observations have been reported in the context of Fe-10Mn-9Al-4.5Ni-0.7C (wt.%) steel in Refs. . Kim has reported that the extraordinary strain hardening observed in Fe-16Mn-10Al-5Ni-0.86C (wt.%) steel primarily arises due to the short-range ordering (SRO) of the constituent atoms present in the FCC matrix. It was shown that the back stresses arising due to strain incompatibility between FCC matrix and B2 phase play a secondary role in influencing strain hardening of the aforementioned steel . This is unlike the major observation of Yang et al. , where it was initially reported that back stresses arising due to strain incompatibility between FCC matrix and B2 phase play a primary role in influencing strain hardening in B2s Fe-Mn-Al-Ni-C steels. Mozumder et al. ) have investigated the compressive deformation behaviour of Fe-10Mn-9Al-4.5Ni-0.7C (wt.%) steel between 950 to 1150 °C at a high strain rate (~10 s -1 ). The microstructure at the aforementioned deformation conditions was reported to comprise of fine intragranular B2 and GB B2 precipitates in BCC phase and FCC matrix respectively . Fig. shows the presence of dislocation cell structures near B2 precipitates in BCC GBs (in Fe-10Mn-9Al-4.5Ni-0.7C (wt.%) steel), highlighting that B2 precipitates (at BCC GBs) are non-shearable by the gliding dislocations ). In addition, κ-carbides (shearable by gliding dislocations) were observed to form within FCC grains and at FCC/BCC interfaces. It was reported that the GB B2 precipitates aid discontinuous dynamic recrystallisation (DDRX) phenomenon (through the introduction of high stored energy near FCC GBs) but retard the growth of FCC grains by retarding GB migration (of FCC GBs) ). On the contrary, BCC phase shows DDRX mechanism at FCC/BCC interfaces ). In addition, the fine intragranular B2 precipitates in BCC phase facilitate continuous dynamic recrystallisation (CDRX) in the aforementioned deformation conditions . A similar investigation (with alloy composition similar to that reported in Ref. )) at a much lower strain rate (~0.001 s -1 ) by Mozumder et al. ) revealed that the mechanism of CDRX in both FCC and BCC phases is associated with progressive transformation of low-angle GBs (or sub-grain boundaries) into high-angle GBs. It was further highlighted that BCC shows DDRX (facilitated by FCC/BCC interfaces) at all temperatures ranging from 950-1150 °C whereas FCC phase exhibits DDRX at initial deformation stages (between 950 and 1150 °C) and dominant CDRX at later stages of deformation (between 950 and 1050 °C) . Most importantly, it was reported that the dissolution of B2 precipitates (present near FCC GBs) in FCC matrix promotes GB migration, leading to DDRX accompanied by twinning in FCC phase . Fig. and)