Mechanism of stress induced irreversible magnetic anisotropy in Fe-based alloy ribbons

Zhang Jian-Qiang; Qin Yan-Jun; Fang Zheng; Fan Xiao-Zhen; Yang Hui-Ya; Kuang Fu-Li; Zhai Yao; Miao Yan-Long; Zhao Zi-Xiang; He Jia-Jun; Ye Hui-Qun; Fang Yun-Zhang

doi:10.7498/aps.71.20221509

Abstract

Fe-based amorphous and nanocrystalline soft magnetic alloys are regarded as the significant dual-green energy-saving materials because of their superior magnetic properties and straightforward fabrication procedure. As such, they have attracted much attention in the fields of the electronic information and electrical power. In this work, Fe_73.5Cu₁Nb₃Si_13.5B₉ (%) amorphous alloy ribbon is subjected to various physical ageing treatments in nitrogen atmosphere. These treatments include annealing at 540 ℃ for 30 min under different tensile stresses and isothermal tempering without tensile stress for several cycles. The origin of stress-induced magnetic anisotropy is investigated through using dynamic strain analysis, the longitudinally driven giant magento-impedance effect, and synchrotron radiation X-ray diffraction. In the process of tensile stress annealing, it is found that the axial strain of ribbon is elastic strain when annealing temperature is below the glass transition point, and plastic strain when annealing temperature is above the glass transition point; the precipitation of nanocrystalline phase has a pinning effect on amorphous matrix, which slows down the strain rates and makes the tend stable. Additionally, isothermal tempering studies show that the stress-induced magnetic anisotropy and lattice plane anisotropy have different relaxation patterns. It is found through numerical fitting that the stress-induced magnetic anisotropy can reach a stable value of 0.144 by infinite tempering, whereas the lattice plane anisotropy can only relax to zero by finite tempering. A model of nanocrystalline grain distribution anisotropy is developed to re-examine the origin of stress-induced magnetic anisotropy. It supports a viewpoint that the nanocrystalline grain distribution anisotropy $\Delta \delta $ is responsible for the stress-induced irreversible magnetic anisotropy ${K_{\text{d}}}$, and that their relationship can be described as a following function: ${K_{\text{d}}} = k\Delta \delta $. Therefore, it is proposed that the stress-induced anisotropy originates from a synergistic interaction between the lattice plane anisotropy and the nanocrystalline grain distribution anisotropy in Fe-based alloy ribbon. This work has important implications for understanding the mechanism of the stress-induced magnetic anisotropy.

Keywords:

irreversible magnetic anisotropy /
lattice plane anisotropy /
nanocrystalline grain distribution anisotropy /
synchrotron radiation

Authors and contacts

1.
College of Physics, Electronic and Information Engineering, Zhejiang Normal University, Jinhua 321004, China
2.
College of Electronic Information and Electrical Engineering, Tianshui Normal University, Tianshui 741001, China
3.
Key Laboratory of Solid State Optoelectronic Devices of Zhejiang Povince, Zhejiang Normal University, Jinhua 321004, China
4.
Tourism College of Zhejiang, Hangzhou 311231, China

Corresponding author: Zhang Jian-Qiang, zhjian8386@163.com ; Fang Yun-Zhang, fyz@zjnu.cn

Funds: Project supported by the Key Specialized Research and Development Program of Xinjiang Uygur Autonomous Region, China (Grant No. KYZ04Y21100), the Fund for Less Developed Regions of the National Natural Science Foundation of China (Grant No. 12064037), the Planning Program on Science and Technology of Gansu Province, China (Grant No. 21JR1RE288) , the Natural Science Foundation of Xinjiang Uygur Autonomous Region, China (Grant No. 2021D01B47), and the High level Pre-research program of Tianshui Normal University, China (Grant No. GJB2021-09).

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References

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[28]	Wu C, Chen H P, Lv H P, Yan M 2016 J. Alloys Compd. 673 278 Google Scholar
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[31]	汪卫华 2013 物理学进展 33 177 Wang W H 2013 Prog. Phys. 33 177

Cited By

图 1 张应力退火过程Fe基合金应变及应变速率曲线　(a) 应变; (b)应变速率

Figure 1. Strain and strain rates curves of Fe-based alloy ribbons during tensile stress annealing: (a) Strains; (b) strain rates.

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图 2 张应力退火Fe基合金残余应变与应力关系曲线　(a) 轴向; (b)横向

Figure 2. Residual macro-strains of Fe-based alloy ribbons as a function of annealing tensile stress: (a) Axial direction; (b) transverse direction.

