Vacuum diffusion welding of TC4 titanium alloy and 316L stainless steel with AlCoCrNiCuAg high-entropy alloy powder interlayer
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摘要:
钛/钢扩散焊复合构件在航空航天高端制造领域有着广阔的应用前景，然而界面脆性金属间化合物是导致其接头性能劣化的主要原因，文中设计了具有液相分离特征的AlCoCrNiCuAg高熵合金粉末中间层，通过形成部分液相降低了依靠单一塑性变形对连接界面组织性能产生的不良影响，研究了在不同焊接温度作用下AlCoCrNiCuAg高熵合金中间层对TC4钛合金和316L不锈钢真空扩散接头界面组织和力学性能的影响规律.结果表明，接头典型界面结构为α-Ti + β-Ti/β-Ti/β-Ti + Ti(Fe,Ni) + Ti2Ni/Ti(Fe,Ni)/TiFe2 + Fe2Cr5Ti17/ Fe2Cr5Ti17 + λ-(Fe,Cr)2Ti + α-Fe/γ-Fe.随着焊接温度的升高，与TiFe2反应层相邻的Ti(Fe,Ni)、α-Fe等反应层厚度逐渐增加，同时接头孔洞等缺陷大幅减少，扩散焊接头抗剪强度在二者协同作用下逐渐升高，在1 010 ℃ /30 min时达到最大181 MPa.高熵合金中间层抑制了接头中TiFe2等脆性金属间化合物的产生，促进了韧性(Fe, Ni)固溶相的形成，实现了钛/钢的可靠连接.
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关键词:
- 高熵合金 /
- 钛合金/不锈钢异质金属 /
- 真空扩散焊 /
- 微观组织演变 /
- 力学性能
Abstract:Titanium/steel composite components by diffusion welding have a broad application prospect in advanced aerospace manufacturing. The IMCs are the main reason for the deterioration of the joint performance. AlCoCrNiCuAg high-entropy alloy powder interlayer with liquid phase separation was designed. By forming parts of the liquid phase, the adverse influence of single plastic deformation on the microstructure and mechanical properties of the interface was reduced. The effect of AlCoCrNiCuAg high-entropy alloy powder interlayer on the interfacial microstructure and mechanical properties of the joints between TC4 titanium alloy and 316L stainless steel by diffusion welding at different temperatures was investigated. The results show that the typical interfacial microstructure of the joints is α-Ti + β-Ti/β-Ti/β-Ti + Ti(Fe,Ni) + Ti2Ni/Ti(Fe,Ni)/TiFe2 + Fe2Cr5Ti17/ Fe2Cr5Ti17 + λ-(Fe,Cr)2Ti + α-Fe/γ-Fe. As the welding temperature increases, the thickness of Ti(Fe,Ni) and α-Fe adjacent to the TiFe2 reaction layer increases, and the defects at the joint pores are reduced. The shear strength of the joints by diffusion welding exhibits an increasing trend under the synergistic action, and the highest shear strength reaches 181 MPa at 1 010 °C for 30 min. The high-entropy alloy powder interlayer inhibits the generation of TiFe2 and other brittle IMCs and promotes the formation of the (Fe,Ni) solid solution phase, achieving a sound bonding between titanium and steel.
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图 1 丝网印刷后的试样
Figure 1. sample screen-printed. (a) surface morphologies; (b) macro image
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图 3 AlCoCrNiCuAg 高熵合金铸锭微观组织
Figure 3. Microstructure of AlCoCrNiCuAg HEA ingot. (a) low-magni fication image of the ingot; (b) magnified image of zone b in 3(a); (c) magnified image of zone c in 3(b); (d) magnified image of zone d in 3(b)
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图 4 AlCoCrNiCuAg 高熵合金铸锭元素分布情况
Figure 4. Elemental distribution of AlCoCrNiCuAg HEA ingot. (a) BEI; (b) Al; (c) Ag; (d) Co; (e) SEI; (f) Cr; (g) Cu; (h) Ni
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图 5 AlCoCrNiCuAg高熵合金粉末
Figure 5. AlCoCrNiCuAg HEA powder. (a) DSC curves; (b) XRD patterns and (c) microstructure
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图 6 不同焊接温度下接头显微组织
Figure 6. Morphology of the joints bonded at different temperatures. (a) 890 ℃; (b) 970 ℃; (c)
