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Fig.
1.
Configuration of the die for bending and tension deformations.
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Yuya Ishiguro, Xinsheng Huang, Yuhki Tsukada, Toshiyuki Koyama, and Yasumasa Chino, Effect of bending and tension deformation on the texture evolution and stretch formability of Mg–Zn–RE–Zr alloy, Int. J. Miner. Metall. Mater., 29(2022), No. 7, pp.1334-1342. https://dx.doi.org/10.1007/s12613-021-2398-8
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Bending and tension deformations were performed on Mg–1.3wt%Zn–0.2wt%RE–0.3wt%Zr (ZEK100) alloy sheets that initially had a transverse direction (TD)-split texture. The effects of bending and tension deformations on the texture formation and room-temperature formability of specimens were investigated. The specimen subjected to 3-pass bending and tension deformations exhibited an excellent Erichsen value of 9.6 mm. However, the Erichsen value deterioration was observed in the specimen subjected to 7-pass deformations. The rolling direction-split texture developed on the surface with an increasing pass number of deformations. Conversely, the clear TD-split texture remained at the central part. As a result, a quadrupole texture was macroscopically developed with an increasing pass number of deformations. The reduction in anisotropy by the formation of the quadrupole texture is suggested to be the main reason for the improvement in stretch formability. By contrast, the generation of coarse grains near the surface is suggested to be the direct cause for the deterioration of the stretch formability of the specimen subjected to 7-pass deformations.
Magnesium (Mg) alloys have been applied to several lightweight structural materials because of their low density and good specific strength [1]. However, Mg alloys exhibit large plastic anisotropy, particularly at room temperature, because of their hexagonal closed packed crystal structure, in which the critical resolved shear stress of non-basal slips is significantly higher than that of basal slips at room temperature [2]. Furthermore, rolling on Mg alloys induces the formation of a strong basal texture with the c-axis parallel to the thickness direction (ND) [3]. Thus, the rolled Mg alloy sheets cannot satisfy the Von Mises condition [4], and their room-temperature stretch formability is considerably lower than that of other structural metals, such as aluminum (Al) alloys. The low press formability of Mg alloy sheets at room temperature hinders the practical use of these structural components in automobiles and home appliances.
Texture formation is closely related to the room-temperature formability of Mg alloys, and the suppression of basal texture formation is essential to improve the room-temperature formability of Mg alloy sheets [5]. Currently, the dilute addition of specific elements and the optimization of rolling can effectively suppress the formation of a strong basal texture. The former is characterized by the dilute addition of rare earth (RE) and calcium (Ca) in Mg–Zn series alloys [6–8]. The addition of RE and Ca to Mg–Zn alloys contributes to the formation of a transverse direction (TD)-split texture and a weak basal texture, resulting in an excellent Erichsen value (>8 mm) [9–13]. The latter is characterized by the optimization of rolling procedures, such as high-temperature rolling [14], warm rolling [15], bending deformation [16–17], and different-speed rolling [18].
Recently, Noguchi et al. [19] have applied bending and tension deformations to AZ31B (Mg–3wt%Al–1wt%Zn) alloy sheets with a strong basal texture. They demonstrated that the bending and tension deformations contribute to a tilting of the basal pole to the rolling direction (RD), resulting in the formation of an RD-split texture; AZ31B alloy sheets with an RD-split texture show a satisfactory Erichsen value of 7 mm. In our previous study [20], high-temperature rolled AZ31B alloy sheets with a weak basal texture intensity were subjected to bending and tension deformations, and an RD-split texture with a large split angle and weak basal texture intensity was obtained with an excellent Erichsen value of 8 mm.
