# Hot Deformation Behavior and Microstructural Evolution of Twin-Roll-Casting Mg Alloy during High-Temperature Compression

Authors: Qingshan Yang; Jiahong Dai; Sensen Chai; Daliang Yu; Bin Jiang; Fusheng Pan
Journal: Advances in Materials Science and Engineering
 (2019)

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## Abstract

The deformation behavior and microstructural evolution of twin-roll-casting AZ31 Mg alloy sheets were investigated via hot compression tests at 0°, 5°, and 10° from the normal direction. Compression strains of 5%, 15%, 25%, and 35% were employed at high temperatures of 450°C and 500°C. The flow stress as well as the difference in the flow stress associated with different sampling directions decreased when the temperature was increased. Furthermore, the volume fraction of dynamically recrystallized grains increased with increasing deformation, whereas the average grain size decreased. The DRX grain size and the volume fraction of dynamically recrystallized grains increased with increasing deformation temperature. During ultrahigh temperature compression, the effect of sampling direction on the compression microstructure is relatively small.


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## Body

## 1. Introduction

Magnesium (Mg) alloys, as the lightest structural alloys, have received increasing attention and have been extensively applied in various transportation systems [1–3]. However, the inherently poor workability of these alloys hinders their use in further engineering applications, owing mainly to the limited number of slip systems operating at room temperature [4–6]. Thus, the automotive applications of Mg alloys are limited mainly to die castings. Wrought products such as sheet and bar have been developed with the aim of broadening the application range of these alloys. In addition, the sheet should be readily formable into complex shapes. Mg alloys are more workable at elevated temperatures than at room temperature, owing to the activation of slip systems other than the basal slip system [7–9]. Hence, the hot forming of Mg alloys has been extensively explored.The formability of Mg alloys can be increased through different fabrication processes, which mainly rely on the hot deformation methods. Mg-Al-Zn alloy, as the most widely used Mg alloys, has been extensively studied. Previous studies have shown that Mg alloys might undergo dynamic recrystallization (DRX) during hot working processes. J. C. Tan and M. J. Tan [10] evaluated the dominance of continuous recrystallization phenomena in the AZ31 alloy exposed to temperatures of 250–400°C. They reported that due to the rapid grain growth, negligible grain refinement occurs during high-temperature DRX. Maximum grain refinement occurred at medium temperatures. Sitdikov and Kaibyshev suggested a temperature- and strain-dependency regime for the grain size variation [11]. Barnett reported that the dynamically recrystallized grains of Mg alloys are less sensitive to deformation conditions than those of other metals [12].A twin-roll-casting (TRC) process combines casting and hot rolling into a single process, which would provide a means of producing Mg strip products at competitive costs for commercial applications [13, 14]. However, reported studies of the associated twin-roll-casting and hot compression (HC) processing of Mg alloys are rare. Therefore, in this work, the hot deformation behavior and microstructural evolution of twin-roll-cast AZ31 alloy were investigated via hot compression at 450°C and 500°C. The effect of different original sampling directions and different accumulated plastic deformations on the high-temperature deformation mechanism of the alloy was explored.


## 2. Experimental Procedure

An 8-mm-thick twin-roll-casting (TRC) AZ31 alloy (Mg-3 Al-1 Zn, in wt.%) was investigated in this work. Cylindrical hot compression testing specimens were machined to a size of Φ5 ×H 5 mm. In preparation for the compression tests, cylindrical samples were cut from the TRC-AZ31 sheet at 0°, 5°, and 10° to the normal direction (ND), as shown in Figure 1.Figure 1
(a) Schematic showing the sampling directions. (b) Size of samples subjected to high-temperature compression.
(a)
(b)To investigate the effects of high temperatures and accumulated plastic deformation, isothermal hot compression tests were performed at 450°C and 500°C for deformations ranging from 5% to 35% in steps of 10%. During the tests, specimens were heated (heating rate: 10°C/s) to the deformation temperature and held isothermally for 240 s. The specimens were then subjected to a hot compression test (strain rate: 0.15 s−1) on a Gleeble1500D machine. After hot deformation, the samples were water cooled to obtain the deformed microstructures.After quenching in water, the deformed specimens were sectioned in the center parallel to the compression axis, and the microstructure was observed via optical microscopy (OM). To further investigate the occurrence of dynamic recrystallization (DRX) during high-temperature compression, the microstructures were examined after various deformation strains. The volume fraction of dynamically recrystallized grains was determined through a point counting technique. The DRX grains were almost readily distinguishable from the pre-existing grains, and the corresponding grain size was determined using an imaging analysis system.


