Microstructures and Mechanical Properties of GH4169 Superalloy Manufactured by Selective Laser Melting

doi:10.11900/0412.1961.2024.00075

Acta Metall Sin

2025, Vol. 61

Issue (12): 1829-1844 DOI: 10.11900/0412.1961.2024.00075

Research paper

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Microstructures and Mechanical Properties of GH4169 Superalloy Manufactured by Selective Laser Melting

SUN Yongfei¹^,², XIANG Chao²(

), ZHANG Tao², WU Wenwei¹^,², ZOU Zhihang², LIU Jinpeng², SUN Guifang²^,³(

), PU Jibin⁴, HAN En-Hou²^,⁵

1 School of Physics and Materials Science, Guangzhou University, Guangzhou 510006, China
2 Institute of Corrosion Science and Technology, Guangzhou 510530, China
3 School of Mechanical Engineering, Southeast University, Nanjing 211189, China
4 State Key Laboratory of Advanced Marine Materials, Ningbo Institute of Materials Technology and Engineering, Chinese Academy of Sciences, Ningbo 315201, China
5 School of Materials Science and Engineering, South China University of Technology, Guangzhou 510641, China

Cite this article:

SUN Yongfei, XIANG Chao, ZHANG Tao, WU Wenwei, ZOU Zhihang, LIU Jinpeng, SUN Guifang, PU Jibin, HAN En-Hou. Microstructures and Mechanical Properties of GH4169 Superalloy Manufactured by Selective Laser Melting. Acta Metall Sin, 2025, 61(12): 1829-1844.

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Abstract

GH4169 materials are widely used in aerospace, nuclear power, petrochemical, and other industries. However, conventional processing methods fail to meet the demands of high-performance and rapid manufacturing for complex structural parts. Therefore, selective laser melting (SLM) has been adopted as a new rapid manufacturing technology to address these demands. The high-temperature gradient and rapid cooling rate generated during SLM result in a considerably different microstructure in the GH4169 alloy compared with those produced via conventional melting and forging methods. Consequently, heat treatment is an essential post-processing step to enhance the precipitation strengthening of the GH4169 superalloy. Thus, it is critical to examine the microstructure and mechanical properties of the SLM-formed GH4169 alloy after heat treatment. This study focuses on fabricating the GH4169 alloy using SLM technology and investigates the microstructure and mechanical properties of the as-built, directly aged, and solution-aged GH4169 alloy specimens. Results reveal that the as-built structures primarily comprise a γ matrix and Laves phase. After direct aging, the γ′/γ″ phase precipitates within the matrix. After solution aging, the Laves phase completely dissolves. Moreover, the δ phase precipitates with a size of < 1 μm become abundant and uniformly distributed within grains and grain boundaries. Simultaneously, the γ′/γ″ phase precipitate within the matrix, resulting in a more homogeneous distribution. The microhardness, tensile strength, and yield strength at room temperature (25 ^oC) of the SLM GH4169 alloy are 311 HV, 961 MPa, and 649 MPa, respectively. Heat treatment substantially improves the hardness and strength of the material. In the solution-aged state, the microhardness reaches 518 HV, with a tensile strength of 1393 MPa and a yield strength of 1233 MPa at room temperature. Notably, these static mechanical properties surpass those of the corresponding forged materials. The tensile properties at 550, 650, and 750 ^oC indicate that the elevated strength of the heat-treated samples at 650 ^oC complies with relevant forging standards. Owing to the substantial temperature gradient and rapid cooling rate during the SLM forming process, the GH4169 sample exhibits a refined cellular and columnar dendritic structure, small grain size, and high dislocation density. Subsequent heat treatment induces γ′/γ″ phase precipitation, enhancing the mechanical properties of the GH4169 alloy through fine crystal strengthening, dislocation strengthening, and precipitation strengthening.

