Abstract
A critical assessment has been performed to determine the stacking fault energy (SFE) of the austenite phase in high manganese steels using X-ray diffraction (XRD). It was found that the SFE varies substantially with the chosen elastic constants. This strong dependence induces substantial errors in the estimated values of the SFE of the austenite and, thus, the mechanical behavior of Fe-Mn-Al-C steels. The SFE of three different Fe-Mn-Al-C alloys with varying aluminum (Al) content was determined in order to establish the main plastic deformation mechanism. The aim of this work is to establish a more straightforward and reliable methodology to calculate the SFE by XRD. In this effort, it was determined that uncertainty in the elastic constants can generate errors in up to 37% of the SFE. Moreover, in the studied case, for average of elastic constant values, the predominant deformation mechanism is defined, but when considering one set of constants, these can present uncertainty of 2.7 mJ/m2 and 4.4 mJ/m2 for alloys of 0% Al and 3% Al, respectively. This would lead them to be within the following plastic deformation mechanism, while for 8% Al the uncertainty is negligible.
Highlights
Given that A and G111 in Equation (1) proportionally affect the calculation of the stacking fault energy (SFE) and their values are a function of the elastic constants; these in turn were obtained from other alloy systems that do not necessarily contain the same alloys or in the same proportions
The analysis consisted of using the different elastic constants reported in the literature for other alloy systems in order to calculate the SFE of the austenitic Hadfield steel in the present work
The flow diagram presents the calculation of the SFE using data obtained by X-ray diffraction (XRD) in addition to values of the elastic constants
Summary
Manganese steel alloys containing aluminum simultaneously exhibit high mechanical resistance and ductility, or high wear resistance [1,2], as well as a high rate of work hardening. This is mainly due to plasticity mechanisms in addition to conventional slip dislocations, such as transformation induced plasticity (TRIP) [3], twinning induced plasticity (TWIP) [4], and microband induced plasticity (MBIP)) [5]. The presence of these plasticity mechanisms in this alloy is largely related to the SFE of austenite [6] which in turn dictates the final mechanical properties and dynamically recrystallized microstructures [7,8,9,10]
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