Furthermore, previous studies suggested that the formation of a TD-split or RD-split texture could enhance room-temperature formability; however, it induces a large plastic anisotropy, especially anisotropy in yield stress [21]. Recently, He et al. [22–24] have reported that sheets subjected to in-plane pre-compression, pre-stretching, and annealing exhibit a quadrupole texture, and sheets with a quadrupole texture exhibit a suppressed in-plane anisotropy and enhanced room-temperature stretch formability. Bending and tension deformations are applicable to the development of an RD-split texture not only in AZ31B alloys but also in Mg–Zn–RE alloys with a TD-split texture. Moreover, the RD-split texture is possibly superimposed on the TD-split texture. Mg–1.3wt%Zn–0.2wt%RE–0.3wt%Zr alloy (ZEK100 alloy) is a popular commercial Mg alloy with a TD-split texture. Adding Zr in Mg–Zn–RE alloys improves the balance of strength and elongation by grain refinement. In this study, bending and tension deformations were performed on rolled ZEK100 alloy sheets, and the effects of these deformations on the texture formation and room-temperature stretch formability of the specimens were investigated.
Commercial ZEK100 alloy rolled sheets with a thickness of 1.2 mm, a width of 63 mm, and a length of 165 mm were prepared as starting materials, in which the longitudinal direction was set to the RD. The configuration of the die is shown in Fig. 1. The bending angle of the die, the curvature radius of the punch, and the working speed of the specimens were set to 45°, 5 mm, and 100 mm·s−1, respectively; machine oil was used as a lubricant. The bending and tension deformations were repeated up to 7-pass, in which the work direction of each bending and tension deformations was set to unidirectional, and the sheet was not turned back after each repetition of bending and tension deformations. In this paper, the specimen subjected to n-pass bending and tension deformations was denoted as “n-pass specimen”. Heat treatment at 573 K for 10 min was conducted after each repetition of bending and tension deformations, and heat treatment at 623 K for 60 min was carried out after the final round of bending and tension deformations.
The (0002) pole figures of the specimens in the RD–TD plane were measured through X-ray analysis (Schulz reflection method) using Rigaku RINT Ultima 2000. Micro-texture analysis was performed via scanning electron microscopy and electron back-scattered diffraction (SEM-EBSD) using a JEOL SEM (JSM-5910) equipped with a TSL OIM data collection system. EBSD analysis was carried out on the RD–ND planes of the specimen preliminary etched with argon ion shower by ELIONIX EIS-200ER. The orientation was rotated to obtain the same observation direction as that of the X-ray texture analysis.
A circular blank with a diameter of 60 mm and a thickness of 1.1 mm was machined from the specimens, and Erichsen tests using a hemispherical punch with a diameter of 20 mm were carried out at room temperature to investigate the stretch formability of the specimens. The punch speed and blank holder force were set to 5 mm/min and 10 kN, respectively. Graphite grease was used as a lubricant. The above experimental conditions were based on Japan industrial standards (JIS) B7729 [25] and Z2247 [26].
Tensile specimens with 12 mm gage length, 4 mm gage width, and 1.2 mm gage thickness were machined from the specimen. Tensile tests at room temperature were carried out with an initial strain rate of 2.8 × 10−3 s−1 by using an Instron universal testing machine (model 5565), in which the tensile direction was set to parallel (RD) and perpendicular (TD) to the RD, respectively. Additional tensile tests were conducted to investigate the Lankford value (r-value), in which the longitudinal and width strains were measured using the specimens deformed to 9% plastic strain.
The results of the Erichsen tests of the ZEK100 alloy sheets subjected to bending and tension deformations are summarized in Fig. 2. The 0-pass specimen, which was not subjected to bending and tension deformations, exhibited a high Erichsen value of 7.6 mm because of the appearance of the TD-split texture as described in Section 3.2. The Erichsen value significantly increased from 7.6 to 9.0 mm after 1-pass bending and tension deformations. Furthermore, increasing pass number of bending and tension deformations up to 3-pass contributed to a monotonous increase in the Erichsen value up to 9.6 mm. The Erichsen value of 9.6 mm in the 3-pass specimen was considerably higher than those (3–5 mm) of common AZ31B alloy sheets, and it was one of the highest values among the results of previous reports, in which the Erichsen test was adopted in accordance with JIS standards [27]. However, more than 3-pass bending and tension deformations did not contribute to further increasing the Erichsen value, and deterioration of the Erichsen value was observed in the 7-pass specimen.
