## 3 Results
### The Rheological Behavior and Microstructure of the Composite
Figure 8: Accumulated strain distribution in the AIMg6/10% SiC MMC specimens under 50% compression at 300, 400, and 500 \({}^{\circ}\)C.  
Figure 9: The effect of strain and strain rate on the average grain diameter depending on temperature, \({}^{\circ}\)C: (**a**) 300, (**b**) 400, (**c**) 500. The dependences are plotted from the results of the EBSD analysis of the microstructure. Figure 11: The effect of strain and strain rate on the density of low-angle boundaries depending on temperature, \({}^{\circ}\)C: (**a**) 300, (**b**) 400, (**c**) 500. The dependences are plotted from the results of the EBSD analysis of the microstructure. \begin{table}
\begin{tabular}{c c c c c c c c c c c c c} \hline \hline \multicolumn{2}{c}{\(\mathbf{Tem_{\
u}}\)\({}^{\circ}\)C} & \multicolumn{10}{c}{**300**} \\ \hline Strain & 0.12 & 0.13 & 0.17 & 0.37 & 0.40 & 0.45 & 0.58 & 0.63 & 0.63 & 0.66 & 0.73 & 0.76 \\ Strain rate, s\({}^{-1}\) & 0.83 & 0.26 & 0.05 & 2.48 & 0.8 & 0.15 & 3.85 & 1.25 & 4.18 & 1.32 & 0.24 & 0.26 \\ D, \(\mu\)m & 5.07 & 3.52 & 5.45 & 2.73 & 2.56 & 4.49 & 1.67 & 1.82 & 1.61 & 1.83 & 3.33 & 2.68 \\ \(P_{L}\) & 0.5 & 0.7 & 0.43 & 0.82 & 0.73 & 0.55 & 0.76 & 0.64 & 0.67 & 0.57 & 0.58 & 0.43 \\ \(S_{L}\), \(\mu\)m\({}^{-1}\) & 0.13 & 0.17 & 0.1 & 0.73 & 0.97 & 0.23 & 1.30 & 1.50 & 0.97 & 0.97 & 0.20 & 0.53 \\ \hline \multicolumn{2}{c}{\(\mathbf{Tem_{\
u}}\)\({}^{\circ}\)C} & \multicolumn{10}{c}{**400**} \\ \hline Strain & 0.07 & 0.11 & 0.17 & 0.34 & 0.43 & 0.49 & 0.60 & 0.63 & 0.79 & 0.88 & 0.83 & 0.92 \\ Strain rate, s\({}^{-1}\) & 0.54 & 0.22 & 0.05 & 2.32 & 0.81 & 0.15 & 4.06 & 4.29 & 1.47 & 0.25 & 1.64 & 0.28 \\ D, \(\mu\)m & 5.46 & 3.89 & 5.6 & 3.63 & 2.9 & 2.89 & 2.98 & 3.66 & 2.73 & 1.81 & 1.92 & 1.86 \\ \(P_{L}\) & 0.35 & 0.77 & 0.38 & 0.63 & 0.76 & 0.79 & 0.60 & 0.44 & 0.57 & 0.65 & 0.85 & 0.76 \\ \(S_{L}\), \(\mu\)m\({}^{-1}\) & 0.07 & 0.43 & 0.13 & 0.43 & 0.9 & 0.63 & 0.47 & 0.13 & 0.47 & 1.10 & 1.20 & 1.20 \\ \hline \multicolumn{2}{c}{\(\mathbf{Tem_{\
u}}\)\({}^{\circ}\)C} & \multicolumn{10}{c}{**500**} \\ \hline Strain & 0.02 & 0.05 & 0.1 & 0.33 & 0.4 & 0.51 & 0.66 & 0.73 & 0.77 & 0.92 & 0.97 & 1.15 \\ Strain rate, s\({}^{-1}\) & 0.3 & 0.1 & 0.03 & 2.36 & 0.81 & 0.16 & 4.57 & 5.00 & 1.54 & 1.84 & 0.29 & 0.35 \\ D, \(\mu\)m & 5.13 & 2.8 The comparison of the initial microstructure (Figure 1a) with the microstructure formed during deformation (Figures 5-7) testifies that, after high-temperature deformation, small grains appear in the microstructure. It can also be seen that inside the initial large grains, there are subgrains with low-angle boundaries (highlighted in gray in Figures 5-7). At the same time, new elongated grains and nearly equiaxed ones are formed in the initial elongated grains along the composite matrix flow direction; the prevailing majority of them retain their geometry throughout the range of temperatures and strain rates under study. At a strain of at least 0.7, some subgrains have an almost equiaxed shape, and the other ones are elongated but with a greater equiaxiality coefficient than the grains containing these subgrains. Another experimentally determined fact is that the matrix grains are formed inside large, deformed grains. Thus, we can say that the grain formation process in the composite matrix is associated with the mechanism of continuous dynamic recrystallization [23; 43]. At the same time, the subboundary migration rate in the matrix is high enough for a significant number of the subgrains to remain equiaxed. Note also that the high-angle boundaries of the new grains also have a migration rate sufficient for a significant part of the recrystallized grains to be equiaxed at strains of at least 0.7. The obtained experimental data confirm the need to construct physically based mathematical models of microstructure evolution that take into account the migration of low- and high-angle boundaries during continuous dynamic recrystallization [43; 44; 62; 63].