Effects of an ultra-high magnetic field up to 25 T on the phase transformations of undercooled Co-B eutectic alloy

doi:10.1016/j.jmst.2021.03.055

Abstract

Abstract:

While there have been multiple recent reports in the literature focusing on the effects of magnetic field on the phase transformation behaviors, the research conducted with an ultra-high magnetic field greater than 20 T is still preliminary. In the current study, the structure evolution of Co-B alloys are experimentally studied with undercooling. The effects of a 25 T magnetic field on the solidification behavior and the subsequent solid-state phase transformation behavior have been investigated. The 25 T magnetic field is confirmed to have little effect on the homogeneous nucleation, but have some influence on the heterogeneous nucleation of Co₃B and Co₂₃B₆ phases by modifying the wetting angle θ. The decomposition of Co₂₃B₆ phase in the subsequent cooling process can be effectively suppressed by applying the 25 T magnetic field. The present work might be helpful for not only theoretically understanding the influence of ultra-high magnetic field on the phase transformation behaviors but a potential technology of field-manipulation of magnetic materials.

Key words: Ultra-high magnetic field, Non-equilibrium solidification, Solid-state phase transformation, Metastable phase

Yixuan He, Yuhao Wu, Fan Bu, Chengxiong Zou, Zhangchi Bian, Qiliang Huang, Tie Liu, Qiang Wang, Jun Wang, Jinshan Li, Eric Beaugnon. Effects of an ultra-high magnetic field up to 25 T on the phase transformations of undercooled Co-B eutectic alloy[J]. J. Mater. Sci. Technol., 2021, 93: 79-88.

Figures/Tables 9

Fig. 1. (a) Cooling history and magnetic field training process of the sample solidified using the fluxing combined with the thermal cycling method. A static magnetic field of 25 T was applied during the cooling process and the subsequent thermal processing of the 11th cycle. The dashed line shows the eutectic temperature, TE. (b) The enlarged figure of the dashed square in Fig. 1(a), indicating a solid-state phase transformation at Ts=1193 K. (c) The corresponding macrograph of the sample after solidification. (d) The DSC curve of the thin slice cut from the sample shown in Fig. 1(c) with a heating rate of 10 K min-1.

Fig. 2. Field dependence of magnetization at room temperature of the sample after solidification. //B and ⊥B indicate directions of the magnetic field imposed for the magnetization measurement with respect to the magnetic field imposed during the solidification. Inset shows the magnified curves around zero magnetic field.

Fig. 3. Microstructures on the polished surface of the sample shown in Fig. 1(c), (a) The longitudinal (parallel to the direction of magnetic field) and (b) the transverse (perpendicular to the direction of magnetic field) structures. (c-e) Higher magnification images of the square regions in Fig. 3(a). (c1-e1) The corresponding close-up views of the dashed squares in Fig. 3(c)-3(e), respectively. The small green rectangle in (d1) indicates the location for preparing in-depth PED and TEM lamella by FIB.

Fig. 4. EBSD analysis of the microstructure shown in Fig. 3(c). (a) Phase map and (b) the corresponding inverse pole figure map. (c) Phase map and (d) inverse pole figure map of the boxed region in Fig. 4(a) and 4(b), performed at a smaller step size. The color bars are shown on the right hand side. The small red rectangle in Fig. 4(c) indicates the location for preparing in-depth TEM lamella by FIB. (e) Orientations of Fcc-Co and the associated Hcp-Co in the granular primary phase plotted onto the pole figures, indicating an obedience of Blackburn orientation relationship. (f) Orientations of Fcc-Co and the associated Co2B in the granular primary phase plotted onto the pole figures, revealing the orientation relationship between them. The purple cross represents the direction of magnetic field.

Fig. 5. TEM analysis of a FIB lift-out lamella prepared from the location in Fig. 4(c). (a) STEM bright-field image. (b-d) SAD patterns taken from the regions indicated by circles in Fig. 5(a). The indices in the bottom right corner indicate the corresponding zone axes. The inserts in the top right corner of Fig. 5(b)-5(d) are the SAD patterns viewing along other zone axes.

Fig. 6. PED analysis of a FIB lift-out lamella prepared from the location in Fig. 3(d1). (a) STEM bright-field image. (b, d) Phase map and (c, e) the corresponding inverse pole figure map of the boxed region in Fig. 6(a). The color bars of Fig. 6(b)-6(e) are shown in the bottom right corner.

Fig. 7. Further TEM characterization of the microstructure shown in Fig. 6(a). (a) Magnified BF-STEM image of the blue boxed region in Fig. 6(a). (b) Magnified HAADF-STEM image of the orange boxed region in Fig. 6(a). (c-h) SAD patterns taken from the regions indicated by circles in Fig. 7(a) and 7(b). The indices in the bottom right corner indicate the corresponding zone axes.

Fig. 8. Illustration of the contacts angles between liquid metal droplet and quartz tube in the case of (a) without and (b) with the magnetic field.

Fig. 9. Ball-and-stick representations of Co23B6 unit cell (a), Fcc-Co unit cell (b) and Co3B unit cell (c). 3D (a1) and (100) views (a2) of coordination polyhedral in the Co23B6 phase.

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