JP7497007B2 - Cu-Al-Mn alloy - Google Patents

Description

The present invention relates to a Cu-Al-Mn alloy.

Conventionally, the present inventors have developed Cu-Al-Mn alloys that exhibit a high shape memory effect and stable superelasticity while maintaining excellent workability (see, for example, Patent Documents 1 to 6 or Non-Patent Documents 1 to 3). Tensile tests of these alloys have shown that, for example, a Cu-8.07 wt% Al-9.68 wt% Mn-0.51 wt% Co alloy has a maximum elastic strain of about 0.1% and an elastic limit of 210 MPa (see, for example, Patent Document 1), a Cu-8.1 wt% Al-10.7 wt% Mn alloy has a maximum elastic strain of about 1% and an elastic limit of 190 MPa (see, for example, Patent Document 2), and a unidirectionally solidified Cu-17.5Al-11Mn alloy (at%) has a maximum elastic strain of about 1% and an elastic limit of 200 MPa (see, for example, Patent Document 3). A large elastic strain amount and an elastic limit of about 140 MPa (see, for example, Non-Patent Document 1), a single crystal of Cu-17Al-15Mn alloy (at%) has a maximum elastic strain amount of about 0.8% and an elastic limit of about 410 MPa at -113°C (see, for example, Non-Patent Document 2), and a unidirectionally solidified material of Cu-17.5Al-11Mn alloy (at%) has a maximum elastic strain amount of about 0.5% and an elastic limit of about 80 MPa (see, for example, Non-Patent Document 3). Note that the maximum elastic strain amount is the maximum value of strain in the range showing elastic deformation.

JP 2003-138330 A International Publication No. WO2011/152009 JP 2000-169920 A JP 2001-20026 A JP 2014-58737 A JP 2015-54977 A

S. Xu, H. Y. Huang, J. Xie, S. Takekawa, X. Xu, T. Omori, and R. Kainuma, “Giant elastocaloric effect covering wide temperature range in columnar-grained Cu71.5Al17.5Mn11 shape memory alloy”, APL. Materials, 2016, 4, 106106 K. Niitsu, Y. Kimura, T. Omori and R. Kainuma, “Cryogenic superelasticity with large elastocaloric effect”, NPG Asia Materials, 2018, 10, e457 S. Xu, T. Kusama, X. Xu, H. Huang, T. Omori, J. Xie, R. Kainuma, “Large [001] single crystals via abnormal grain growth from columnar polycrystal”, Materialia, 2019, 6, 100336

Most Cu-Al-Mn alloys, such as those described in Patent Document 1 and Non-Patent Documents 1 to 3, have a maximum elastic strain of approximately 1% or less. Thus, no Cu-Al-Mn alloys with a maximum elastic strain of more than 1% have been found to date, and from the perspective of expanding the range of applications, there has been a demand for the development of Cu-Al-Mn alloys with a larger maximum elastic strain.

The present invention was made with a focus on these issues, and aims to provide a Cu-Al-Mn alloy with a larger maximum elastic strain.

In order to achieve the above object, the Cu-Al-Mn alloy according to the present invention is characterized in that it contains 14 at% to 22 at% Al, 5 at% to 14.5 at% Mn, and 0.001 at% to 10 at% Ni, with the balance being Cu and unavoidable impurities, and has a maximum elastic strain of 1.5% or more. Alternatively, the Cu-Al-Mn alloy according to the present invention is characterized in that it contains 14 at% to 22 at% Al, 5 at% to 14.5 at% Mn, with the balance being Cu and unavoidable impurities, has a maximum elastic strain of 1.5% or more, is single crystal, and has a crystal orientation in the deformation direction of the crystal grains measured by electron backscatter diffraction (EBSD) that has a deviation angle from the crystal orientation <100> within a range of 0° to 30° . Alternatively, the Cu-Al-Mn alloy according to the present invention is characterized in that it contains 14 at% to 22 at% Al, 5 at% to 14.5 at% Mn, with the remainder being Cu and unavoidable impurities, has a maximum elastic strain of 1.5% or more, is polycrystalline, and has a crystal orientation in the deformation direction, as measured by electron backscatter diffraction (EBSD), with a deviation angle from the crystal orientation <100> within a range of 0° to 30°.

