EFFECTS OF GRAIN REFINEMENT ON CREEP PROPERTIES OF K417G SUPERALLOY

doi:10.11900/0412.1961.2014.00245

Acta Metall Sin

2014, Vol. 50

Issue (11): 1384-1392 DOI: 10.11900/0412.1961.2014.00245

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EFFECTS OF GRAIN REFINEMENT ON CREEP PROPERTIES OF K417G SUPERALLOY

DU Beining, YANG Jinxia, CUI Chuanyong(

), SUN Xiaofeng

Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016

Cite this article:

DU Beining, YANG Jinxia, CUI Chuanyong, SUN Xiaofeng. EFFECTS OF GRAIN REFINEMENT ON CREEP PROPERTIES OF K417G SUPERALLOY. Acta Metall Sin, 2014, 50(11): 1384-1392.

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Abstract

Grain size is one of the most important parameters which affect the mechanical properties of cast polycrystalline superalloys. To study the effect of grain refinement on the creep behaviors of K417G superalloy, the creep behaviors of K417G superalloy with four grain sizes were investigated at 760 ℃/645 MPa, 900 ℃/315 MPa and 950 ℃/235 MPa. The longitudinal section of the fracture surface, crack propagation path, dislocation structure and plastic deformation distribution in the vicinity of the cracks were investigated by using SEM, TEM and EBSD techniques, thus the deformation mechanism and effect of grain refinement on the creep properties of K417G superalloy were determined under different creep conditions. The results showed that the effects of grain refinement on the creep property of the alloy varied with the temperatures and stress. At 760 ℃/645 MPa, grain refinement improved the creep life and reduced the steady-state deformation rate of the alloy. The creep deformation was dominated by intragranular deformation. At 900 ℃/315 MPa, as grain size decreased, the creep life increased firstly and then decreased, while the steady-state deformation rate decreased firstly and then increased. The creep deformation showed a competitive effect of intragranular deformation and grain boundary sliding. At 950 ℃/235 MPa, the creep life decreased and the steady-state deformation rate increased with the decrease of the grain size. Grain boundary sliding was the main deformation mode. At the same time, grain refinement could cause a refinement of the dendrite and carbide of the alloy, which would also affect the creep behavior of the alloy to a small extent. The TEM observation showed that at 760 ℃/645 MPa, the dislocations interacted with g' particles through shearing mechanism and no dislocation network was found in the matrix. While at 900 ℃/315 MPa and 950 ℃/235 MPa, the dislocations crossed the g' particles through Orowan bypass mechanism, dislocation network formed in the matrix, and M₂₃C₆ precipitated in the interior of the grains, which had a orientation relationship between the M₂₃C₆ precipitates and matrix .

Key words: superalloy grain size creep property

Received: 02 July 2014

ZTFLH:

TG113.25

Fund: Supported by National Natural Science Foundation of China (Nos.51171179, 51128101, 51271171 and 11332010), National Basic Research Program of China (No.2010CB631206) and Program of One Hundred of Talented People of Chinese Academy of Sciences

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	Beining DU
	Jinxia YANG
	Chuanyong CUI
	Xiaofeng SUN

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https://www.ams.org.cn/EN/10.11900/0412.1961.2014.00245 OR https://www.ams.org.cn/EN/Y2014/V50/I11/1384

Table 1 Average size of grains, carbides and y' phase of K417G superalloy

Fig.1 Morphologies of grain distributions (a~d), dendrites (e~h), carbides (i~l) and g' phases (m~p) for specimens A (a, e, i, m), B (b, f, j, n), C (c, g, k, o), D (d, h, l, p) of K417G superalloy

Table 2 Creep lives of specimens A~D under different conditions (h)

Fig.2 Creep curves of specimens A~D under 760 ℃/645 MPa (a), 900 ℃/315 MPa (b) and 950 ℃/235 MPa (c)

Table 3 Steady-state deformation rate K for K417G alloy with four different grain sizes at different conditions (s^-¹)

Fig.3 Microstructures of specimen A tested at 760 ℃/645 MPa (a), specimen B tested at 900 ℃/315 MPa (b), specimen C tested at 760 ℃/645 MPa (c), specimen D tested at 900 ℃/315 MPa (d) and 950 ℃/235 MPa (e, f)

Fig.4 All Euler images (a, d, g), grain boundary images (b, e, h) and local misorientation images (c, f, i) of specimen D tested at 760 ℃/645 MPa (a~c), 900 ℃/315 MPa (d~f) and 950 ℃/235 MPa (g~i)

Fig.5 TEM image of precipitates (a), selected area diffraction pattern (b) and dislocation structure (c) of specimen C tested at 950 ℃/235 MPa, TEM images of specimen D tested at 760 ℃/645 MPa (d), 900 ℃/315 MPa (e) and 950 ℃/235 MPa (f)

Fig.6 Schematic diagrams of intragranular deformation (a) and grain boundary sliding (b) (s—applied stress)

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