Microstructure Evolution and Solidiﬁcation Behavior of a Novel Semi-Solid Alloy Slurry Prepared by Vibrating Contraction Inclined Plate

: In this work, based on the A356 alloy, a novel Al–Si–Mg–Cu–Fe–Sr alloy with good mechanical property and high thermal conductivity was developed. The semi-solid slurry of the alloy was prepared via the vibrating contraction inclined plate. The microstructure evolution and solidiﬁcation behavior of the alloy were investigated. The results demonstrated that, compared with the A356 alloy, the enhanced property of the Al–Si–Mg–Cu–Fe–Sr alloy was associated with the size of primary α -Al grains and morphology of eutectic Si phases. In addition, the preparation process parameters of semi-solid slurries, including the pouring temperature, inclination angle, and vibration frequency, had a crucial effect on the size and morphology of primary α -Al grains. The optimized pouring temperature, inclination angle, and vibration frequency were 670 ◦ C, 45 ◦ , and 60 Hz, respectively. In this condition, for the primary α -Al grains, a minimum grain diameter of 64.31 µ m and a maximum shape factor of 0.80 were obtained. This work provides a reference for the application of the alloy with high performance in the ﬁeld of automobile and communication.


Introduction
Semi-solid metal (SSM) processing technology, a modern and advanced technology, has an advantage of fabricating metal parts with complicated structure, high quality, and improved mechanical properties [1][2][3]. It is necessary to obtain the semi-solid slurry with spherical grains during SSM processing [4]. Some preparation methods of semi-solid slurries have been developed, such as mechanical stirring [5], electromagnetic stirring [6], gas induced semi-solid [7], and the indirect ultrasonic vibration method [8].
In order to develop the low-cost and simplified method, an inclined plate process for preparing the semi-solid slurry is proposed [9]. The melt is poured onto the inclined plate above the liquidus temperature and then the semi-solid slurry is formed when the melt flows through the inclined plate. For example, Taghavi et al. [10] studied the effect of the inclined plate length and angle on the thixotropic microstructure of the A356 alloy and found that the inclination angle of 40 • and length of inclined plate of 40 cm were optimized parameters to prepare the semi-solid slurry. Kund [11] pointed out that the microstructure of the A356 alloy was affected by the inclined plate length and cooling rate, i.e., when the plate length was 250 mm, the desirable microstructure was obtained. Khosravi et al. [12] explored the optimization of the inclined plate process in the semi-solid A356 alloy; the result indicated that the pouring temperature of 660 • C, the cooling plate length of 360 mm, and inclination angle of 48 • were the optimized parameters. It can be concluded that the process parameters of semi-solid slurries play a significant role in determining the microstructure, thus affecting the property of alloys.
These studies enhance our understanding of the preparation of semi-solid slurries. To avoid slurry adhesion on the plate surface and improve the slurry quality, we design a vibrating contraction inclined plate, including the cooling system, the vibrating system, and the tapered-runner design on the inclined plate. Compared with the common inclined plate process, the vibrating contraction inclined plate process has some advantages as follows. Firstly, the chilling effect is provided by the cooling water, which promotes the heterogeneous nucleation. Secondly, the shearing effect induced by the vibrating system inhibits the growth of dendrites and makes the primary α-Al grains gradually evolve into spherical grains. Finally, the aim of the tapered-runner design is to change the heat and mass transfer via the contact between the melt and inner wall and further avoid the slurry adhesion on the plate surface.
The A356 alloy that is viewed as the most common aluminum alloy is used for SSM processing technology. With the development of automobile and communication, high requirements are put forward for the properties of alloys. Therefore, a novel alloy with a good combination of mechanical properties and thermal conductivity should be developed. Alloying has an important effect on the microstructure and mechanical property of aluminum alloys [13]. For example, the appropriate addition of Mg and Cu elements helps improve the mechanical property of aluminum alloys [14,15]. The Sr element has a unique advantage of varying the morphology of eutectic Si phases [16,17]. Appropriately increasing the Fe element enhances the demolding ability [18] and thermal stability [19].
Therefore, in this work, a novel Al-Si-Mg-Cu-Fe-Sr alloy was developed, and its semi-solid slurry was prepared via the vibrating contraction inclined plate. The enhanced property was analyzed by the microstructure observation. Furthermore, the effect of pouring temperature, inclination angle, and vibration frequency on the size and morphology of primary α-Al grains was investigated. The microstructural evolution and solidification behavior of the alloy were analyzed.