The Cu-Al-Mn alloy of the present invention has a large maximum elastic strain of 1.5% or more and a wide elastic deformation range. The Young's modulus can also be reduced to 50 GPa or less. For this reason, it can be used as a material that must be able to elastically deform even when subjected to a relatively large strain, such as a spring material or a biomaterial, or a material that must have a low Young's modulus.

In the Cu-Al-Mn alloy of the present invention, when Al is less than 14 at%, the α phase appears and the elastic deformation region becomes narrow. When Al is more than 22 at%, the alloy becomes extremely brittle and the elastic deformation region becomes narrow. When Mn is less than 5 at%, the α phase appears and the elastic deformation region becomes narrow. When Mn is more than 14.5 at%, the elastic modulus becomes high and the elastic deformation region becomes narrow.

The Cu-Al-Mn alloy according to the present invention is particularly preferably one in which the Al is 16 at% to 21 at% and the Mn is 7 at% to 14.5 at%. In this case, the maximum elastic strain can be made larger, for example, the maximum elastic strain can be made 3% or more.

The Cu-Al-Mn alloy according to the present invention may further contain 0.001 at% to 10 at% Ni. In this case, the inclusion of Ni can strengthen the matrix structure, but if the Ni content is more than 10 at%, the hardenability decreases. The Cu-Al-Mn alloy according to the present invention is preferably made of a single crystal, but may be made of polycrystals. If it is made of polycrystals, it is preferable that the <100> crystal orientation is oriented in the deformation direction, and for example, it is preferable that 50% or more of the crystal orientations in the deformation direction of the crystal grains measured by the electron backscatter diffraction (EBSD) method have a deviation angle from the <100> crystal orientation within the range of 0° to 30°. In the Cu-Al-Mn alloy according to the present invention, the crystal grain size is preferably equal to or larger than the cross-sectional size of the material. For example, in the case of a plate material, it is preferable that the crystal grain size is equal to or larger than the plate thickness, and it is even more preferable that the crystal grain size is equal to or larger than the plate width.

The present invention provides a Cu-Al-Mn alloy with a larger maximum elastic strain.

1 is a graph showing a stress-strain curve of a single crystal of a Cu-17Al-14Mn alloy (at %), which is a Cu-Al-Mn based alloy according to an embodiment of the present invention. 1 is a processing process chart showing the manufacturing steps of (a) a fine crystal grain sample and (b) a coarse crystal grain sample of a Cu-17Al-13.5Mn-3Ni alloy (at %), which is a Cu-Al-Mn based alloy according to an embodiment of the present invention. FIG. 1 shows an inverse pole figure orientation map (left, shown in black and white) and an inverse pole figure (right) showing crystal orientations in (a) RD, (b) TD, and (c) ND of a fine crystal grain sample of a Cu-17Al-13.5Mn-3Ni alloy (at %), which is a Cu-Al-Mn alloy according to an embodiment of the present invention; (d) an inverse pole figure orientation map (upper left, shown in black and white) showing crystal orientation in MD; a map showing crystal grains that are within 30° of the <001> orientation (upper left), and an inverse pole figure (right). FIG. 1 shows an inverse pole figure orientation map (left, shown in black and white) and an inverse pole figure (right) showing crystal orientation in (a) RD, (b) TD, and (c) ND of a coarse crystal grain sample of a Cu-17Al-13.5Mn-3Ni alloy (at %), which is a Cu-Al-Mn alloy according to an embodiment of the present invention; (d) an inverse pole figure orientation map (upper left, shown in black and white) showing crystal orientation in MD; a map (lower left, shown in black and white) showing crystal grains that are within 30° of the <001> orientation; and an inverse pole figure (right) of the same. 1 is a graph showing stress-strain curves of (a) a fine crystal grain sample and (b) a coarse crystal grain sample of a Cu-17Al-13.5Mn-3Ni alloy (at %), which is a Cu-Al-Mn based alloy according to an embodiment of the present invention;

Hereinafter, the embodiment of the present invention will be described based on examples.
The Cu-Al-Mn alloy according to the embodiment of the present invention contains 14 at% to 22 at% Al, 5 at% to 14.5 at% Mn, and the balance is Cu and unavoidable impurities, and has a maximum elastic strain of 1.5% or more.