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图 3 张应力退火Fe基合金薄带　(a) LDGMI效应; (b)磁各向异性与退火张应力关系

Figure 3. Fe-based alloy ribbons annealed with different tensile stress: (a) LDGMI effect; (b) the magnetic anisotropy as a function of annealing tensile stress.

DownLoad: Full-Size Img PowerPoint

图 4 Fe基合金薄带SMA的弛豫动力学曲线

Figure 4. Relaxation dynamics curve of SMA in Fe-based alloy ribbons.

DownLoad: Full-Size Img PowerPoint

图 5 张应力退火及回火Fe基合薄带XRD谱　(a)轴向; (b)横向

Figure 5. The XRD patterns of Fe-based alloy ribbons annealed with tensile stress and isothermal tempered treatment: (a) The diffraction vector is parallels to ribbon’s axial direction; (b) the diffraction vector is parallels to ribbon’s transverse direction.

DownLoad: Full-Size Img PowerPoint

图 6 Fe基合金LPA弛豫动力学曲线

Figure 6. Relaxation dynamics curve of LPA in Fe-based alloy ribbons.

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图 7 自由退火Fe基合金薄带SRXRD图谱　(a)全谱(3°—38°); (b) (110)分峰拟合

Figure 7. The SRXRD patterns of Fe-based alloy ribbons annealed without tensile stress: (a) The full spectrum diagram of SRXRD (3°—38°); (b) the multi-peaks fitting of (110) diffraction peak.

DownLoad: Full-Size Img PowerPoint

图 8 NGDA诱导感生磁各向异性与应力关系曲线

Figure 8. Dependence of the magnetic anisotropy induced by NGDA on tensile stress in Fe-based alloy ribbons.

DownLoad: Full-Size Img PowerPoint

表 1 自由退火Fe基合金薄带的结构参数

Table 1. Structural parameters of Fe-based alloy ribbons annealed without tensile stress.

衍射矢量	晶粒尺寸/nm					晶化分数	晶粒间隙
衍射矢量	D₍₁₁₀₎	D₍₂₀₀₎	D₍₂₁₁₎	D₍₂₂₀₎	D₍₃₁₀₎	V_cr/%	δ₀/nm
轴向	9.38	10.87	11.27	9.45	12.94	51.04	2.76
横向	9.30	11.77	12.03	10.40	12.66	51.27	2.74
平均值	11.00					51.16	2.75

DownLoad: CSV

表 2 张应力退火Fe基合金薄带结构和磁学参数

Table 2. Structural and magnetic parameters of Fe-based alloy ribbons annealed with different tensile stress.

张应力 σ/MPa	分布各向异性 ∆δ/nm	磁各向异性
张应力 σ/MPa	分布各向异性 ∆δ/nm	H_k/(A·m^–1)	K/(J·m^–3)	K_d/(J·m^–3)	K_e/(J·m^–3)
0	0	47.51	27.25	0	—
53	0.05	1181.73	692.14	99.67	592.47
117	0.14	2001.46	1229.06	176.98	1052.08
170	0.20	3194.23	1972.59	284.05	1688.54
223	0.28	4540.54	2777.20	399.92	2377.28
270	0.38	5645.52	3495.28	503.32	2991.96
343	0.51	7335.80	4498.91	647.84	3851.07
410	0.65	9380.54	5786.89	833.31	4953.58

