HIGH TEMPERATURE CREEP DEFORMATION MECHANISM OF BSTMUF601 SUPERALLOY

doi:10.11900/0412.1961.2014.00293

Acta Metall Sin

2015, Vol. 51

Issue (3): 349-356 DOI: 10.11900/0412.1961.2014.00293

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HIGH TEMPERATURE CREEP DEFORMATION MECHANISM OF BSTMUF601 SUPERALLOY

SUN Chaoyang¹(

), SHI Bing¹, WU Chuanbiao¹, YE Naiwei², MA Tianjun³, XU Wenliang³, YANG Jing¹

1 School of Mechanical and Engineering, University of Science and Technology Beijing, Beijing 100083
2 Ningbo Baoxin Stainless Steel Co. Ltd., Ningbo 315807
3 Special Steel Business Unit, Baoshan Iron & Steel Co. Ltd., Shanghai 200940

Cite this article:

SUN Chaoyang, SHI Bing, WU Chuanbiao, YE Naiwei, MA Tianjun, XU Wenliang, YANG Jing. HIGH TEMPERATURE CREEP DEFORMATION MECHANISM OF BSTMUF601 SUPERALLOY. Acta Metall Sin, 2015, 51(3): 349-356.

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Abstract

Muffle tube is the core component in a large bright annealing muffle furnace. A lot of defects will be found on the muffle tube after long-term application under high temperature, self-weight and uneven temperature conditions, and among them creep deformation is serious, directly affecting the usability and life expectancy of muffle tube. High temperature creep and rupture properties are important indicators of the muffle tube material, and BSTMUF601 nickel-based superalloy materials are commonly used in a muffle tube. Because of good oxidation resistance at high temperatures, high strength and good creep resistance, nickel-base superalloy materials are taken seriously especially its creep mechanism. For different alloys or alloys in different conditions, the conclusions about creep mechanism are different. So the research of each alloy is necessary. Creep tests of BSTMUF601 superalloy for elevated temperature were carried out under different temperatures and stresses. The creep deformation characteristic of BSTMUF601 superalloy was investigated based on the creep curves. And then, a creep constitutive model for elevated temperature was proposed by introducing a modified θ projection method, which contained three stages of creep. The predicted results by using the model are in good agreement with the experimental results. The average relative error of the model fitted is 1.86%. Compared with the model ignored the second stage of creep and the model ignored the first stage of creep, the average relative error is reduced 0.10% and 6.02%, respectively. It is indicated that the model will be a wider range of application whereas the prediction precision is not reduced. Dislocation structure and its distribution for creep specimens and void evolution for creep rupture specimens have been carried by analyzing the microscopic structure. The results show that the creep stress index is close to 5 during the steady-state creep stage for different temperatures. The dislocation climb mechanism controlls the creep deformation process. There is no stacking fault or microtwin observed in phase or matrix. Cracks originate from the cavities at grain boundary and along the boundary, which lead to fracture. Grain boundary fracture is the main creep rupture mechanism.

Key words: BSTMUF601 alloy creep deformation steady creep rate creep rupture

ZTFLH:

TG142.1

Fund: Supported by National Natural Science Foundation of China (Nos.50831008 and 51105029) and National Science and Technology Major Project (No.2014ZX04014-51)

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	Chaoyang SUN
	Bing SHI
	Chuanbiao WU
	Naiwei YE
	Tianjun MA
	Wenliang XU
	Jing YANG

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https://www.ams.org.cn/EN/10.11900/0412.1961.2014.00293 OR https://www.ams.org.cn/EN/Y2015/V51/I3/349

Fig.1 Microstructures of BSTMUF601 alloy before creep (a) and crept at 1095 ℃ under applied stress of 5.7 MPa (b)

Fig.2 Experimental and predicted creep curves of BSTMUF601 alloy crept at 1095 ℃ (a), 980 ℃ (b) and 870 ℃ (c) under different applied stresses

Fig.3 Predicted creep curves with different models compared with experimental results of BSTMUF601 alloy crept at 1095 ℃ under applied stress of 7.7 MPa

Table 1 Steady-state creep rates of BSTMUF601 alloy at different conditions

Fig.4 lnε?s - lnσ curves of BSTMUF601 alloy at differenttemperatures(σ—appliedstress, ε?s —seady-state creep rate, n—creep stress index)

Fig.5 TEM images of BSTMUF601 alloy crept at 1095 ℃ under applied stress of 5.7 MPa

(a) dislocation in γ matrix
(b) dislocation tangle
(c) dislocation pile-up around γ′ particles
(d) dislocation climb

Fig.6 OM image of BSTMUF601 alloy crept at 870 ℃ under applied stress of 32 MPa after creep rupture

Fig.7 Morphologies on the longitudinal (a, b) and cross (c, d) sections with cavity nucleation (a, c) and microcrack (b, d) at grain boundaries near the fracture of BSTMUF601 alloy crept at 1095 ℃ under applied stress of 7.7 MPa

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