# Effects of High-Density Pulse Currents on the Solidification Structures of Cu-SiCp/AZ91D Composites

Authors: Xi Hao; Weixin Hao; Guihong Geng; Teng Ma; Chen Wang; Fuqiang Zhao; Hao Song; Yugui Li
Journal: Advances in Materials Science and Engineering
 (2019)

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## Abstract

In this study, Cu-SiCp/AZ91D composites were prepared with high-density pulse currents. The wettability between SiCp and matrix during solidification was improved by coating 0.095-μm thick copper film on the surface of SiCp. By comparing the composites prepared with/without pulse currents, the solidification structure and its formation mechanism of Cu-SiCp/AZ91D composites were analyzed under different conditions. The Cu-SiCp/AZ91D composites prepared without high-density pulse currents were mainly composed of α-Mg, β-Mg17Al12, and a small amount of Mg2Si phases, with coarse grains and uneven structures. Under the action of high-density pulse currents, the structures of Cu-SiCp/AZ91D composites were transformed into α-Mg and Mg2Si phases with refined grain, and the homogeneity of the structures was improved significantly.


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## Body

## 1. Introduction

Magnesium matrix composites are widely used in aerospace, construction, marine, and mineral processing industries due to their low density, good mechanical properties, and good corrosion resistance [1–3]. However, the performance of traditional magnesium alloys can no longer meet the needs of social development, and people are committed to the preparation of high-performance magnesium alloys. At present, the commonly used preparation methods of magnesium matrix composites include powder metallurgy, stirring casting, in situ synthesis, and melt infiltration methods [4–6]. After treatment, the reinforced particles are evenly distributed, and the properties of alloys are improved. However, these preparation methods require strict pretreatment procedures, high manufacturing costs, and complex operation. As a new technology, the treatment of alloy melt by using high-density pulsed current has attracted the attention of researchers, and some research results have been achieved. Especially under the action of high-density pulsed current, it can effectively inhibit the segregation of the second phase and refine the solidification structure. At the same time, this technology has the characteristics of in situ synthesis technology for some composite materials [7–9].SiC particles are often used as reinforcing phase for magnesium matrix composites. However, the surface activity of micron and nano-SiC particles is easy to agglomerate, and the wettability of SiC particles is poor [10]. The wettability can generally be improved by increasing the surface energy of the reinforcing phase to lower the surface tension of the melt. Preheat treatment of reinforcing particles, addition of appropriate elements to melt, surface coating, and ultrasonic dispersion can be adopted. Therefore, the modification of the SiC surface is beneficial to promote the wettability of interface and the uniform distribution of reinforcing particles in the process of liquid casting. At present, the volume fraction of SiC reinforcing phase added by the full liquid stirring casting method is 5 vol.%∼10 vol.% [11]. In this paper, a new type of full liquid treatment device under the condition of electric pulse is used. SiC particles coated with copper film are added into the AZ91D matrix as reinforcing phase to improve the wettability of the matrix and reinforcing phase. The Cu-SiCp/AZ91D composites prepared under different conditions are studied. The microstructures of AZ91D composites and the strengthening mechanism are discussed, which provides a new design concept and method for future research.