## 3. Results and Discussion

### 3.1. Flow Stress Behavior

Figure2 shows the true stress-strain curves for different deformations ranging from 5% to 35% under a strain rate of 0.15 s−1 at 450°C. No steady state was observed for the 0° and 5° samples subjected to a low deformation of 5%. A flow-stress steady state was observed when the deformation increased to 15%, 25%, and 35%. Most samples exhibited an almost steady-state flow behavior, and work hardening was restricted to very small strains (<0.05) followed by mild flow softening, leading to a steady-state flow. The temperature-dependent flow behavior observed for Mg alloys was attributed to the activation of nonbasal slip systems at elevated temperatures. Chapuis and Liu reported that increasing the plastic deformation temperature of Mg alloys can result in high strain rate sensitivity, and secondary slip modes can be easily activated [15]. The true stress values of TRC-AZ31 with different sampling directions and different accumulated plastic deformations during the steady stage at 450°C are listed in Table 1. For the same deformation, the steady-state stress increased with the sampling direction. The difference in the flow stress associated with different sampling directions is attributed to the grain orientation of the twin-roll-cast AZ31 sheet alloy. Furthermore, the variation in the steady-state stress between different sampling directions decreased with increasing deformation, from 6 MPa at 15% deformation to 2 MPa at 35% deformation. Therefore, large strain and more complete recrystallization induced by hot deformation can improve the anisotropy of the twin-roll-cast AZ31 sheet alloy.Figure 2
True stress-true strain curves of the TRC-AZ31 alloy during hot compression at 450°C: (a) 5% strain; (b) 15% strain; (c) 25% strain; (d) 35% strain.
(a)
(b)
(c)
(d)Table 1
True stress (MPa) of the TRC-AZ31 alloy during the stable stage at 450°C.
Strain (%)
Sampling direction
0°
5°
10°
5
—
—
26
15
28
34
40
25
29
36
37
35
29
31
33Figure3 shows the true stress-strain curves obtained under the same deformation conditions at 500°C. It can be seen that each sample reached a steady state. The true stress values of TRC-AZ31 with different sampling directions and different accumulated plastic deformations during the steady stage at 500°C are summarized in Table 2. It can be observed that the steady-state stress decreased with increasing temperature, from an average of 35 MPa at 450°C to 28 MPa at 500°C. However, for a given deformation at 450°C, the steady-state stress increased with the sampling direction, which differed from the trends observed for deformation at 500°C. This may have resulted from the fact that as the temperature increases, activation of the nonbasal slip, such as prismatic a and pyramidal plane slip c+a, is facilitated [16].Figure 3
True stress-true strain curves of the TRC-AZ31 alloy during hot compression at 500°C: (a) 5% strain; (b) 15% strain; (c) 25% strain; (d) 35% strain.
(a)
(b)
(c)
(d)Table 2
True stress (MPa) of the TRC-AZ31 alloy during the stable stage at 500°C.
Strain (%)
Sampling direction
0°
5°
10°
5
29
26
24
15
25
27
26
25
28
25
27
35
27
24
33