Tensile properties of the specimens subjected to bending and tension deformations are summarized in Table 1. In the RD, despite the presence of some scattering, the 0.2% proof stress (YS) decreased with increasing pass number of bending and tension deformations, whereas the fracture and uniform elongations increased. In the TD, no pronounced change was observed with an increasing pass number of deformations. The strain hardening exponent and r-value are indexes of elongation and thinning of specimens, respectively, and the Erichsen value increases with increasing strain hardening exponent and decreasing r-value. The strain hardening exponent for both directions increased after bending and tension deformations. The r-value decreased in the RD and increased in the TD with increasing pass number of deformations. The lowest r-value anisotropy was obtained at the 3-pass specimen, in which the highest Erichsen value was obtained.
| Sample | YS / MPa | UTS / MPa | FE / % | Strain hardening exponent | UE / % | r-value | |||||||||||
| RD | TD | RD | TD | RD | TD | RD | TD | RD | TD | RD | TD | ||||||
| 0-pass | 223 | 112 | 257 | 228 | 20.7 | 34.9 | 0.08 | 0.27 | 6.3 | 21.7 | 0.76 | 0.53 | |||||
| 1-pass | 152 | 92 | 235 | 220 | 25.4 | 36.1 | 0.18 | 0.37 | 12.6 | 21.6 | 0.70 | 0.60 | |||||
| 3-pass | 151 | 93 | 231 | 223 | 28.1 | 32.2 | 0.17 | 0.36 | 13.3 | 21.3 | 0.62 | 0.65 | |||||
| 5-pass | 139 | 94 | 228 | 224 | 28.5 | 33.8 | 0.18 | 0.34 | 13.4 | 21.9 | 0.48 | 0.71 | |||||
| 7-pass | 145 | 100 | 229 | 227 | 30.1 | 33.6 | 0.18 | 0.32 | 14.1 | 20.3 | 0.46 | 0.76 | |||||
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Fig. 3 shows the representative stress–strain curves and work hardening curves obtained by the tensile tests. The YS in the TD exhibited a considerably lower value compared with that in the RD at all pass numbers of deformations. Furthermore, the work hardening behavior in the TD was linear. Concerning the work hardening curves in the TD, the work hardening rate initially decreased, increased once, and then decreased again. The increase in work hardening coefficient and the increase in work hardening rate suggest a generation of tension twinning [28–31]. Thus, the variation in work hardening coefficient and work hardening rate may imply an occurrence of tension twinning. By contrast, the above work hardening behaviors were not observed in the RD.
The (0002) plane pole figures of the specimens with and without bending and tension deformations are shown in Fig. 4. When the specimen was subjected to bending and tension deformations, tension and compression deformations were imposed on the surface of the tension side (T-side) and compression side (C-side), respectively. Thus, the textures of both surfaces machined by 0.1 mm were measured. The specimen without bending and tension deformation exhibited a typical TD-split texture shown in Mg–Zn–RE alloys, in which the basal pole was inclined to approximately 40° from the ND to the TD. In the 1-pass specimen, a concentric texture was observed on both surfaces, followed by an inclination of the basal pole toward the RD. The inclination angle of the basal pole increased with increasing pass number of deformations, and a clear RD-split texture formed on the specimen subjected to more than 3-pass deformations, accompanied by an increase in the basal texture intensity. In specific, a high texture intensity of 11.3 was obtained in the 7-pass specimen. Noguchi et al. [19] conducted the bending and tension deformations of AZ31B alloy sheets with an initial basal texture intensity of 7.7, and they reported that the basal texture intensity increased up to 17.4 after 7-pass deformations. The increase in basal texture intensity after bending and tension deformations was smaller for the ZEK100 alloy sheets than the AZ31B alloy sheets. The basal texture intensity of commercial AZ31B alloy sheets is approximately 10–20 [32]. Rolled Mg–Zn–RE sheets exhibit a TD-split texture and a weak basal texture intensity [9–10]. These results indicate that the formation of a strong basal texture is suppressed when not only rolling but also bending and tension deformations are applied to the sheet production of Mg–Zn–RE alloys.