Materials and Methods
An Al-8.2Si-0.46Mg-0.53Fe-0.15Cu-0.01Sr (wt%) alloy, termed the Al-Si-Mg-Cu-Fe-Sr alloy, was used as the experimental material. The Al-Si-Mg-Cu-Fe-Sr alloy was melted at 750 • C in a graphite clay crucible using a resistance furnace. After the melt was completely melted, degassing and deslagging were carried out at 720 • C and then held for 30 min. The melt temperature was reduced to 700 • C and then casted into a mold (Ø45 mm × 350 mm) to form cylindrical ingots. For comparison, the A356 alloy (Al-7.3Si-0.41Mg-0.15Fe (wt%)) was prepared by the same casting process.
The effect of various parameters on the microstructure of the semi-solid alloy was investigated using the vibrating contraction inclined plate process, as shown in Figure 1a. The process parameters, such as pouring temperature, inclination angle, and vibration frequency, were listed in Table 1. The alloy was melted at 750 • C. When the melt was completely melted, degassing and deslagging were carried out at 720 • C and then held for 30 min. After cooling to the target temperature, the melt was poured into a tundish. The function of the tundish was to ensure that the melt was steadily introduced into the taperedrunner of the inclined plate coated by a thin layer of TiO 2 , and the melt entered a mold with a preheated temperature of 200 • C, as shown in Figure 1b. The size of the tapered-runner was shown in Figure 1c. The melt and mold were cooled down to room temperature.

Pouring Temperature (°C)
Inclination Angle (°) Vibration Frequency (Hz)  660  45  0  670  45  0  680  45  0  690  45  0  700  45  0  670  15  0  670  30  0  670  60  0  670  45  30  670  45  60  670  45  90 Specimens for optical metallography observation were ground, mechanically polished, and then etched using a Keller's agent for 10 s. Microstructure was observed using an optical microscopy (OM, OLYMPUS-DSX-500, Japan). The Image-Pro Plus analysis software was used to analyze the average grain diameter and shape factor of primary α-Al grains, which could be calculated by [1] where , , , , and were the average diameter, shape factor, area, number, and perimeter of the primary α-Al grains, respectively. The secondary phases in the alloy were observed by a scanning electron microscope (SEM, Zeiss Supra 55, Germany) equipped with the energy dispersive spectroscopy (EDS).   0  670  45  0  680  45  0  690  45  0  700  45  0  670  15  0  670  30  0  670  60  0  670  45  30  670  45  60  670  45  90 Specimens for optical metallography observation were ground, mechanically polished, and then etched using a Keller's agent for 10 s. Microstructure was observed using an optical microscopy (OM, OLYMPUS-DSX-500, Tokyo, Japan). The Image-Pro Plus analysis software was used to analyze the average grain diameter and shape factor of primary α-Al grains, which could be calculated by [1] where D, F s , A, N, and C were the average diameter, shape factor, area, number, and perimeter of the primary α-Al grains, respectively. The secondary phases in the alloy were observed by a scanning electron microscope (SEM, Zeiss Supra 55, Jena, Germany) equipped with the energy dispersive spectroscopy (EDS).
Tensile tests were carried out at a tensile rate of 2 mm/min using a universal tensile machine (UTM, Instron5582, Norwood, MA, USA). Each specimen was measured at least three times, and the average value was calculated. The specimens were processed into cylinders (Ø12.7 mm × 3 mm) to measure the thermal diffusivity using the laser flash diffusivity instrument (FLD, NETZSCH LFA 427, Jena, Germany). The specimen density was determined using Archimedes method. In addition, the specific heat was measured with a differential scanning calorimeter (DSC, Setaram DSC131, Caluire-et-Cuire, France). Therefore, the thermal conductivity was calculated by [16] where λ, α, ρ, and c p were the thermal conductivity, thermal diffusivity, density, and specific heat, respectively. Figure 2 shows microstructure of the A356 and Al-Si-Mg-Cu-Fe-Sr alloys. Coarse dendrites are observed in the A356 alloy, as shown in Figure 2a. Compared with the A356 alloy, the Al-Si-Mg-Cu-Fe-Sr alloy displays a finer dendrite structure, as shown in Figure 2b. In addition, secondary phases also are observed in Figure 2. Tensile tests were carried out at a tensile rate of 2 mm/min using a universal tensile machine (UTM, Instron5582, USA). Each specimen was measured at least three times, and the average value was calculated. The specimens were processed into cylinders (⌀12.7 mm × 3 mm) to measure the thermal diffusivity using the laser flash diffusivity instrument (FLD, NETZSCH LFA 427, Germany). The specimen density was determined using Archimedes method. In addition, the specific heat was measured with a differential scanning calorimeter (DSC, Setaramd DSC131, French). Therefore, the thermal conductivity was calculated by [16] = ,

