Effect of High-Temperature Ageing on Microstructure and Creep Properties of S31042 Heat-Resistant Steel

doi:10.11900/0412.1961.2020.00109

Acta Metall Sin

2021, Vol. 57

Issue (1): 82-94 DOI: 10.11900/0412.1961.2020.00109

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Effect of High-Temperature Ageing on Microstructure and Creep Properties of S31042 Heat-Resistant Steel

GUO Qianying¹, LI Yanmo², CHEN Bin², DING Ran¹, YU Liming¹, LIU Yongchang¹(

)

^1.State Key Laboratory of Hydraulic Engineering Simulation and Safety, School of Materials Science and Engineering, Tianjin University, Tianjin 300354, China
^2.Luoyang Ship Material Research Institute, Luoyang 471023, China

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GUO Qianying, LI Yanmo, CHEN Bin, DING Ran, YU Liming, LIU Yongchang. Effect of High-Temperature Ageing on Microstructure and Creep Properties of S31042 Heat-Resistant Steel. Acta Metall Sin, 2021, 57(1): 82-94.

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Abstract

S31042 steel is a typical 25Cr-20Ni-type austenitic heat-resistant steel with excellent oxidation and corrosion resistance, and its creep rupture strength can be improved by the addition of Nb and N. This austenitic steel is widely used in superheater and reheater in ultrasupercritical power plants. At high temperatures, its performance is associated with the formation and evolution of Z, MX, and M₂₃C₆ phases. Till date, few studies have addressed the precipitation behavior of the Z phase in austenitic steel and the reinforcing mechanism of different M₂₃C₆ phases remains unclear. To clarify this, the ageing treatment of S31042 steel was performed at 1050^oC, and the evolution behavior, thermal stability, and strengthening mechanism of the precipitates during creep tests were investigated. Furthermore, the relation between precipitate evolution and high-temperature performance was elucidated via OM, SEM, TEM, and creep tests. The supersaturation degree of the alloying components in solution-treated S31042 steel decreased after ageing at 1050^oC and the driving force for M₂₃C₆ phase formation became smaller, resulting in a discontinuous distribution of the rod-like M₂₃C₆ phase along the austenite grain boundaries during the creep tests. At high stress levels, this discontinuous distribution of the rod-like M₂₃C₆ phase along the austenite grain boundaries increased the resistance to grain boundary sliding without changing the ductility, thus improving the rupture ductility of the steel. At low stress levels, the strengthening effects of the M₂₃C₆ phase discontinuously distributed along the austenite grain boundaries in aged steel were not as strong as those in solution-treated steel.

Key words: S31042 steel ageing creep rupture precipitate high-temperature performance

Received: 02 April 2020

ZTFLH:

TG132.33

Fund: National Natural Science Foundation of China(U1660201)

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	Qianying GUO
	Yanmo LI
	Bin CHEN
	Ran DING
	Liming YU
	Yongchang LIU

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https://www.ams.org.cn/EN/10.11900/0412.1961.2020.00109 OR https://www.ams.org.cn/EN/Y2021/V57/I1/82

Fig.1 OM images (a, b), SEM image (c), and EDS result (d) of solution-treated (a) and ageing-treated (b-d) S31042 steel samples

Fig.2 TEM images (a, c) and EDS (b, d) of the precipitates in solution-treated (a, b) and ageing-treated (c, d) S31042 steel samples

Fig.3 TEM (a, c) and HRTEM (b) images, and SAED pattern (d) of intragranular precipitates of solution-treated (a, b) and ageing-treated (c, d) S31042 steel samples after creep at 700^oC under 200 MPa for 505 h (a, b) and 354 h (c, d)

Fig.4 SEM images of intragranular precipitates in solution-treated (a-c) and ageing-treated (d-f) S31042 steel samples after creep at 700^oC under 200 MPa for 100 h (a, d), 250 h (b, e), 505 h (c), and 354 h (f)

Fig.5 TEM image (a) and SAED pattern (b) of the grain boundary precipitates in solution-treated S31042 steel sample after creep at 700^oC under 200 MPa for 505 h

Fig.6 TEM images (a, c, d) and SAED pattern (b) of the grain boundary precipitates in ageing-treated S31042 steel sample after creep at 700^oC under 200 MPa for 354 h

Fig.7 SEM images of the grain boundary precipitates in solution-treated (a-c) and ageing-treated (d-f) S31042 steel samples after creep at 700^oC under 200 MPa for 100 h (a, d), 250 h (b, e), 505 h (c) and 354 h (f)

Fig.8 Creep strain-time curves (a) and creep stress-rupture time curves (b) of solution-treated and ageing-treated S31042 steel samples crept at 700^oC under different stresses

Fig.9 Morphologies of fracture surfaces of solution-treated (a-d) and ageing-treated (e-h) S31042 steel samples after creep at 700^oC under 300 MPa (a, e), 250 MPa (b, f), 220 MPa (c, g), and 200 MPa (d, h)

Fig.10 Creep fracture profiles on longitudinal sections of solution-treated (a-c) and ageing-treated (d-f) S31042 steel samples after creep at 700^oC under 300 MPa (a, d), 250 MPa (b, e), and 220 MPa (c, f)

Fig.11 Creep fracture profiles on longitudinal sections (a, b) and microstructures near fracture surface (c, d) of solution-treated (a, c) and ageing-treated (b, d) S31042 steel samples after creep at 700^oC under 200 MPa

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