## 2. Experimental

Cu-SiCp/AZ91D composites contain 10 vol.% Cu-SiCp, in which a layer of 0.095 μm copper film is deposited on the surface of SiCp. The mass of Cu is 17.3% of that of Cu-SiCp. The sample size of AZ91D magnesium alloy is 16 mm × 16 mm × 30 mm. The chemical composition of the AZ91D alloy is shown in Table 1 [12]. The magnesium alloy was used as the matrix in the experiment, and 10 μm SiC particles were chosen as the reinforcer to prepare Cu-SiCp/AZ91D composites.Table 1
Chemical composition of AZ91D alloy.
ω (%)
Cu
Al
Zn
Mn
Si
Mg
0.015
9
0.67
0.25
0.05
Bal.
Note: reproduced from Zhang et al. [12], under the Creative Commons Attribution License/public domain.Figure1 shows the schematic diagram of the electric pulse melting device used in this study. The preparation process is described as follows. Firstly, magnesium alloy samples were placed in the boron nitride crucible, and then, SiCp was placed on the surface of magnesium alloys. The pressure in the vacuum box was pumped to 2 × 10−4 Pa, and then, argon gas was filled to the pressure of 50 kPa. Then turning on the high-frequency induction power supply, the samples were heated to 700°C in the vacuum box, and all the samples were melted in the crucible. Then, the metal melt was heated for 10 min. Finally, the electric pulse was applied to the metal melt for 5 min. The electric pulse treatment process of the metal melt was provided as follows. First, set the pulse width 10 μs, the frequency is 30 Hz, and start the power, then read the required current peak on the oscilloscope by adjusting the voltage, and finally the heating device was closed to start the cooling process in the furnace. When the body was completely solidified, the pulse power supply was turned off.Figure 1
Schematic diagram of the electric pulse melting device.The structure and composition of the samples were analyzed by SS-550 Shimadzu scanning electron microscope, Phoenix EDAX-2000 energy dispersive spectrometer, and X-ray diffractometer (6000×).


## 3. Results and Discussion

### 3.1. XRD Analysis of Solidification Structures

XRD analysis was carried out with the prepared magnesium matrix composites (Figure2). As shown in Figure 2, the Cu-SiCp/AZ91D magnesium matrix composites prepared under conventional conditions mainly consist of three phases: α-Mg, β-Mg17Al12, and Mg2Si. The composites prepared under pulse currents mainly consist of two phases: α-Mg and Mg2Si, and the diffraction peaks of Mg2Si are enhanced.Figure 2
XRD spectrum of Cu-SiCp/AZ91D magnesium matrix composites.