Microstructure
where , , , and were the thermal conductivity, thermal diffusivity, density, and specific heat, respectively.  Secondary phases of the A356 and Al-Si-Mg-Cu-Fe-Sr alloys are further observed by SEM, as shown in Figure 3. The EDS result for Point A in Figure 3a shows that the needle phase mainly consists of Al and Si elements, as shown in Figure 3c. The EDS point for Point B shows that the needle phase contains mainly Al, Fe, and Si elements, as shown in Figure 3e. According to the literature, the Point A and Point B are the eutectic Si phase and β-AlFeSi phase, respectively [20]. The SEM micrograph of secondary phases in the Al-Si-Mg-Cu-Fe-Sr alloy is shown in Figure 3b. The EDS point scanning result for Point C is shown in Figure 3d; this result shows that the fibrous phase mainly consists of Al and Si elements. The EDS result for Point D shows that the needle phase contains mainly Al and Fe elements, as shown in Figure 3f. The result indicates that the Point C and Point D present a eutectic Si phase and iron-rich intermetallics, respectively. Secondary phases of the A356 and Al-Si-Mg-Cu-Fe-Sr alloys are further observed by SEM, as shown in Figure 3. The EDS result for Point A in Figure 3a shows that the needle phase mainly consists of Al and Si elements, as shown in Figure 3c. The EDS point for Point B shows that the needle phase contains mainly Al, Fe, and Si elements, as shown in Figure 3e. According to the literature, the Point A and Point B are the eutectic Si phase and β-AlFeSi phase, respectively [20]. The SEM micrograph of secondary phases in the Al-Si-Mg-Cu-Fe-Sr alloy is shown in Figure 3b. The EDS point scanning result for Point C is shown in Figure 3d; this result shows that the fibrous phase mainly consists of Al and Si elements. The EDS result for Point D shows that the needle phase contains mainly Al and Fe elements, as shown in Figure 3f. The result indicates that the Point C and Point D present a eutectic Si phase and iron-rich intermetallics, respectively.

