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Journal of Materials Engineering and Performance

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Open Access 22.06.2020

Modification of Mg₂Si Phase Morphology in Mg-4Si Alloy by Sb and Nd Additions

verfasst von: Hao Dong, Siming Xiang, Jie Lv, Yu Wang, Lu Li, Wenbin Yu

Erschienen in: Journal of Materials Engineering and Performance | Ausgabe 6/2020

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Abstract

We reported the effects of compound modification with Nd and Sb on the microstructure evolution and mechanical properties of Mg-4Si alloys. The characterization results showed that adding 1.0 wt.% Sb and 1.0 wt.% Nd to the alloy can effectively change the morphology of Mg₂Si particles. The primary Mg₂Si particles changed from coarse dendrites to regular polygons, and the average particle size decreased from 78.3 to 6.5 μm. Meanwhile, the Chinese eutectic Mg₂Si became small short fiber. The experimental results showed that the Nd₄Sb₃ phase could be formed after adding 1.0 wt.% Sb and 1.0 wt.% Nd to the alloy. The Nd₄Sb₃ phase could act as the heterogeneous nucleation core of Mg₂Si phase, which increased the nucleation rate of Mg₂Si and improved the morphology of Mg₂Si particles. The mechanical properties test found that the tensile properties and Brinell hardness of the alloy were improved with Sb and Nd alloyed. After adding 1.0 wt.% Sb and 1.0 wt.% Nd to the alloy, the ultimate tensile strength increased from 113 to 184 MPa, the elongation increased from 2.23 to 4.61%, and the Brinell hardness increased from 65.45 to 87.32 HB.

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Introduction

Lightweight magnesium alloys have broad applications in various fields including electronic, aerospace (Ref 1, 2), and automation because of their high specific strength, high stiffness, relatively low density, good electrical conductivity, and excellent machinability (Ref 3, 4). However, one of the disadvantages of magnesium alloys is that the high-temperature mechanical properties of this material are somewhat poor, and this greatly limits broader industrial applications (Ref 5, 6).

Recent studies have reported methods to improve the heat-resistance problem of magnesium alloys such as microalloying (Ref 7), deformation strengthening (Ref 8), and second phase strengthening (Ref 9). Apparently, introducing Mg₂Si particles into the alloy was the most widely valuable because they are convenient and do not require complicated equipment. Furthermore, the Mg₂Si phase has some excellent characteristics such as low density (1.88 g/cm³), high melting point (1087 °C), high hardness (HV 460), high elastic modulus (120 GPa), high elastic modulus (120 GPa),and low thermal expansion coefficient (7.5 × 10⁻⁶ K⁻¹) (Ref 10); the Mg₂Si phase can be stably present at high temperatures and enhance the mechanical properties of the material. Thus, the Mg₂Si phase is an ideal reinforcement phase for magnesium alloys.

However, many rough dendritic primary Mg₂Si and Chinese eutectic Mg₂Si are produced during the solidification of Mg-Si alloy throughout the magnesium matrix. These features negatively affect the physical properties of magnesium alloys. In view of this, optimizing the morphology and structure of Mg₂Si particles is necessary to improve the alloy performance.

There have been many studies demonstrating that the morphology of Mg₂Si can be modified upon adding different modifiers. Previous studies have indicated that coarse dendritic primary Mg₂Si particles were changed to regular polygons after adding Sb (Ref 11, 12), Nd (Ref 13, 14), Ba (Ref 15), or P (Ref 10, 16) to Mg-Si alloys: The modification mechanism of these elements can be concluded as the formation of a heterogeneous nucleation core of the Mg₂Si phase. In addition, the Y (Ref 17, 18), KBF₄ (Ref 19), and Bi (Ref 20) can also modify the coarse dendritic primary Mg₂Si because they inhibit the growth of Mg₂Si phase. Furthermore, the combination of two modifiers such as Ba-Sb (Ref 21), Sr-Sb (Ref 22), and Ca-Sb (Ref 23) can alert the coarse dendritic primary Mg₂Si as well. However, the size of most modification Mg₂Si particles is larger than 20 μm, and thus, we need more effective modifiers to further refine the primary Mg₂Si particles.

Previous studies have found that Sb transformed coarse dendritic primary Mg₂Si into regular polygonal particles by increasing the number of heterogeneous nucleation sites (Ref 11). Nd is also an effective modifier for Mg₂Si phase. Therefore, Sb and Nd would have synergistic modification effects. Thus, Nd and Sb were added to the Mg-4Si alloys to see the modification effect, and the objective of this work is to find an effective compound modifier and to evaluate the effect of Nd-Sb addition on the microstructure of Mg-4Si alloys, as well as to explore the mechanism of Nd and Sb compound modification.

