Effect of heat treatment on microstructure and microhardness of FGH96 inertia friction welding
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摘要: 采用惯性摩擦焊接方法进行了FGH96高温合金焊接，借助光学显微镜、扫描电子显微镜、显微硬度仪对焊态和热处理态FGH96惯性摩擦焊接头组织和显微硬度进行了研究. 结果表明，焊缝中心区内发生完全动态再结晶，再结晶晶粒细小，晶粒尺寸为4.6 μm ± 0.3 μm，且二次γ′ 相完全溶解，导致硬度低于母材组织. 随着远离焊缝，二次γ′相含量逐渐增加，距焊缝1.5 mm后γ′相体积分数基本保持不变，但γ′相形貌由球形逐渐向立方体转变，导致硬度逐渐增加. 经热处理后，焊缝区域内二次γ′相的含量与形貌变化规律与焊态相似，但热处理后基材晶粒尺寸从11.4 μm ± 0.3 μm增大至13.5 μm ± 1.0 μm，是导致热处理后基材硬度较焊态较低的原因；另外热处理后三次γ′相的析出是导致热处理态焊缝硬度高于焊态的原因.Abstract: Using the inertial friction welding method, FGH96 high-temperature alloy was welded. The microstructure and properties of the welded and heat-treated FGH96 joint were studied by means of optical microscope, scanning electron microscope and microhardness tester. The results show that complete dynamic recrystallization occurs in the central area of the weld, the recrystallized grains are fine, the grain size is 4.6 μm ± 0.3 μm, and the secondary γ′ phase is completely dissolved, resulting in a lower hardness than the parent material organization. With the distance from the weld, the secondary γ′ phase content gradually increased, and the volume fraction of γ′ phase remained basically unchanged after 1.5 mm from the weld, but the γ′ phase morphology gradually changed from spherical to cubic, leading to a gradual increase in hardness. After heat treatment, the content and morphology of the secondary γ′ phase in the weld area changed similarly to the weld state, but the grain size of the base material increased from 11.4 μm ± 0.3 μm to 13.5 μm ± 1.0 μm after heat treatment, which is the reason for the lower hardness of the base material after heat treatment compared with the weld state. In addition, the precipitation of three γ′ phases after heat treatment is the reason for the higher hardness of the weld in the heat-treated state than in the welded state.
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Keywords:
- FGH96 /
- inertia friction welding /
- grain size /
- γ′ precipitated phase /
- hardness
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图 1 FGH96合金宏观组织形貌
Figure 1. Macro-organization of FGH96 alloy. (a) OM cross-sectional micrograph of IFW joints of FGH96; (b) enlarged image of area B; (c) enlarged image of area C
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图 2 FGH96焊态试样(As-weld)不同区域γ′相SEM形貌
Figure 2. Images of γ' precipitates for as-weld component by SEM observation
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图 3 FGH96热处理态试样(HT)不同区域γ′相SEM形貌
Figure 3. Images of γ' precipitates for HT component by SEM observation
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图 4 As-weld与HT试样不同区域碳化物SEM形貌
Figure 4. Images of carbites distribution by SEM observation. (a) As-weld; (b) HT
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图 5 As-weld和HT试样焊缝及附近区域晶粒尺寸和取向分布
Figure 5. Grain size and orientation distribution (inverse pole figure, IPF) for As-weld and HT components by EBSD. (a) As-weld; (b) HT
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图 6 As-weld和HT试样动态再结晶区域晶粒取向及晶界和晶粒大小统计图
Figure 6. Misorientation distribution and grain size distribution for dynamic recrystallization zone of as-weld and HT conponents by EBSD. (a) As-weld IPF; (b) As-weld grain boundary map; (c) As-weld grain size distribution; (d) HT IPF; (e) HT grain boundary map; (f) HT grain size distribution
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图 7 As-weld和HT试样基体区域晶粒取向差分布和晶粒大小统计
Figure 7. Misorientation distribution and grain size distribution for as-weld and HT base metal by EBSD. (a) As-weld IPF; (b) As-weld grain boundary map; (c) As-weld misorientation distribution; (d) As-weld grain size distribution; (e) HT IPF; (f) HT grain boundary map; (g) HT misorientation distribution; (h) HT grain size distribution
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