The relationship between the stretch formability and texture distribution of the specimens subjected to bending and tension deformations was then analyzed. The 1-pass specimen exhibited a symmetric texture. However, the 1-pass specimen exhibited a lower Erichsen value than the 3-pass and 5-pass specimens. Thus, the excellent Erichsen value shown in the 3-pass specimen cannot be explained by the texture distribution shown in Fig. 4.
Fig. 5 shows the texture profiles along with the ND of the 7-pass specimen. The component of the TD-split texture remained at the quarter layers (x = ±0.3 mm), resulting in the concentric texture distribution, which was also observed on the surface of the 1-pass specimen, as shown in Fig. 4. Moreover, a clear TD-split texture remained at the center (x = 0.0 mm) of the 7-pass specimen. These results imply that the RD-split texture was developed from the surface to the center of the specimen as the pass number of deformations increased. This phenomenon explains the lower Erichsen value of the 1-pass specimen than that of the 3-pass specimen.
Fig. 6 shows the basal pole figures measured by SEM-EBSD in the RD–ND plane, which roughly corresponds to the average texture through the thickness. The 0-pass and 1-pass specimens showed a typical TD-split texture, and the components of the RD-split texture developed with increasing pass number of deformations. In the 7-pass specimen, the quadrupole texture was observed. Concerning the basal texture intensity, no clear difference was observed between the specimens with and without bending and tension deformations. The texture developments shown in Fig. 6 suggest that the quadrupole texture was macroscopically developed with an increase in the pass number of the bending and tension deformations.
Microstructures of the specimens without and with bending and tension deformations were measured using SEM-EBSD to elucidate the reason for the enhancement in room-temperature stretch formability. The results are summarized in Fig. 7. In the 1-, 3-, and 7-pass specimens, coarse grains were distributed from near the surface to the quarter layer in the ND, and the region with coarse grains increased with increasing pass number of deformations. Coarser grains were observed on the C-side than on the T-side. The specimen subjected to bending deformation has a large strain anisotropy between the surface and center of the sheet because the maximum tension and compression strains are imposed on the T-side and C-side, respectively, and no strain is imposed on the center of the sheet [17]. Thus, microstructural changes occurred near the surface. For example, coarse grains are recrystallized near the surface region, where the strain energy is stored with graded distribution toward the ND in the case of Al alloy sheets subjected to bending deformation [33]. Thus, the coarse grains observed in the ZEK100 alloy sheets subjected to bending and tension deformations recrystallized similarly to those in the Al alloys subjected to bending deformations. In our previous study, recrystallization of coarse grains near the surface was observed in AZ31B alloy sheets subjected to bending and tension deformations, and coarse grains often exhibited the same orientation as the components of RD-split texture [19–20]. This result indicates that grain growth with the same orientation as the components of RD-split texture occurs not only in AZ31B alloy sheets but also in ZEK100 alloy sheets subjected to bending and tension deformations.
Fig. 8(a) shows the average Schmid factor of the basal slip calculated from the results of SEM-EBSD, in which a tensile stress was applied to the RD, TD, and ±45° inclined from the RD. A high Schmid factor indicates that applied stress can be largely resolved to the activation of basal slip. Thus, the high Schmid factor toward the RD and TD is strongly related to the enhancement of ductility (decrease in yield stress) toward the RD and TD, respectively. When a tensile stress was applied to ±45° inclined from the RD, the Schmid factor exhibited a high value independent of the pass number of bending and tension deformations. When a tensile stress was applied to the RD, the Schmid factor was almost monotonously increased with increasing pass number of deformations. Conversely, when a tensile stress was applied to the TD, the Schmid factor slightly decreased with increasing pass number of deformations. The tendencies of the Schmid factor variation in the RD and TD qualitatively corresponded to the variation in the YS obtained by the tensile tests, as shown in Table 1. The monotonic increase in Schmid factor to the RD and the slight decrease in Schmid factor to the TD imply that the ductility and formability of the specimen may be improved with an increase in the pass number of the deformation.