Experimental Procedures

First, Mg ingot (> 99.9 wt.%) and Si ingot (> 99.8 wt.%) should be available for the preparation of Mg-4Si alloy. 1100 g pure Mg ingots were melted to 700 °C, and 40 g fine silicon particles were added to the metal solution after the pure magnesium is melted. And Mg ingot was added more due to Mg burned easily. A small amount of covering agent was added to the surface of the molten metal during the smelting process to protect the molten metal. This was held at 700 °C for 20 min and stirred evenly after slag removal. The molten magnesium solution can be poured into a cast iron mold preheated at 250 °C. This is the basis of subsequent experiments.

A previous study showed that the best modification effect was achieved after adding 1.0 wt.% Sb to the Mg-based alloy when adding a single modification element Sb (Ref 21). In this case, the only variable in the experiment was the difference in Nd content. The 1.0 wt.% Sb was added to the re-melted Mg-4Si alloys, and different amounts of Mg-30Nd alloy were added to the re-melted Mg-4Si alloys. The molten metal was kept at 700 °C for 20 min. After stirring, the molten metal was poured into a cast iron mold preheated at 250 °C to obtain the samples: This produced bars 20 mm in diameter. Table 1 shows the designed ratios of the Nd and Sb contents of the prepared ingots.

Table 1

Alloy number and nominal Nd/Sb contents

Alloy number	1	2	3	4	5
Sb content, wt.%	0	1.0	1.0	1.0	1.0
Nd content, wt.%	0	0	0.5	1.0	2.0

All metallographic samples in this experiment were taken from the same position of ingot. The samples were finely ground with different meshes of sandpaper, polished with a diamond spray polish, and then etched with 0.1% acetic acid. First of all, the phase constituent of the experimental Mg-4Si alloy was determined by XRD (Shimadzu XRD-7000) using Cu Kα radiation in step mode from 20° to 80° with a scanning speed of 2° min⁻¹ and an acquisition step of 0.02°(2θ). After that, OLYMPUS-PMG3 optical microscope (OM) was used to observe the microstructure of the samples. Finally, AxioVision software was used to calculate the average size and density of Mg₂Si particles. The calculation process is as follows (Ref 24):

$${\text{Mean}}\;{\text{size}} = \frac{1}{m}\mathop \sum \limits_{j = 1}^{m} \left( {\frac{1}{n}\mathop \sum \limits_{i = 1}^{n} L_{i} } \right)_{j}$$

(1)

$${\text{Mean}}\;{\text{density}} = \frac{1}{m}\mathop \sum \limits_{j = 1}^{m} \left( {\frac{1}{n}\mathop \sum \limits_{i = 1}^{n} D_{i} } \right)_{j}$$

(2)

where L_i was the size of a single Mg₂Si particle and D_i is the density of Mg₂Si particles, respectively. Term n was the amount of Mg₂Si particles counted in this area at 71,300 μm², and m was the number of the measurement areas. A JSM-6610 scanning electron microscope (SEM) was used to analyze the microscopic appearance and element composition of the second phase. Nanoscale second phase particles were observed and analyzed by transmission electron microscopy (TEM), and the samples were prepared by focusing particle beams. Titan G2 60-300 model was used for TEM observation at 300 kV. The elemental composition of the second phase was obtained by mapping analysis, and the crystal structure of the second phase was determined by selected area electron diffraction.

Tensile test bars were prepared in accordance with the ASTMB557 M-02a standard, and the gauge length was set to 30 mm, and the cross section diameter was 6 mm. This tensile test was performed by use of a CMT5504 universal testing machine controlled by computer in the constant crosshead speed of 1 mm/min, and each sample was tested five times at room temperature. The fracture surface was observed by SEM, and the average ultimate tensile strength (UTS) and elongation were calculated. The hardness of samples was tested by use of a Brinell hardness tester (HBE-D3000A) under 2450 N load, with 15 s residence time and Φ 2.5 indenter. The present values in this paper are the average value of five random different positions.

Experiment Results and Discussion

Phase Analysis

Figure 1 shows the XRD examination results of Alloy 1 to 5, and it is clear that Mg₂Si phase and Mg phase were observed in the Mg-4Si alloy, indicating that Mg₂Si phase was formed during the solidification.

Microstructure Evolution

Figure 2 shows the microstructure of Mg-4Si alloys under different Nd and Sb addition values. The microstructure of unmodified Mg-4Si alloy (Fig. 2a) is composed of white α-Mg matrix, and Chinese eutectic Mg₂Si and coarse black primary Mg₂Si dendrites had a size of about 78 μm. According to the binary phase diagram of magnesium–silicon, dendritic primary Mg₂Si is first precipitated during the solidification process and then precipitates Chinese character eutectic Mg₂Si.

