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Acta Metall Sin  2018, Vol. 54 Issue (5): 742-756    DOI: 10.11900/0412.1961.2017.00535
Special Issue for the Solidification of Metallic Materials Current Issue | Archive | Adv Search |
Control of Solidification Process and Fabrication of Functional Materials with High Magnetic Fields
Qiang WANG1(), Meng DONG1,2, Jinmei SUN1,2, Tie LIU1, Yi YUAN3
1 Key Laboratory of Electromagnetic Processing of Materials (Ministry of Education), Northeastern University, Shenyang 110819, China
2 School of Materials Science and Engineering, Northeastern University, Shenyang 110819, China
3 School of Metallurgy, Northeastern University, Shenyang 110819, China
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Qiang WANG, Meng DONG, Jinmei SUN, Tie LIU, Yi YUAN. Control of Solidification Process and Fabrication of Functional Materials with High Magnetic Fields. Acta Metall Sin, 2018, 54(5): 742-756.

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Abstract  

In recent years, the research on materials processing under high magnetic fields has developed rapidly. This paper reviews the progress of solidification process control of metal materials and the preparation of new materials under high magnetic fields. The influences of Lorentz force, thermoelectromagnetic force and magnetic force on the melt flow, solute distribution and microstructure evolution in the alloy, the effects of magnetic moment on the crystal orientation of magnetic phase, and the effects of magnetic dipole-dipole interactions on phase arrangement in alloys were mainly introduced. At the same time, this paper also summarizes the progress of preparing new functional materials such as gradient MnSb/MnSb-Sb composites, gradient magnetostrictive materials, and materials which have anisotropy of crystal orientation by the solidification method under high magnetic fields. The high magnetic fields control the solidification process of the metals to improve the microstructure of the materials and further improve the material properties. This provides a new way for the development of new functional materials.
Key words:  high magnetic field      alloy      solidification      functional material      graded material      anisotropic material     
Received:  14 December 2017     
ZTFLH:  TG 430.99  
Fund: Supported by National Natural Science Foundation of China (Nos.51425401, 51404060, 51690161, 51574073 and 51774086)
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Qiang WANG
Meng DONG
Jinmei SUN
Tie LIU
Yi YUAN

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https://www.ams.org.cn/EN/10.11900/0412.1961.2017.00535     OR     https://www.ams.org.cn/EN/Y2018/V54/I5/742

Fig.1  Temperature fluctuations in the molten silicon when magnetic field strength (H) is 0, 39800 and 79600 A/m[34]
Fig.2  Schematic illustration of increase or decrease of Deff due to thermo-electromagnetic convection effect (TEMCE) and electromagnetic braking effect (EMBE) (Deff—effective diffusivity, f(B)—magnetic field induction intensity)[56]
Fig.3  BSE images of directionally solidified Al-4.5%Cu (mass fraction) alloy under different magnetic fields[62]
(a)transverse, 0 T (b) transverse, 2 T (c) transverse, 6 T
(d) longitudinal, 0 T (e) longitudinal, 2 T (f) longitudinal, 6 T
Fig.4  Microstructures of samples under different experimental conditions[66]
(a) 0 T, 0 A (b) 0 T, 90 A (c) 10 T, 0 A (d) 10 T, 90 A
Fig.5  Micrographs of MnSb/Sb-MnSb gradients in Mn-89.7%Sb (mass fraction) alloys solidified without and with 11.5 T magnetic field in different field gradients and various holding time (B—magnetic induction intensity, g—gravitational acceleration, BdB/dz—the gradient of the magnetic field in the direction of the z axis)[68]
(a) 0 T, 30 min (b) BdB/dz = -114 T2/m, 30 min (c) BdB/dz = -282 T2/m, 30 min (d) BdB/dz = -282 T2/m, 90 min (e) BdB/dz = 282 T2/m, 30 min
Fig.6  Microstructures (a~d) and volume fraction distribution in longitudinal section (e) of directionally solidified Al-8%Fe (mass fraction) alloy grown at 30 μm/s under various applied magnetic fields (V—solidification rate)[74]
(a) 0 T (b) 0.4 T (c) 1 T (d) 6 T (e) volume fraction distribution of the primary Al3Fe phase (The starting point of the abscissa distance corresponds to the top position of the above metallograph)
Fig.7  Longitudinal microstructures of the Mn-89.7%Sb (mass fraction) alloy specimens after the annealing process at 0 and 11.5 T with different annealing time[76]
(a) 0 T, 30 min (b) 11.5 T, 30 min (c) 11.5 T, 60 min (d) 11.5 T, 90 min
Fig.8  Inverse pole figures of the TbFe2 alloys treated without (a) and with (b) 8.8 T magnetic field[84]
Fig.9  Microstructures (a, c) and the volume fractions of the MnSb and Sb phases along the depth from the top surface layer in the specimen (b, d) for Mn-89.7%Sb (mass fraction) hypoeutectic alloy solidified under BdB/dz=-250 T2/m (a, b) and 314 T2/m (c, d) [87]
Fig.10  <111> orientation degrees (O<111>) of (Tb, Dy)Fe2 through the depths of alloys solidified in various high magnetic field gradients (a) and the maximum magnetostriction of alloys solidified in various high magnetic fields at 3.184×105 A/m (b)[91]
Fig.11  Saturation magnetization distributions in Mn-89.7%Sb (mass fraction) alloys solidified without (a) and with (b) a symmetrically graded magnetic field of 12 T, and corresponding magnetic-field gradient distribution (c)(Ms—saturation magnetization, G—magnetic field gradient) [92]
Fig.12  Magnetostrictions as functions of the magnetic field under different compressive stresses for the master and treated alloys [84]
Fig.13  Macrostructures of the Bi-4.36%Mn (mass fraction) alloy solidified under various conditions[99]
(a) 0 T (b) 11.5 T
Fig.14  Optical micrographs of the longitudinal section of the Tb0.27Dy0.73Fe1.95 alloys[100]
(a) master
(b) remelted without magnetic field
(c) remelted with a 4.4 T magnetic field
Fig.15  Longitudinal section microstructures of Tb0.27Dy0.73Fe1.95 alloy with 50 μm/s pulling rate under different magnetic field conditions
(a) 0 T (b) 6 T
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