Microstructure
In addition, element distributions of Al-Si-Mg-Cu-Fe-Sr alloy are determined, as shown in Figure 4. It is found that Al, Si, and Fe elements form the iron-rich intermetallics, and Mg, Cu, and Sr elements are almost dissolved in the matrix, as shown in Figure 4b-g. Meanwhile, the iron-rich intermetallics mainly consist of Al, Si, and Fe elements. Based on the previous work, the iron-rich phase is determined to be the β-AlFeSi phase [14]. In addition, element distributions of Al-Si-Mg-Cu-Fe-Sr alloy are determined, as shown in Figure 4. It is found that Al, Si, and Fe elements form the iron-rich intermetallics, and Mg, Cu, and Sr elements are almost dissolved in the matrix, as shown in Figure 4bg. Meanwhile, the iron-rich intermetallics mainly consist of Al, Si, and Fe elements. Based on the previous work, the iron-rich phase is determined to be the β-AlFeSi phase [14].   Table 2. The UTS, YS, and EL of the Al-Si-Mg-Cu-Fe-Sr alloy are 192.2 MPa, 117.3 MPa, and 3.8%, respectively, which increase by 28%, 48%, and 3% in contrast to the A356 alloy.  In addition, element distributions of Al-Si-Mg-Cu-Fe-Sr alloy are determined, as shown in Figure 4. It is found that Al, Si, and Fe elements form the iron-rich intermetallics, and Mg, Cu, and Sr elements are almost dissolved in the matrix, as shown in Figure 4bg. Meanwhile, the iron-rich intermetallics mainly consist of Al, Si, and Fe elements. Based on the previous work, the iron-rich phase is determined to be the β-AlFeSi phase [14].   Table 2. The UTS, YS, and EL of the Al-Si-Mg-Cu-Fe-Sr alloy are 192.2 MPa, 117.3 MPa, and 3.8%, respectively, which increase by 28%, 48%, and 3% in contrast to the A356 alloy.   Table 2. The UTS, YS, and EL of the Al-Si-Mg-Cu-Fe-Sr alloy are 192.2 MPa, 117.3 MPa, and 3.8%, respectively, which increase by 28%, 48%, and 3% in contrast to the A356 alloy.   Figure 5b displays the thermal conductivity of the A356 and Al-Si-Mg-Cu-Fe-Sr alloys. The Al-Si-Mg-Cu-Fe-Sr alloy possesses a higher thermal conductivity compared with the A356 alloy. The thermal diffusivity, density, and specific heat of two alloys are summarized in Table 3. The thermal conductivity of the Al-Si-Mg-Cu-Fe-Sr alloy is calculated by Formula (3) to be 164.42 W/(m·K), which is 8% larger than that of the A356 alloy.  Figure 6 shows the microstructure of the Al-Si-Mg-Cu-Fe-Sr alloy prepared by the vibrating contraction inclined plate with an inclination angle of 45° and vibration frequency of 0 Hz under different pouring temperatures. When the pouring temperature is 660 °C, coarse dendrites are observed, as shown in Figure 6a, and the blocked slurry ratio increases on the vibrating contraction inclined plate. The grain diameter and shape factor of primary α-Al grains are 76.78 µm and 0.63, respectively. As the pouring temperature increases to 670 °C, few dendrites are almost found, and the primary α-Al grains display a spherical/near spherical shape, as shown in Figure 6b. The primary α-Al grains diameter reduces to 69.56 µm, and the shape factor increases to 0.71. When the pouring temperature increases to 680 °C, the primary α-Al grains mainly consist of a few of the dendrites and spherical/near spherical grains, as shown in Figure 6c. The grain diameter and shape factor of primary α-Al grains are 74.43 µm and 0.68, respectively. As the pouring temperature further increases to 690 °C, the number of dendrites increases significantly; however, the number of near spherical grains decreases, as shown in Figure 6d. The average diameter of primary α-Al grains increases to 78.15 µm, and the shape factor decreases to 0.65. When   Figure 5b displays the thermal conductivity of the A356 and Al-Si-Mg-Cu-Fe-Sr alloys. The Al-Si-Mg-Cu-Fe-Sr alloy possesses a higher thermal conductivity compared with the A356 alloy. The thermal diffusivity, density, and specific heat of two alloys are summarized in Table 3. The thermal conductivity of the Al-Si-Mg-Cu-Fe-Sr alloy is calculated by Formula (3) to be 164.42 W/(m·K), which is 8% larger than that of the A356 alloy.  Figure 6 shows the microstructure of the Al-Si-Mg-Cu-Fe-Sr alloy prepared by the vibrating contraction inclined plate with an inclination angle of 45 • and vibration frequency of 0 Hz under different pouring temperatures. When the pouring temperature is 660 • C, coarse dendrites are observed, as shown in Figure 6a, and the blocked slurry ratio increases on the vibrating contraction inclined plate. The grain diameter and shape factor of primary α-Al grains are 76.78 µm and 0.63, respectively. As the pouring temperature increases to 670 • C, few dendrites are almost found, and the primary α-Al grains display a spherical/near spherical shape, as shown in Figure 6b. The primary α-Al grains diameter reduces to 69.56 µm, and the shape factor increases to 0.71. When the pouring temperature increases to 680 • C, the primary α-Al grains mainly consist of a few of the dendrites and spherical/near spherical grains, as shown in Figure 6c. The grain diameter and shape factor of primary α-Al grains are 74.43 µm and 0.68, respectively. As the pouring temperature further increases to 690 • C, the number of dendrites increases significantly; however, the number of near spherical grains decreases, as shown in Figure 6d. The average diameter of primary α-Al grains increases to 78.15 µm, and the shape factor decreases to 0.65. When the pouring temperature is 700 • C, some dendrites and a few rose-like grains are observed, as shown in Figure 6e. The grain diameter and shape factor of primary α-Al grains are 88.65 µm and 0.63, respectively. Therefore, when the pouring temperature increases from 660 to 700 • C, the grain diameter firstly decreases and then increases, and the shape factor displays an opposite variation trend, as shown in Figure 7. Therefore, the optimized pouring temperature is confirmed to be 670 • C.

