Fig. 1. EBSD inverse pole figure (IPF) (a) and phase maps for the homogenized Al0.5CoCrFeMnNi (b). (c) BSE-SEM micrograph of the homogenized Al0.5CoCrFeMnNi at low magnification. (d) BSE-SEM micrograph of a BCC phase. (e) BSE-SEM micrograph of a BCC phase in #4 marked in (d) at high magnification.

Fig. 2. TEM micrographs and selected area diffraction patterns of the Al0.5CoCrFeMnNi as processed by HRDSR at 673 K (a) and CoCrFeMnNi as processed by HRDSR at room temperature (b). The EBSD IPF (c), phase (d) and GB maps (e) of the Al0.5CoCrFeMnNi as processed by HRDSR. In the GB map, low angle boundaries (2°-5°) are in blue, intermediate angle boundaries (5°-15°) are in yellow and high angle boundaries (>15°) are in red.

Fig. 3. The variation in the Vickers hardness of the Al0.5CoCrFeMnNi samples as processed by HRDSR and homogenized as a function of temperature at a given annealing time of 1 h.

Fig. 4. XRD curves of samples homogenized (a) and processed by HRDSR (b) before and after heat treatment for 1 h at several temperatures.

Fig. 5. The engineering stress-engineering strain curves for the homogenized (a) and samples processedby HRDSR (b) before and after heat treatment at their peak hardness temperatures (i.e., at 973 K for the homogenized sample and 873 K for the sample processed with HRDSR) for different annealing times.

Fig. 6. The engineering stress-engineering strain curves of the Al0.5CoCrFeMnNi processed by HRDSR (a), homogenized Al0.5CoCrFeMnNi (b) and homogenized CoCrFeMnNi and CoCrFeMnNi processed by HRDSR annealed at 1273 K (c) for different annealing times between 3 min and 1 h.

Fig. 7. The phase map (a) and the SEM micrograph (b) of the homogenized sample after annealing at 1273 K for 60 min.

Fig. 8. The IPF maps, phase maps and GB maps of Al0.5CoCrFeMnNi processed by HRDSR after annealing for annealing times of 5 min (a), 15 min (b) and 60 min (c) at 1273 K. (d) The IPF maps, phase maps and GB maps of CoCrFeMnNi processed by HRDSR after annealing for 5 min at 1273 K.

Fig. 9. (a) The fraction of DRXed grains, (b) the fraction of high-angle grain boundaries (HAGBs), (c) the volume fraction of the BCC phase, (d) the size and aspect ratio (given as numbers next to symbols) of the BCC phase particles, (e) the grain size of the FCC matrix phase, and (f) the fraction of annealing twins in the FCC matrix, which were measured from the EBSD data of the homogenized and HRDSRprocessed samples after annealing at 1273 K for different annealing times.

Fig. 10. TEM micrographs of Al0.5CoCrFeMnNi processed by HRDSR (a) and CoCrFeMnNi (b) after annealing at 1273 K for 5 min.

Fig. 11. The strain hardening rates of the (a) homogenized and (b) HRDSRprocessed Al0.5CoCrFeMnNi and (c) the homogenized and HRDSRprocessed CoCrFeMnNi as a function of the true strain.

Fig. 12. The KM plots for the homogenized (a) and Al0.5CoCrFeMnNi processed by HRDSR (b) annealed at different temperatures. The plots of $\left( \sigma -{{\sigma }_{\text{y}}} \right)\theta $ vs. $\left( \sigma -{{\sigma }_{\text{y}}} \right)$ for the homogenized Al0.5CoCrFeMnNi before and after annealing (c) and the Al0.5CoCrFeMnNi processed by HRDSR before and after annealing (d), respectively. (e) The ${{\theta }_{\text{h}}}$ values plotted as a function of annealing time. (f) The strain-hardening-exponent (n) values of the homogenized and HRDSRprocessed samples before and after annealing plotted as a function of annealing time.

Fig. 13. The plots for the FCC phase and BCC phase in Al0.5CoCrFeMnNi and the FCC phase in CoCrFeMnNi [14] for determining the C (m3 s-1) values of Eq. (3).

Fig. 14. Comparison of the experimentally measured yield strength values and the yield strength values calculated by Eqs. (4) and (10).

Fig. 15. The curves for the yield strength vs. uniform elongation (a) and tensile strength vs. uniform elongation (b) for the Al0.5CoCrFeMnNi, CoCrFeMnNi and Fe41Mn25Ni24Co8Cr2 fabricated using cold rolling or severe plastic deformation studied by several investigators [[6], [7], [8], [9], [10], [11]], including the data presented in this study.