In addition, the Cu-Al-Mn alloy according to the embodiment of the present invention preferably contains 16 at% to 21 at% Al. It is particularly preferable that the Mn content is 7 at% to 14.5 at%. The alloy may further contain 0.001 at% to 10 at% Ni. The Cu-Al-Mn alloy according to the embodiment of the present invention is preferably made of a single crystal, but may be made of polycrystals. If it is made of polycrystals, it is preferable that the <100> crystal orientation is oriented in the deformation direction. The crystal orientation can be achieved by a combination of unidirectional solidification and thermomechanical treatment.

A Cu-17Al-14Mn alloy (at%) was produced and subjected to a tensile test. The Cu-17Al-14Mn alloy was produced as follows. First, an alloy having a composition of Cu; 69 at%, Al; 17 at%, Mn; 14 at% was melted and cast into a mold to produce an ingot. The ingot was remelted and cast in a unidirectional solidification furnace equipped with a water-cooled copper mold and a heater to produce a unidirectionally solidified ingot of 150 mm x 80 mm x 40 mm. Then, a test piece of 1 mm x 10 mm x 50 mm was cut out so that the longitudinal direction was the solidification direction. This test piece was cooled from 900 ° C to 450 ° C at 3 ° C / min, and further heated to 900 ° C at 10 ° C / min., and the cooling and heating cycle heat treatment was repeated 23 times, and then it was solution treated at 900 ° C for 3 hours and quenched by putting it into water.

In this way, a plate-shaped Cu-17Al-14Mn alloy sample was produced, measuring 50 mm in length, 10 mm in width, and 1 mm in thickness. The produced Cu-17Al-14Mn alloy sample was a single crystal, with a crystal orientation relative to the solidification direction being the <100> orientation.

A tensile test was performed on the manufactured Cu-17Al-14Mn alloy sample. The tensile direction was the solidification direction. The tensile test was performed by repeatedly applying and releasing a tensile load up to 400 MPa, then up to 450 MPa, and then up to 500 MPa, increasing the upper limit stress by 50 MPa each time. The stress-strain curve obtained from this tensile test is shown in Figure 1.

As shown in Figure 1, the sample broke at a stress of 612 MPa, but up until then, the sample moved along almost the same curve by repeatedly applying and releasing a tensile load, and it was confirmed that the sample was elastically deformed. Also, as shown in Figure 1, it was confirmed that the engineering strain was 3.58% when the engineering stress was 550 MPa, and 4.31% when the stress was 600 MPa. It was also confirmed that the maximum elastic strain of the sample was 4.31%. It was also confirmed that the slope of the stress-strain curve gradually decreased as the strain increased, and that the Young's modulus changed. It was confirmed that the apparent Young's modulus at a strain of 3.58%, that is, the Young's modulus when the range from the origin to a strain of 3.58% is considered to be linear, was 15.4 GPa, and the apparent Young's modulus at a strain of 4.31% was 14 GPa.

Two types of Cu-17Al-13.5Mn-3Ni alloys (at%) were produced and tensile tests were performed. Each Cu-17Al-13.5Mn-3Ni alloy was produced by the process shown in Figures 2(a) and (b), respectively. In each process, first, an alloy with a composition of Cu; 66.5 at%, Al; 17 at%, Mn; 13.5 at%, Ni; 3 at% was melted and cast into a mold to produce an ingot with a diameter of 34 mm.

In the process shown in FIG. 2(a), the ingot was hot rolled at 900°C to be processed into a plate shape, and then air cooled. The plate thickness at this time was 5.8 mm. Next, annealing was performed at 500°C for 60 minutes, quenched in water, and cold rolling was performed to further process it into a thinner plate shape. The plate thickness at this time was 3.3 mm, and the rolling ratio was 43.1%. Annealing was performed again at 600°C for 60 minutes, quenched in water, and cold rolling was performed to further process it into a thinner plate shape. The plate thickness at this time was 1.6 mm, and the rolling ratio was 51.5%. Annealing was performed again at 600°C for 60 minutes, quenched in water, and cold rolling was performed to further process it into a thinner plate shape. The plate thickness at this time was 1.0 mm, and the rolling ratio was 37.5%. The specimen was again annealed at 500°C for 30 minutes, quenched in water, and cold rolled to form a thinner plate. The plate thickness was 0.4 mm, and the reduction ratio was 60%. The reduction ratio of the four cold rolling processes was 93.1%. Finally, the specimen was heated to 800°C at 3.3 K/min, heat-treated at 800°C for 10 minutes, and quenched in water. In this way, a polycrystalline Cu-17Al-13.5Mn-3Ni alloy specimen with fine grains (hereinafter also referred to as a "fine grain specimen") was produced.

