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Acta Metall Sin  2018, Vol. 54 Issue (5): 682-700    DOI: 10.11900/0412.1961.2018.00080
Special Issue for the Solidification of Metallic Materials Current Issue | Archive | Adv Search |
Progress in the Solidification of Monotectic Alloys
Jiuzhou ZHAO(), Hongxiang JIANG
Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China
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Jiuzhou ZHAO, Hongxiang JIANG. Progress in the Solidification of Monotectic Alloys. Acta Metall Sin, 2018, 54(5): 682-700.

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Abstract  

Monotectic alloys or alloys with a miscibility gap in the liquid state are a broad kind of materials. Many of them have great potential applications in industry. However, these alloys have an essential drawback that the miscibility gap poses problems during solidification. When a homogeneous single phase liquid is cooled into the miscibility gap, the components are no longer miscible and two liquid phases develop. Generally, the liquid-liquid decomposition begins with the nucleation of the minority phase droplets. These droplets grow and coarsen then. They can also settle or float due to the specific gravity differences between phases and migrate due to the temperature gradient or concentration gradient. The motions of the droplets cause the formation of a microstructure with serious phase segregation. Researchs have been carried out to investigate the solidification process of monotectic alloys on ground as well as under the microgravity conditions in space. The feasibility of controlling the microstructures of monotectic alloys by using electric field, magnetic field, microalloying, etc. has been investigated. Meanwhile, plenty of efforts have been made to model and simulate the microstructure evolution of monotectic alloy during the L-L phase transformation. This article will review the research work in this field during the last few decades and propose some perspectives for future studies on the solidification process of monotectic alloys.
Key words:  monotectic alloy      solidification      thermodynamic      thermophysical property      simulation     
Received:  06 March 2018     
ZTFLH:  TG14  
  TG2  
Fund: Supported by National Natural Science Foundation of China (Nos.51771210, 51471173 and 51501207) and China's Manned Space Station Project (No.TGJZ800-2-RW024)
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Jiuzhou ZHAO
Hongxiang JIANG

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https://www.ams.org.cn/EN/10.11900/0412.1961.2018.00080     OR     https://www.ams.org.cn/EN/Y2018/V54/I5/682

Fig.1  Relationship between ΔGm and xB for A-B binary monotectic alloys (A, B—the two components of A-B binary monotectic alloys, ΔGm—the molar Gibbs free energy of mixing, ΔHm—the molar mixing enthalpy, ΔSm—the molar mixing entropy, xB—the molar or atomic fraction of the component B, T—the absolute temperature, TC—the critical temperature)
(a) T>TC (b) T<TC
Fig.2  Schematic phase diagram of the binary monotectic alloy showing the miscibility gap (solid line) and spinodal line (dashed line)
Fig.3  Measured and calculated temperature (T) profile, the binodal line temperature (Tb), and the nucleation rate in front of the solidification interface along the central z-axes for the Al-5%Pb (mass fraction) sample continuously solidified at the rate of 5 mm/s[131]
Fig.4  Maximum nucleation rate (Imax) of the minority phase droplets (MPDs) and the axial vector of the flow velocity (VCZ) in front of the solidification interface along the radial direction for the Al-5%Pb (mass fraction) alloy continuously solidified at the rate of 5 mm/s[96]
Fig.5  Convective velocities of the melt in front of the solidification interface for the Al-5%Pb (mass fraction) samples continuously solidified at the rate of 5 mm/s in the magnetic field of different strengths[66]
Fig.6  Maximum nucleation rates of the MPDs at the solidification interface along the radial direction for the Al-5%Pb (mass fraction) alloys continuously solidified at the rate of 5 mm/s in the static magnetic field of different strengths [66]
Fig.7  Volume fraction of the MPDs in the melt at the solidification interface along the radial direction for the Al-5%Pb (mass fraction) alloys continuously solidified at the rate of 5 mm/s in the magnetic field of different strengths [96]
Fig.8  Microstructures of the Al-7%Pb (mass fraction) alloys continuously solidified at the rate of 8 mm/s under the effect of the direct current of 0 A/cm2 (a), 170 A/cm2 (b) and 438 A/cm2 (c), respectively[63]
Fig.9  Effect of the electric current pulses (ECPs) on the microstructure of Bi-10%Cu-10%Sn (a, b) and Cu-25%Bi-25%Sn (mass fraction) (c, d) alloys continuously solidified at the rate of 10 mm/s[65]
(a, c) without the ECP treatment
(b, d) with the ECP of the peak current density of 3×108 A/m2, the frequency of the ECPs is 50 Hz, the duration of each electro-pulse is 6 μs[65]
Fig.10  Microstructures of Al-5%Pb-xBi (mass fraction) alloys with x=0 (a) and x=0.10% (b) continuously solidified at the rate of 10 mm/s[180]
Fig.11  Marangoni migration velocities for r direction (uM-r), z direction (uM-z) and Stokes migration velocity uSof the Pb-rich droplets with average size as a function of position in front of the solidification interface for Al-5.0%Pb-xBi (mass fraction) alloys with x=0 and x=0.10%[180]
Fig.12  Microstructures of Al-9.0%Bi-xTiC (mass fraction) alloys with x=0 (a), x=0.034% (b), x=0.05% (c), x=0.066% (d), x=0.084% (e) and x=0.126% (f)[180]
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