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根据马氏体相变的k-s模型和西山模型,{121}r是奥氏体与马氏体之间的最小畸变界面,同时构成此界面的是两个最小畸变方向,也就是马氏体的两个最快长大方向,<101>r、<111>r。在母相对马氏体相变无约束的情况下,如表面马氏体转变,马氏体的宏观惯习面则保持为{121}r面。而通常,马氏体相变造成的点阵畸变要改变马氏体的长大方向。低屈服强度的母相将部分甚至完全通过塑性变形来完成形状协调,这样马氏体的长大方向将旋转一定角度。母相屈服强度较高时,如{3,10,15}r马氏体,形状协调主要通过母相的弹性变形来完成,因而产生很高的应变能。在这种情况下,马氏体会通过产生{112}α细小孪晶的自身协调来长大,因此马氏体的最快长大方向由<101>r转向{112}α孪晶面的法线方向。依据上述观点,作者通过建立参考坐标系计算出了铁基马氏体的各种惯习面:(5,-7.0008,5)r,(3.12,-4.72,4)r(2,-5.186,2)r,(2,-4.83,2)r,(-9.01,3,15.01)r和(-9.79,3,15.79)r。
According to the martensitic transformation ks model and the Western Hills model, {121} r is the smallest distortion between austenite and martensite interface, while the composition of this interface is the two minimum distortion direction, which is martensite The two fastest growing direction, <101> r, <111> r. In the case of no relative martensite transformation of the mother relative to martensite, the macroscopical habit of martensite remains as {121} r. In general, the lattice distortion caused by the martensitic transformation changes the growth direction of the martensite. The low yield strength of the mother phase will be partially or completely through the plastic deformation to complete the shape coordination, so that the growth direction of martensite will rotate a certain angle. When the yield strength of the matrix is high, such as {3, 10, 15} r martensite, the coordination of shapes is mainly achieved by the elastic deformation of the matrix, resulting in a high strain energy. In this case, the martensite grows by self-coordination resulting in {112} α twins, so the fastest growing direction of martensite turns from <101> r to {112} α twins Line direction. From the above point of view, the authors calculate various familiar habitats of iron-based martensite by establishing a reference coordinate system: (5, -7.0008, 5) r, (3.12, -4.72, 4) r 2) r, (2, -4.83,2) r, (-9.01, 3,15.01) r and (-9.79,3,15.79) r.