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