Key words: selective laser melting GH4169 heat treatment microstructure mechanical property

Received: 12 March 2024

ZTFLH:

TG146.1

Fund: Youth Innovation Fund of Institute of Corrosion Science and Technology(E1551601);Opening Project of State Key Laboratory of Advanced Marine Materials(2024Z02)

Corresponding Authors: XIANG Chao, Tel: (020)22309456, E-mail: cxiang@icost.ac.cn; SUN Guifang, professor, Tel: (025)52090501, E-mail: gfsun@seu.edu.cn

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	Articles by authors
	SUN Yongfei
	XIANG Chao
	ZHANG Tao
	WU Wenwei
	ZOU Zhihang
	LIU Jinpeng
	SUN Guifang
	PU Jibin
	HAN En-Hou

URL:

https://www.ams.org.cn/EN/10.11900/0412.1961.2024.00075 OR https://www.ams.org.cn/EN/Y2025/V61/I12/1829

Fig.1 Morphology (a) and particle size distribution (b) of GH4169 superalloy powders (D₁₀, D₅₀, and D₉₀ are the particle sizes of the powder at 10%, 50%, and 90% cumulative distribution, respectively)

Fig.2 Dimensions of tensile test specimens (unit: mm)

Table 1 Parameters of heat treatment process

Fig.3 XRD spectra of GH4169 superalloy specimens in AB, DA, and SA states (Inset is a partially magnified spectra)

Table 2 Intergranular spacings of austenite in AB, DA, and SA states

Fig.4 OM images of GH4169 superalloy specimens in different states at the XOY surface (a-c) and XOZ surface (d-f)
(a, d) AB state (b, e) DA state (c, f) SA state

Fig.5 Low (a-c) and high (d-f) magnified SEM images of GH4169 superalloy specimens in different states
(a, d) AB state (b, e) DA state (c, f) SA state

Fig.6 EPMA surface mappings of GH4169 superalloy specimens in different states
(a) AB state (b) DA state (c) SA state

Fig.7 Inverse pole figure (IPF) maps of GH4169 superalloy specimens in AB (a, d), DA (b, e), and SA (c, f) states (BD—building direction)
(a-c) XOY surface (d-f) XOZ surface

Table 3 Grain size (intercept lengths) of GH4169 superalloy specimens in AB, DA, and SA states

Table 4 Room-temperature tensile properties of GH4169 superalloy specimens

Fig.8 Low (a-c) and high (d-f) magnified SEM images showing the tensile fracture morphologies at room temperature of GH4169 superalloy specimens
(a, d) AB state (b, e) DA state (c, f) SA state

Fig.9 High-temperature engineering stress-strain curves of GH4169 superalloy specimens in AB, DA, and AS states

Table 5 High-temperature tensile properties of GH4169 superalloy specimens

Fig.10 SEM images showing the high-temperature tensile fracture morphologies of GH4169 superalloy specimens at 550 ^oC (a, d, g), 650 ^oC (b, e, h), and 750 ^oC (c, f, i)
(a-c) AB state (d-f) DA state (g-i) SA state

Fig.11 TEM bright-field images of cellular structures of GH4169 superalloy specimens in AB (a), DA (b), and SA (c) states

Fig.12 High-angle annular dark field (HAADF) images and EDS mappings of cellular structure of GH4169 superalloy specimens in different states
(a) AB state (b) DA state (c) SA state

Fig.13 TEM bright-field images of matrix and Laves phase, and corresponding SAED patterns of the circle areas (insets) of samples
(a-f) γ matrix bright-field image (a) and SAED patterns with [100] axis (b) and [110] axis (c); Laves phase bright-field image (d) and SAED patterns with [10

1 ¯

0] axis (e) and [11

2 ¯

0] axis (f) of sample in AB state (g-j) γ matrix bright-field images under [100] axis (g) and [110] axis (i), and corresponding SAED patterns (h, j) of sample in DA state (k-o) γ matrix bright-field image under [100] axis (k) and SAED pattern (l), intragranular γ matrix bright-field image under [110] axis (m) and SAED pattern (n), and grain boundary γ matrix bright-field image under [110] axis (o) and SAED pattern (p) of sample in SA state

Fig.14 TEM bright-field images (a, e) and SAED patterns with [001] axis (insets), and corresponding TEM dark-field images of spots 1-3 indicated by the arrows (b-d, f, g) of specimens in DA (a-d) and SA (e-h) states

Fig.15 Schematics of microstructure evolution of GH4169 superalloy specimens in different states
(a) AB state (b) DA state (c) SA state

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