Microstructure Evolution and Mechanical Properties of Dissimilar Material Diffusion-Bonded Joint for High Cr Ferrite Heat-Resistant Steel and Austenitic Heat-Resistant Steel

doi:10.11900/0412.1961.2020.00446

Acta Metall Sin

2022, Vol. 58

Issue (2): 141-154 DOI: 10.11900/0412.1961.2020.00446

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Microstructure Evolution and Mechanical Properties of Dissimilar Material Diffusion-Bonded Joint for High Cr Ferrite Heat-Resistant Steel and Austenitic Heat-Resistant Steel

HUA Yu¹, CHEN Jianguo², YU Liming¹, SI Yonghong², LIU Chenxi¹(

), LI Huijun¹, LIU Yongchang¹(

)

^1.State Key Laboratory of Hydraulic Engineering Simulation and Safety, School of Materials Science and Engineering, Tianjin University, Tianjin 300354, China
^2.Tianjin Special Equipment Inspection Institute, Tianjin 300192, China

Cite this article:

HUA Yu, CHEN Jianguo, YU Liming, SI Yonghong, LIU Chenxi, LI Huijun, LIU Yongchang. Microstructure Evolution and Mechanical Properties of Dissimilar Material Diffusion-Bonded Joint for High Cr Ferrite Heat-Resistant Steel and Austenitic Heat-Resistant Steel. Acta Metall Sin, 2022, 58(2): 141-154.

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Abstract

High Cr ferrite heat-resistant steel has excellent geometric structure stability, low radiation swelling rate, and good corrosion resistance of liquid metal. TP347H austenitic heat-resistant steel is based on the traditional 18-8 austenitic steel with the addition of a certain amount of Nb and a small amount of N to precipitate MX-type carbonitride, which results in superior high-temperature properties. Steam with high temperature and pressure flowing through supercritical thermal power units may exhibit heterogeneous connections between high Cr ferrite and austenitic heat-resistant steel components in the supercritical thermal power units. In this study, the vacuum diffusion-bonding of dissimilar materials between high Cr ferritic and TP347H austenitic heat-resistant steel was performed, the effects of diffusion-bonding time and post weld heat treatment (PWHT) process on the microstructural evolution and mechanical properties of the diffusion-affected zone was examined. The results indicated that with the extension of diffusion-bonding time, the interfacial bonding rate gradually increased. The interaction due to the difference in deformation storage energy and dislocation slips resulted in dynamic recrystallization, and the fine grains formed at the diffusion-bonding interface evolved into a serrated interface. Fine and dispersed MX and M₂₃C₆ phases were precipitated in the austenite grain boundaries and at the grain boundaries of the diffusion-bonding zone. After PWHT, the grains in the diffusion-bonding zone were further refined, dislocations were stable, dislocation density reduced, small-angle grain boundaries increased, and element diffusion was more sufficient. Tensile tests at different temperatures showed that the fractured sites were all in the matrix, which indicates that high-quality diffusion-bonding joints of dissimilar materials were achieved.

Key words: high Cr ferritic heat-resistant steel TP347H austenitic heat-resistant steel diffusion-bonding microstructure mechanical property

Received: 04 November 2020

ZTFLH:

TG457.1

Fund: National Natural Science Foundation of China(52034004);Tianjin Natural Science Foundation(18JCQNJC03300)

About author: LIU Chenxi, associate professor, Tel: (022)85356410, E-mail: cxliu@tju.edu.cnLIU Yongchang, professor, Tel: (022)85356410, E-mail: ycliu@tju.edu.cn

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	Yu HUA
	Jianguo CHEN
	Liming YU
	Yonghong SI
	Chenxi LIU
	Huijun LI
	Yongchang LIU

URL:

https://www.ams.org.cn/EN/10.11900/0412.1961.2020.00446 OR https://www.ams.org.cn/EN/Y2022/V58/I2/141

Table 1 Chemical compositions of materials for experiments

Fig.1 Sketch diagrams for the process curves

Fig.2 Schematics of tensile specimen (unit: mm, R_a—roughness)

Fig.3 OM images of the parent metals for diffusion-bonding

Fig.4 Low (a1-e1) and high (a2-e2) magnified OM images and SEM images (a3-e3) showing the microstructures of the diffusion-bonding joints with the bonding temperature of 1050^oC and bonding stress of 15 MPa, for the different bonding time

Fig.5 Interfacial bonding percentage as a function of the diffusion-bonding time

Fig.6 SEM images of the diffusion-bonding joints with the bonding temperature of 1050^oC, bonding stress of 15 MPa, and the bonding time of 120 min after PWHT

Fig.7 EBSD analyses of the diffusion-bonding joint area before PWHT

Fig.8 EBSD analyses of the diffusion-bonding joint area after PWHT

Fig.9 TEM analyses of the diffusion-bonding joints before PWHT

Fig.10 TEM analyses of the diffusion-bonding joints after PWHT

Fig.11 EDS line scanning results of the diffusion-bonding joint after PWHT

Table 2 Tensile test results of the diffusion-bonding joints before and after PWHT

Fig.12 Physical drawing of tensile fracture specimen

Fig.13 Engineering stress-strain curves of the diffusion-bonding joints before and after PWHT under testing temperatures of 25^oC (a) and 600^oC (b)

Fig.14 Low (a, c) and high (b, d) magnified tensile fracture morphologies of the diffusion-bonding joints at 25^oC before (a, b) and after (c, d) PWHT

Fig.15 Low (a, c) and high (b, d) magnified tensile fracture morphologies of the diffusion-bonding joints at 600°C before (a, b) and after (c, d) PWHT

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