### 3.2. SEM Analysis of Solidification Structures

In order to further analyze the tissue changes, the samples were photographed at a high solution for elemental scanning. The scanning results are listed in Table2. The XRD spectrum of Figure 2 and Table 2 indicated that the material was composed of α-Mg phase (Spectrogram 1 and Spectrogram 4). The black skeletal dendrite is α-Mg17Al12 phase (Spectrogram 2). The new phase Mg2Si is formed on the dendrite of β-Mg17Al12 (Spectrogram 3). The gray-white structure near Mg2Si is composed of α-Mg and Al4C3 as well as less attached Cu (Spectrogram 5).Table 2
AZ91D and Cu-SiCp/AZ91D magnesium matrix composite element scanning atomic content table.
Elemental atomic percentage
C
Mg
Al
Si
Zn
Cu
Spectrogram 1
—
90.97
8.27
—
0.76
—
Spectrogram 2
—
60.48
39.52
—
—
Spectrogram 3
—
66.71
—
33.29
—
Spectrogram 4
—
93.78
5.68
—
0.54
—
Spectrogram 5
21.94
51.23
23.84
—
—
2.99Figure3 shows high-resolution SEM photographs of AZ91D magnesium alloy, Cu-SiCp/AZ91D magnesium matrix composite, and Cu-SiCp/AZ91D composite in pulsed electric fields. The AZ91D magnesium alloy is mainly composed of gray-black α-Mg and dark-black skeletal eutectic β-Mg17Al12 (Figure 3(a)). The phase of β-Mg17Al12 grows along the grain boundary. Figures 3(b) and 3(c) show that the hard strengthening phase Mg2Si grows along the β-phase after adding Cu-SiCp, and the Mg2Si phase replaces the β-Mg17Al12 phase after applying pulsed electric fields. This is consistent with the bright white structure shown in Figures 4(b) and 4(c), the formation of Mg2Si diffraction peaks in Figure 2, and the disappearance of Mg17Al12 diffraction peaks. The results show that Mg2Si precipitates as a heterogeneous nucleation point at the grain boundary. SiC and Mg17Al12 peaks were not observed in the XRD spectra (Figure 2). It was inferred that the formation of Mg2Si was ascribed to the reaction of SiCp and Al [6]:(1)3SiC+4Al=Al4C3+3SiC(2)Mg+2Si=Mg2SiFigure 3
High times SEM of AZ91D magnesium alloy and Cu-SiCp/AZ91D magnesium matrix composites: (a) AZ91D, (b) Cu-SiCp/AZ91D, and (c) pulsed electric field+Cu-SiCp/AZ91D).Figure 4
Photos of AZ91D magnesium alloy and Cu-SiCp/AZ91D magnesium matrix composites: (a) AZ91D, (b) Cu-SiCp/AZ91D, and (c) pulsed electric field +Cu-SiCp/AZ91D.
(a)
(b)
(c)SiCp in the copper-SiCp was depleted, and Cu was distributed among the dendrites. Formed Al4C3 was dispersed in the vicinity of Mg2Si [2]. Al4C3 was mixed with the matrix α-Mg, thus changing the color from gray to gray-white (red circle in Figure 3(c)), which was consistent with Spectrogram 5 in Table 2. The color change in Figure 3(b) was not obvious because SiCp was not mixed evenly, and the content of Al4C3 was too small. As a heterogeneous nucleation point, Al4C3 increased the nucleation rate and refined grains [13, 14].Copper-SiCp used in this study could effectively change the wettability between particles and melt, but segregation of copper-SiCp still occurred, and a large number of copper-SiCp had not yet reacted with Al in the melt. Dendrites in the structure were mainly composed of β-Mg17Al12 and Mg2Si phases. Al4C3 had fewer heterogeneous nucleation points and poor homogeneity, and the grain refinement effect was not observed (Figure 3(b)). When high-density pulse currents were applied, the Lorentz force was produced by the metal melt under the action of electric fields [15], and the first cyclotron force of the Lorentz force formed strong convection together with the melt, thus resulting in the decreased temperature gradient, widened two-phase zone in the melt. Therefore, the segregation of Cu-SiCp was effectively restrained, and Cu-SiCp was allowed to join the melt and maintained in the uniformly mixing state. Due to the wetting effect and the increase in the contact area, Cu-SiCp reacted with Mg17Al12 sufficiently, thus resulting in phase replacement of β-Mg17Al12 phase by the vermicular Mg2Si (Figure 3(c)). In addition, the formation of a large number of heterogeneous nucleation points Al4C3 increased the nucleation rate, promoted heterogeneous nucleation, obtained uniform structures, and further refined the grains [16] (Figure 4(c)).In the magnesium alloy of AZ91D,α-Mg formed the matrix, and the β-Mg17Al12 phase was distributed along the crystal boundary with the large crystal grain. In the Cu-SiCp/AZ91D composite material obtained under conventional conditions, the tissue was mainly composed of three phases: β-Mg17Al12, Mg2Si, and a small amount of Al4C3 phase. Under pulsed electric fields, the composite material showed the uniform structure, and the vermicular Mg2Si phase replaced the β-Mg17Al12 phase. In the vicinity of the Mg2Si phase, α-Mg was mixed with Al4C3 to form the gray-white zone. When a high-density pulse current is applied, the Lorentz force is generated in the melt under the electric field [16], and the melt is strongly convected by the Lorentz force, resulting in a decrease in the temperature gradient inside the melt and a widening of the two-phase region. In this way, the nucleation rate of Cu-SiCp/AZ91D increased, and crystal grains were refined. After adding Cu-SiCp particles, the Al4C3 phase was not detected because the following hydrolysis reaction occurred in the sampling preparation process [6]:(3)Al4C3+12H2O=4AlOH3+3CH4↑