By adding 1.0 wt.% Sb to the Mg-4Si alloy, the morphology of primary Mg₂Si particles can significantly change from coarse dendrites to regular polygons (Fig. 2b) and the size reduced to about 20 μm, while the amount of Chinese eutectic Mg₂Si was reduced. To better modify the refined primary Mg₂Si particles, increasing ratios of Nd were added to the 1.0 wt.% Sb metamorphic Mg-4Si alloy. The addition of Nd makes the average particle size decrease significantly, and the particle size of primary Mg₂Si increases slightly when the addition amount of Nd is up to 1.0 wt.%.

Figure 2(c) shows that after adding 1.0 wt.% Sb and 0.5 wt.% Nd, the number of primary Mg₂Si particles decreased with increasing eutectic Mg₂Si content, and the particle size changed slightly. Figure 2(d) shows that with the increase in Nd content, the average size of primary Mg₂Si particles decreased significantly upon addition of 1.0 wt.% Nd. The Mg₂Si particles have the best polygon, and the average particle size obtained by OM is 6.5 μm. However, the amount of primary Mg₂Si particles decreased, and the size became larger when the Nd was continuously added to the alloy (Fig. 2e). At the same time, the changes in the average size and density of the primary Mg₂Si particles are plotted in Fig. 3; the density of the primary Mg₂Si particles increased with decreasing size. Figure 4 shows the magnified SEM observation on the alloys with different Sb and Nd addition, indicating that the Chinese-script eutectic Mg₂Si was significantly refined after the compound modification of Sb and Nd, and the amount of the eutectic Mg₂Si reduced with the addition of Nd up to 1.0 wt.%.

Modification Mechanism

The results show that the addition of 1.0 wt.% Sb and 1.0 wt.% Nd has obvious compound modification effect on the primary Mg₂Si phase of Mg-4Si alloy. The modification mechanism of Nd and Sb on Mg-4Si alloy was studied by SEM. There were white cores in the middle or edge of the modified Mg₂Si phase (Fig. 5a and b), which could act as a heterogeneous nucleation core of the primary Mg₂Si particles. Figure 5(a) and (c) shows the SEM images and EDS analysis of the 1 wt.% Sb modified Mg-4Si alloy. Figure 5(a) shows that there are some white cores in the primary Mg₂Si particles. There is a point sweep of the white cores in Fig. 5(a), which reveals that the constituent elements of the white cores are Mg, Si, and Sb. Previous studies showed that the Mg₃Sb₂ phases can be formed in the Mg-Si alloy after adding Sb. These acted as nucleation sites for the primary Mg₂Si particles (Ref 25). It can be seen from Fig. 5(a) that the Mg₃Sb₂ phase is too small, and the nucleation rate of the primary Mg₂Si was minimally improved, so the average size of the primary Mg₂Si particles was about 20 μm.

Figure 5(b) shows that the amount of white cores in the primary Mg₂Si particles obviously increased after adding 1 wt.% Sb and 1 wt.% Nd to the Mg-4Si alloy. Meanwhile, the average size of primary Mg₂Si particles decreased to 6.5 μm and was evenly distributed in the matrix; eutectic Mg₂Si changed from Chinese characters to small short fibers. The point sweep of the white core in the primary Mg₂Si particles in Fig. 5(d) reveals that there are Mg, Si, Sb, and Nd on the white cores—the possible intermetallic compounds between these elements include Mg₃Sb₂, NdSi₂, and Nd₄Sb₃.

The element composition of the core of the primary Mg₂Si particles will be confirmed in a future TEM study. Figure 6 shows a high-power bright TEM image with mapping analysis. The bright image (Fig. 6a) shows a dark phase that we think is the α-Mg phase, and there is also a white phase inside the Mg₂Si particles that is heterogeneous nucleation core of the primary Mg₂Si particles. The mapping analysis shows that there are Nd and Sb enrichments in the white core of the primary Mg₂Si particles (Fig. 6e and f). The white intermediate phase is likely a compound of Nd and Sb (Ref 26).

Figure 7 shows the high-power bright-field TEM image and selected area electron diffraction image of Mg-4Si alloy with 1.0 wt.% Sb and 1.0 wt.% alloyed Nd. The SAD pattern was collected from at least two regional axes by tilting the sample to determine the crystal structure (Ref 27). The target and selected area electron diffraction aperture were adjusted, and the intermetallics of Nd and Sb nanoparticles were studied. The area circled by the solid circle of 100 nm is the area of the selected area electron diffraction analysis. The SAD patterns were analyzed, and the results suggest that the core of the primary Mg₂Si consists of a Nd₄Sb₃ phase and a zone axis $A = [1\overline{3} 1]$. Through these, the Nd₄Sb₃ phase has a cubic structure with lattice parameters of 0.9406 nm and belongs to the I-43d (220) space group. In addition, the Mg₂Si phase has a face-centered cubic structure with lattice parameters of 0.65 nm (Ref 28). This belongs to the Fm-3m (225) space group. Figure 8 shows the crystal structure of the Mg₂Si phase and the Nd₄Sb₃ phase, respectively.