In the process shown in FIG. 2(b), the ingot with a diameter of 34 mm was hot-rolled at 900°C to be processed into a plate shape, and then air-cooled. The plate thickness at this time was 5.8 mm. Next, annealing was performed at 500°C for 60 minutes, quenched in water, and cold-rolled to be processed into a thinner plate shape. The plate thickness at this time was 3.3 mm, and the rolling ratio was 43.1%. Annealing was performed again at 600°C for 60 minutes, quenched in water, and cold-rolled to be processed into a thinner plate shape. The plate thickness at this time was 1.6 mm, and the rolling ratio was 51.5%. Annealing was performed again at 500°C for 30 minutes, quenched in water, and cold-rolled to be processed into a thinner plate shape. The plate thickness at this time was 0.4 mm, and the rolling ratio was 75%. The reduction ratio of the three cold rollings up to this point was 93.1%. Finally, the sample was heated to 800°C at 0.5 K/min, heat-treated at 800°C for 10 minutes, and then quenched in water. In this way, a polycrystalline Cu-17Al-13.5Mn-3Ni alloy sample with coarse crystal grains (hereinafter also referred to as the "coarse crystal grain sample") was produced.

Crystal orientation analysis was performed using the EBSD method on the fine grain sample manufactured by the process in Figure 2(a) and the coarse grain sample manufactured by the process in Figure 2(b). The obtained inverse pole figure orientation map and inverse pole figure are shown in Figures 3 and 4, respectively. Note that the RD (rolling direction) shown in Figures 3 and 4 is the rolling direction, the TD (transverse direction) is the direction perpendicular to the rolling direction in the rolling plane, the ND (normal direction) is the normal direction to the rolling plane, and the MD is the direction at 45 degrees to the RD in the rolling plane.

In the fine grain sample, as shown in Figure 3, it was confirmed that the grain size of about half of the grains was almost the same as or larger than the sheet thickness of 0.4 mm. In addition, as shown in Figure 3(d), it was confirmed that 70.9% of the grains measured by MD had a deviation angle from the crystal orientation <100> within the range of 0° to 30°, and the crystal orientation <100> was aligned in the rolling direction. In the coarse grain sample, as shown in Figure 4, it was confirmed that the grain size of most of the grains was larger than the sheet thickness of 0.4 mm. In addition, as shown in Figure 4(d), it was confirmed that 87.9% of the grains measured by MD had a deviation angle from the crystal orientation <100> within the range of 0° to 30°, and the crystal orientation <100> was aligned in the rolling direction.

Next, a tensile test was performed on the fine grain sample produced by the process in FIG. 2(a) and the coarse grain sample produced by the process in FIG. 2(b). The tensile direction was MD. The tensile test was performed by repeatedly pulling the sample to a strain of 0.5%, then pulling it to a strain of 1.0%, and then pulling it to a strain of 1.5%, and so on, increasing the upper limit strain by 0.5% each time and deforming it to zero load. The stress-strain curves obtained by this tensile test are shown in FIG. 5(a) and (b), respectively.

As shown in Figure 5(a), the fine crystal grain sample was broken at a stress of 621 MPa. However, it was confirmed that up until that point, the curve shifted slightly when the tensile load was applied and released repeatedly, but the sample was mostly elastically deformed. It was also confirmed that the maximum elastic strain of the fine crystal grain sample was 2.40%. It was also confirmed that as the strain increased, the slope of the stress-strain curve gradually became smaller, indicating a change in Young's modulus. It was confirmed that the apparent Young's modulus at a strain of 1.5% was 29 GPa.

As shown in Figure 5(b), the coarse grain sample was broken at a stress of about 600 MPa. However, it was confirmed that up until that point, the curve shifted slightly when the tensile load was applied and released repeatedly, but the sample was still largely elastically deformed. It was also confirmed that the maximum elastic strain of the coarse grain sample was about 3.25%. It was also confirmed that as the strain increased, the slope of the stress-strain curve gradually became smaller, indicating a change in Young's modulus. It was confirmed that the apparent Young's modulus at a strain of 2.5% was 21 GPa.

