Effect of Short-Range Ordering on the Tension-Tension Fatigue Deformation Behavior and Damage Mechanisms of Cu-Mn Alloys with High Stacking Fault Energies
HAN Dong1, ZHANG Yanjie1, LI Xiaowu1,2()
1.Department of Materials Physics and Chemistry, School of Materials Science and Engineering, Northeastern University, Shenyang 110819, China 2.Key Laboratory for Anisotropy and Texture of Materials, Ministry of Education, Northeastern University, Shenyang 110819, China
Cite this article:
HAN Dong, ZHANG Yanjie, LI Xiaowu. Effect of Short-Range Ordering on the Tension-Tension Fatigue Deformation Behavior and Damage Mechanisms of Cu-Mn Alloys with High Stacking Fault Energies. Acta Metall Sin, 2022, 58(9): 1208-1220.
The cyclic-deformation mechanism of face-centered cubic (fcc) pure metals or single-phase alloys, i.e., decreasing the stacking fault energy (SFE) of materials through alloying could lead to the transition of dislocation slip mode from wavy slip to planar slip, thereby, improving fatigue properties has been achieved after extensive research. However, except for diminishing SFE, alloying treatment can increase the degree of short-range ordering (SRO) in the alloy, which could equally promote the activation of planar slip just as the lower SFE does in alloys. However, most studies only emphasized the unilateral effect of SFE but ignored the action of SRO. For some single-phase fcc alloys, such as Cu-Mn, Cu-Ni, and some high-entropy alloys, the effect of SRO cannot be ignored. Therefore, in this study, the high SFE Cu-Mn alloys with different SRO degrees were selected as the target materials and general rules and micromechanisms for the effect of SRO on their tension-tension fatigue deformation and damage behavior were investigated under different stress amplitudes. The results show that with the increase of SRO degree, the dislocation slip mode changes from wavy to planar slip. Fatigue-cracking mode changes from dominating intergranular cracking to slip-band cracking, and the tension-tension fatigue life of Cu-Mn alloys is improved. The abovementioned effects are manifested as a synchronous improvement of fatigue strength coefficient ($σ^{'}_{f}$) and fatigue strength exponent (b) in the Basquin relation. The analysis shows that the enlargement of $σ^{'}_{f}$ is mainly owing to the solid solution strengthening of Mn element, and the planar-slip enhanced work-hardening capacity, whereas the increase in b stems from the higher deformation uniformity and slip reversibility governed by planar slip. In summary, this study provides guide for improving the fatigue properties of fcc metals.
Table 1 Stress amplitudes of Cu-Mn alloys in tension-tension fatigue test
Fig.1 OM images of the initial microstructures of Cu-5%Mn (a), Cu-10%Mn (b), Cu-15%Mn (c), and Cu-20%Mn (d) alloys
Fig.2 XRD spectra of Cu-Mn alloys
Alloy
Rm / MPa
Rp0.2 / MPa
δt / %
δu / %
Cu-5%Mn
285
79
55.2
46.5
Cu-10%Mn
320
95
56.2
48.5
Cu-15%Mn
338
107
56.9
48.7
Cu-20%Mn
365
115
56.9
52.5
Table 2 Mechanical properties of Cu-Mn alloys with different Mn contents at room temperature[16]
Fig.3 Stress amplitude-number of reversals to failure (S-N) curves of Cu-Mn alloys with different Mn contents
Fig.4 Relationship between the fatigue strength coefficient (σ) and static mechanical properties in Cu-Mn alloys (a) comparison of σ and true ultimate tensile strength (σT) (b) relationship between σ and strength
Fig.5 SEM images showing the surface morphologies and damage features of Cu-5%Mn (a), Cu-10%Mn (b), Cu-15%Mn (c), and Cu-20%Mn (d) alloys fatigued at stress amplitude of 90 MPa
Fig.6 SEM images showing the damage features of Cu-15%Mn (a) and Cu-20%Mn (b) alloys at stress amplitude of 115 MPa (Arrow in Fig.6a shows the crack propagation direction, and sign A represents the position of the crack turning to the intergranular propagation, inset in Fig.6b shows the locally enlarged image)
Fig.7 Effect of the stress amplitude on the fatigue damage and cracking behaviors in tension-tension fatigue of Cu-20%Mn alloy (GB refers to grain boundary, and SB represents slip band) (a) 90 MPa (b) 115 MPa (c) 160 MPa
Fig.8 TEM images of Cu-5%Mn (a), Cu-10%Mn (b), Cu-15%Mn (c), and Cu-20%Mn (d) alloys fatigued at low stress amplitude of 90 MPa
Fig.9 TEM images of Cu-5%Mn (a), Cu-10%Mn (b, c), Cu-15%Mn (d), and Cu-20%Mn (e) alloys fatigued at an intermediate stress amplitude of 115 MPa
Fig.10 TEM images of Cu-5%Mn (a), Cu-10%Mn (b), Cu-15%Mn (c), and Cu-20%Mn (d) alloys fatigued at a high stress amplitude of 130 MPa
Fig.11 Schematic of S-N curves in a lg-lg scale showing the effect of σ and fatigue strength exponent (b) on the fatigue properties of the alloy
Fig.12 Relationship between σ and Rm in some typical fcc metals[20,34,36-38]
Fig.13 Schematics showing the effect of slip mode on the intergranular deformation homogeneity of Cu-Mn alloys (a) wavy slip (b) planar slip
Fig.14 SEM images showing the morphologies of fatigue source zone on the fracture surface of Cu-5%Mn (a), Cu-10%Mn (b), Cu-15%Mn (c), and Cu-20%Mn (d) alloys fatigued at a stress amplitude of 90 MPa
Fig.15 Schematic showing the effect of short-range ordering (SRO) on the tension-tension fatigue properties and deformation microstructures of Cu-Mn alloys
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