On High Temperature Tensile Fracture Behavior of 316LN Austenitic Stainless Steel

doi:10.11901/1005.3093.2014.120

Chinese Journal of Materials Research

2014, Vol. 28

Issue (7): 481-489 DOI: 10.11901/1005.3093.2014.120

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On High Temperature Tensile Fracture Behavior of 316LN Austenitic Stainless Steel

Congfeng WU¹,Shilei LI¹,Hailong ZHANG¹,Xitao WANG^1,^**(

),Genqi WANG²

1. State Key Laboratory for Advanced Metals and Materials, University of Science and Technology Beijing, Beijing 100083
2. Yantai Taihai Marnoir Nuclear Equipment Co. Ltd., Yantai 264003

Cite this article:

Congfeng WU,Shilei LI,Hailong ZHANG,Xitao WANG,Genqi WANG. On High Temperature Tensile Fracture Behavior of 316LN Austenitic Stainless Steel. Chinese Journal of Materials Research, 2014, 28(7): 481-489.

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Abstract

Hot ductility, stress-strain behavior and high temperature tensile fracture behavior of wrought 316LN stainless steel were investigated. Hot tensile tests were carried out on a Gleeble 1500D thermal simulator system at a strain rate of 0.5 s^-1 over the temperature range 650-1300℃. The percentage reduction of area (RA) decreased with the increasing deformation temperature over the range of 650-850℃, and then starting from 850℃, it began to increase dramatically with values over 85% above 1000℃. When the deformation temperature comes to 1300℃, RA decreased sharply as a result of the grain coarsening due to over-heating. With the help of optical microscopy, dynamic recrystallization (DRX) was observed for the steel deformed at temperature over 1000℃. The enhancement of ductility induced by DRX was considered to play an important role in inhibition of the crack propagation. The high temperature tensile failure process of 316LN includes the nucleation, growth, and aggregation of microscopic cavities. The SEM/EDS results show that the sulfide and alumina at grain boundaries may be responsible to the formation process of cracks.

Key words: metallic materials austenitic stainless steel hot ductility hot tensile dynamic recrystallization fracture behavior

Received: 14 March 2014

Fund: *Supported by National High Technology Research and Development Program of China No.2012AA03A507.

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https://www.cjmr.org/EN/10.11901/1005.3093.2014.120 OR https://www.cjmr.org/EN/Y2014/V28/I7/481

Table 1 Chemical composition of austenitic stainless steel 316LN (mass fraction, %)

Fig.1 Metallographic photograph (a) and grain size (b) of 316LN

Fig.2 True stress–strain curves at different deformation temperatures for wrought 316LN

Fig.3 Effect of hot tension temperature on the microstructures developed in the 316LN alloy, (a) 650℃, (b) 950℃, (c) 1000℃, (d) 1100℃, (e) 1150℃, (f) 1300℃

Fig.4 Variation of the average grain size of the 316LN alloy with deformation temperature

Fig.5 Difference between homogenous strain, ε_p, and fracture strain, ε_t, as a function of deformation temperature

Fig.6 Variation of tensile peak strength (a) and percentage reduction of area (b) with deformation temperature, and the macroscopic photograph of the fractures at different temperatures (c)

Fig.7 Metallographic photograph near the fracture of specimen tensioned at 1300℃

Fig.8 Characteristic curves of high temperature tensile for 316LN

Fig.9 Fracture morphologies of the 316LN tensile samples, (a) 650℃, (b) 750℃, (c) 850℃, (d) 950℃, (e) 1000℃, (f) 1100℃

Fig.10 EDS analysis of the particles in the dimple of the 316LN tensile samples, (a) 650℃, (b) 700℃, (c) 850℃, (d) 1100℃

Fig.11 Formation process of microvoids in the tensile samples of 316LN, (a) the schematic diagram of dimple formation, (b) the cavities near the fracture at 1000℃, (c) the cavities near the fracture at 850℃, (d) the cavities near the fracture at 1100℃

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