Mechanical Property and Thermal Conductivity
Metals 2021, 11, x FOR PEER REVIEW 7 of 13 the pouring temperature is 700 °C, some dendrites and a few rose-like grains are observed, as shown in Figure 6e. The grain diameter and shape factor of primary α-Al grains are 88.65 µm and 0.63, respectively. Therefore, when the pouring temperature increases from 660 to 700 °C, the grain diameter firstly decreases and then increases, and the shape factor displays an opposite variation trend, as shown in Figure 7. Therefore, the optimized pouring temperature is confirmed to be 670 °C.   Figure 8 shows the microstructure of Al-Si-Mg-Cu-Fe-Sr alloy prepared at a pouring temperature 670 °C and vibration frequency of 0 Hz under various inclination angles. When the inclination angle is 15°, some dendrites are observed, as shown in Figure 8a. The grain diameter and shape factor of primary α-Al grains are 82.73 µm and 0.64, respectively. When the inclination angle increases from 15° to 30°, a number of the dendrites decreases and spherical/near spherical grains increases, as shown in Figure 8b. The grain diameter and shape factor are 81.36 µm and 0.66, respectively. As the inclination angle increases to 45°, the primary α-Al grains mainly consist of spherical/near spherical grains, as shown in Figure 8c. The grain diameter and the shape factor are 69.56 µm and 0.71, respectively. However, when the inclination angle is 60°, a few dendrites are observed, as the pouring temperature is 700 °C, some dendrites and a few rose-like grains are observed, as shown in Figure 6e. The grain diameter and shape factor of primary α-Al grains are 88.65 µm and 0.63, respectively. Therefore, when the pouring temperature increases from 660 to 700 °C, the grain diameter firstly decreases and then increases, and the shape factor displays an opposite variation trend, as shown in Figure 7. Therefore, the optimized pouring temperature is confirmed to be 670 °C.   Figure 8 shows the microstructure of Al-Si-Mg-Cu-Fe-Sr alloy prepared at a pouring temperature 670 °C and vibration frequency of 0 Hz under various inclination angles. When the inclination angle is 15°, some dendrites are observed, as shown in Figure 8a. The grain diameter and shape factor of primary α-Al grains are 82.73 µm and 0.64, respectively. When the inclination angle increases from 15° to 30°, a number of the dendrites decreases and spherical/near spherical grains increases, as shown in Figure 8b. The grain diameter and shape factor are 81.36 µm and 0.66, respectively. As the inclination angle increases to 45°, the primary α-Al grains mainly consist of spherical/near spherical grains, as shown in Figure 8c. The grain diameter and the shape factor are 69.56 µm and 0.71, respectively. However, when the inclination angle is 60°, a few dendrites are observed, as  Figure 8 shows the microstructure of Al-Si-Mg-Cu-Fe-Sr alloy prepared at a pouring temperature 670 • C and vibration frequency of 0 Hz under various inclination angles. When the inclination angle is 15 • , some dendrites are observed, as shown in Figure 8a. The grain diameter and shape factor of primary α-Al grains are 82.73 µm and 0.64, respectively. When the inclination angle increases from 15 • to 30 • , a number of the dendrites decreases and spherical/near spherical grains increases, as shown in Figure 8b. The grain diameter and shape factor are 81.36 µm and 0.66, respectively. As the inclination angle increases to 45 • , the primary α-Al grains mainly consist of spherical/near spherical grains, as shown in Figure 8c. The grain diameter and the shape factor are 69.56 µm and 0.71, respectively. However, when the inclination angle is 60 • , a few dendrites are observed, as shown in Figure 8d. The grain diameter and shape factor of the primary α-Al grains were 72.25 µm and 0.56, respectively. Therefore, when the inclination angle increases from 15 • to 60 • , the grain diameter firstly decreases and then increases, and the shape factor firstly increases and then decreases, as shown in Figure 9. It is found that the inclination angle of 45 • is an optimized processing parameter. shown in Figure 8d. The grain diameter and shape factor of the primary α-Al grains were 72.25 µm and 0.56, respectively. Therefore, when the inclination angle increases from 15° to 60°, the grain diameter firstly decreases and then increases, and the shape factor firstly increases and then decreases, as shown in Figure 9. It is found that the inclination angle of 45° is an optimized processing parameter.   