Corrigendum to “Transition from the twinning induced plasticity to the γ-ε transformation induced plasticity in a high manganese steel” [Acta Materialia 161(2018) 273-284]

DOI of original article: https://doi.org/10.1016/j.actamat.2018.09.020. The authors regret that the crystallographic orientation relationship between the face-centered-cubic (FCC) γ-austenite and that of the hexagonal-close-packed (HCP) ε-martensite was incorrectly represented in Fig. 7. Certain modifications in Fig. 9 and Fig. 10 are necessary. The corrections do not affect main conclusions reached as a result of this research, except that {111}_γ//{30–32}_ε orientation relation was identified, instead of {111}_γ//{11–21}_ε. The authors would like to apologize for any inconvenience caused. For the measured data with a filename suffix ‘ang’, obtained from the EDAX electron back-scatter diffraction (EBSD) system. The HCP lattice with the three Euler angles equal to zero correspond to the setup shown in Fig. 7a. A γ-matrix with the three Euler angles (0°,55°,45°) rotating 180° around one <111> axis corresponds to the twin orientation with the three Euler angles (60°,55°,45°), as shown in Fig. 7b. Then in both, the <110> axis is parallel with the x-axis. For the γ-ε transformation, the crystallographic orientation relation between them are: {111}_γ//{0002}_ε and <110> _γ//<11-20>_ε. If the matrix experiences the transformation, the HCP lattice is shown in Fig. 7a with one <11-20> axis parallel with the x-axis and one <0002> axis perpendicular to the {111} plane of the matrix. In Fig. 7b, the {10-11} poles (plane normals projected in the pole figure), the {11-21} poles and the {30-32} poles are plotted in the same pole figure. Right after the transformation, the six {10-11} poles are close to the six {111} poles, while the {30-32} poles are overlapping with the six {111} poles from the matrix. Please note that the six {111} poles are from both the matrix and the twin, since the γ-ε transformation occurred after twinning. Fig. 7 can explain the emerging HCP peaks obtained from neutron diffraction, for example, the relative increase of the {10-11} peak intensity in doublet of the {0002} and {10-11} in Fig. 6, or the increasing of the {30-32} peak intensity, right after the γ-ε transformation during a tensile test. After the correction in Fig. 7, we should plot the {30-32} pole figures, instead of the {11-21} pole figures in Fig. 9 and Fig. 10. Right after the γ-ε transformation, besides the orientation relation with {111}_γ//{0002}_ε and <110> _γ//<11-20>_ε, the six {30-32} planes of ε-martensite are parallel with the six {111} planes of the matrix (phase transformation often occurred in the deformation twins, as shown in Fig. 9).