) is stable at higher temperatures and becomes unstable as the temperature is decreased with bifurcation at θ = 1 (T ref =333.15 K) which is in correspondence with experimental observations [1]. The onset of instability is associated with a deformation mode where the shifts become non-zero as discussed in [2].…”

Section: Fig 16supporting

confidence: 85%

“…Therefore, the predicted maximum possible temperature hysteresis is θ M f − θ A f = 1.55 (516.38 K). This is within an order of magnitude of the experimental value 30 K [1].…”

Section: Fig 16supporting

confidence: 75%

“…At the transformation temperature (A f ), 333.15 K [1], the transformation stretch associated with the B2 to B19 MT is found to be …”

Section: Fig 16mentioning

confidence: 99%

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Erratum to: An effective interaction potential model for the shape memory alloy AuCd

Guthikonda

Elliott

2010

Continuum Mech. Thermodyn.

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PreambleThis Erratum concerns our previous work published in this journal as: Guthikonda and Elliott (2009) (21)). However, due to the nature of the particular bug found in the computer code, only computations where multiple types of pair interactions (for example, the AuCd computations) are affected. The purpose of this erratum, therefore, is twofold: (1) to present corrected results corresponding to the model parameters as given in the original manuscript and (2) to report the results for an updated set of model parameter obtained by performing the fitting procedure described in the original manuscript with the corrected numerical code. Corrected results for original parametersCorrecting the coding error and regenerating the results for the parameters given in Table 5 results in three corrections to the original manuscript. First, the fitted value of C p in Table 4 changes from 26.1109 to 6.75 J mol −1 K −1 . Second, the variation of heat capacity per mole at constant pressure C p of B2 Au-47.5at%Cd versus non-dimensional temperature θ originally given in Fig. 8 now has the form shown in Fig. 16. Finally, the variation of heat capacity at constant pressure C p of the B2, L1 0 , B19, and αIrV crystal structures for Au-47.5at%Cd with respect to non-dimensional temperature θ originally given in Fig. 15 now has the form shown in Fig. 17. The corrected C p curves show that the original model parameters result in a B19 phase that has a negative C p for temperatures between θ = 1.31 and 2.18. This indicates that this B19 phase is thermodynamically unstable for these temperatures. As a result, the discussion and conclusions presented in the original manuscript no longer apply for the model with the original set of parameters. However, as will be seen in Sect. 3, they do apply to the model when an updated set of parameters is used.The online version of the original article can be found under

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Section: Fig 16supporting

confidence: 85%

“…Therefore, the predicted maximum possible temperature hysteresis is θ M f − θ A f = 1.55 (516.38 K). This is within an order of magnitude of the experimental value 30 K [1].…”

Section: Fig 16supporting

confidence: 75%

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Erratum to: An effective interaction potential model for the shape memory alloy AuCd

Guthikonda

Elliott

2010

Continuum Mech. Thermodyn.

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“…Therefore, the transformation twins may be produced due only to the formation of martensite/matrix boundary regardless of constraints from the surrounding matrix crystal. This can well be understood from the existence of intramartensite twins in the single interface transformation of AuCd (11) and CuAlNi(12) alloys. However, when a martensite is embedded in the matrix crystal as in the present case, the shape deformation due to the lattice change cannot be performed freely because of the matrix constraints, and so in addition to the primary internal twinning accompanied with the transformation itself, strains must occur in the martensite and/or the surrounding matrix to relax the constraints.…”

