# Influence of Sc on Microstructure and Mechanical Properties of High Zn-Containing Mg Alloy

Authors: Lidong Wang; Jie Yang; Limin Wang; Zhanyi Cao
Journal: Advances in Materials Science and Engineering
 (2014)

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## Abstract

Microstructures and mechanical properties of Mg-11Zn and Mg-11Zn-1Sc (wt%) alloys were investigated. The main secondary phase of Mg-11Zn and Mg-11Zn-1Sc alloys is MgZn2 phase. Rare earth Sc element is an effective grain refiner and the grain size of Mg-11Zn-1Sc alloy is greatly refined. The mechanical properties of the Mg-11Zn alloy were greatly improved with incorporation of 1 wt% Sc, especially for the elevated temperature strength. Such mechanical property enhancement is ascribed to the refinement and pinning mechanism of high heat-resistant Sc and Sc-containing intermetallic particles in Mg alloy.


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## Body

## 1. Introduction

Mg is the lightest structural metal and exhibits many good properties, such as high specific strength and stiffness, machinability, and impact and dent resistance. However, its poor mechanical properties, especially low strength, hamper its widespread applications. Zn and rare earths, as important alloying elements, are often added in Mg alloys to enhance their mechanical properties. Most research works involved with Mg-Zn-RE (rare earth) alloy system are focused on low Zn content (<6 wt%) system and Mg-Zn-Y alloy is the most representative one [1–4]. High Zn content alloys have low production temperatures and good flowability, but relevant research is not comprehensive and most works are focused on the Mg-Al-Zn alloy system [5–7].According to the Mg-Sc phase diagram, Sc has large solid solubility inα-Mg matrix. Moreover, Sc can effectively improve the high temperature strength and creep resistance of Mg-RE-Sc alloys [8–10]. For these reasons, this paper concentrates on studying the influence of Sc on high Zn-containing Mg alloys.


## 2. Experimental Procedure

The nominal compositions of the investigated alloys are Mg-11Zn (in wt%, alloy A) and Mg-11Zn-1Sc (in wt%, alloy B). They were prepared from commercial pure Mg (>99.8 wt%), Zn (>99.95 wt%), and Mg-Sc master alloy. The alloys were made by melting Mg in graphite crucible covered by antioxidizing flux in a furnace, and then Zn particles were added. The Mg-Sc master alloy was lastly added to the crucible. After stirring the molten alloy and setting for approximately 30 min at 720°C for homogenization, the alloy melt was casted into a copper mould at approximately 720°C and the size of the ingot is 70 × 40 × 13 mm3. Specimens were mechanically polished and then etched with picric acid-ethanol-H2O (for grain size observation) and HNO3-ethanol (for dendritic structure observation) solutions, respectively. Structures were observed by optical microscopy, transmission electron microscopy (TEM), scanning electron microscopy (SEM), and X-ray diffraction (XRD). Uniaxial tensile test was carried out at room temperature (RT), 200°C, and 280°C under a strain rate of 1.52 × 10−4 s−1 on dog bone specimens with nominal size of 11 mm in length, 3.5 mm in width, and 1.5 mm in thickness. For tensile test at elevated temperatures, the heating-plus-holding time was 10 min for the balance of temperature.