### 3.3. Refinement Mechanism of Solidification Structures

Figure3 shows the metallographic pictures of AZ91D magnesium alloy, Cu-SiCp/AZ91D magnesium matrix composite, and Cu-SiCp/AZ91D composite under pulsed electric fields. As shown in Figure 4(a), AZ91D magnesium alloy is composed of black matrix and gray reticulated structure, and its grain size is relatively large. As shown in Figure 3(b), after adding Cu-SiCp, a little bright white fine structure occurs in the gray-white reticulated structure (marked by the blue ellipse), and the grains near the bright white structure are refined Cu-SiCp that can provide potential nucleation points for the melt, thus increasing the number of fine grains in the composites. The copper-SiCp particles have the pinning effect on grain boundaries and inhibit the grain growth [17]. As shown in Figure 4(c), after applying pulsed electric fields and adding Cu-SiCp, all the gray-white reticulated structures become the finer bright white structures with dense dendrites and fine grains.According to the theory of electromagnetic field dynamics, under the action of pulse currents, the particles and the whole melt are affected by the changing electromagnetic force. This vibration will produce the following effects on the aggregation of particles in the melt. Firstly, the vibration of the electromagnetic force can break coagulated Cu-SiCp into smaller particles, as shown in Figure 5(a). Secondly, under the action of pulse currents, the SiC particles of different sizes are also affected by inertial force, which results in the relative motion between them. The effect of relative motion also weakens the coagulation effect of Cu-SiCp, as shown in Figure 5(b). Furthermore, under the action of pulsed electric fields, the undercooling of the alloy melt increases, thus leading to the increase in the viscosity of the alloy melt and weakening the coagulation effect of Cu-SiCp particles [10, 18].Figure 5
Particle condensation process under the influence of electromagnetic force.
(a)
(b)In order to study the effect of pulse currents on the nucleation rate of alloy melt, the nucleation rate of classical nucleation theory [15] is expressed as follows:(4)N=nKThexp−16πσsl3Tm23Lm2ΔT2KT⋅exp−ΔGAKT,where h is the Planck constant; n is the number of atoms per unit volume; K is the Boltzmann constant; T is the absolute temperature; SL is the surface free energy; Tm is the melting point; ΔT=ΔTm−T is the undercooling of the alloy melt; Lm is the latent heat of melting; ΔGA is the liquid atom nucleation barrier. When the axisymmetric current j→=jrez→ passes through a cylindrical conductive melt, the magnetic field B→=Bre0→ is formed. Pulse currents usually affect the undercooling of the alloy melt through the generated Joule heat and electromagnetic force. In addition, when pulse currents are applied during the melt solidification process, more solute atoms are stimulated to break the energy barrier and enter the matrix due to the effect of instantaneous discharge. At the same time, pulse currents enhance the vibration of atoms deviating from the equilibrium position, reduce the energy barrier, and change the nucleation barrier. Therefore, in the original nuclear rate equation (1), ΔGA=ΔG0+ΔGE, where G0 is the thermodynamic barrier for the nucleation without applying an external field and GE is the thermodynamic barrier for the nucleation after applying an external field. Then, we get(5)ΔGA=ΔG0+ΔGE=ΔG0+K1⋅j2⋅ξ2⋅V,ξ=σ0−σn⋅σn−2σ0−1.Among them,K1 is a parameter related to materials; J is the pulsed current density; σ0 is the conductivity of disordered dielectrics; σn is the conductivity of nuclei; V is the volume of nuclei; and K is the Boltzmann constant. For the crystalline melt, if σn>σ0, then ξ>0. Therefore, it can be concluded that the pulse currents reduce the nucleation barrier in the alloy melt. The effect of pulse currents increases the nucleation rate in the alloy melt, and the increase in the nucleation rate leads to the grain refinement in the alloy melt. When EPT is applied after heat preservation, the pulse currents contact directly with the melt and the nucleation growth stops, thus forming an equiaxed region, which can effectively improve the nucleation rate of liquid metal and semisolid metal and trigger the heterogeneous nucleation mechanism [19]. Fine structures were obtained during the rapid solidification because the increase in the undercooling promoted the nucleation rate. The mechanism of dendrite breakage induced by Loren magnetic force under electric pulse treatment allowed the grain refinement [16, 20].