In previous studies, the modification and refinement mechanism of different elements in Mg-4Si alloy was discussed. Adding alloying elements and appropriate modifiers can effectively change the morphology of Mg₂Si particles. This method is simple and efficient. The modification mechanism of the addition of Sb or Nd is to form a kind of heterogeneous nucleation core of Mg₂Si particles, and it will increase the nucleation rate (Ref 11, 14). For example, the Mg₃Sb₂ phase will be formed, while Sb was added to the Mg-Si alloys (Ref 12). These are the nucleation centers of primary Mg₂Si particles. When Nd is added to the alloy, NdSi₂ can play a similar role to the Mg₂Si particles (Ref 14). However, when Sb and Nd were added at the same time, no Mg₃Sb₂ or NdSi₂ particles were observed. In contrast, only Nd₄Sb₃ particles were detected in the newly formed phase; no other intermediate phase was observed. This can be explained by the differences in electronegativity of different atoms.

Electronegativity is a measure of an atom’s ability to attract electrons. A higher electronegativity implies a stronger ability to attract electrons. In general, larger electronegativity differences lead to higher attraction and greater potential for compound formation. The electronegativity of Nd, Sb, Mg, and Si is 1.14, 2.05, 1.31, and 1.98, respectively. Obviously, the electronegativity difference between Nd and Sb is much larger than the electronegativity difference between Mg and Sb, or Nd and Si. Therefore, Nd and Sb combine to form Nd₄Sb₃ phases instead of Mg₃Sb₂ phases and NdSi₂ phases as other studies have done.

In order to investigate whether the Nd₄Sb₃ phase can be used as the heterogeneous nucleation core of the Mg₂Si phase, the lattice mismatch between Nd₄Sb₃ and Mg₂Si was calculated according to Bramfitt theory. The Bramfitt theoretical calculation formula is shown as follows (Ref 25):

$$\delta_{{\left( {hkl} \right)n}}^{{\left( {hkl} \right)s}} = \frac{1}{3}\mathop \sum \limits_{i = 1}^{3} \frac{{\left| {d\left[ {uvw} \right]_{s}^{i} \cos \theta - d\left[ {uvw} \right]_{n}^{i} } \right|}}{{3d_{{\left[ {uvw} \right]_{n} }}^{i} }}$$

(3)

Here, (hkl)_s is the low-index crystal plane of the heterogeneous substrate, and [uvw]_s is the low-index crystal orientation in the (hkl)_s plane. Term (hkl)_n is the low-index crystal plane of the new crystal nucleus, and [uvw]_n is the low-index crystal orientation in the (hkl)_n plane. Terms d_[uvw]s and d_[uvw]n are atomic spatial distances along the [uvw]_s and [uvw]_n orientations, and θ is the angle between [uvw]_s and [uvw]_n orientations (θ < 90°).

Through the study of Bramfitt theory, the energy at the boundary of the heterogeneous nucleation core and the Mg₂Si phase affects the formation of the heterogeneous core. This is mainly related to the energy at the contact surface, and the key to the formation of the heterogeneous nucleation core is that the lattice mismatch of the contact surface is less than 15%.

Figure 9 shows the (001) crystal plane of the Mg₂Si phase and the (211) crystal plane of the Nd₄Sb₃ phase. The planar mismatch of some possible crystallographic orientations for Mg₂Si nucleation on the Nd₄Sb₃ particles was calculated according to Fig. 9 and Bramfitt theory. Table 2 shows that the disregistry reaches 9.33% when the orientation relationship between Nd₄Sb₃ and Mg₂Si is (211)_Nd4Sb3∥(001)_Mg2Si. From Bramfitt’s theory, the mismatch between two-phase planes is less than 15%, and one phase can act as a heterogeneous nucleation point for the other phase. Therefore, the Nd₄Sb₃ phase can be used as a heterogeneous nucleus of primary Mg₂Si phase. The formation of a large number of fine Nd₄Sb₃ particles improved the nucleation rate of primary Mg₂Si particles. Therefore, during solidification, the core of the primary Mg₂Si increases and is evenly distributed in the matrix. The primary Mg₂Si particles do not grow into dendritic crystals, but rather become a small regular polygon.