### 3.2. Microstructural Evolution

Figure4 shows the initial longitudinal microstructure of the as-received TRC-AZ31 alloy. It can be observed that it consisted of dendritic columnar grains. Due to the high cooling rate and directional heat transfer during the TRC processes, large columnar grains have grown against the heat extraction direction, where the solidifying material has been in contact with the cold casting rolls.Figure 4
Optical micrograph of the TRC-AZ31 sheet alloy in the longitudinal orientation.Figure5 reveals the microstructure after deformation at 450°C and strains ranging from 5% to 35% for sampling directions of 0°, 5°, and 10°. In general, the dynamic recrystallization process is classified into continuous and discontinuous DRX [17]. Continuous recrystallization is considered a recovery process accompanied by a progressive increase in boundary misorientation and the conversion of low-angle boundaries into high-angle boundaries [18]. This type of recrystallization may be accompanied by gradual softening in the flow curve, resulting in a plateau in the true stress-true strain curves. As shown in Figure 5, for the 0° sample with 5% strain, the necklace DRX grains are concentrated on grain boundaries due to the occurrence of nonbasal slip at high temperatures of 450°C. This indicated DRX behavior depended on the temperature-dependent deformation mode. At 450°C and mainly low strains, microscopic strain localization at slip lines resulted in the formation of bulges at the grain boundaries, thereby leading to nucleation of DRX grains. At moderate and high strains, DRX occurred via nucleation in slip bands, and in both cases, rapid dislocation climb led to the formation of low-angle boundaries [19]. Moving dislocations are trapped by these sub-boundaries and are gradually converted into true high-angle boundaries. The results obtained for the AZ31 samples with 5° and 15° directions are similar to those obtained for the 0° direction. High-temperature compression may be accompanied by dislocation annihilation and grain boundary migration. Moreover, grain rotation is easily activated at high temperature.Figure 5
Microstructures of the twin-roll-cast (TRC) AZ31 alloy with different original sampling directions and different deformations under 450°C compression: (a) 0°-5%; (b) 5°-5%; (c) 10°-5%; (d) 0°-15%; (e) 5°-15%; (f) 10°-15%; (g) 0°-25%; (h) 5°-25%; (i) 10°-25%; (j) 0°-35%; (k) 5°-35%; (l) 10°-35%.Figure6 shows the microstructural evolution of the as-compressed samples at 500°C. The nucleation of DRX grains is similar to that of 450°C compression. For the higher temperature, the degree of DRX was larger than the compression at 450°C, which resulted in growth of the grains. Figure 7 shows the volume fraction of dynamically recrystallized grains (DRX-G). It was determined to quantify the effect of deformation temperature and the degree of deformation on the microstructure after high-temperature compression. It can be seen that the volume fraction of DRX-G increased with increasing level of deformation. This is typical of nucleation and growth type of transformations. During high-temperature compression, dislocation climb leads to the formation of low-angle boundaries. When the strain increases, moving dislocations are trapped by these sub-boundaries and are gradually converted into true high-angle boundaries. The volume fraction and size of dynamically recrystallized grains at 500°C were higher than the fraction and size associated with 450°C and the same deformation conditions. During hot compression, work hardening occurred in the newly formed recrystallized grains, and the size of these grains became limited as the driving force for further growth was reduced. As the temperature decreased, the level of work hardening increased, and the growth of the new grains was limited, thereby leading to a reduction in the DRX grain size. As shown in Figures 5 and 6, at low strain levels, the average grain size decreased with increasing strain. Once the dynamically recrystallized grains were established, the DRX grain size changed only slightly with increasing strain.Figure 6
Microstructures of the twin-roll-cast (TRC) AZ31 alloy with different original sampling directions and different deformations at 500°C compression: (a) 0°-5%; (b) 5°-5%; (c) 10°-5%; (d) 0°-15%; (e) 5°-15%; (f) 10°-15%; (g) 0°-25%; (h) 5°-25%; (i) 10°-25%; (j) 0°-35%; (k) 5°-35%; (l) 10°-35%.Figure 7
Volume fraction of dynamically recrystallized grains after hot deformation: (a) 450°C; (b) 500°C.
(a)
(b)


