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Above all, the microstructural evolution Alloy SFE the CG specimen after tensile testing is similar to the Alloy SFE specimen, except that the emergence of deformation twins is postponed to a higher strain level with increasing the grain size. Discussion Features of grain size effect on the tensile deformation mechanisms For FCC metals and alloys with low SFE, SFs and deformation twins are favored in contrast to those materials with high SFE under plastic deformation 11 In the present study, systematic results indicate that grain size influences significantly on the deformation mechanisms and the structure configurations of a CuAl alloy during tensile test.

Dislocations were detected from the very small strain of 0. In the FG specimen, the planar dislocation activity was quite limited at the Alloy SFE of 0. In the MG and CG specimens, however, dislocations were highly developed at the strain of 0.

With increasing the strain, SFs multiplied significantly in the three samples, as shown in Fig. For the deformation twins, it was interesting to note that they emerged at different true strains of 0. With increasing the strain, deformation twins increased significantly in the three samples, as shown in Fig. These results indicate that with increasing the grain size, dislocation slip was highly activated, but the Alloy SFE of deformation twinning was postponed to a higher strain level. In contrast, SFs existed throughout the tensile process, indicating that SFs may contribute significantly to the plastic deformation of the CuAl alloys. Figure 4: Schematic illustration on the deformation patterns developed with increasing the tensile true strain.

Dislocations and stacking faults were detected at the small strain of 0. The numbers of dislocations, stacking faults and deformation twins were statistically estimated with increasing the strain until necking. The Alloy SFE of 0.

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X-axis is related to the tensile true strain. Full size image The above-mentioned microstructural evolution process indicates that grain size affects significantly on Alloy SFE slip, SFs and twinning activity in the CuAl alloy. It has been reported that grain refinement will make twinning difficult in the coarse-grained regime 22 Recent studies indicate that crystallographic orientation, SFE and grain size are all key parameters in determining the deformation twinning behavior of FCC materials With decreasing the grain size, dislocation slip would be increasingly inhibited and the activation of deformation twins became relatively easier at a critical grain size 27 Present results coincide with the above mentioned predictions 222327 For the SFs, Alloy SFE appeared at a small strain of 0.

In fact, recent report by Meyers et al.

Stacking-fault energy

The present paper Alloy SFE shows the importance of SFs on deformation in conventional tensile test of a polycrystalline material. In accordance with the deformation patterns, the strain-hardening behavior is also different for the three specimens. When the strain is smaller than 0. This is possibly because SFs dominate in the FG specimen but dislocations dominate in the MG and CG specimens at this early stage, and SFs can enhance strength much higher than dislocations.

However, the strain-hardening rate decreases continuously in the FG specimen since it becomes increasingly difficult to introduce more SFs or other Alloy SFE mechanisms within small grains small spaces Alloy SFE higher strains. In comparison with the FG specimen, the strain-hardening rates of the MG and CG specimens are much higher when the strain is larger than 0. In that case, the strain-hardening behaviors of the MG and CG specimens should be compared.

In contrast to the CG specimen, the strain-hardening rate is much higher for the MG specimen, as shown in Fig. This is because, for the MG specimen, the densities of dislocations and SFs are higher at the Alloy SFE stage of tensile straining in contrast to the CG specimen, as exhibited in Fig. In addition, deformation twins were also recognized when the strain approached to 0. Overall, the higher densities of dislocations and SFs and the early onset of deformation twinning are responsible for the higher strain-hardening rate for the MG specimen in comparison with the CG specimen.

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When the strain is larger than 0. Note that if the strain-hardening curve of the FG Alloy SFE was shifted to the higher strain region in Fig. This is possibly Alloy SFE the deformation mechanisms are originated mainly from SFs and deformation twinning in the later stages of strain-hardening for the three specimens.


Thus TB can impede the dislocation movement efficiently, inducing a significant increase in strength. For example, Meyers et al. In each case, the experimentally observed Hall—Petch slope for twinning is higher than that for the dislocation slip As a result, Alloy SFE those materials with low SFE where deformation twinning involves, there is always a higher strain-hardening rate.

For example, in CG FeMn In the present study, a plateau region in the MG specimen and an increased strain-hardening stage in the CG specimen appeared but different deformation patterns were obtained concerning the role of deformation twinning during tensile test. For Alloy SFE FG specimen, deformation twins were observed when the tensile strain is only 0. For the MG specimen, deformation twins did not appear until the strain approached to 0. This indicates that the plateau stage B may be not induced by deformation twins. Similarly, for the CG specimen, deformation twins did not appear until the strain of 0.

The stacking-fault energy (SFE) is a materials property on a very small scale. It is noted Alloy SFE the SFE of the brass decreases with increasing alloy content.

However, the SFE of the Cu-Al alloy decreases faster and reaches a lower minimum.‎Influences on Stacking · ‎Alloying Elements · ‎Effects of Stacking Fault. Metallic Alloys I know that by decreasing SFE makes decreasing climb phenomena. but I don't know Alloy SFE mechanism. do you help me?


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