Figure 10 shows microstructure of Al-Si-Mg-Cu-Fe-Sr alloy with a pouring temperature of 670 °C and inclination angle of 45° under different vibration frequencies. When the vibration frequency is 0 Hz, few dendrites almost are found, and the primary α-Al grains display a spherical/near spherical shape, as shown in Figure 10a. The grain diameter and shape factor are 69.56 µm and 0.71, respectively. With the vibration frequency increases from 30 to 60 Hz, the primary α-Al grains mainly consist of spherical/near spherical grains, as shown in Figure 10b and c; the grain diameter decreases from 66.99 to 64.31 µm, and the shape factor increases from 0.77 to 0.80. However, when the vibration frequency increases to 90 Hz, the number of the spherical/near spherical grains decreases, shown in Figure 8d. The grain diameter and shape factor of the primary α-Al grains were 72.25 µm and 0.56, respectively. Therefore, when the inclination angle increases from 15° to 60°, the grain diameter firstly decreases and then increases, and the shape factor firstly increases and then decreases, as shown in Figure 9. It is found that the inclination angle of 45° is an optimized processing parameter.   Figure 10 shows microstructure of Al-Si-Mg-Cu-Fe-Sr alloy with a pouring temperature of 670 °C and inclination angle of 45° under different vibration frequencies. When the vibration frequency is 0 Hz, few dendrites almost are found, and the primary α-Al grains display a spherical/near spherical shape, as shown in Figure 10a. The grain diameter and shape factor are 69.56 µm and 0.71, respectively. With the vibration frequency increases from 30 to 60 Hz, the primary α-Al grains mainly consist of spherical/near spherical grains, as shown in Figure 10b and c; the grain diameter decreases from 66.99 to 64.31 µm, and the shape factor increases from 0.77 to 0.80. However, when the vibration frequency increases to 90 Hz, the number of the spherical/near spherical grains decreases, Figure 9. Average grain diameter and average shape factor as functions of inclination angle. The pouring temperature and vibration frequency are 670 • C and 0 Hz, respectively. Figure 10 shows microstructure of Al-Si-Mg-Cu-Fe-Sr alloy with a pouring temperature of 670 • C and inclination angle of 45 • under different vibration frequencies. When the vibration frequency is 0 Hz, few dendrites almost are found, and the primary α-Al grains display a spherical/near spherical shape, as shown in Figure 10a. The grain diameter and shape factor are 69.56 µm and 0.71, respectively. With the vibration frequency increases from 30 to 60 Hz, the primary α-Al grains mainly consist of spherical/near spherical grains, as shown in Figure 10b,c; the grain diameter decreases from 66.99 to 64.31 µm, and the shape factor increases from 0.77 to 0.80. However, when the vibration frequency increases to 90 Hz, the number of the spherical/near spherical grains decreases, and the number of the dendrites increases, as shown in Figure 10d. The grain diameter and shape factor are 72.19 µm and 0.72, respectively. Therefore, when the vibration frequency increases from 0 to 90 Hz, the grain diameter firstly decreases and then increases, and the shape factor firstly increases and then decreases, as shown in Figure 11. The primary α-Al grains having the minimum grain size and maximum shape factor are obtained at a vibration frequency of 60 Hz. and the number of the dendrites increases, as shown in Figure 10d. The grain diameter and shape factor are 72.19 µm and 0.72, respectively. Therefore, when the vibration frequency increases from 0 to 90 Hz, the grain diameter firstly decreases and then increases, and the shape factor firstly increases and then decreases, as shown in Figure 11. The primary α-Al grains having the minimum grain size and maximum shape factor are obtained at a vibration frequency of 60 Hz.