A Cu-14.5Al-14.5Mn alloy (at%) was manufactured and subjected to a tensile test. This alloy was manufactured by the method shown in FIG. 2(a) of Example 2. The manufactured alloy sample was subjected to crystal orientation analysis by the EBSD method in the same manner as in Example 2. As a result, it was confirmed that 91.0% of the crystal grains measured by MD had a deviation angle from the crystal orientation <100> orientation within the range of 0° to 30°, and that the crystal orientation <100> orientation was aligned in the rolling direction. In addition, a tensile test was performed on the manufactured alloy sample in the same manner as in Example 2. As a result, it was confirmed that the alloy was almost elastically deformed until it was broken, that the maximum elastic strain was 2.50%, and that the apparent Young's modulus was 22 GPa.

A Cu-15Al-14Mn alloy (at%) was manufactured and subjected to a tensile test. This alloy was manufactured by the method shown in FIG. 2(a) of Example 2. The manufactured alloy sample was subjected to crystal orientation analysis by EBSD method in the same manner as in Example 2. As a result, it was confirmed that 90.2% of the crystal grains measured by MD had a deviation angle from the crystal orientation <100> orientation within the range of 0° to 30°, and the crystal orientation <100> orientation was aligned in the rolling direction. In addition, a tensile test was performed on the manufactured alloy sample in the same manner as in Example 2. As a result, it was confirmed that the alloy was almost elastically deformed until it was broken, the maximum elastic strain was 2.95%, and the apparent Young's modulus was 22 GPa.

A Cu-19Al-8Mn alloy (at%) was manufactured and subjected to a tensile test. This alloy was manufactured by the method shown in FIG. 2(a) of Example 2. The manufactured alloy sample was subjected to crystal orientation analysis by the EBSD method in the same manner as in Example 2. As a result, it was confirmed that 55.3% of the crystal grains measured by MD had a deviation angle from the crystal orientation <100> within the range of 0° to 30°, and that the crystal orientation <100> was aligned in the rolling direction. In addition, a tensile test was performed on the manufactured alloy sample in the same manner as in Example 2. As a result, it was confirmed that the alloy was almost elastically deformed until it was broken, that the maximum elastic strain was 1.98%, and that the apparent Young's modulus was 48 GPa.

A Cu-21Al-7Mn alloy (at%) was manufactured and subjected to a tensile test. This alloy was manufactured by the method shown in FIG. 2(a) of Example 2. The manufactured alloy sample was subjected to crystal orientation analysis by the EBSD method in the same manner as in Example 2. As a result, it was confirmed that 50.0% of the crystal grains measured by MD had a deviation angle from the crystal orientation <100> orientation within the range of 0° to 30°, and the crystal orientation <100> orientation was aligned in the rolling direction. In addition, a tensile test was performed on the manufactured alloy sample in the same manner as in Example 2. As a result, it was confirmed that the alloy was almost elastically deformed until it was broken, with a maximum elastic strain of 1.70% and an apparent Young's modulus of 49 GPa.

A Cu-17Al-10.5Mn-1Ni alloy (at%) was manufactured and subjected to a tensile test. This alloy was manufactured by the method shown in FIG. 2(a) of Example 2. The manufactured alloy sample was subjected to crystal orientation analysis by the EBSD method in the same manner as in Example 2. As a result, it was confirmed that 68.4% of the crystal grains measured by MD had a deviation angle from the crystal orientation <100> orientation within the range of 0° to 30°, and that the crystal orientation <100> orientation was aligned in the rolling direction. In addition, a tensile test was performed on the manufactured alloy sample in the same manner as in Example 2. As a result, it was confirmed that the alloy was almost elastically deformed until it was broken, that the maximum elastic strain was 2.02%, and that the apparent Young's modulus was 30 GPa.

A Cu-21Al-6.3Mn-6Ni alloy (at%) was manufactured and subjected to a tensile test. This alloy was manufactured by the method shown in FIG. 2(a) of Example 2. The manufactured alloy sample was subjected to crystal orientation analysis by the EBSD method in the same manner as in Example 2. As a result, it was confirmed that 62.8% of the crystal grains measured by MD had a deviation angle from the crystal orientation <100> orientation within the range of 0° to 30°, and that the crystal orientation <100> orientation was aligned in the rolling direction. In addition, a tensile test was performed on the manufactured alloy sample in the same manner as in Example 2. As a result, it was confirmed that the alloy was almost elastically deformed until it was broken, with a maximum elastic strain of 1.61% and an apparent Young's modulus of 45 GPa.