Table 2

Calculated values for planar disregistry between Mg₂Si and Nd₄Sb₃

	(001)Nd₄Sb₃∥(001) Mg₂Si			(110)Nd₄Sb∥(001) Mg₂Si			(211)Nd₄Sb₃∥(001) Mg₂Si
(hkl)Nd₄Sb₃	[010]	[320]	[120]	[$\overline{1} 00$]	[$\overline{2} 10$]	[$\overline{3} 20$]	[$1\overline{1} \overline{1}$]	[$10\overline{2}$]	[$01\overline{1}$]
(hkl)Mg₂Si	[100]	[110]	[010]	[100]	[110]	[010]	[100]	[110]	[010]
d(hkl)Nd₄Sb₃	9.40	2.59	4.19	9.40	4.19	2.59	5.41	6.35	6.42
d(hkl)Mg₂Si	6.35	4.49	6.35	6.35	4.49	6.35	6.35	4.49	6.35
θ deg	0	12	0	0	15	0	0	15	10
δ		46.15			40.23			9.33

The results show that the average size of the primary Mg₂Si particles is much smaller than that of the single Nd or Sb element after adding Nd and Sb at the same time. This is due to that adding 1.0 wt.% Nd and 1.0 wt.% Sb to Mg-4Si alloy can form a Nd₄Sb₃ phase, which is the heterogeneous nucleation center of primary Mg₂Si particles. Therefore, the nucleation rate of the primary Mg₂Si phase is greatly increased, and the morphology of Mg₂Si changes from a coarse dendritic shape to a regular polygon. However, as the Nd content exceeds 1.0 wt.%, the primary Mg₂Si particles begin to grow slightly larger. This is because of the Nd-Sb binary phase diagram. The Nd₄Sb₃ phase can be formed when the contents of Nd and Sb are close to each other. With increasing addition of Nd, the Nd₅Sb₃ phase can finally be formed, but it cannot act as a heterogeneous nucleation site for the primary Mg₂Si particles. Therefore, the nucleation rate of primary Mg₂Si decreases and the primary Mg₂Si particles become much larger. Meanwhile, the amount of Chinese eutectic Mg₂Si increases sharply with much more alloyed Nd. This is called the over-modification phenomenon.

Mechanical Properties

The tensile mechanical properties and hardness of different samples were tested to investigate the effect of adding different amounts of modifier on the mechanical properties of Mg-4Si alloy (Fig. 10 and 11).

Hardness

The change of hardness can be found in Fig. 10 of Mg-4Si alloy after adding different amounts of Nd and Sb. Figure 10 shows that the Brinell hardness of the unmodified Mg-4Si alloy is at least HB 65.45, and the Brinell hardness value of the alloy first increases and then decreases upon addition of different amounts of modifiers. The maximum value was HB 89.17, and this was achieved upon modification of 1.0 wt.% Sb and 1.0 wt.% Nd. These results indicate that the hardness value of the Mg-4Si alloy is related to the morphology of the primary Mg₂Si particles. The fine regular polygonal particles contribute to the improvement of the hardness. This is because the stress at the contact point of the Mg₂Si particles with the magnesium matrix is reduced after deformation. Thus, it is difficult to initiate cracks at the interface between the primary Mg₂Si particles and magnesium matrix. Thus, the hardness of the alloy increased via 1.0 wt.% Sb and 1.0 wt.% Nd modification.

Tensile Properties and Fracture Characteristics

Tensile properties of Mg-4Si alloy modified by different content Sb and Nd are shown in Fig. 11. The ultimate tensile strength in the experiment is raised from 113.24 to 175.38 MPa when the Mg-4Si alloy was modified by adding 1.0 wt.% Nd and 1.0 wt.% Sb. With the elongation increases from 2.23% to 4.61%, it is clear that improvement of the mechanical properties of the alloy is closely related to the morphology of the Mg₂Si-reinforced phase. This is because of the thermal expansion coefficient between the matrix and the reinforcing phase and the Griffith formula.

An improved coefficient of thermal expansion (CTE) mismatch can increase the ultimate tensile strength of the Mg-4Si alloy (Ref 29). Due to the large difference in the CTE between α-Mg and Mg₂Si reinforcement phase, there is a relatively large residual stress between Mg₂Si and magnesium matrix during alloy smelting. Residual stress concentration at the grain boundary produces many high-density dislocations between the magnesium matrix and the Mg₂Si reinforcing phase, and the dislocation motion of the material becomes more difficult resulting in an increase in the strength of the material. The CTE mismatch is related to the size and shape of the reinforcing phase particles(Ref 30). The eutectic Mg₂Si was still refined after adding 1.0 wt.% Sb and 1.0 wt.% Nd to the Mg-4Si alloy; thus, the alloys were further strengthened with the addition of Nd up to 1.0 wt.%.