## 3. Results and Discussion

### 3.1. Microstructure

The optical micrographs (OM) of alloys A and B etched with picric acid-ethanol-H2O solution are shown in Figure 1. The average grain sizes of the two alloys are approximately 380 and 100 μm, respectively, which were calculated by the linearly intercepted method. Figure 2 illustrates the OMs of the two alloys etched with HNO3-ethanol solution, and the primary interdendritic spacing of the two alloys was calculated to be 16 and 9 μm, respectively. It indicates that both the grain size and the primary interdendritic spacing are refined by the addition of 1 wt% Sc. The refining effect on the grain size is much higher than that on the primary interdendritic spacing.OMs of alloys A and B etched with picric acid-ethanol-H2O solution.
(a)
(b)OMs of alloys A and B etched with HNO3-ethanol solution.
(a)
(b)Generally, grain size can be refined via two ways. One is the addition of foreign nucleating agents such as Zr to increase the number of nuclei. The other is the presence of solute elements to enhance constitutional supercooling for activating nucleation. In the present work, on account of Sc quantity being only 1 wt% and having large solid solubility in theα-Mg matrix, no enough Sc atoms were enriched and aggregated at the solid/liquid interface to result in the constitutional supercooling during the solidification process. The industrial grade Mg contains some impurity elements such as Al, Mn, and Fe. During the solidification process, Sc atoms are active and they quickly react with impurities to form intermetallic particles such as Al3Sc and Mn2Sc. The Sc-containing intermetallic particles increase the number of nuclei. Similarly, Sc addition can refine grain size in as-cast Mg-Gd [11] and ZK60 [12] alloys. A new group of Mg-RE materials with Mn and Sc were developed and showed superior creep resistance, which reportedly results from the formation of a thermally stable Mn2Sc particles phase [8, 10]. Al3Sc particles may serve as heterogeneous nuclei during solidification to refine the grain size in as-cast structure and improve mechanical properties by fine-grain strengthening in Al alloys [13, 14]. Thus, the above literature findings support our hypothesis that Sc reacts with impurities to form Sc-containing intermetallic particles that result in an increase in the nuclei number, which is the main cause of grain size refining in alloy B.The XRD analyses of the two alloys are given in Figure3. Both the two alloys are composed of α-Mg and MgZn2 phases. Generally, there are always RE-containing phases in the Mg-Zn-RE alloy system. However, no Sc-containing phases are observed in alloy B. Figure 4 displays the TEM image of alloy B, and rod-shaped precipitates are observed. The corresponding selected area diffraction pattern shows that these phases are MgZn2 phase. Their long axes are always parallel to the 0001
Mg direction [15].Figure 3
XRD patterns of alloys A and B.Figure 4
TEM image of alloy B.The XRD analysis indicates that alloy B interestingly consists of no Sc-containing phases, whereas when RE elements are added to Mg-Zn alloy system, the RE and Zn will compete with each other to occupy the Mg crystal lattice, therefore decreasing each other’s solubility limits in theα-Mg matrix. Then, the RE, Zn, and Mg elements will preferentially form binary or ternary RE-containing phases. For example, in Mg-Zn-Y alloy system, Mg3Y1Zn6 phase (I-phase) occurred when Y was added to the Mg-Zn alloy,even if the Y content was less than 1 wt% [16]. Table 1 lists the metallic radius and electronegativity of Mg, Zn, and Sc elements [17]. Compared with Zn, the metallic radius and electronegativity of Sc are closer to those of Mg. According to the principle of compatibility and similitude, Sc is superior to Zn for occupying the Mg crystal lattice and thus can readily be dissolved in the α-Mg matrix. That explains why there is no Sc-containing phase found in alloy B.Table 1
Metallic radius and electronegativity of the Mg, Zn, and Sc.
Elements
Mg
Sc
Zn
Atomic radius (nm)
0.1602
0.1641
0.153
Electronegativity
1.31
1.27
1.65


### 3.2. Mechanical Properties

The tensile performance of alloys A and B was assessed in the temperature range from RT to 280°C, and the representative stress-strain curves were shown in Figure5. The corresponding mechanical properties, including the ultimate tensile stress (σ
b), 0.2% yield stress (σ
0.2), and elongation at failure (ε), were listed in Table 2. The RT σ
b of the two alloys are almost the same, suggesting that Sc plays a minor role in improving the room temperature σ
b. However, the σ
0.2 is greatly enhanced by the addition of Sc. The σ
0.2 of alloy B is 1.4 times that of alloy A, and the σ
0
.
2 increment is about 45 MPa. At 200°C, the σ
b and σ
0.2 of alloy B are 175 and 144 MPa, which are 1.9 and 1.7 times those of alloy A. At 280°C, the σ
b and σ
0.2 of alloy B are 2.7 and 4.6 times those of alloy A. The above results indicate that 1 wt% Sc can effectively enhance the alloy’s strength, especially for the yield strength at elevated temperatures.Table 2
Tensile properties of alloys A and B at RT, 200°C, and 280°C.
Alloys
σ
b (MPa)
σ
0.2 (MPa)
ε (%)
RT
200°C
280°C
RT
200°C
280°C
RT
200°C
280°C
(A)
217
91
45
118
83
22
8.7
32.3
40.0
(B)
227
175
120
163
144
102
5.0
14.1
4.5Stress-strain curves of alloys A and B at RT, 200°C, and 280°C.
(a)
(b)The yield strength of metals and alloys varies with grain size, and the relationship usually follows the Hall-Petch equation [18]:
(1)
σ
=
σ
0
+
k
d
-
1
/
2
,
where σ is the 0.2% yield stress (σ
0.2, MPa) and d is a measure of grain size in μm. σ
0 and k are parameters determined for the polycrystalline material. In the current work, σ
0 is expected to be a constant value with consideration of the low Sc content. k
=
300
μ
m MPa has been used to evaluate the Hall-Petch effects in the Mg-(0.2~2.4)at%Zn alloy system [19]. Thus, this value will also be employed in the present work to estimate the grain size effect on the yield strength. According to the Hall-Petch equation, as a reduction in grain size from 380 μm to 100 μm, alloy B is expected to have a σ
0.2 increment of about 15 MPa at RT. This value is much smaller than the experimental value of 45 MPa. Therefore, the σ
0.2 increment does not solely depend on the grain refining effect, and other influencing factors should also be considered. Sc is solid solvated in the matrix and thus can strengthen the alloy by solution hardening. It is known that dislocation slipping and pile-up lead to crack initiations, and then the cracks propagate and result in final fracture during tensile test. The Sc-containing intermetallic particles disperse homogeneously in the Mg matrix, which is beneficial to hinder dislocation slipping, disperse dislocations, and weaken their pile-up, and thus, the strengths of the alloy are reinforced. The pinning mechanism of Sc-containing intermetallic particles results in dislocation slipping weakening and ductility decrease of alloy B at RT and elevated temperature.When test temperature rises, dislocation slipping and pile-up accelerate and grain boundaries soften. If dislocations gather at grain boundary, the alloy’s strength will rapidly deteriorate. In alloy B, the finer gain size means higher content of grain boundary, which is not beneficial to enhancing the strength of the alloy at elevated temperature. It is believed that there are two reasons for high temperature strengthening of Sc added alloy. One is that Sc can increase the melting point of the Mg-Sc solid solution [8]. The other is that the pinning mechanism of high melting point Sc-containing intermetallic particles can remarkably hinder dislocation slipping and gather at grain boundary. The similar phenomenon has been reported in Mg-Sc-RE alloys [10] that thermally stable particles are strong obstacles to dislocation slipping.