Microstructure Evolution and Improved Property
Compared with the A356 alloy, the Al-Si-Mg-Cu-Fe-Sr alloy displays a finer dendrite structure. This is because the Sr element can decrease the eutectic reaction temperature of the cast Al-Si alloy, which increases the solidification temperature range and number of dendrites [21,22]. Therefore, the more dendrites, the finer the primary α-Al grains in the certain area. In addition, the Sr element, as a surface-active element, can cause a component supercooling effect through surface adsorption, thus preventing the growth of eutectic Si phases with a needle shape [23]. The eutectic Si phases grow by the twin  Figure 10d. The grain diameter and shape factor are 72.19 µm and 0.72, respectively. Therefore, when the vibration frequency increases from 0 to 90 Hz, the grain diameter firstly decreases and then increases, and the shape factor firstly increases and then decreases, as shown in Figure 11. The primary α-Al grains having the minimum grain size and maximum shape factor are obtained at a vibration frequency of 60 Hz.

Microstructure Evolution and Improved Property
Compared with the A356 alloy, the Al-Si-Mg-Cu-Fe-Sr alloy displays a finer dendrite structure. This is because the Sr element can decrease the eutectic reaction temperature of the cast Al-Si alloy, which increases the solidification temperature range and number of dendrites [21,22]. Therefore, the more dendrites, the finer the primary α-Al grains in the certain area. In addition, the Sr element, as a surface-active element, can cause a component supercooling effect through surface adsorption, thus preventing the growth of eutectic Si phases with a needle shape [23]. The eutectic Si phases grow by the twin Figure 11. Average grain diameter and average shape factor as functions of vibration frequency. The!pouring temperature and inclination angle are 670 • C and 45 • , respectively.

Microstructure Evolution and Improved Property
Compared with the A356 alloy, the Al-Si-Mg-Cu-Fe-Sr alloy displays a finer dendrite structure. This is because the Sr element can decrease the eutectic reaction temperature of the cast Al-Si alloy, which increases the solidification temperature range and number of dendrites [21,22]. Therefore, the more dendrites, the finer the primary α-Al grains in the certain area. In addition, the Sr element, as a surface-active element, can cause a component supercooling effect through surface adsorption, thus preventing the growth of eutectic Si phases with a needle shape [23]. The eutectic Si phases grow by the twin plane reentrant edge (TPRE) mechanism, resulting in a change in morphology of eutectic Si phases, i.e., from the coarse needle shape to a finely fibrous shape [24].
The Al-Si-Mg-Cu-Fe-Sr alloy has better mechanical properties than the A356 alloy. On the one hand, the YS (σ ys ) is relevant to the size of primary α-Al grains, which follows the Hall-Petch relationship [25]: where σ 0 is the single crystal yield strength, K y is the strengthening co-efficient, and d is the size of the primary α-Al grains. Therefore, it is expected that a decrease in size of primary α-Al grains will cause an increase in strength. Compared with the A356 alloy, the Al-Si-Mg-Cu-Fe-Sr alloy has finer primary α-Al grains, leading to improved mechanical properties. On the other hand, the morphology of eutectic Si phases plays an important role in the mechanical behavior of Al-Si alloys [26,27]. In the A356 alloy, eutectic Si phases possess a coarse needle shape, which accelerates the crack propagation rate and decreases the mechanical property [28]. However, in the Al-Si-Mg-Cu-Fe-Sr alloy, eutectic Si phases with a short fibrous shape due to the addition of Sr element are obtained, which helps the improvement in mechanical property [29].
In addition to mechanical property, the Al-Si-Mg-Cu-Fe-Sr alloy has a higher thermal conductivity in comparison with the A356 alloy. This is closely associated with the morphology of eutectic Si phases [16,30]. In the A356 alloy, the formation of needle-shaped eutectic Si phases results in the decrease in mean free path and increase in electron scattering [30]. On the contrary, in the Al-Si-Mg-Cu-Fe-Sr alloy, eutectic Si phases with a short fibrous shape play an important role in increasing the electron channel, thereby decreasing the electron scattering and increasing the mean free path [16]. Therefore, the acquisition of fibrous eutectic Si phases is beneficial for the increase in thermal conductivity.