The other strengthening mechanism is related to the size of the primary Mg₂Si particles; the relationship between the particle diameter (d) and the fracture stress (σ_c) was demonstrated by the Griffith equation as follows (Ref 12):

$$\sigma_{c }= k_{c} d^{ - 0.5}$$

(4)

Here, k_c is the fracture toughness of the particle, and d is the diameter of the particle. Griffith’s theory states that the fracture stress of the test alloy increases with decreased particle diameter. The primary Mg₂Si particle size decreases significantly in the Mg-4Si alloy with the addition of 1.0 wt.% Nd and 1.0 wt.% Sb. This means that more stress is needed to break the Mg-4Si alloy after 1.0% Nd and 1.0% Sb addition. This improves the UTS and elongation values.

The typical fracture surface of the test alloy after adding different amounts of Nd and Sb to the alloys is shown in Fig. 12. Figure 12(a) shows that the cross section of the unmodified Mg-4Si alloy consists of a flat tearing surface on the Mg₂Si particles. These tearing surfaces are irregularly shaped with cracks. This is attributed to the presence of coarse dendritic primary Mg₂Si and Chinese eutectic Mg₂Si in the unmodified Mg-4Si alloy. The sharp edges of the unmodified primary Mg₂Si particles generate a large amount of stress when they are in contact with the magnesium matrix, and these particles are concentrated at the grain boundaries. The crack is generated under a tensile load, and this crack expanded along the edge of the unmodified primary Mg₂Si and eutectic Mg₂Si, which will reduce the strength and elongation of the alloy.

Figure 12(b–e) shows the fracture surface of the alloy with different Nd and Sb addition. It can be seen that the smaller the particles falling off, the less obvious the crack growth is. The Mg₂Si phase prefers to act as the potential crack initiation site, so the refined Mg₂Si phases could decrease the stress concentration and prevent the crack initiation (Ref 31, 32). This indicated that the ultimate tensile strength improved due to that the morphology of primary Mg₂Si was changed from coarse dendrite to regular polygon by the addition of Sb and Nd. Meanwhile, the morphology of eutectic Mg₂Si was changed from Chinese character to small short rod. Small fine polygonal Mg₂Si particles are benefitted to prevent the generation and development of cracks. Therefore, the ultimate tensile strength and elongation of the alloy have been greatly improved.

Conclusions

(1)

The effect of the addition of Sb and Nd compound modification is as follows: The morphology of primary Mg₂Si particles changes from coarse dendrite to regular shaped polygon, and the average size of the primary Mg₂Si particles decreased to 6.5 μm from 78 μm after adding 1.0 wt.% of Sb and 1.0 wt.% Nd. Furthermore, the amount of eutectic Mg₂Si reduced with addition of Nd elements up to 1.0 wt.%. The Chinese-shaped eutectic Mg₂Si is metamorphosed into a small short rod shape distributed in matrix. Therefore, the simultaneous addition of Sb and Nd is much better than the addition of Sb or Nd alone.

(2)

The Nd₄Sb₃ phase appeared in the core of the primary Mg₂Si particles after adding 1 wt.% Nd and 1 wt.% Sb to the Mg-4Si alloy. The crystal lattice mismatch between Nd₄Sb₃ and Mg₂Si was 9.33% (less than 15%), and thus, the Nd₄Sb₃ phase can be used as heterogeneous nucleation core of primary Mg₂Si particles. Therefore, the nucleation rate of the Mg₂Si phase is increased, and the primary Mg₂Si particles become regular and uniformly distributed in the magnesium matrix.

(3)

The hardness and tensile strength of the alloy increased with the modification of Sb and Nd. The Brinell hardness of the alloy increased from HB 65.45 to HB 89.17. In addition, the mechanical properties showed that the UTS value increased from 113.24 to 175.38 MPa, and the elongation changes from 2.23 to 4.61%. These are attributed to the compound modification for primary and eutectic Mg₂Si particles.

Acknowledgments

We thank LetPub (www.letpub.com) for linguistic assistance during the preparation of this manuscript. This work was supported by the National Natural Science Foundation of China (Grant numbers 51975484 and 51605392).

Conflict of interest

The authors declare that they have no conflict of interest.

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W. Jiang, G. Li, Z. Fan, L. Wang, and F. Liu, Investigation on the Interface Characteristics of Al/Mg Bimetallic Castings Processed by Lost Foam Casting, Metall. Mater. Trans. A, 2016, 47, p 2462–2470CrossRef

Z. Jiang, Z. Fan, W. Jiang, G. Li, Y. Wu, F. Guan et al., Interfacial Microstructures and Mechanical Properties of Mg/Al Bimetal Produced by a Novel Liquid–Liquid Compound Casting Process, J. Mater. Process. Technol., 2018, 261, p 149–158CrossRef

H.R. Bakhsheshi-Rad, E. Hamzah, S. Farahany, and M.P. Staiger, The Mechanical Properties and Corrosion Behavior of Quaternary Mg-6Zn-0.8Mn-xCa Alloys, J. Mater. Eng. Perform., 2014, 24, p 598–608CrossRef