## 3.1. Microstructure

The optical micrographs (OM) of alloys A and B etched with picric acid-ethanol-H2O solution are shown in Figure 1. The average grain sizes of the two alloys are approximately 380 and 100 μm, respectively, which were calculated by the linearly intercepted method. Figure 2 illustrates the OMs of the two alloys etched with HNO3-ethanol solution, and the primary interdendritic spacing of the two alloys was calculated to be 16 and 9 μm, respectively. It indicates that both the grain size and the primary interdendritic spacing are refined by the addition of 1 wt% Sc. The refining effect on the grain size is much higher than that on the primary interdendritic spacing.OMs of alloys A and B etched with picric acid-ethanol-H2O solution.
(a)
(b)OMs of alloys A and B etched with HNO3-ethanol solution.
(a)
(b)Generally, grain size can be refined via two ways. One is the addition of foreign nucleating agents such as Zr to increase the number of nuclei. The other is the presence of solute elements to enhance constitutional supercooling for activating nucleation. In the present work, on account of Sc quantity being only 1 wt% and having large solid solubility in theα-Mg matrix, no enough Sc atoms were enriched and aggregated at the solid/liquid interface to result in the constitutional supercooling during the solidification process. The industrial grade Mg contains some impurity elements such as Al, Mn, and Fe. During the solidification process, Sc atoms are active and they quickly react with impurities to form intermetallic particles such as Al3Sc and Mn2Sc. The Sc-containing intermetallic particles increase the number of nuclei. Similarly, Sc addition can refine grain size in as-cast Mg-Gd [11] and ZK60 [12] alloys. A new group of Mg-RE materials with Mn and Sc were developed and showed superior creep resistance, which reportedly results from the formation of a thermally stable Mn2Sc particles phase [8, 10]. Al3Sc particles may serve as heterogeneous nuclei during solidification to refine the grain size in as-cast structure and improve mechanical properties by fine-grain strengthening in Al alloys [13, 14]. Thus, the above literature findings support our hypothesis that Sc reacts with impurities to form Sc-containing intermetallic particles that result in an increase in the nuclei number, which is the main cause of grain size refining in alloy B.The XRD analyses of the two alloys are given in Figure3. Both the two alloys are composed of α-Mg and MgZn2 phases. Generally, there are always RE-containing phases in the Mg-Zn-RE alloy system. However, no Sc-containing phases are observed in alloy B. Figure 4 displays the TEM image of alloy B, and rod-shaped precipitates are observed. The corresponding selected area diffraction pattern shows that these phases are MgZn2 phase. Their long axes are always parallel to the 0001
Mg direction [15].Figure 3
XRD patterns of alloys A and B.Figure 4
TEM image of alloy B.The XRD analysis indicates that alloy B interestingly consists of no Sc-containing phases, whereas when RE elements are added to Mg-Zn alloy system, the RE and Zn will compete with each other to occupy the Mg crystal lattice, therefore decreasing each other’s solubility limits in theα-Mg matrix. Then, the RE, Zn, and Mg elements will preferentially form binary or ternary RE-containing phases. For example, in Mg-Zn-Y alloy system, Mg3Y1Zn6 phase (I-phase) occurred when Y was added to the Mg-Zn alloy,even if the Y content was less than 1 wt% [16]. Table 1 lists the metallic radius and electronegativity of Mg, Zn, and Sc elements [17]. Compared with Zn, the metallic radius and electronegativity of Sc are closer to those of Mg. According to the principle of compatibility and similitude, Sc is superior to Zn for occupying the Mg crystal lattice and thus can readily be dissolved in the α-Mg matrix. That explains why there is no Sc-containing phase found in alloy B.Table 1
Metallic radius and electronegativity of the Mg, Zn, and Sc.
Elements
Mg
Sc
Zn
Atomic radius (nm)
0.1602
0.1641
0.153
Electronegativity
1.31
1.27
1.65


