Orientations of type II twin boundaries in B2→B19′ martensitic transformation in dynamic theory

Кащенко, М. П.; Чащина, В. Г.

doi:10.1134/s1029959916010112

Cited by 5 publications

(1 citation statement)

References 12 publications

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“…To date, thermoelastic MT was studied for industrially important allows: Ti-Ni-Cu systems [4], Ti-Ni-Hf [5], Ni-Mn-Ti alloys [6], Ni-Mn-Ga systems [7,8] to name a few. Using the ideas about the role of DNC and controlling wave process in calculating the morphological features of MT in alloys with SM effect [9,10], including specific twinning variants [11], leads to good agreement with the experiment. Therefore, the problem of independent consideration of the dynamic mechanism of thermoelastic growth in the SM alloys seems to be relevant.…”

Section: Introductionsupporting

confidence: 55%

Molecular dynamics simulation of the effect of dislocations on the martensitic transformations in a two-dimensional model

Кащенко¹,

Baimova²,

Babicheva³

et al. 2017

LoM

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Investigation of the thermoelastic martensitic transformation is of high interest nowadays because of the numerous applications of the materials with such structural peculiarities. Thermodynamics, kinetics, structure, morphology of martensitic transformation still remain unclear in many respects. From this point of view, the effective way to study various properties of metallic crystals on atomistic level is molecular dynamics simulation, for which good qualitative agreement with the experiment can be achieved even with simple Morse or Lennard-Jones interatomic potentials. In this paper, the effect of dislocations on the direct and reverse martensitic transformation is studied by molecular dynamics simulation in a two-dimensional model of the ordered alloy with the AB stoichiometry. The three dimensional analog to this structure is B2 superstructure based on bcc lattice, which is characteristic for intermetallic NiTi alloy. It is found, that the dislocations can be considered as the nucleation centers for martensite phase, increasing the temperature of the direct martensitic transformation in comparison with the homogeneous martensitic transformation. The martensite domains found in the structure after transformation and the reverse martensitic transformation takes place in the presence of the domain boundaries, meaning that the austenite nucleates heterogeneously. At the reverse transformation, splitting of perfect dislocations into partials dislocations took place. Thus, it was established in the present study that, on the one hand, dislocations affect the direct martensitic transformation as the nucleation centers, and from the other hand, reverse martensitic transformation changes the dislocation structure of the modeled alloy.

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