Y. Chen, L. Wang, Y. Feng, E. Guo, S. Zhao, and L. Wang, Effect of Ca and Sm Combined Addition on the Microstructure and Elevated-Temperature Mechanical Properties of Mg-6Al Alloys, J. Mater. Eng. Perform., 2019, 28, p 2892–2902CrossRef

M. Cong, Z. Li, J. Liu, M. Yan, K. Chen, Y. Sun et al., Effect of Ca on the Microstructure and Tensile Properties of Mg–Zn–Si Alloys at Ambient and Elevated Temperature, J. Alloys Compd., 2012, 539, p 168–173CrossRef

W. Jiang, Z. Fan, G. Li, L. Yang, and X. Liu, Effects of Melt-to-Solid Insert Volume Ratio on the Microstructures and Mechanical Properties of Al/Mg Bimetallic Castings Produced by Lost Foam Casting, Metall. Mater. Trans. A, 2016, 47, p 6487–6497CrossRef

X. Qian, N. Parson, and X.G. Chen, Effect of Homogenization Treatment and Microalloying with Mn on the Microstructure and Hot Workability of AA6060 Aluminum Alloys, J. Mater. Eng. Perform., 2019, 28, p 4531–4542CrossRef

T. Sakthivel, G. Sasikala, M.K. Dash, and P. Syamala Rao, Creep Deformation and Rupture Behavior of P92 Steel Weld Joint Fabricated by NG-TIG Welding Process, J. Mater. Eng. Perform., 2019, 28, p 4364–4378CrossRef

P. Nieroda, A. Kolezynski, J. Leszczynski, J. Nieroda, and P. Pasierb, The Structural, Microstructural and Thermoelectric Properties of Mg₂Si Synthesized by SPS Method Under Excess Mg Content Conditions, J. Alloys Compd., 2019, 775, p 138–149CrossRef

10.

C. Li, X. Liu, and Y. Wu, Refinement and Modification Performance of Al–P Master Alloy on Primary Mg₂Si in Al–Mg–Si Alloys, J. Alloys Compd., 2008, 465, p 145–150CrossRef

11.

L. Liao, X. Zhang, H. Wang, X. Li, and N. Ma, Influence of Sb on Damping Capacity and Mechanical Properties of Mg₂Si/Mg–9Al Composite Materials, J. Alloys Compd., 2007, 430, p 292–296CrossRef

12.

H.Y. Wang, F. Liu, L. Chen, M. Zha, G.J. Liu, and Q.C. Jiang, The Effect of Sb Addition on Microstructures and Tensile Properties of Extruded Al–20Mg₂Si–4Cu Alloy, Mater. Sci. Eng. A, 2016, 657, p 331–338CrossRef

13.

K.K.A. Kumar, A. Viswanath, U.T.S. Pillai, B.C. Pai, and M. Chakraborty, Influence of Neodymium Addition on the Microstructure, Mechanical and Thermal Properties of Mg-Si Alloys, Proc. Eng., 2013, 55, p 103–108CrossRef

14.

H. J-l, C.-p. Tang, X.-m. Zhang, and Y.-l. Deng, Modification of Mg₂Si in Mg-Si Alloys with Neodymium, Trans. Nonferr. Met. Soc., 2013, 23, p 3161–3166CrossRef

15.

K. Chen, Z.Q. Li, J.S. Liu, J.N. Yang, Y.D. Sun, and S.G. Bian, The Effect of Ba Addition on Microstructure of in Situ Synthesized Mg₂Si/Mg–Zn–Si Composites, J. Alloys Compd., 2009, 487, p 293–297CrossRef

16.

J. Hou, C. Li, and X. Liu, Nucleating Role of an Effective in Situ Mg₃P₂ on Mg₂Si in Mg–Al–Si Alloys, J. Alloys Compd., 2011, 509, p 735–739CrossRef

17.

Q.C. Jiang, H.Y. Wang, Y. Wang, B.X. Ma, and J.G. Wang, Modification of Mg₂Si in Mg–Si Alloys with Yttrium, Mater. Sci. Eng. A, 2005, 392, p 130–135CrossRef

18.

G. Mao, H. Yan, C. Zhu, Z. Wu, and W. Gao, The Varied Mechanisms of Yttrium (Y) Modifying a Hypoeutectic Al–Si Alloy Under Conditions of Different Cooling Rates, J. Alloys Compd., 2019, 806, p 909–916CrossRef

19.

M.-B. Yang, F.-S. Pan, J. Shen, and L. Bai, Comparison of Sb and Sr on Modification and Refinement of Mg₂Si Phase in AZ61-0.7Si Magnesium Alloy, Trans. Nonferr. Met. Soc., 2009, 19, p 287–292CrossRef

20.