Effect of Pouring Temperature on Primary α-Al Grains
With the increase in pouring temperature from 670 to 700 • C, there is an increase in grain diameter and a decrease in shape factor. The chilling effect is provided by the cooling water tank, resulting in the formation of crystal nuclei on the inclined plate. These crystal nuclei are detached from the inclined plate and are collected in the mold. The low pouring temperature results in a large sub-cooling degree and nucleation ratio [31]. On the other hand, the low pouring temperature causes the primary α-Al nucleus to not be remelted, thus increasing the effective nucleation ratio [31]. Therefore, the low pouring temperature makes the primary α-Al grains grow into the spherical shape and possess a small size [32]. However, when the pouring temperature further decreases to 660 • C, due to the deterioration of melt fluidity, some primary α-Al nuclei grow up and firmly attach on the inclined plate instead of being brought into the melt, resulting in an increase in blocked slurry ratio [33], thereby increasing the grain size. In addition, the obvious adhesion phenomenon emerges at the pouring temperature of 660 • C. It is not easy to solve the blockage problem by changing the vibration frequency and/or inclination angle. Therefore, the pouring temperature has a great influence on the adhesion phenomenon.

Effect of Inclination Angle on Primary α-Al Grains
When the inclination angle is 45 • , the desirable primary α-Al grains are acquired. The gravity acceleration component of the melt along the inclined plate is determined by the inclination angle. This affects the flowing speed of the melt and the shearing effect. The shearing force along the inclined plate (τ) as a function of the inclination angle (α) is expressed as: where η is the viscosity of the alloy; g is the gravity acceleration; L is the distance originated from the flow starting point of the inclined plate; h is the vertical distance from the inclined plate surface. Therefore, when the inclination angle is 15 • , the velocity of flow is slow and the shearing effect is small, which is detrimental to the breaking of dendrites [12]. As the inclination angle increases, the shearing effect increases, and the primary α-Al grains tend to grow into the spherical shape. However, when the inclination angle further increases to 60 • , the flowing velocity increases, while the shearing time decreases, which decreases the shearing effect. Therefore, the morphology of primary α-Al grains varies again.

Effect of Vibration Frequency on Primary α-Al Grains
When the vibration frequency increases from 0 to 90 Hz, the grain diameter decreases initially and increases afterwards. The vibration frequency will affect the vibration amplitude. The contact time between the inclined plate and melt and the shearing effect are controlled by vibration amplitude [34]. When the vibration frequency is small, the vibration period and amplitude of the inclined plate are large, while the contact between the melt and inclined plate is poor, which decreases the shearing effect on breaking the dendrites [34]. The small vibration frequency results in the short contact time, which decreases the heat-exchange between the melt and inclined plate and increases the grain size. In addition, the short contact time can also cause an inhomogeneous cooling of the melt, resulting in a change in grain size. As the vibration frequency increases, mutual movement between the primary α-Al grains and unsolidified liquid phases in the semi-solid slurry is enhanced, resulting in a viscous shear in the semi-solid slurry [35]. Under the shearing effect, most primary α-Al grains are broken into new grains or nucleation cores, which helps to decrease the size of primary α-Al grains. However, when the vibration frequency increases to 90 Hz, the vibration period and amplitude are decreased, and the effect of vibration on the breaking of dendrites is not obvious.

Conclusions
A novel Al-Si-Mg-Cu-Fe-Sr alloy with good performance was developed. The process parameters of the semi-solid slurry prepared by the vibrating contraction inclined plate were optimized. The solidification behavior of the semi-solid alloy was discussed. The main conclusions were summarized as follows: (1) Compared with the A356 alloy, the Al-Si-Mg-Cu-Fe-Sr alloy had a better combination of mechanical property and thermal conductivity, which was related to the size of primary α-Al grains and morphology of eutectic Si phases. (2) The process parameters had an important effect on the solidification behavior of primary α-Al grains in the semi-solid Al-Si-Mg-Cu-Fe-Sr alloy prepared by the vibrating contraction inclined plate. Compared with the vibration frequency, the pouring temperature or inclination angle may be dominant during preparing the semisolid slurry. Institutional Review Board Statement: Not applicable.

Informed Consent Statement: Not applicable.
Data Availability Statement: Data presented in this article are available at request from the corresponding author.