## 3.1. Flow Stress Behavior

Figure2 shows the true stress-strain curves for different deformations ranging from 5% to 35% under a strain rate of 0.15 s−1 at 450°C. No steady state was observed for the 0° and 5° samples subjected to a low deformation of 5%. A flow-stress steady state was observed when the deformation increased to 15%, 25%, and 35%. Most samples exhibited an almost steady-state flow behavior, and work hardening was restricted to very small strains (<0.05) followed by mild flow softening, leading to a steady-state flow. The temperature-dependent flow behavior observed for Mg alloys was attributed to the activation of nonbasal slip systems at elevated temperatures. Chapuis and Liu reported that increasing the plastic deformation temperature of Mg alloys can result in high strain rate sensitivity, and secondary slip modes can be easily activated [15]. The true stress values of TRC-AZ31 with different sampling directions and different accumulated plastic deformations during the steady stage at 450°C are listed in Table 1. For the same deformation, the steady-state stress increased with the sampling direction. The difference in the flow stress associated with different sampling directions is attributed to the grain orientation of the twin-roll-cast AZ31 sheet alloy. Furthermore, the variation in the steady-state stress between different sampling directions decreased with increasing deformation, from 6 MPa at 15% deformation to 2 MPa at 35% deformation. Therefore, large strain and more complete recrystallization induced by hot deformation can improve the anisotropy of the twin-roll-cast AZ31 sheet alloy.Figure 2
True stress-true strain curves of the TRC-AZ31 alloy during hot compression at 450°C: (a) 5% strain; (b) 15% strain; (c) 25% strain; (d) 35% strain.
(a)
(b)
(c)
(d)Table 1
True stress (MPa) of the TRC-AZ31 alloy during the stable stage at 450°C.
Strain (%)
Sampling direction
0°
5°
10°
5
—
—
26
15
28
34
40
25
29
36
37
35
29
31
33Figure3 shows the true stress-strain curves obtained under the same deformation conditions at 500°C. It can be seen that each sample reached a steady state. The true stress values of TRC-AZ31 with different sampling directions and different accumulated plastic deformations during the steady stage at 500°C are summarized in Table 2. It can be observed that the steady-state stress decreased with increasing temperature, from an average of 35 MPa at 450°C to 28 MPa at 500°C. However, for a given deformation at 450°C, the steady-state stress increased with the sampling direction, which differed from the trends observed for deformation at 500°C. This may have resulted from the fact that as the temperature increases, activation of the nonbasal slip, such as prismatic a and pyramidal plane slip c+a, is facilitated [16].Figure 3
True stress-true strain curves of the TRC-AZ31 alloy during hot compression at 500°C: (a) 5% strain; (b) 15% strain; (c) 25% strain; (d) 35% strain.
(a)
(b)
(c)
(d)Table 2
True stress (MPa) of the TRC-AZ31 alloy during the stable stage at 500°C.
Strain (%)
Sampling direction
0°
5°
10°
5
29
26
24
15
25
27
26
25
28
25
27
35
27
24
33