Fig. 8(b) shows the profiles of the average Schmid factor of the basal slip along the ND of the 1-, 3-, and 7-pass specimens measured by SEM-EBSD. When a tensile stress was applied to the RD, the Schmid factor showed a large variation in the ND and exhibited a maximum value near the surface, especially with the large pass numbers. Conversely, when a tensile stress was applied to the TD, the Schmid factor did not show a relatively large variation.
Figs. 9 and 10 show the histogram and related mapping of the Schmid factor when a tensile stress was applied to the TD and RD, respectively. When a tensile stress was applied to the TD, a large proportion of grains exhibited a high Schmid factor around 0.4–0.5, although a slight decrease was observed with an increase in the pass number of deformations. By contrast, when a tensile stress was applied to the RD, a low proportion of grains with a high Schmid factor around 0.4–0.5 was observed in the specimen without deformation, and the proportion of grains with a high Schmid factor increased with increasing pass number of deformations. Concerning the related mapping of the Schmid factor, when a tensile stress was applied to the TD, grains with a high Schmid factor of approximately 0.4–0.5 were distributed throughout the specimen, and the proportion of coarse grains with a low Schmid factor (<0.2) increased with increasing pass number of deformations around the surface. By contrast, when a tensile stress was applied to the RD, an opposite tendency was observed, in which the proportion of coarse grains with a high Schmid factor of approximately 0.4–0.5 increased with increasing pass number of deformations around the surface. Figs. 9 and 10 indicate that the specimens with the components of an RD-split texture, such as the 7-pass specimen, exhibited grains with a high Schmid factor near the surface when a tensile stress was applied to the RD, and the specimen with the components of a TD-split texture, such as the 1-pass specimen, exhibited grains with a high Schmid factor near the surface when a tensile stress was applied to the TD.
As shown in Fig. 6, in the 7-pass specimen, an RD-split texture formed near the surface and a TD-split texture remained in the center. Thus, the quadrupole texture could be macroscopically formed. In other words, the quadrupole texture shown in Fig. 6 can be expressed as a spatially graded texture, in which the RD-split texture gradually changed to the TD-split texture through the thickness from the surface to the center. He et al. [24] reported that AZ31 alloys processed by in-plane pre-compression, pre-stretching, and annealing exhibited good stretch formability, suggesting that the formation of RD-split and TD-split textures contributes to the reduction of anisotropy in the Schmid factor, resulting in enhanced room-temperature formability. Thus, the reduction in anisotropy of the Schmid factor attained by the formation of quadrupole texture is suggested to be the main reason for the improvement in stretch formability of ZEK100 alloy sheets subjected to bending and tension deformations. Conversely, the 7-pass specimen exhibited a lower Erichsen value than the 3-pass specimen, regardless that the anisotropy between the Schmid factors in the RD and the TD was lower in the 7-pass specimen than in the 3-pass specimen. Thus, the stretch formability deterioration of the 7-pass specimen cannot be explained in terms of the Schmid factor anisotropy.
The surface profile around the fractured site after the Erichsen tests was investigated to clarify the reason for the deterioration of stretch formability of the 7-pass specimen. The results are summarized in Fig. 11. A pronounced uneven surface formed on the 7-pass specimen. Fig. 12 shows the average grain size on the surface (C-side and T-side), center part, and all-region measured by SEM-EBSD. The average grain size in the all-region monotonically increased with an increasing pass number of deformations, whereas a small change in the grain size in the central region was observed. By contrast, an increase in grain size was observed at the T-side and C-side similar to that at the all-region, in which the grain size at the C-side was considerably larger than that at the T-side.