## 3.1. XRD Analysis of Solidification Structures

XRD analysis was carried out with the prepared magnesium matrix composites (Figure2). As shown in Figure 2, the Cu-SiCp/AZ91D magnesium matrix composites prepared under conventional conditions mainly consist of three phases: α-Mg, β-Mg17Al12, and Mg2Si. The composites prepared under pulse currents mainly consist of two phases: α-Mg and Mg2Si, and the diffraction peaks of Mg2Si are enhanced.Figure 2
XRD spectrum of Cu-SiCp/AZ91D magnesium matrix composites.


## 3.2. SEM Analysis of Solidification Structures

In order to further analyze the tissue changes, the samples were photographed at a high solution for elemental scanning. The scanning results are listed in Table2. The XRD spectrum of Figure 2 and Table 2 indicated that the material was composed of α-Mg phase (Spectrogram 1 and Spectrogram 4). The black skeletal dendrite is α-Mg17Al12 phase (Spectrogram 2). The new phase Mg2Si is formed on the dendrite of β-Mg17Al12 (Spectrogram 3). The gray-white structure near Mg2Si is composed of α-Mg and Al4C3 as well as less attached Cu (Spectrogram 5).Table 2
AZ91D and Cu-SiCp/AZ91D magnesium matrix composite element scanning atomic content table.
Elemental atomic percentage
C
Mg
Al
Si
Zn
Cu
Spectrogram 1
—
90.97
8.27
—
0.76
—
Spectrogram 2
—
60.48
39.52
—
—
Spectrogram 3
—
66.71
—
33.29
—
Spectrogram 4
—
93.78
5.68
—
0.54
—
Spectrogram 5
21.94
51.23
23.84
—
—
2.99Figure3 shows high-resolution SEM photographs of AZ91D magnesium alloy, Cu-SiCp/AZ91D magnesium matrix composite, and Cu-SiCp/AZ91D composite in pulsed electric fields. The AZ91D magnesium alloy is mainly composed of gray-black α-Mg and dark-black skeletal eutectic β-Mg17Al12 (Figure 3(a)). The phase of β-Mg17Al12 grows along the grain boundary. Figures 3(b) and 3(c) show that the hard strengthening phase Mg2Si grows along the β-phase after adding Cu-SiCp, and the Mg2Si phase replaces the β-Mg17Al12 phase after applying pulsed electric fields. This is consistent with the bright white structure shown in Figures 4(b) and 4(c), the formation of Mg2Si diffraction peaks in Figure 2, and the disappearance of Mg17Al12 diffraction peaks. The results show that Mg2Si precipitates as a heterogeneous nucleation point at the grain boundary. SiC and Mg17Al12 peaks were not observed in the XRD spectra (Figure 2). It was inferred that the formation of Mg2Si was ascribed to the reaction of SiCp and Al [6]:(1)3SiC+4Al=Al4C3+3SiC(2)Mg+2Si=Mg2SiFigure 3
High times SEM of AZ91D magnesium alloy and Cu-SiCp/AZ91D magnesium matrix composites: (a) AZ91D, (b) Cu-SiCp/AZ91D, and (c) pulsed electric field+Cu-SiCp/AZ91D).Figure 4
Photos of AZ91D magnesium alloy and Cu-SiCp/AZ91D magnesium matrix composites: (a) AZ91D, (b) Cu-SiCp/AZ91D, and (c) pulsed electric field +Cu-SiCp/AZ91D.
(a)
(b)