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图 8
1010 ℃焊接温度下接头界面元素分布情况Figure 8. Elemental distribution at the interface of the joint bonded at 1 010 ℃. (a) BEI; (b) Ti; (c) Cr; (d) Ag; (e) Al; (f) Fe; (g) Co; (h) Cu
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图 9 扩散焊接头微观组织演变示意图
Figure 9. Schematic of the microstructure evolution process. (a) physical contact and atomic diffusion; (b) eutectic phase melting and voids generating; (c) Ag-riched phase generating and shrinkage of voids; (d) growth and evolution of reaction phases
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图 11 不同焊接温度下焊接接头断裂路径
Figure 11. Fracture paths of the joints bonded at different temperatures of. (a) 890 ℃; (b) 970 ℃; (c)
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图 12 不同焊接温度下接头断口形貌
Figure 12. Fracture morphologies of the joints at different temperatures of. (a) 890 ℃; (b) 930 ℃; (c) 970 ℃; (d)
1010 ℃表 1 母材和中间层的化学成分 (质量分数，%)
Table 1 Chemical compositions of the base metals and interlayer
材料 Cr Ni Al V Mo Co Cu Ag Mn Ti Fe TC4 — — 6.1 5.7 — — — — — 余量 — 316L 16.5 10.2 — — 2.0 — — — 1.6 — 余量 HEA interlayer 13.1 21.8 6.8 — — 14.9 16.0 27.3 — — — 
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表 2 图3中标记点化学成分 (质量分数，%)
Table 2 Elemental quantitative analysis results of the marked locations in Fig. 3
位置 Al Co Cr Cu Ni Ag 可能相 P1 1.87 2.42 1.97 10.97 2.59 80.18 Ag-rich FCC P2 20.80 22.76 25.02 7.15 24.17 0.01 BCC P3 32.57 7.09 19.12 11.34 26.02 3.85 B2-NiAl P4 1.82 0.17 0.19 19.43 0.24 78.15 Ag-rich FCC P5 7.42 0.18 0.22 38.27 0.47 53.44 FCC P6 14.34 0.17 0.27 77.90 0.16 7.17 Cu-rich FCC
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表 3 图6中标记点化学成分（质量分数，%）
Table 3 Elemental quantitative analysis results of the marked locations in Fig. 6
位置 Ti Fe Al Co Cr Ni Cu Ag V 可能相 P1 73.26 0.52 18.51 0.50 1.62 0.48 0.60 2.18 2.31 β-Ti P2 49.46 1.33 7.68 2.26 1.67 2.87 1.30 32.76 0.67 β-Ti + AgTi P3 59.50 6.05 5.04 8.67 7.05 9.61 1.89 3.23 1.09 β-Ti + Ti(Fe,Ni) P4 1.15 64.07 3.76 4.55 22.64 3.62 0.02 0.08 0.11 α-(Fe,Cr) + γ-(Fe,Cr) P5 70.07 9.69 9.35 0.50 3.58 2.02 0.72 0.84 3.23 β-Ti + FeTi P6 63.98 14.96 4.17 1.33 2.41 10.14 0.76 0.22 2.02 β-Ti + Ti(Fe,Ni) + Ti2Ni P7 49.88 32.60 2.51 1.05 4.03 8.20 0.72 0.07 0.93 Ti(Fe,Ni) P8 27.55 52.01 0.59 0.24 12.34 6.76 0.06 0.02 0.43 TiFe2 + χ-Fe2Cr5Ti17 P9 8.63 60.15 0.70 0.24 23.64 6.18 0.07 0.01 0.38 χ-Fe2Cr5Ti17 + λ-(Fe,Cr)2Ti + α-Fe P10 5.66 62.71 1.35 0.22 23.74 5.67 0.21 0.01 0.43 χ-Fe2Cr5Ti17 + λ-(Fe,Cr)2Ti + α-Fe P11 0.38 66.52 0.12 0.24 17.76 14.66 0.22 0.01 0.10 γ-Fe
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表 4 图12中标记点化学成分 (质量分数，%)
Table 4 Elemental quantitative analysis results of the marked locations in Fig. 9
位置 Ti Fe Al Co Cr Ni Ni Ag 可能相 P1 30.06 56.76 1.81 0.08 7.05 10.76 0.04 0.01 TiFe2 P2 53.65 30.69 2.85 1.89 3.32 6.19 1.44 0.01 β-Ti + TiFe P3 64.90 15.11 3.18 3.10 2.18 10.12 1.30 0.11 β-Ti + Ti(Fe,Ni) P4 18.12 67.99 5.25 0.86 5.19 2.25 0.21 0.13 TiFe2 + χ + α-Fe P5 59.29 22.53 3.65 2.24 3.00 7.71 1.52 0.07 β-Ti + Ti(Fe,Ni) P6 78.26 11.29 1.62 1.54 1.44 5.22 0.59 0.03 β-Ti + Ti(Fe,Ni) P7 56.94 28.98 1.99 1.33 4.12 5.37 1.29 0.00 β-Ti + Ti(Fe,Ni) P8 24.61 53.89 0.64 0.25 13.28 4.28 0.15 0.42 Ti(Fe,Ni) + χ-Fe2Cr5Ti17
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