Koike et al. [34] pointed out that the activity of prismatic <a> slip exhibits a strong dependence on grain size; in the case of the coarse grain size, the activity of the prismatic <a> slip is restricted only to the grain boundary vicinity. Thus, microstructure with coarse grain size often deteriorates the room-temperature formability of Mg alloy sheets. Chino et al. [35] suggested that the coarse grain size promotes an increase in the frequency of twinning, leading to a large plastic anisotropy and inducing the deterioration of ductility. The generation of
In our previous study, the stretch formability of the AZ31B alloy sheets subjected to bending and tension deformations deteriorated because of the formation of coarse grains near the surface [20]. A series of experiments indicated that excessive repetition of bending and tension deformations induces grain coarsening near the surface and deteriorates the room-temperature stretch formability independent of alloy compositions. By contrast, grains with a high Schmid factor for RD tension form at the region of coarse grains near the surface. Therefore, optimizing the pass number of bending and tension deformations aiming to minimize grain coarsening and maximize grains with a high Schmid factor is essential to enhance room-temperature formability in Mg alloy sheets.
Bending and tension deformations were conducted to ZEK100 alloy sheets, which initially exhibited a TD-split texture, and the effects of these deformations on the texture formation and room-temperature stretch formability were investigated. The results are summarized as follows.
(1) The Erichsen value significantly increased from 7.6 to 9.0 mm by 1 pass bending and tension deformations. Furthermore, increasing the pass number up to 3-pass contributed to the increase in Erichsen value up to 9.6 mm. However, the Erichsen value deteriorated in the specimen subjected to 7-pass bending and tension deformations.
(2) The RD-split texture developed on the surface of the specimen subjected to bending and tension deformations. By contrast, a clear TD-split texture remained at the center even in the specimen subjected to 7-pass deformations. As a result, a quadrupole texture, which was expressed as spatially graded texture through the thickness, was macroscopically developed.
(3) In the specimen subjected to bending and tension deformations, coarse grains formed near the surface, and the region with coarse grains increased with increasing pass number of deformations. The coarse grains often showed the same orientation as the components of the RD-split texture, which exhibited a high Schmid factor when a tensile stress was applied to the RD. The anisotropy of the Schmid factor decreased with increasing pass number of deformation. The reduction of anisotropy in the Schmid factor is suggested to be the reason for the improvement in the stretch formability of ZEK100 alloy sheets subjected to bending and tension deformations.
(4) The generation of coarse grains near the surface followed by bending and tension deformations was the direct cause for the deterioration in stretch formability of the specimen subjected to 7-pass bending and tension deformations.
The authors have no conflict associated with this manuscript.
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Figures(12) / Tables(1)
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| Sample | YS / MPa | UTS / MPa | FE / % | Strain hardening exponent | UE / % | r-value | |||||||||||
| RD | TD | RD | TD | RD | TD | RD | TD | RD | TD | RD | TD | ||||||
| 0-pass | 223 | 112 | 257 | 228 | 20.7 | 34.9 | 0.08 | 0.27 | 6.3 | 21.7 | 0.76 | 0.53 | |||||
| 1-pass | 152 | 92 | 235 | 220 | 25.4 | 36.1 | 0.18 | 0.37 | 12.6 | 21.6 | 0.70 | 0.60 | |||||
| 3-pass | 151 | 93 | 231 | 223 | 28.1 | 32.2 | 0.17 | 0.36 | 13.3 | 21.3 | 0.62 | 0.65 | |||||
| 5-pass | 139 | 94 | 228 | 224 | 28.5 | 33.8 | 0.18 | 0.34 | 13.4 | 21.9 | 0.48 | 0.71 | |||||
| 7-pass | 145 | 100 | 229 | 227 | 30.1 | 33.6 | 0.18 | 0.32 | 14.1 | 20.3 | 0.46 | 0.76 | |||||
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