(c)SiCp in the copper-SiCp was depleted, and Cu was distributed among the dendrites. Formed Al4C3 was dispersed in the vicinity of Mg2Si [2]. Al4C3 was mixed with the matrix α-Mg, thus changing the color from gray to gray-white (red circle in Figure 3(c)), which was consistent with Spectrogram 5 in Table 2. The color change in Figure 3(b) was not obvious because SiCp was not mixed evenly, and the content of Al4C3 was too small. As a heterogeneous nucleation point, Al4C3 increased the nucleation rate and refined grains [13, 14].Copper-SiCp used in this study could effectively change the wettability between particles and melt, but segregation of copper-SiCp still occurred, and a large number of copper-SiCp had not yet reacted with Al in the melt. Dendrites in the structure were mainly composed of β-Mg17Al12 and Mg2Si phases. Al4C3 had fewer heterogeneous nucleation points and poor homogeneity, and the grain refinement effect was not observed (Figure 3(b)). When high-density pulse currents were applied, the Lorentz force was produced by the metal melt under the action of electric fields [15], and the first cyclotron force of the Lorentz force formed strong convection together with the melt, thus resulting in the decreased temperature gradient, widened two-phase zone in the melt. Therefore, the segregation of Cu-SiCp was effectively restrained, and Cu-SiCp was allowed to join the melt and maintained in the uniformly mixing state. Due to the wetting effect and the increase in the contact area, Cu-SiCp reacted with Mg17Al12 sufficiently, thus resulting in phase replacement of β-Mg17Al12 phase by the vermicular Mg2Si (Figure 3(c)). In addition, the formation of a large number of heterogeneous nucleation points Al4C3 increased the nucleation rate, promoted heterogeneous nucleation, obtained uniform structures, and further refined the grains [16] (Figure 4(c)).In the magnesium alloy of AZ91D,α-Mg formed the matrix, and the β-Mg17Al12 phase was distributed along the crystal boundary with the large crystal grain. In the Cu-SiCp/AZ91D composite material obtained under conventional conditions, the tissue was mainly composed of three phases: β-Mg17Al12, Mg2Si, and a small amount of Al4C3 phase. Under pulsed electric fields, the composite material showed the uniform structure, and the vermicular Mg2Si phase replaced the β-Mg17Al12 phase. In the vicinity of the Mg2Si phase, α-Mg was mixed with Al4C3 to form the gray-white zone. When a high-density pulse current is applied, the Lorentz force is generated in the melt under the electric field [16], and the melt is strongly convected by the Lorentz force, resulting in a decrease in the temperature gradient inside the melt and a widening of the two-phase region. In this way, the nucleation rate of Cu-SiCp/AZ91D increased, and crystal grains were refined. After adding Cu-SiCp particles, the Al4C3 phase was not detected because the following hydrolysis reaction occurred in the sampling preparation process [6]:(3)Al4C3+12H2O=4AlOH3+3CH4↑