DownLoad: CSV

[1]	姚可夫, 施凌翔, 陈双琴, 邵洋, 陈娜, 贾蓟丽 2018 物理学报 67 016101 Google Scholar Yao K F, Shi L X, Chen S Q, Shao Y, Chen N, Jia J L 2018 Acta Phys. Sin. 67 016101 Google Scholar
[2]	Li Y M, Jia X J, Zhang W, Zhang Y, Xie G Q, Qiu Z Y, Luan J H, Jiao Z B 2021 J. Mater. Sci. Technol. 65 171 Google Scholar
[3]	Corte-Leon P, Zhukova V, Blanco J M, González-Legarreta L, Ipatov M, Zhukov A 2020 J. Magn. Magn. Mater. 510 166939 Google Scholar
[4]	Sai Ram B, Paul A K, Kulkarni S V 2021 J. Magn. Magn. Mater. 537 16820
[5]	Li F C, Liu T, Zhang J Y, Shuang S, Wang Q, Wang A D, Wang J G, Yang Y 2019 Mater. Today Adv. 4 100027 Google Scholar
[6]	马海健, 魏文庆, 鲍文科, 神祥博, 王长春, 王伟民 2020 稀有金属材料与工程 49 2904 Ma H J, Wei W Q, Bao W K, Shen X B, Wang C C, Wang W M 2020 Rare Metal Mat. Eng. 49 2904
[7]	Liu T, Wang A D, Zhao C L, Yue S Q, Wang X M, Liu C T 2019 Mater. Res. Bull. 112 323 Google Scholar
[8]	Lukshina V A, Dmitrieva N V, Cerdeira M A, Potapov A P 2012 J. Alloys Compd. 536 374 Google Scholar
[9]	Correa A M, Bohn F 2018 J. Magn. Magn. Mater. 453 30 Google Scholar
[10]	Varga L K 2020 J. Magn. Magn. Mater. 500 166327 Google Scholar
[11]	Fang Y Z, Zheng J J, Wu F M, Xu Q M, Zhang J Q, Ye H Q, Zheng J L, Li T Y 2010 Appl. Phys. Lett. 96 092508 Google Scholar
[12]	Néel L 1954 J. Phys. 4 225
[13]	Hofmann B, Kronmüller H 1996 J. Magn. Magn. Mater. 152 91 Google Scholar
[14]	Herzer G 1996 J. Magn. Magn. Mater. 157-158 133 Google Scholar
[15]	Nielsen O V, Nielsen H J V 1980 Solid State Commun. 35 281 Google Scholar
[16]	Ohnuma M, Hono K, Yanai T, Fukunaga H, Yoshizawa Y 2003 Appl. Phys. Lett. 83 2859 Google Scholar
[17]	Ohnuma M, Hono K, Yanai T, Nakano H, Fukunaga H, Yoshizawa Y 2005 Appl. Phys. Lett. 86 152513 Google Scholar
[18]	Ohnuma M, Yanai T, Hono K, Nakano M, Fukunaga H, Yoshizawa Y, Herzer G 2010 J. Appl. Phys. 108 093927 Google Scholar
[19]	Nutor R K, Xu X J, Fan X Z, He X W, Fang Y Z 2018 Chinese J. Phys. 56 180 Google Scholar
[20]	Nutor R K, Xu X J, Fan X Z, He X W, Lu X A, Fang Y Z 2019 J. Magn. Magn. Mater. 471 544
[21]	Nutor R K, Fan X Z, He X W, Xu X J, Lu X A, Jiang J Z, Fang Y Z 2019 J. Alloys Compd. 774 1243 Google Scholar
[22]	Kurlyandskaya G V, Lukshina V A, Larrañaga A, Orue I, Zaharova A A, Shishkin D A 2013 J. Alloys Compd. 566 31 Google Scholar
[23]	Ohnuma M, Herzer G, Kozikowski P, Polak C, Budinsky V, Koppoju S 2012 Acta. Mater. 60 1278 Google Scholar
[24]	Leary A M, Keylin V, Ohodnicki P R, McHenry M E 2015 J. Appl. Phys. 117 17A338 Google Scholar
[25]	Herzer G, Schulz R US Patent 6 254 695 B1 [2001-06-03]
[26]	Hilzinger H R 1981 Proceedings of the 4th International Conference on Rapidly Quenched Metals Sendai, Japan, August 24–28, 1981 p701
[27]	许校嘉, 方峥, 陆轩昂, 叶慧群, 范晓珍, 郑金菊, 何兴伟, 郭春羽, 李文忠, 方允樟 2019 物理学报 68 137501 Google Scholar Xu X J, Fang Z, Lu X A, Ye H Q, Fan X Z, Zheng J J, He X W, Guo C Y, Li W Z, Fang Y Z 2019 Acta Phys. Sin. 68 137501 Google Scholar
[28]	Wu C, Chen H P, Lv H P, Yan M 2016 J. Alloys Compd. 673 278 Google Scholar
[29]	Allia P, Baricco M, Tiberto P, Vinai F 1993 J. Appl. Phys. 74 3137 Google Scholar
[30]	Fan X Z, He X W, Nutor R K, Pan R M, Zheng J J, Ye H Q, Wu F M, Jiang J Z, Fang Y Z 2019 J. Magn. Magn. Mater. 469 349 Google Scholar
[31]	汪卫华 2013 物理学进展 33 177 Wang W H 2013 Prog. Phys. 33 177

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