Section: Multiplicity Of Lattice Invariant Strainsmentioning

confidence: 99%

Additional Strains in Twinned Fe–Ni Martensites

1974

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The possibility of additional strains in twinned Fe-Ni martensites (32.5 %Ni) has been examined by analysing the traces of the twin interface planes, based on the two surface method with X-ray and optical microscopy techniques, besides electron microscopy of the fine details of twins. It has been verified from the two-surface analysis that the twin interface planes coincide with the (112) twinning plane within a few degrees, and therefore that large deviations between those planes, as detected in a previous electron microscopy, are apparent ones due to some bucklings of foil specimens. On the other hand, electron microscopy suggests the occurrence of slip on a plane including the [111] twinning shear direction, revealing two kinds of twin traces even over a narrow region of the same martensite, and furthermore indicates the existence of planar faults or thin twins on the (121) Or(211)T plane, accompanying streaks normal to the plane in diffraction patterns. From these results, it is suggested that the transformation twins in Fe-Ni martensites are subjected to additional strains by which (Received March 18, 1974) It is well known that transformation twins exist in martensites of many ferrous alloys and steels(1). When one of the present authors found the transformation twins in Fe-Ni martensites, he also detected some deviations of the twin interface planes from the (112) twinning plane, and suggested that the twin plates were subjected to slip along a plane including the [111] twinning shear direction(2). This suggestion was experimentally supported later by Rowlands et al. (3), and they considered the deviation to be an evidence for the existence of multiple lattice invariant strains. Accordingly, phenomenological multiple shear theories of martensitic transformation have newly been developed on the premise of additional strains (4)(5)On the other hand, Patterson and Wayman(6) did not observe any deviation between the twin interface and twinning planes, although they studied on nearly the same composition of Fe-Ni alloy. Recently, Patrician et al. (7) pointed out that such a deviation was due to an experimental error which might be caused by a substantial buckling of foil specimens.In view of the importance of additional strains for the elucidation of the transformation mechanism, it has been desired to check the genuineness of the deviation excluding the effect of specimen buckling. In the present experiment, the interface planes of transformation twins were analyzed by the two-surface method with X-ray and optical microscopy techniques. Consequently, it was clarified that the amount of deviation electron microscopy.The experimental results will be reported below, and discussed on the authenticity of trace analysis by electron microscopy and the multiplicity of lattice invariant strains.An ingot of Fe-32.5 wt %Ni alloy was prepared by melting electrolytic iron and nickel (99.99 %) in a vacuum induction furnace. A part of the ingot was shaped in a plate of 5 mm in thickness by repeating quartz capsules.After...

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“…The shape memory effect has been first observed in 1951 on Au-Cd alloy [1]. The next shape memory alloy (SMA), In-Tl [2], has been discovered a few years later.…”

Section: Introductionmentioning

confidence: 99%

Influence of comp ound twinning on Young’s moduli in NiTi martensite

Šesták

Černý

Pokluda

2009

ESOMAT 2009 - 8th European Symposium on Martensitic Transformations

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Abstract. NiTi shape memory alloy has been widely used in many engineering applications (e.g. mechatronic devices, medical tools, seismic sensors etc.). In this work, the Young's moduli of twinned NiTi martensite in selected crystallographic directions are calculated from first principles and compared with previous data for perfect (untwinned) NiTi structure. The obtained results show that the selected twinning mode does not have a significant influence on the Young's moduli and, thus, their reduction observed in some experiments is probably caused by changes in martensitic microstructure (arrangement of twinning variants).

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Plastic Deformation and Diffusionless Phase Changes in Metals — the Gold-Cadmium Beta Phase

Cited by 139 publications

References 4 publications

Erratum to: An effective interaction potential model for the shape memory alloy AuCd

Erratum to: An effective interaction potential model for the shape memory alloy AuCd

Additional Strains in Twinned Fe–Ni Martensites

Influence of comp ound twinning on Young’s moduli in NiTi martensite

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Plastic Deformation and Diffusionless Phase Changes in Metals — the Gold-Cadmium Beta Phase

Cited by 139 publications

References 4 publications

Erratum to: An effective interaction potential model for the shape memory alloy AuCd

Erratum to: An effective interaction potential model for the shape memory alloy AuCd

Additional Strains in Twinned Fe&ndash;Ni Martensites

Influence of comp ound twinning on Young’s moduli in NiTi martensite

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Additional Strains in Twinned Fe–Ni Martensites