Prakt. Met. Sonderband 52 (2018) 167 
Clsed p, 
Steel. For te 
8 remove by 
ngs, 
Cd area The 
ns of Scanning Ol 
Er Ciffracfion 
of the EB), 
Order {9 study 
(C) (d) 
Figure 2: (a) SEM image of an HV1 indent in the austenitic Mn-steel, (b) showing 
deformation lines around the indent, and (c) the higher magnification reveals surface 
steps, (d) some characteristic deformation lines are marked for further analysis. 
Id hardness 
A 
be achieved, 
ng lon milled . (a) . . (b) . 
7 te edge Figure 3: Inverse pole figure overlay on image quality, (a) hardness indent with 
on a he deformation lines in a grain oriented close to (101), (b) higher magnification reveals no 
es misorientation across the surface steps. 
rent, which 
surfa Lo . . . 
a9 un However, in literature, twin thicknesses between 10 to 80 nm in austenitic Mn-steels have 
0 been proposed [9,10], which is in the range of the 70 nm-step size used for the EBSD map 
aa in this study. Therefore, it is not possible to exclude twinning as reason for the deformation 
nf Fare lines based solely on the EBSD measurements. But according to the study of Wang et al. [8] 
en . ‘ on copper single crystals and the study of Kang et al. [7] on a polycrystalline austenitic Mn- 
yo fie steel, compressive deformation parallel to the surface normal of the (101)-plane leads to 
ug cal deformation by dislocation slip only, and additionally to the formation of a two-fold symmetric 
deformation pattern. Such a two-fold symmetry is observed in this study as well. which is