MECHANISM OF B IN HYDROGEN-RESISTANCE J75 ALLOY

doi:10.11900/0412.1961.2015.00255

Acta Metall Sin

2015, Vol. 51

Issue (12): 1538-1544 DOI: 10.11900/0412.1961.2015.00255

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MECHANISM OF B IN HYDROGEN-RESISTANCE J75 ALLOY

Hao LIANG¹,Mingjiu ZHAO²(

),Shenghu CHEN²,Yong XU¹,Yongli WANG²,Lijian RONG²

1 Institute of Systems Engineering, China Academy of Engineering Physics, Mianyang 621900
2 Key Laboratory of Nuclear Materials and Safety Assessment, Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016

Cite this article:

Hao LIANG,Mingjiu ZHAO,Shenghu CHEN,Yong XU,Yongli WANG,Lijian RONG. MECHANISM OF B IN HYDROGEN-RESISTANCE J75 ALLOY. Acta Metall Sin, 2015, 51(12): 1538-1544.

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Abstract

With the development of hydrogen economy, the demand of structural materials with high strength suitable for service in hydrogen or hydrogen-bearing environments such as storage of hydrogen gas was incremental. An optional structural materials is J75 alloy, which is mainly strengthened by an ordered fcc γ' phase, Ni₃(Al, Ti), coherent with the austenite matrix. Investigation on J75 alloy indicated that the commercial alloy free of B would lose about half its ductility when charged with hydrogen, accompanied by a change of fracture mode from ductile rupture to brittle-appearing intergranular fracture. Otherwise, an improvement in ductility and hydrogen resistant performance was observed in the J75 alloy with trace B, however, its role in the alloy is unclear. So, in present work, mechanism of B in the J75 hydrogen-resistant alloy was investigated by means of OM, SEM, TEM, EPMA, 3DAP, SIMS, hydrogen penetration, thermal hydrogen charging experiments and tensile tests. It was found that a lot of Ti segregated at grain boundaries (GBs) in the alloy free of B, resulted in abundant precipitation of cellular η phases. However, the cellular η phase was not observed in the alloy with B, and it could be attributed to the segregation of B atoms at GBs and inhibited the segregation of Ti. A lower hydrogen diffusion coefficient was observed in the alloy with B than that in the alloy free of B by hydrogen permeation, indicating that diffusion velocity of H atoms in the alloy had been decreased by the addition of B. Moreover, segregation of B at GBs could not only inhibit the precipitation of η phases but also decrease the number of H atoms there, which would improve the hydrogen-resistant performance of the alloy.

Key words: J75 alloy B hydrogen-resistant performance η phase

Fund: Supported by National Natural Science Foundation of China and China Academy of Engineering Physics (No.U1230118) and National Natural Science Foundation of China (No.51171178)

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	Hao LIANG
	Mingjiu ZHAO
	Shenghu CHEN
	Yong XU
	Yongli WANG
	Lijian RONG

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https://www.ams.org.cn/EN/10.11900/0412.1961.2015.00255 OR https://www.ams.org.cn/EN/Y2015/V51/I12/1538

Table 1 Chemical compositions of Fe-Ni base austenite J75 alloys with and without B (mass fraction / %)

Fig.1 OM image of 0B alloy (a), bright-field TEM (b) and HRTEM (c) images of cellular η phase at grain boundaries (GBs)

Fig.2 OM image of 20B alloy (a), TEM bright-field image (b) and SAED pattern (c) of carbide at GBs

Fig.3 Tensile fracture morphologies of 0B (a, c) and 20B (b, d) alloys before (a, b) and after (c, d) hydrogen charging

Table 2 Room temperature tensile properties of 0B and 20B alloys

Fig.4 SEM image of η phases and γ′ precipitates in 0B alloy

Table 3 Room temperature tensile properties and hydrogen-induced ductility loss of 0B and 20B alloys after hydrogen charging

Fig.5 Microstructures (a, b) and EPMA analysis of Fe (a1, b1) and Ti (a2, b2) in 0B (a~a2) and 20B (b~b2) alloys (I—intensity)

Fig.6 SIMS image of B distribution in 20B alloy

Fig.7 3DAP images of H (a) and B (b) atom distributions after hydrogen charging in 20B alloy (The box size is 8.6 nm×9.4 nm×237 nm)

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