Advances in Secondary Phase Evolution and Performance Enhancement of Allvac 718Plus Superalloy

doi:10.11900/0412.1961.2024.00191

Acta Metall Sin

2025, Vol. 61

Issue (1): 43-58 DOI: 10.11900/0412.1961.2024.00191

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Advances in Secondary Phase Evolution and Performance Enhancement of Allvac 718Plus Superalloy

TANG Liting, GUO Qianying, LI Chong, DING Ran, LIU Yongchang(

)

School of Materials Science and Engineering, Tianjin University, Tianjin 300354, China

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TANG Liting, GUO Qianying, LI Chong, DING Ran, LIU Yongchang. Advances in Secondary Phase Evolution and Performance Enhancement of Allvac 718Plus Superalloy. Acta Metall Sin, 2025, 61(1): 43-58.

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Abstract

Allvac 718Plus is a newly developed nickel-based superalloy derived from Inconel 718 alloy via composition optimization. Its maximum service temperature is approximately 55 ^oC higher than that of Inconel 718. With its excellent combination of creep resistance, fatigue resistance, machinability, and weldability, the Allvac 718Plus is highly suitable for manufacturing high-temperature components that can operate at up to 700 ^oC. As a precipitation-strengthened superalloy that is relatively new with limited application history, understanding the evolution of its secondary phases during heat treatment is crucial for optimizing its properties via microstructure control. In this context, the secondary phases found in Allvac 718Plus are introduced, including the primary strengthening γ′ phase, the main grain-boundary η phase, and the γ″, δ, σ, and C14 Laves phases that form under specific conditions. The precipitation behaviors of the γ′ and η phases during standard heat treatments are examined, along with the effects of presolidification and direct aging treatments. Additionally, the evolution of secondary phases during prolonged thermal exposure are explored. The results demonstrate that the formation of a more stable composite γ″-γ′ structure is a promising strategy to achieve long-term serviceability for the alloy. The influence of the microstructural evolution of secondary phases during high-temperature service on fatigue and creep resistance is also analyzed, focusing on the roles of the two primary secondary phases. Furthermore, this paper highlights the correlation between the sluggish kinetics of γ′ phase precipitation in Allvac 718Plus and its weldability. A comprehensive overview of the harmful effects of the Laves and η phases on cracking during welding and strain-age cracking is also provided.

Key words: Allvac 718Plus alloy secondary phase heat treatment high-temperature property weldability

Received: 05 June 2024

ZTFLH:

TG166.7

Fund: National Natural Science Foundation of China(52034004);National Key Research and Development Program(2022YFB3705300)

Corresponding Authors: LIU Yongchang, professor, Tel: 13512214280, E-mail: ycliu@tju.edu.cn

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https://www.ams.org.cn/EN/10.11900/0412.1961.2024.00191 OR https://www.ams.org.cn/EN/Y2025/V61/I1/43

Phase	Formula	Crystal structure	Lattice constant (a, b, c)
γ	-	fcc (A1)	a = 0.377 nm
γ′	Ni₃(Al, Ti)	fcc (L1₂)	a = 0.379 nm
γ″	Ni₃Nb	bct (D0₂₂)	a = 0.391 nm (c / a = 1.99)
η	Ni₃Nb_0.5(Ti, Al)_0.5	Hexagonal (D0₂₄)	a = 0.512 nm, c = 0.836 nm
δ	Ni₃Nb	Orthogonal (D0_a)	a = 0.514 nm, b = 0.423 nm, c = 0.453 nm
MX	(Nb, Ti)(C, N)	fcc (B1)	a = 0.443-0.444 nm
C14 Laves	(Ni, Cr, Fe)₂(Nb, Mo, Ti)	Hexagonal (D0₂₄)	a = 0.88 nm, c = 0.45 nm
σ	(Fe, Ni)Cr	Tetragonal ( $D 4 h 14$ )	a = 0.49 nm, c = 0.78 nm

Table 1 Crystal structures and compositions of main phases in Allvac 718Plus alloy^[4,18-22]

Fig.1 Crystallographic prototype structures of the γ′ (a) and η (b) phases in Allvac 718Plus alloy

Fig.2 Crystallographic prototypes structures of the two topological closed-packed (TCP) phases in Allvac 718Plus alloy^[18]
(a) σ phase (b) Laves phase

Fig.3 TEM-EDS mapping results of the Laves phase (a, b)^[34] and σ phase (c, d) in Allvac 718Plus alloy

Fig.4 SEM images of the grain-boundary η phase with different morphologies and the serrated boundary induced by needle-like η phase in Allvac 718Plus solution treated for 1 h at 1000 ^oC (a, b) and 920 ^oC (c, d), respectively, followed by the dual aging treatment (The yellow arrows denote the growth directions of the granular η phase)^[10]

Fig.5 Schematics of the evolution of secondary phases in rapidly-solidified Allvac 718Plus alloy during solution treatment at 960 ^oC for 1 h (a), 6 h (b), 8 h (c), 14 h (d), and 24 h (e) (The secondary phases consist of the η phase, the MC carbides, and the Laves (C14) phase)^[34]

Table 2 Vickers microhardnesses and equivalent maximum pressures as measured for single and double aged Allvac 718Plus alloys^[46]

Table 3 Coarsening rates of γ′ phase of the rapidly-solidified and forged Allvac 718Plus alloy at 704 and 760 ^oC^[29]

Fig.6 TEM images showing the γ″/γ′ co-precipitates in the rapidly-solidified Allvac 718Plus alloy after long-term thermal exposure for 50 h (a, d), 200 h (b, e), and 1000 h (c, f)^[29]
(a-c) 704 ^oC (d-f) 760 ^oC

Fig.7 Bright-field TEM image showing the η phase, δ phase, and σ phase in the rapidly-solidified Allvac 718Plus alloy after the thermal exposures of 760 ^oC for 1000 h (a), the corresponding selected area electron diffraction (SAED) patterns (b, c), elemental maps images (d), and elemental line-scanning results from TEM-EDS spectrum (e)^[29]

Table 4 Microstructure information and corresponding room-temperatures (25 ^oC) and high-temperature (704 ^oC) tensile properties of forged Allvac 718Plus alloy after long-term thermal exposures at 704 and 760 ^oC^[38]

Fig.8 Schematics showing the tensile precipitation-strengthened mechanisms at room temperature (a, b) and elevated temperature (c, d) of the forged Allvac 718Plus alloy after the long-term thermal exposures of 704 ^oC, 100 h (a, c) and 760 ^oC, 1000 h (b, d) samples^[38]

Fig.9 A qualitative model schematic illustration directly showing the evolution of γ″/γ′ coprecipitates^[28]
(a) all evolution process in forged Allvac 718Plus alloy during long-term thermal exposures at 705 ^oC
(b) the evolution from γ′ to sandwich-γ″/γ′/γ″ coprecipitates
(c) the evolution from sandwich-γ″/γ′/γ″ coprecipitates to partly compact-γ″/γ′ coprecipitates
(d) the evolution from sandwich-γ″/γ′/γ″ coprecipitates and partly compact-γ″/γ′ coprecipitates to all compact-γ″/γ′/γ″ coprecipitates

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