Nergy intensity of VBIT-4 Autophagy fracture in comparison in comparison with alloy (Figure 10c). On the other hand, in this case, the predominantly ductile dimple microstructure in the surface fracture can also be observed. In the fracture, a characteristic orientation on the dimples is observed, apparently corresponding to the initial dendritic structure with the ingot (Figure 10d). The fracture surface of the tensile specimen on the Al Ni alloy is the most flat, which indicates a low energy intensity of fracture in comparison with the Al0 La and Al Ce alloys (Figure 10e). The fracture mechanism is mixed; locations of ductile dimple fracture periodically alternate with areas of brittle fracture by the quasi-cleavage mechanism (Figure 10f). The formation of such an inhomogeneous fracture surface is apparently connected using the presence of huge principal eutectic particles within the cast structure with the Al Ni alloy. The fracture surfaces of the HPT-processed Ethyl Vanillate Cancer aluminum alloys right after tensile testing are shown in Figure 11. The reduction on the tensile specimen on the HPT-processed Al0 La alloy is additional significant than in as-cast state, which is the outcome of additional prolonged localized strain (Figure 11a). The fracture from the tensile specimen, also as inside the as-cast state, proceeds mostly by the ductile dimple mechanism (Figure 11b).Components 2021, 14,localized strain (Figure 11a). The fracture in the tensile specimen, also as in the as-cast state, proceeds mainly by the ductile dimple mechanism (Figure 11b). The fracture surface in the tensile specimen of the HPT-processed Al Ce alloy is flat, as well as in as-cast state (Figure 11c). The fracture mechanism is mixed; both places of 13 of 18 ductile dimple fracture and flat quasi-cleavage areas without a pronounced relief are observed (Figure 11d). A sizable number of secondary cracks with a length from 50 to 1500 m (in the whole thickness from the tensile specimen) are also observed inside the fracture.Figure 11. Fracture surfaces with the HPT-processed aluminum alloys right after tensile tests: (a,b) Al0 Figure 11. Fracture surfaces from the HPT-processed aluminum alloys soon after tensile tests: (a,b) Al0 La; (c,d) Al Ce; (e,f) Al Ni. La; (c,d) Al Ce; (e,f) Al Ni.The fracture surface in the tensile specimen from the HPT-processed Al Ce alloy The fracture surface in the tensile specimen with the HPT-processed Al Ni alloy may be the most flat, but in as-castis much more developed inThe fracture with the alloy in as-cast state is flat, too because the relief state (Figure 11c). comparison mechanism is mixed; both (Figure 11e). The fracture mechanism quasi-cleavage with quite a few compact (much less relief areas of ductile dimple fracture and flat is mixed: locations places without having a pronounced thanare observed (Figure 11d). A large number of secondary cracks having a length from 50 to 1500 (within the complete thickness on the tensile specimen) are also observed inside the fracture. The fracture surface of your tensile specimen of your HPT-processed Al Ni alloy is the most flat, but the relief is a lot more created in comparison together with the alloy in as-cast state (Figure 11e). The fracture mechanism is mixed: areas with several small (significantly less than 1 ) flat dimples and regions of brittle fracture by the quasi-cleavage mechanism are observed (Figure 11f). It must be noted that in fractures with the HPT-processed Al Ce and Al Ni alloys, the oriented and periodic structures disappear. This is because of the formation of a more uniform structure of alloys for the duration of the HPT method, namely, t.