## 3.2. Mechanical Properties

The tensile performance of alloys A and B was assessed in the temperature range from RT to 280°C, and the representative stress-strain curves were shown in Figure5. The corresponding mechanical properties, including the ultimate tensile stress (σ
b), 0.2% yield stress (σ
0.2), and elongation at failure (ε), were listed in Table 2. The RT σ
b of the two alloys are almost the same, suggesting that Sc plays a minor role in improving the room temperature σ
b. However, the σ
0.2 is greatly enhanced by the addition of Sc. The σ
0.2 of alloy B is 1.4 times that of alloy A, and the σ
0
.
2 increment is about 45 MPa. At 200°C, the σ
b and σ
0.2 of alloy B are 175 and 144 MPa, which are 1.9 and 1.7 times those of alloy A. At 280°C, the σ
b and σ
0.2 of alloy B are 2.7 and 4.6 times those of alloy A. The above results indicate that 1 wt% Sc can effectively enhance the alloy’s strength, especially for the yield strength at elevated temperatures.Table 2
Tensile properties of alloys A and B at RT, 200°C, and 280°C.
Alloys
σ
b (MPa)
σ
0.2 (MPa)
ε (%)
RT
200°C
280°C
RT
200°C
280°C
RT
200°C
280°C
(A)
217
91
45
118
83
22
8.7
32.3
40.0
(B)
227
175
120
163
144
102
5.0
14.1
4.5Stress-strain curves of alloys A and B at RT, 200°C, and 280°C.
(a)
(b)The yield strength of metals and alloys varies with grain size, and the relationship usually follows the Hall-Petch equation [18]:
(1)
σ
=
σ
0
+
k
d
-
1
/
2
,
where σ is the 0.2% yield stress (σ
0.2, MPa) and d is a measure of grain size in μm. σ
0 and k are parameters determined for the polycrystalline material. In the current work, σ
0 is expected to be a constant value with consideration of the low Sc content. k
=
300
μ
m MPa has been used to evaluate the Hall-Petch effects in the Mg-(0.2~2.4)at%Zn alloy system [19]. Thus, this value will also be employed in the present work to estimate the grain size effect on the yield strength. According to the Hall-Petch equation, as a reduction in grain size from 380 μm to 100 μm, alloy B is expected to have a σ
0.2 increment of about 15 MPa at RT. This value is much smaller than the experimental value of 45 MPa. Therefore, the σ
0.2 increment does not solely depend on the grain refining effect, and other influencing factors should also be considered. Sc is solid solvated in the matrix and thus can strengthen the alloy by solution hardening. It is known that dislocation slipping and pile-up lead to crack initiations, and then the cracks propagate and result in final fracture during tensile test. The Sc-containing intermetallic particles disperse homogeneously in the Mg matrix, which is beneficial to hinder dislocation slipping, disperse dislocations, and weaken their pile-up, and thus, the strengths of the alloy are reinforced. The pinning mechanism of Sc-containing intermetallic particles results in dislocation slipping weakening and ductility decrease of alloy B at RT and elevated temperature.When test temperature rises, dislocation slipping and pile-up accelerate and grain boundaries soften. If dislocations gather at grain boundary, the alloy’s strength will rapidly deteriorate. In alloy B, the finer gain size means higher content of grain boundary, which is not beneficial to enhancing the strength of the alloy at elevated temperature. It is believed that there are two reasons for high temperature strengthening of Sc added alloy. One is that Sc can increase the melting point of the Mg-Sc solid solution [8]. The other is that the pinning mechanism of high melting point Sc-containing intermetallic particles can remarkably hinder dislocation slipping and gather at grain boundary. The similar phenomenon has been reported in Mg-Sc-RE alloys [10] that thermally stable particles are strong obstacles to dislocation slipping.


## 4. Conclusions

The grain size of the Mg-11Zn alloy was greatly refined with Sc element. The refinement mechanism of Sc is that Sc reacts with impurities to generate Sc-containing intermetallic particles, which increase the nuclei number. The yield strength and ultimate tensile strength of the Mg alloy are greatly improved by Sc element at RT mainly due to the fine-grain strengthening effect and the dissolved strengthening effect of Sc element. The higher elevated temperature strength of alloy B is attributed to Sc induced melting point increase of Mg-Sc solid solution and the pinning mechanism of high melting point Sc-containing intermetallic particles to hinder dislocation slipping.



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*Source: 975041-2014-12-18.xml*