## 3.3. Refinement Mechanism of Solidification Structures

Figure3 shows the metallographic pictures of AZ91D magnesium alloy, Cu-SiCp/AZ91D magnesium matrix composite, and Cu-SiCp/AZ91D composite under pulsed electric fields. As shown in Figure 4(a), AZ91D magnesium alloy is composed of black matrix and gray reticulated structure, and its grain size is relatively large. As shown in Figure 3(b), after adding Cu-SiCp, a little bright white fine structure occurs in the gray-white reticulated structure (marked by the blue ellipse), and the grains near the bright white structure are refined Cu-SiCp that can provide potential nucleation points for the melt, thus increasing the number of fine grains in the composites. The copper-SiCp particles have the pinning effect on grain boundaries and inhibit the grain growth [17]. As shown in Figure 4(c), after applying pulsed electric fields and adding Cu-SiCp, all the gray-white reticulated structures become the finer bright white structures with dense dendrites and fine grains.According to the theory of electromagnetic field dynamics, under the action of pulse currents, the particles and the whole melt are affected by the changing electromagnetic force. This vibration will produce the following effects on the aggregation of particles in the melt. Firstly, the vibration of the electromagnetic force can break coagulated Cu-SiCp into smaller particles, as shown in Figure 5(a). Secondly, under the action of pulse currents, the SiC particles of different sizes are also affected by inertial force, which results in the relative motion between them. The effect of relative motion also weakens the coagulation effect of Cu-SiCp, as shown in Figure 5(b). Furthermore, under the action of pulsed electric fields, the undercooling of the alloy melt increases, thus leading to the increase in the viscosity of the alloy melt and weakening the coagulation effect of Cu-SiCp particles [10, 18].Figure 5
Particle condensation process under the influence of electromagnetic force.
(a)
(b)In order to study the effect of pulse currents on the nucleation rate of alloy melt, the nucleation rate of classical nucleation theory [15] is expressed as follows:(4)N=nKThexp−16πσsl3Tm23Lm2ΔT2KT⋅exp−ΔGAKT,where h is the Planck constant; n is the number of atoms per unit volume; K is the Boltzmann constant; T is the absolute temperature; SL is the surface free energy; Tm is the melting point; ΔT=ΔTm−T is the undercooling of the alloy melt; Lm is the latent heat of melting; ΔGA is the liquid atom nucleation barrier. When the axisymmetric current j→=jrez→ passes through a cylindrical conductive melt, the magnetic field B→=Bre0→ is formed. Pulse currents usually affect the undercooling of the alloy melt through the generated Joule heat and electromagnetic force. In addition, when pulse currents are applied during the melt solidification process, more solute atoms are stimulated to break the energy barrier and enter the matrix due to the effect of instantaneous discharge. At the same time, pulse currents enhance the vibration of atoms deviating from the equilibrium position, reduce the energy barrier, and change the nucleation barrier. Therefore, in the original nuclear rate equation (1), ΔGA=ΔG0+ΔGE, where G0 is the thermodynamic barrier for the nucleation without applying an external field and GE is the thermodynamic barrier for the nucleation after applying an external field. Then, we get(5)ΔGA=ΔG0+ΔGE=ΔG0+K1⋅j2⋅ξ2⋅V,ξ=σ0−σn⋅σn−2σ0−1.Among them,K1 is a parameter related to materials; J is the pulsed current density; σ0 is the conductivity of disordered dielectrics; σn is the conductivity of nuclei; V is the volume of nuclei; and K is the Boltzmann constant. For the crystalline melt, if σn>σ0, then ξ>0. Therefore, it can be concluded that the pulse currents reduce the nucleation barrier in the alloy melt. The effect of pulse currents increases the nucleation rate in the alloy melt, and the increase in the nucleation rate leads to the grain refinement in the alloy melt. When EPT is applied after heat preservation, the pulse currents contact directly with the melt and the nucleation growth stops, thus forming an equiaxed region, which can effectively improve the nucleation rate of liquid metal and semisolid metal and trigger the heterogeneous nucleation mechanism [19]. Fine structures were obtained during the rapid solidification because the increase in the undercooling promoted the nucleation rate. The mechanism of dendrite breakage induced by Loren magnetic force under electric pulse treatment allowed the grain refinement [16, 20].


## 4. Conclusion

Cu-SiCp/AZ91D composites prepared without high-density pulse currents mainly consisted of three phases: α-Mg, β-Mg17Al12, and Mg2Si. By applying high-density pulse currents, the structures of Cu-SiCp/AZ91D composites were transformed into the phases of α-Mg and Mg2Si.Cu-SiCp/AZ91D composites were prepared by different testing methods. The results showed that the Cu-SiCp/AZ91D composites under high-density pulse currents had uniform structures, and the grains were significantly refined. The nucleation barrier was reduced, and the nucleation rate was effectively increased by applying high-density pulse currents. Therefore, the fine structure was obtained.The microstructures of Cu-SiCp/AZ91D composites were transformed into α-Mg, Al4C3 and Mg2Si phases under the action of high-density pulse currents. Al4C3 and Mg2Si phases as heterogeneous nucleation points increased the nucleation rate of the composites. The Al4C3 phase was not detected in the obtained tissues due to the hydrolysis reaction.



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*Source: 1684580-2019-04-03.xml*