Burning Loss Mechanism of Sc During Vacuum Induction Melting of Nickel-Based Superalloys

doi:10.11900/0412.1961.2024.00242

Acta Metall Sin

2026, Vol. 62

Issue (2): 363-371 DOI: 10.11900/0412.1961.2024.00242

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Burning Loss Mechanism of Sc During Vacuum Induction Melting of Nickel-Based Superalloys

YAN Jing¹, ZHANG Jiali¹, DENG Rui², HE Yang¹(

), WEN Xinli², ZHANG Qingquan², QIAO Lijie¹

1 Beijing Innovation Center for Materials Genome Engineering, University of Science and Technology Beijing, Beijing 100083, China
2 Materials Research Institute, Beijing Beiye Functional Materials Corporation, Beijing 100192, China

Cite this article:

YAN Jing, ZHANG Jiali, DENG Rui, HE Yang, WEN Xinli, ZHANG Qingquan, QIAO Lijie. Burning Loss Mechanism of Sc During Vacuum Induction Melting of Nickel-Based Superalloys. Acta Metall Sin, 2026, 62(2): 363-371.

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Abstract

Rare-earth elements significantly enhance key service performances of nickel-based superalloys. However, due to burning loss, the actual yield of rare-earth elements within the alloy is challenging to control precisely in practice. This study investigates the burning loss pathways of Sc during the melting and casting of a nickel-based superalloy BYG36. Samples were collected from six typical locations in the vacuum induction melting system where burning or volatilization products might be present. The samples were thoroughly characterized regarding Sc content, phases, morphology, and atomic-scale structures. While no Sc residue was found in the furnace ash, observation window, or entry nozzle—indicating minimal volatilization of Sc—a substantial amount of Sc was found adhering to the inner side surface of the crucible, the crucible rim, and the inner side surface of the sprue. Atomic-scale characterizations revealed that the Sc-rich phase on the inner surface of the crucible was a cubic-structured Al_1.3Sc_0.7O₃, in contrast to the previously assumed orthogonal-structured ScAlO₃. Intermingling with Al₂O₃ particles in the refractory materials, this cubic-structured phase likely formed through reactions of Sc with Al₂O₃ during the melting process. In contrast, Sc residue on the crucible rim and the inner side surface of the sprue was identified as cubic-structured Sc₂O₃ particles deposited directly on the refractory material surfaces. These inclusions originated from reactions of Sc with O in the alloy melt and adhered to the refractory surfaces as the melt slowly flowed over the crucible rim and sprue during casting.

Key words: nickel-based superalloy Sc rare earth element burning loss

Received: 18 July 2024

ZTFLH:

TG132.3

Fund: National Natural Science Foundation of China(52271049)

Corresponding Authors: HE Yang, professor, Tel: 13521862031, E-mail: yanghe@ustb.edu.cn

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	YAN Jing
	ZHANG Jiali
	DENG Rui
	HE Yang
	WEN Xinli
	ZHANG Qingquan
	QIAO Lijie

URL:

https://www.ams.org.cn/EN/10.11900/0412.1961.2024.00242 OR https://www.ams.org.cn/EN/Y2026/V62/I2/363

Fig.1 Schematic of the vacuum induction melting system (1—furnace cover, 2—crucible, 3—heater, 4—rotator, 5—liquid metal, 6—thermocouple, 7—observation window, 8—sprue, 9—entry nozzle, 10—mold) (a) and photos of samples taken from residue on the inner side surface of the crucible (b), residue on the crucible rim (c), residue on the inner side surface of the sprue (d), and residue on the inner surface of the entry nozzle (e)

Fig.2 Cross-sectional SEM-secondary electron (SE) image (a) and corresponding EDS elemental mapping results (b) of the residue on the inner side surface of the crucible

Fig.3 Cross-sectional STEM high-angle annular dark field (HAADF) image (a) and corresponding EDS elemental mapping results (b), HRTEM image (c), integral differential phase contrast (iDPC) image (d), and fast Fourier transform (e) of the interface between matrix and Sc-rich region of the residue on the inner side surface of the crucible

Fig.4 Atomic resolution STEM-HAADF image (a) and corresponding EDS chemical images (b-f) of the Sc-rich region of the residue on the inner side surface of the crucible, and the EDS intensity of Sc, Al, and O along the yellow arrow in Fig.4a (g)

Fig.5 Cross-sectional SEM-SE image (a) and corresponding EDS elemental mapping results (b) of the residue on the crucible rim

Fig.6 Cross-sectional SEM-SE image (a) and EDS elemental mapping results (b) of the residue on the inner side surface of the sprue, and a higher magnification SEM-SE image of the Sc-rich region (c) and locally enlarged SEM image of the square area in Fig.6c showing more details on the microstructure of Sc-rich region (d)

Fig.7 Cross-sectional STEM-HAADF image (a) and EDS elemental mapping results (b), HRTEM (c) and select area electron diffraction (SAED) pattern (d) of interface between matrix and Sc-rich region of the residue on the inner side surface of the sprue

Fig.8 Atomic model (a), atomic resolution STEM-HAADF image (b), iDPC image (c), and EDS elemental mapping results (d) of the Sc₂O₃ (a, b—lattice constants)

Fig.9 SEM-SE image (a) and corresponding EDS elemental mapping results (b) on a typical Sc-containing inclusion in the alloy matrix

Fig.10 SEM-SE image (a) and corresponding EDS elemental mapping results (b) of the residue on the inner surface of the entry nozzle

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