[Comparative Example 1]
As a comparative example, a Cu-6.2Al-12.1Mn alloy (at%) was manufactured and subjected to a tensile test. This alloy was manufactured by the method shown in FIG. 2(a) of Example 2. The manufactured alloy sample was subjected to crystal orientation analysis by the EBSD method in the same manner as in Example 2. As a result, it was confirmed that 25.3% of the crystal grains measured by MD had a deviation angle from the crystal orientation <100> within the range of 0° to 30°. In addition, the manufactured alloy sample was subjected to a tensile test in the same manner as in Example 2. As a result, it was confirmed that the maximum elastic strain was 0.36% and the apparent Young's modulus was 157 GPa.

[Comparative Example 2]
As a comparative example, a Cu-16.1Al-21.3Mn alloy (at%) was manufactured and subjected to a tensile test. This alloy was manufactured by the method shown in FIG. 2(a) of Example 2. The manufactured alloy sample was subjected to crystal orientation analysis by the EBSD method in the same manner as in Example 2. As a result, it was confirmed that 40.8% of the crystal grains measured by MD had a deviation angle from the crystal orientation <100> within the range of 0° to 30°. In addition, the manufactured alloy sample was subjected to a tensile test in the same manner as in Example 2. As a result, it was confirmed that the maximum elastic strain was 0.71% and the apparent Young's modulus was 174 GPa.

[Comparative Example 3]
As a comparative example, a Cu-16.8Al-11.3Mn-11.4Ni alloy (at%) was manufactured and subjected to a tensile test. This alloy was manufactured by the method shown in FIG. 2(a) of Example 2. The manufactured alloy sample was subjected to crystal orientation analysis by the EBSD method in the same manner as in Example 2. As a result, it was confirmed that 36.7% of the crystal grains measured by MD had a deviation angle from the crystal orientation <100> orientation within the range of 0° to 30°. In addition, the manufactured alloy sample was subjected to a tensile test in the same manner as in Example 2. As a result, it was confirmed that the maximum elastic strain was 0.40% and the apparent Young's modulus was 180 GPa.

The alloy compositions and test results of Examples 1 to 8 and Comparative Examples 1 to 3 are summarized and shown in Table 1. As shown in Table 1, in Comparative Examples 1 to 3, the maximum elastic strain was 1% or less, whereas in Examples 1 to 8, plastic deformation hardly occurs up to at least 1.5%, and the maximum elastic strain is 1.5% or more and 5% or less, and it can be said that there is a wide elastic deformation range. Therefore, the Cu-Al-Mn alloy of the embodiment of the present invention can be used as a material that needs to undergo elastic deformation even when subjected to a relatively large strain, such as a spring material or a biomaterial. In addition, while the Young's modulus is 150 GPa or more in Comparative Examples 1 to 3, the Young's modulus is also low at 50 GPa or less in Examples 1 to 8, so the Cu-Al-Mn alloy of the embodiment of the present invention can also be used as a material that needs to have a low Young's modulus.

Claims (3)

A Cu-Al-Mn alloy containing 14 at% to 22 at% Al, 5 at% to 14.5 at% Mn, 0.001 at% to 10 at% Ni, with the balance being Cu and unavoidable impurities, and having a maximum elastic strain of 1.5% or more. % to 22 at% Al, 5 at% to 14.5 at% Mn, with the balance being Cu and unavoidable impurities; and the maximum elastic strain is 1.5% or more;
A Cu-Al-Mn alloy consisting of a single crystal, characterized in that the crystal orientation of the deformation direction of the crystal grains, as measured by electron backscatter diffraction (EBSD) method, has a deviation angle from the crystal orientation <100> within a range of 0° to 30° . % to 22 at% Al, 5 at% to 14.5 at% Mn, with the balance being Cu and unavoidable impurities; and the maximum elastic strain is 1.5% or more;
A Cu-Al-Mn alloy comprising polycrystals, characterized in that 50% or more of the crystal grains have a crystal orientation in the deformation direction, as measured by electron backscatter diffraction (EBSD), with a deviation angle from the crystal orientation <100> within the range of 0° to 30°.

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