## 3.2. Microstructural Evolution

Figure4 shows the initial longitudinal microstructure of the as-received TRC-AZ31 alloy. It can be observed that it consisted of dendritic columnar grains. Due to the high cooling rate and directional heat transfer during the TRC processes, large columnar grains have grown against the heat extraction direction, where the solidifying material has been in contact with the cold casting rolls.Figure 4
Optical micrograph of the TRC-AZ31 sheet alloy in the longitudinal orientation.Figure5 reveals the microstructure after deformation at 450°C and strains ranging from 5% to 35% for sampling directions of 0°, 5°, and 10°. In general, the dynamic recrystallization process is classified into continuous and discontinuous DRX [17]. Continuous recrystallization is considered a recovery process accompanied by a progressive increase in boundary misorientation and the conversion of low-angle boundaries into high-angle boundaries [18]. This type of recrystallization may be accompanied by gradual softening in the flow curve, resulting in a plateau in the true stress-true strain curves. As shown in Figure 5, for the 0° sample with 5% strain, the necklace DRX grains are concentrated on grain boundaries due to the occurrence of nonbasal slip at high temperatures of 450°C. This indicated DRX behavior depended on the temperature-dependent deformation mode. At 450°C and mainly low strains, microscopic strain localization at slip lines resulted in the formation of bulges at the grain boundaries, thereby leading to nucleation of DRX grains. At moderate and high strains, DRX occurred via nucleation in slip bands, and in both cases, rapid dislocation climb led to the formation of low-angle boundaries [19]. Moving dislocations are trapped by these sub-boundaries and are gradually converted into true high-angle boundaries. The results obtained for the AZ31 samples with 5° and 15° directions are similar to those obtained for the 0° direction. High-temperature compression may be accompanied by dislocation annihilation and grain boundary migration. Moreover, grain rotation is easily activated at high temperature.Figure 5
Microstructures of the twin-roll-cast (TRC) AZ31 alloy with different original sampling directions and different deformations under 450°C compression: (a) 0°-5%; (b) 5°-5%; (c) 10°-5%; (d) 0°-15%; (e) 5°-15%; (f) 10°-15%; (g) 0°-25%; (h) 5°-25%; (i) 10°-25%; (j) 0°-35%; (k) 5°-35%; (l) 10°-35%.Figure6 shows the microstructural evolution of the as-compressed samples at 500°C. The nucleation of DRX grains is similar to that of 450°C compression. For the higher temperature, the degree of DRX was larger than the compression at 450°C, which resulted in growth of the grains. Figure 7 shows the volume fraction of dynamically recrystallized grains (DRX-G). It was determined to quantify the effect of deformation temperature and the degree of deformation on the microstructure after high-temperature compression. It can be seen that the volume fraction of DRX-G increased with increasing level of deformation. This is typical of nucleation and growth type of transformations. During high-temperature compression, dislocation climb leads to the formation of low-angle boundaries. When the strain increases, moving dislocations are trapped by these sub-boundaries and are gradually converted into true high-angle boundaries. The volume fraction and size of dynamically recrystallized grains at 500°C were higher than the fraction and size associated with 450°C and the same deformation conditions. During hot compression, work hardening occurred in the newly formed recrystallized grains, and the size of these grains became limited as the driving force for further growth was reduced. As the temperature decreased, the level of work hardening increased, and the growth of the new grains was limited, thereby leading to a reduction in the DRX grain size. As shown in Figures 5 and 6, at low strain levels, the average grain size decreased with increasing strain. Once the dynamically recrystallized grains were established, the DRX grain size changed only slightly with increasing strain.Figure 6
Microstructures of the twin-roll-cast (TRC) AZ31 alloy with different original sampling directions and different deformations at 500°C compression: (a) 0°-5%; (b) 5°-5%; (c) 10°-5%; (d) 0°-15%; (e) 5°-15%; (f) 10°-15%; (g) 0°-25%; (h) 5°-25%; (i) 10°-25%; (j) 0°-35%; (k) 5°-35%; (l) 10°-35%.Figure 7
Volume fraction of dynamically recrystallized grains after hot deformation: (a) 450°C; (b) 500°C.
(a)
(b)


## 4. Conclusions

The hot deformation behavior and microstructural evolution were investigated for twin-roll-cast AZ31 alloys subjected to compression strains at high temperatures and different sampling directions. In our present work, the conclusions can be mainly drawn as follows:(1)
The results revealed that the flow stress decreases with increasing temperature, from an average of 35 MPa at 450°C to 28 MPa at 500°C(2)
The anisotropy of the flow stress associated with different sampling directions decreased with increasing temperature(3)
The volume fraction and grain size of the dynamically recrystallized grains increased when the deformation temperature increased from 450°C to 500°C



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*Source: 1820671-2019-12-18.xml*