Second-phase Precipitation in Mo/Nb/Ta/Ti Minor-alloyed 310S Stainless Steel at 700℃

doi:10.11901/1005.3093.2017.627

Chinese Journal of Materials Research

2018, Vol. 32

Issue (5): 371-380 DOI: 10.11901/1005.3093.2017.627

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Second-phase Precipitation in Mo/Nb/Ta/Ti Minor-alloyed 310S Stainless Steel at 700℃

Yang LV¹, Donghui WEN¹, Zhenhua WANG¹, Qing WANG¹(

), Rui TANG², Huan HE³

1 Key Laboratory of Materials Modification by Laser, Ion and Electron Beams (Ministry of Education), School of Materials Science and Engineering, Dalian University of Technology, Dalian 116024, China
2 Science and Technology on Reactor Fuel and Materials Laboratory, Nuclear Power Institute of China, Chengdu 610213, China
3 Guangxi Key Laboratory of Processing for Non-Ferrous Metal and Featured Materials, Nanning 530004, China

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Yang LV, Donghui WEN, Zhenhua WANG, Qing WANG, Rui TANG, Huan HE. Second-phase Precipitation in Mo/Nb/Ta/Ti Minor-alloyed 310S Stainless Steel at 700℃. Chinese Journal of Materials Research, 2018, 32(5): 371-380.

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Abstract

The microstructural stability and second-phase precipitation of austenitic stainless steels (ASSs) with high Cr and Ni contents at high temperatures affect their mechanical property directly. The effect of minor-addition of Mo, Nb, Ta, and Ti on the second-phase precipitation in a low-carbon 310S stainless steel (Fe-25Cr-22Ni-0.046C, %, mass fraction) has been investigated in the present work. Alloy ingots were prepared by vacuum arc melting, and hot rolled at 1150℃ for multiple passes into sheets. The sheet samples were then heat-treated in sequence: solid-solution at 1150℃ for 0.5 h followed by water cooling, stabilization at 900℃ for 0.5 h followed by furnace cooling, and aging treatment at 700℃ for different times (25~408 h). The steels were characterized by means of XRD, OM, SEM and TEM. Their mechanical property were examined after different treatments. Experimental results show that the co-addition of minor Mo/Nb/Ta/Ti improves the strength of the steels. However, the brittle σ-phase began to appear at the early stage of stabilization process in the Mo/Nb/Ta/Ti-modified steel, while it was not existed in the master steel 310S. During the aging process, the content of σ-phase particles increases with the increase of aging time, and the coarse Cr₂₃C₆ particles will be dissolved finally, which will deteriorate the mechanical property of the steels. Both the types and amounts of minor-alloying elements affect the second-phase precipitation, and then the microstructural stability.

Key words: metallic materials austenitic stainless steels 310S alloy micro-alloying phase precipitation microstructural stability

Received: 20 October 2017

Fund: Supported by International Science & Technology Cooperation Program of China (No. 2015DFR60370), Fundamental Research Funds for the Central Universities (No. DUT16ZD212), International Thermonuclear Experimental Reactor (ITER) Program of China (No. 2015GB121004), National Key Research and Development Plans (Nos. 2017YFB0702400 & 2017YFB0306100), Open Fund Project of Guangxi Key Laboratory of Processing for Non-Ferrous Metal and Featured Materials (No. GXKFJ16-11)

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	Yang LV
	Donghui WEN
	Zhenhua WANG
	Qing WANG
	Rui TANG
	Huan HE

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https://www.cjmr.org/EN/10.11901/1005.3093.2017.627 OR https://www.cjmr.org/EN/Y2018/V32/I5/371

Table 1 Chemical composition of alloys (%, mass fraction)

Fig.1 XRD spectra of 310S and M-310S alloys after solid-solution and 408 h-aging treatments at 700℃

Fig.2 OM (a) and SEM (b) images of M-310S alloy after solid solution treatment

Fig.3 OM and SEM images of the microstructure in 310S (a, b) and M-310S (c, d) after stabilization treatment at 900℃ for 0.5 h

Fig.5 OM and SEM images of the microstructure inM-310Salloy and agedat 700℃ for 25 h (a1 and a2), 50 h (b), 100 h (c), 200 h (d), 300 h (e) and 408 h (f1 and f2)

Fig.4 OM and SEM images of 310S aged at 700℃ for 25 h (a1 and a2), 50 h (b), 100 h (c), 200 h (d), 300 h (e) and 408 h (f1 and f2)

Table 2 Summary of types, sizes, and volume fractions (f) of the precipitated particles in the 310S and M- 310S alloys at different aging time

Fig.6 TEM bright-field images and SAED patterns of the σ-FeCr (a) and (Ta,Nb,Ti)C (b) in the aged M-310S alloy for 408 h

Fig.7 Engineering tensile stress-strain curves of the stabilized alloys at room temperature

Fig.8 Variation tendency of the microhardness H_Vwith the aging time at 700℃ of 310S and M-310S alloys, in which the H_V values at stabilization are taken as the ones of 0 h aging

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