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Subsequently, the 800, 1000, 1200, and 2000 grits with the SiC papers were used to manually grind the sample to approximately 50 µm. The disks were then electropolished using a twin-jet method in an electrolyte solution of 25% HNO3 and 75% methanol by volume around 238 K. TEM measurements were carried out using a JEM–2100F microscope with an accelerating voltage of 200 kV.
The larger the area of cleavage fracture is, the less plastic work will be absorbed in plastic deformation, and the smaller the plastic deformation will be. It results in the plastic deformation for the Ti75Fe17Sn5Mo3 and Ti75Fe15Sn5Mo5 alloys being smaller than while that for the Ti75Fe19Sn5Mo1 alloy. The results are consistent with the mechanical experimental data observed Table 1. In Figure 9b, a small amount of the intergranular fracture-type dimples are distributed; however, the intergranular fracture-type dimples are not observed in Figure 9d,f. The grain boundary can be easily damaged when the sample is subjected to compressive stress, as a small amount of TiFe phases precipitate along the grain boundary.
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As the differences of diffraction angle for the strongest diffraction peak between the β-Ti and α-Ti phases are small, Figure 1b is a local magnification diagram of Figure 1a, to distinguish the diffraction peaks of the two phases. In fact, this result is consistent with the type of matrix phase and the second phase of Ti75Fe20Sn5 alloy , which suggests that the addition of minor Mo does not change the type of phase. Accordingly, that the addition of Mo changes the matrix phase and the second phase of Ti75Fe20Sn5 alloy. Thus, the matrix phase of the Ti75Fe19Sn5Mo1 and Ti75Fe15Sn5Mo5 alloys is the α-Ti phase, the second phases are the β-Ti and TiFe phases, while the matrix phase of Ti75Fe17Sn5Mo5 alloy is the β-Ti phase, and the second phases are the α-Ti and TiFe phases. The surface morphology of the high entropy alloys after electrochemical corrosion is shown in Figure 4. The surface was etched after electrochemical corrosion for 60 min.
The phenomenon can be explained by using the grain boundary wetting . In the reported Ti–Fe, Ti–Co, Ti–Fe–Sn alloys, the continuous and discontinuous layers that are composed of the α-Ti phases are the complete and non-complete wetting of the grain boundary , respectively. In Figure 2b, the continuous layer that is formed by a large number of α-Ti phases at the boundary is the complete wetting of the gain boundary, as shown in the letter P in Figure 2b.
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Ti75Fe19Sn5Mo1, Ti75Fe17Sn5Mo3, Ti75Fe15Sn5Mo5. Musil, J.; Kunc, F.; Zeman, H.; Poláková, H. Relationships between hardness, Young’s modulus and elastic recovery in hard nanocomposite coatings. Technol. Louzguine, D.V.; Kato, H.; Inoue, A. High strength and ductile binary Ti–Fe composite alloy. Cao, S.Z.; Xia, S.L.; Chen, Y.Y.; Xu, L.J.; Wang, X.P.; Han, J.C.; Jia, Y. Phase transformations of the L12-Ti3Al phase in γ-TiAl alloy.
In Figure 4f, the diffraction spots of BCC β-Ti phase are electron diffraction in Figure 4e. The crystal band axis of the β-Ti phase is [1¯13], and the three corresponding diffraction planes of , (2¯11¯), and (1¯21¯) is also labeled in Figure 4f, respectively. The melt containing Ti–Mo and Fe–Mo clusters can form solid solution during cooling. In addition, the interaction forces of Fe–Sn and Mo–Sn atom pairs are weak, and the solid solution is easy to form in the alloy solution during the cooling due to the positive heat of mixing of Fe–Sn and Sn–Mo atom pairs . Therefore, when a small amount of Mo element replaces Fe element, no intermetallic compound containing Mo element can form. The addition of Mo changes the concentration of clusters containing Fe in alloy solution, which results the content of TiFe intermetallics decreasing.
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Trans. Zhao, G.H.; Ketov, S.V.; Mao, H.H.; Borgenstam, A.; Louzguine-Luzgin, D.V. Ti–Fe–Sn–Nb hypoeutectic alloys with superb yield strength and significant strain-hardening. Scripta Mater. T value of Ti75Fe20Sn5 alloy and thus improve the safety in the application of engineering materials. The microstructures of the samples were observed by transmission electron microscope and the samples with thickness of 300–500 µm were cut from as-cast samples.
The electrochemical corrosion behavior of the high entropy alloys was basically the same, the corrosion mainly occurred at the grain boundary due to interdendritic segregation. The corrosion degree of the three high entropy alloys was different from each other, which corresponds to different corrosion properties. A small number of corrosion particles were attached to the surface of TiZrTaNbMo alloy, and no obvious corrosion was observed, denoting excellent corrosion resistance as shown in Figure 4b. Severe corrosion occured on the surface of TiZrTaNbSn alloy, and there was a large number of corrosion pits and cracks on the surface as shown in Figure 4c.
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Moreover, the mechanical properties were improved after the addition of Mo element, which showed better biocompatibility than pure titanium and stainless steel . The effect of elements can not only affect the mechanical properties, but also the electrochemical property which is a key parameter for biological materials . Alloying designation is still a hot topic in material research, especially for the high entropy alloy, due to the complex element interactions. Figure 9 shows the fracture morphology of Ti–Fe–Sn–Mo samples compressed at room temperature. A large area of ductile fracture is observed in Figure 9a for the fracture morphology of the Ti75Fe19Sn5Mo1 alloy.
The movement of dislocation in the grain boundary is affected by the grain boundary, which results in the stress concentration caused at the grain boundary. When the concentration stress reaches the grain boundary strength, the crack at the grain boundary leads to the formation of dimples of intergranular fracture. Figure 2 shows the microstructure of the Ti–Fe–Sn–Mo alloys.
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The microstructure of TiZrTaNb, TiZrTaNbMo and TiZrTaNbSn alloys is dendrite with single BCC structures. The addition of Mo and Sn elements promotes dendrite growth and interdendritic segregation. The microstructure and element distribution of different high entropy alloys were analyzed by SEM and EDS as shown in Figure 2. The microstructure showed a bright region and dark region in BSE mode corresponding to the dendrite and interdendritic, which resulted from the element segregation.
Li, P.Y.; Zhang, H.; Tong, T.; He, Z.R. The rapidly solidified β-type Ti–Fe–Sn alloys with high specific strength and low elastic modulus. Alloys Compds. The continuity of the α-Ti phase for the Ti75Fe15Sn5Mo5 alloy almost disappears in Figure 2f. A large number of discontinuous independent grains of the α-Ti phase can be observed in Figure 2f.
For hypereutectic Ti–Fe alloys, the high content of brittle TiFe phase leads to the low ductility of the alloys. It is necessary to reduce the content of Fe to control the content of TiFe phase. Therefore, some researchers choose the Ti70.5Fe29.5 eutectic component as base alloy . When the minor Sn and Nb elements are added into eutectic Ti70.5Fe29.5 alloy, the grain size is refined and the content of TiFe phase is further reduced, which can improve the strength and ductility of the Ti–Fe-based alloys .
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In addition, the more the Mo content is, the less the TiFe phase intermetallic compounds precipitate. This is consistent with the volume fraction that was calculated by XRD. The volume fraction of TiFe phase decreases with the increase of Mo content. The high Fe content results in deposition along the grain boundary of Ti phase.
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