X.-F. Wu, Y. Wang, K.-Y. Wang, R.-D. Zhao, and F.-F. Wu, Enhanced Mechanical Properties of Hypoeutectic Al-10Mg₂Si Cast Alloys by Bi Addition, J. Alloys Compd., 2018, 767, p 163–172CrossRef

21.

K. Chen and Z. Li, Effect of Co-modification by Ba and Sb on the Microstructure of Mg₂Si/Mg–Zn–Si Composite and Mechanism, J. Alloys Compd., 2014, 592, p 196–201CrossRef

22.

D.H. Kang, G.T. Bae, and N.J. Kim, Effect of Sb and Sr Additions on the Microstructural Evolution of Mg-Sn-Al-Si Based Alloys, Mater. Trans., 2008, 49, p 936–940CrossRef

23.

H.-C. Yu, H.-Y. Wang, L. Chen, M. Zha, C. Wang, C. Li et al., Spheroidization of Primary Mg₂Si in Al-20Mg₂Si-4.5Cu Alloy Modified with Ca and Sb During T6 Heat Treatment Process, Mater. Sci. Eng. A, 2017, 685, p 31–38CrossRef

24.

S. Farahany, H. Ghandvar, N.A. Nordin, A. Ourdjini, and M.H. Idris, Effect of Primary and Eutectic Mg₂Si Crystal Modifications on the Mechanical Properties and Sliding Wear Behaviour of an Al–20Mg₂Si–2Cu–xBi Composite, J. Mater. Sci. Technol., 2016, 32, p 1083–1097CrossRef

25.

Y. Wang and X. Guo, Heterogeneous Nucleation of Mg₂Si and Mg₂(Si, Sn) on Mg₃Sb₂ Nucleus in Mg Containing Si Alloys, Mater. Chem. Phys., 2019, 223, p 336–342CrossRef

26.

L. Sheng, L. Wang, T. Xi, Y. Zheng, and H. Ye, Microstructure, Precipitates and Compressive Properties of Various Holmium Doped NiAl/Cr(Mo, Hf) Eutectic Alloys, Mater. Des., 2011, 32, p 4810–4817CrossRef

27.

H. Chang Shin, J. Son, B.K. Min, Y.S. Choi, K.M. Cho, D.H. Cho et al., The Effect of Ce on the Modification of Mg₂Si Phases of As-Cast Eutectic Mg-Si Alloys, J. Alloys Compd., 2019, 792, p 59–68CrossRef

28.

A. Gil-Santos, I. Marco, N. Moelans, N. Hort, and O. Van der Biest, Microstructure and Degradation Performance of Biodegradable Mg-Si-Sr Implant Alloys, Mater. Sci. Eng. C Mater. Biol. Appl., 2017, 71, p 25–34CrossRef

29.

M. Wang, D. Chen, Z. Chen, Y. Wu, F. Wang, N. Ma et al., Mechanical Properties of in Situ TiB₂/A356 Composites, Mater. Sci. Eng. A, 2014, 590, p 246–254CrossRef

30.

R. Du, D. Yuan, F. Li, D. Zhang, S. Wu, and S. Lü, Effect of in Situ TiB₂ Particles on Microstructure and Mechanical Properties of Mg₂Si/Al Composites, J. Alloys Compd., 2019, 776, p 536–542CrossRef

31.

B.N. Du, Z.P. Xiao, Y.X. Qiao, L. Zheng, B.Y. Yu, D.K. Xu et al., Optimization of Microstructure and Mechanical Property of a Mg-Zn-Y-Nd Alloy by Extrusion Process, J. Alloys Compd., 2019, 775, p 990–1001CrossRef

32.

L.-Y. Sheng, F. Yang, T.-F. Xi, Y.-F. Zheng, and J.-T. Guo, Microstructure and Room Temperature Mechanical Properties of NiAl–Cr(Mo)–(Hf, Dy) Hypoeutectic Alloy Prepared by Injection Casting, Trans. Nonferr. Met. Soc., 2013, 23, p 983–990CrossRef

Titel: Modification of Mg2Si Phase Morphology in Mg-4Si Alloy by Sb and Nd Additions
verfasst von: Hao Dong
Siming Xiang
Jie Lv
Yu Wang
Lu Li
Wenbin Yu
Publikationsdatum: 22.06.2020
Verlag: Springer US
Erschienen in: Journal of Materials Engineering and Performance / Ausgabe 6/2020
Print ISSN: 1059-9495
Elektronische ISSN: 1544-1024
DOI: https://doi.org/10.1007/s11665-020-04812-y

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Abstract

Publisher's Note

Introduction

Experimental Procedures

Experiment Results and Discussion

Phase Analysis

Microstructure Evolution

Modification Mechanism

Mechanical Properties

Hardness

Tensile Properties and Fracture Characteristics

Conclusions

Acknowledgments

Conflict of interest

Publisher's Note

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