## 2 Material and Research Methods  
The V95\(\backslash\)10% SiC aluminum matrix composite and the V95\(\backslash\)0% SiC material were manufactured using powder metallurgy technologies with and without the addition of reinforcing particles, respectively. The V95\(\backslash\)10% SiC and V95\(\backslash\)0% SiC materials were not extruded after sintering. The size of the used SiC particles with an average diameter of 3.0 \(\pm\) 0.5 \(\upmu\)m corresponded to F1200 (FEPA-Standard 42-2:2006). The V95 alloy powder particles had a shape close to a solid sphere. The particle diameter ranged between 1 and 60 \(\upmu\)m. The V95 alloy (similar to the 7075 aluminum alloy in the chemical composition) had the following chemical composition, wt%: Al 89.73, Zn 5.72, Mg 1.95, Cu 1.71, Mn 0.34, Fe 0.26, Cr 0.14, Ni 0.06, Si 0.05, Ti 0.05, and Zn 0.02. Raw material constituents of the V95\(\backslash\)10% SiC MMC and the V95\(\backslash\)0% SiC material were mixed by a vibromixer. Sintering was carried out at 470 \({}^{\circ}\)C for 60 min. The sintering pressure was 30 MPa. There were no additives for modifying the surface of the SiC particles. Particle examination and fracture surface analysis after specimen deformation were performed using a Vega II Tescan scanning electron microscope. The microstructure of the specimens before deformation was studied by the electron backscatter diffraction (EBSD) technique using a Vega II Tescan scanning electron microscope with an EBSD Oxford HKL NordlysF+ analysis accessory. Figure 1 shows the SEM image and the EBSD image of the matrix of the V95\(\backslash\)10% SiC metal matrix composite and the V95\(\backslash\)0% SiC material after sintering. When constructing EBSD images, we assumed that high-angle boundaries had a misorientation of more than 15\({}^{\circ}\) and that the low-angle boundaries were in the range from 2 to 15\({}^{\circ}\). The grain boundaries in the EBSD images are black, and the low-angle boundaries are shown in gray. Dark spots on the EBSD images correspond to places where it was impossible to determine the orientation of the matrix lattice, and they generally correspond to areas with a large accumulation of SiC particles. The scanning pitch in the EBSD analysis was 0.3 \(\upmu\)m. The size of the scanned area was 300 \(\times\) 200 \(\upmu\)m. For EBSD analysis and search for pores and microcracks, the specimens were first mechanically polished. Then, they were ion-polished by a Linda SEMPrep2 ion milling device for 30 min at an accelerating voltage of 10 kV with the angle of specimen inclination to the ion beam equal to 7\({}^{\circ}\). Cylindrical specimens were tested for compression and tension in the Instron 8801 servohydraulic experimental system. The compression specimen had a diameter of \(d_{0}=6\pm 0.05\) mm and a height of \(h_{0}=9\pm 0.05\) mm. The cylindrical tensile specimen had the following dimensions: \(d_{0}=5\pm 0.05\) mm and the length of the working part \(l_{0}=25\pm 0.1\) mm. In compression  
Figure 1: An SEM image of the microstructure of the V95\(\backslash\)10% SiC metal matrix composite (**a**); An EBSD image of V95\(\backslash\)10% SiC (**b**) and V95\(\backslash\)0% SiC sintered powder (**c**). tests, a graphite-based lubricant was used to reduce friction between the punch and the specimen. The lubricant provided the coefficient of Coulomb friction between the punch and the aluminum alloys equal to 0.09 at 300 \({}^{\circ}\)C; at temperatures of 400 and 500 \({}^{\circ}\)C, the coefficient of friction was 0.1 and 0.13, respectively. After the test, despite lubrication, the specimen became barrel-shaped (Figure 2) in the entire deformation temperature range. In order to determine the stress-strain state evolution in the specimen during the test, its computational model was constructed and solved by the finite element method in the DEFORM program. An isothermal viscoplastic model with isotropic strain hardening was adopted for the specimen material.