Inhibitor and Secondary Recrystallization Behavior of Giant Magnetostriction of Fe-Ga Thin Sheet

doi:10.11900/0412.1961.2022.00455

Acta Metall Sin

2024, Vol. 60

Issue (11): 1559-1570 DOI: 10.11900/0412.1961.2022.00455

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Inhibitor and Secondary Recrystallization Behavior of Giant Magnetostriction of Fe-Ga Thin Sheet

ZHAI Xinya¹, HE Zhenghua¹(

), SHA Yuhui², ZHU Xiaofei³, LI Feng¹, CHEN Lijia¹, ZUO Liang²^,³

1 School of Materials Science and Engineering, Shenyang University of Technology, Shenyang 110870, China
2 Key Laboratory for Anisotropy and Texture of Materials, Ministry of Education, Northeastern University, Shenyang 110819, China
3 Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China

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ZHAI Xinya, HE Zhenghua, SHA Yuhui, ZHU Xiaofei, LI Feng, CHEN Lijia, ZUO Liang. Inhibitor and Secondary Recrystallization Behavior of Giant Magnetostriction of Fe-Ga Thin Sheet. Acta Metall Sin, 2024, 60(11): 1559-1570.

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Abstract

The core issue in the study of giant magnetostriction of Fe-Ga alloy thin sheet is to obtain preferential texture through secondary recrystallization. In this work, the evolution of the texture, precipitation, and grain boundary characteristics of an Fe-Ga alloy thin sheet during the annealing process were investigated using XRD, SEM, EBSD, and TEM. The mechanism of the secondary recrystallization of the Goss ({110}<001>) texture in the Fe-Ga alloy thin sheet was analyzed. The results show that the primary recrystallized thin sheet is composed of strong γ-fibers and has a weak Goss texture. Moreover, high-density MnS and NbC precipitates of size 20-40 nm are dispersedly distributed in the matrix grains after primary recrystallization. The coarsening of the precipitates and a decrease in the volume fraction and density weaken the inhibiting force during the annealing process. The density of the precipitates inside the Goss grains is lower than that of the precipitates in the matrix grains with γ-texture during the process from primary recrystallization to secondary recrystallization. Before the occurrence of secondary recrystallization, Goss grains do not exhibit a number and size advantages over the matrix grains but are surrounded by higher-energy grain boundaries than the matrix grains. The differences between the Goss and matrix grains in terms of precipitation and high-energy grain boundary characteristics during primary recrystallization provide an additional driving force for the secondary recrystallization of Goss grains. Therefore, a perfect secondary recrystallization of the Goss texture with a saturation magnetostriction coefficient of 250 × 10^‒6 is produced in the Fe-Ga alloy thin sheet without the introduction of the surface energy effect using a special annealing atmosphere.

Key words: Fe-Ga alloy thin sheet secondary recrystallization texture magnetostriction

Received: 13 September 2022

ZTFLH:

TG142.77

Fund: National Natural Science Foundation of China(52004164);National Natural Science Foundation of China(51931002);National Natural Science Foundation of China(51671049);Education Department Program of Liaoning Province(LQGD2020013)

Corresponding Authors: HE Zhenghua, associate professor, Tel: (024)25496301, E-mail: hezhh@sut.edu.cn

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	ZHAI Xinya
	HE Zhenghua
	SHA Yuhui
	ZHU Xiaofei
	LI Feng
	CHEN Lijia
	ZUO Liang

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https://www.ams.org.cn/EN/10.11900/0412.1961.2022.00455 OR https://www.ams.org.cn/EN/Y2024/V60/I11/1559

Fig.1 SEM images (a, d) and constant φ₂ = 45° sections of orientation distribution function (ODF) in the sub-surface layer (S = 0) (b, e) and central layer (S = 0.5) (c, f) of secondarily cold-rolled (a-c) and primarily recrystallized (d-f) Fe-Ga alloy thin sheet (φ₁, Φ, φ₂—Euler angles, S—relative position from center to center, RD—rolling direction, ND—normal direction)

Fig.2 TEM image (a) and EDS of precipitates NbC (b) and MnS (c) in Fe-Ga alloy thin sheet after primary recrystallization

Fig.3 SEM images of precipitates in Fe-Ga alloy thin sheet at annealing temperatures of 800^oC (a), 850^oC (b), 900^oC (c), and 950^oC (d)

Fig.4 Size distributions of precipitates in Fe-Ga alloy thin sheet at annealing temperatures of 800^oC (a), 850^oC (b), 900^oC (c), and 950^oC (d)

Fig.5 EBSD orientation image maps of Fe-Ga alloy thin sheet along the rolling plane during the heating process at annealing temperatures of 800^oC (a), 850^oC (b), 900^oC (c), 950^oC (d), and 1000^oC (e) (TD—transverse direction)

Fig.6 Constant φ₂ = 45° sections of ODFs of Fe-Ga alloy thin sheet along the rolling plane during the heating process at annealing temperatures of 800^oC (a), 850^oC (b), 900^oC (c), 950^oC (d), and 1000^oC (e)

Fig.7 Magnetostriction curves (a) and saturation mag-netostriction coefficients (3/2)λ_s as a function of annealing temperatures (b) of Fe-Ga alloy thin sheet

Fig.8 Changes of average particle size, volume fraction, and Zenner factor of precipitated phase of Fe-Ga alloy thin sheet at different annealing temperatures

Fig.9 EBSD orientation image maps (a-c), SEM images of precipitates (d-f), and precipitate size distributions (g-i) within the grains with main texture components at annealing temperatures of 800^oC (a, d, g), 900^oC (b, e, h), and 950^oC (c, f, i) in Fe-Ga alloy thin sheet

Fig.10 Densities of precipitates within grains with main texture components at different annealing temperatures in Fe-Ga alloy thin sheet

Fig.11 Grain boundary characteristic distributions of matrix and Goss grains in Fe-Ga alloy thin sheet at annealing temperatures of 800^oC (a), 850^oC (b), 900^oC (c), and 950^oC (d)

Table 1 Volume fractions of grain boundaries in Fe-Ga alloy thin sheet at different annealing temperatures

Fig.12 Schematics of mechanism of secondary recrystallization in Fe-Ga alloy thin sheet

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