CN117802367A

CN117802367A - Aluminum alloy material

Info

Publication number: CN117802367A
Application number: CN202311657194.8A
Authority: CN
Inventors: 黑崎友仁; 箕田正; 玉置充宏; 金珍教
Original assignee: UACJ Corp
Current assignee: UACJ Corp
Priority date: 2019-10-08
Filing date: 2020-10-08
Publication date: 2024-04-02
Also published as: JP7414452B2; CN113661264A; KR20220079494A; CN113661264B; JP2021059762A; EP4043602A4; US20220127701A1; WO2021070889A1; TW202120708A; EP4043602A1

Abstract

The aluminum alloy material of the present invention contains Mg:5.0 to 7.0 mass percent (same as the following), ca: less than 0.1%, the remainder comprising aluminum and unavoidable impurities, and having a tensile strength of 350MPa or more.

Description

Aluminum alloy material

Technical Field

The present invention relates to a high-strength aluminum alloy material that suppresses strength anisotropy.

Background

In recent years, for example, aluminum alloy materials have been required for various products such as housings of electric appliances in order to achieve high strength and light weight. By using an aluminum alloy material having higher strength, the amount of the aluminum alloy material used can be reduced while maintaining the strength of the product equal to that of the conventional product, and thus the product can be reduced in weight.

Here, the high-strength aluminum alloy is, for example, a 6000-series alloy, 7000-series alloy, or the like. However, the heat-treated alloy requires a solid solution and a time-efficient heat treatment process, and thus has a problem of low productivity. In addition, 7000 series alloys contain a large amount of Zn and Cu, and therefore have a problem that corrosion is likely to occur depending on the use environment.

From the above viewpoints, a non-heat-treated aluminum alloy may be used. As the non-heat-treated aluminum alloy, a 5000-series alloy of the type having the highest strength is typical. The 5000 alloy is generally excellent in corrosion resistance, does not require solid solution and heat treatment with good efficiency, and therefore has high productivity. Further, by adding an additive element to the 5000 alloy, strength of 6000 series alloy or more can be achieved. Based on this, 5000 series aluminum alloy materials containing Mg as a main additive element in an amount of 5 wt% or more have been proposed (see patent documents 1 to 3).

Prior art literature

Patent literature

Patent document 1: japanese patent laid-open No. 2007-186747

Patent document 2: japanese patent laid-open No. 2001-98338

Patent document 3: japanese patent laid-open No. 7-197170

Disclosure of Invention

[ problem to be solved by the invention ]

In the aluminum alloy materials described in patent documents 1 to 3, the Mg content is increased to 5 wt% or more for the purpose of increasing the strength. However, there is no consideration concerning strength anisotropy in the aluminum alloy material.

In the case of an aluminum alloy material, when strength anisotropy is strong, there is a concern that rigidity in a specific direction in a final product is lowered, and reliability is lowered. In addition, in the manufacturing process of products such as molding, there is a concern that defects such as dimensional accuracy may occur. Particularly, in an aluminum alloy material (H-state material) having an increased strength by performing work hardening, there is a problem that strength anisotropy is easily and significantly exhibited as compared with an annealed aluminum alloy material (O-state material).

The present invention has been made to solve the above-described problems, and an object thereof is to provide an aluminum alloy material which ensures high strength and suppresses strength anisotropy by controlling a metallographic structure.

[ means of solving the problems ]

In order to solve the above problems, an aluminum alloy material according to an aspect of the present invention contains Mg:7.0 to 10.0 mass%, the same as the following), ca: less than 0.1%, the remainder comprising aluminum and unavoidable impurities, and having a tensile strength of 500MPa or more and an elongation at break of 3% or more and less than 10%. The aluminum alloy material according to the present invention further comprises Mg:5.0 to 7.0 mass percent of Ca:0.1 mass% or less, the remainder comprising aluminum and unavoidable impurities, the tensile strength being 350MPa or more, and the aluminum alloy material further comprising Mg:5.7 to 7.0 mass%.

In addition, the aluminum alloy material contains Mn:0.05 to 1.0 mass%.

In addition, the standard deviation of tensile strength of the aluminum alloy material in a plane formed by a final machine direction and a sheet width direction of the aluminum alloy material, the tensile strength being 0 ° direction as the final machine direction, 45 ° direction 45 ° from the final machine direction toward the sheet width direction and the 0 ° direction, and 90 ° direction 90 ° from the final machine direction toward the sheet width direction and the 0 ° direction, is 20 or less.

The orientation density calculated using the crystal orientation distribution function ODF is 5 or less for {013} < 100 > and {011} < 100 >.

The {011} < 211 > orientation density calculated by using the crystal orientation distribution function ODF is 0.4 times or more the {112} < 111 > orientation density.

[ Effect of the invention ]

According to one aspect of the present invention, an aluminum alloy material that ensures high strength and suppresses strength anisotropy can be produced.

Drawings

Fig. 1 is a diagram showing a measurement direction of tensile strength of an aluminum alloy material according to the present embodiment.

Detailed Description

The present inventors have conducted intensive investigations on alloy compositions and metallographic structures capable of suppressing strength anisotropy in high-strength aluminum alloy materials containing a large amount of Mg (magnesium). As a result, it was found that strength anisotropy can be suppressed by adjusting the alloy composition and manufacturing process and controlling an appropriate metallographic structure.

Hereinafter, the aluminum alloy material according to the embodiment of the present invention will be described in detail. The aluminum alloy material according to the present embodiment is used for members requiring strength and isotropy in strength, such as home electric appliances, buildings, structures, and transportation machines. Hereinafter, the unit is simply referred to as "%".

(element which must be contained in aluminum alloy)

[Mg]

Mg (magnesium) exists mainly in the form of solute element, and has the effect of improving strength. By setting the Mg content in the aluminum alloy to 7.0% or more, the effect of improving the strength can be sufficiently obtained.

However, if the Mg content in the aluminum alloy exceeds 10.0%, cracking may occur during hot rolling, which may make manufacturing difficult. Therefore, the Mg content in the aluminum alloy is preferably in the range of 7.5% to 9.0%, more preferably in the range of 7.5% to 8.5%.

[Ca]

Ca (calcium) exists mainly in the form of a compound in aluminum alloys, and even in a small amount, there is a concern that cracking during hot working is caused to lower workability. If the content of Ca in the aluminum alloy is 0.1% or less, cracking in hot working can be suppressed. The content of Ca in the aluminum alloy is more preferably 0.05% or less.

(element selectively contained in aluminum alloy)

[Si]

Si (silicon) mainly generates second-phase particles (for example, elemental Si, al-Si-Fe-Mn-based compounds) and acts as nucleation sites for recrystallized nuclei, thereby having an effect of refining the crystal grains. By setting the Si content in the aluminum alloy to 0.02% or more, the effect of making the crystal grains fine can be obtained satisfactorily.

However, if the Si content in the aluminum alloy exceeds 0.3%, coarse second phase particles are formed in large amounts, and the elongation at break of the produced aluminum alloy material may be reduced. Therefore, the Si content in the aluminum alloy is preferably in the range of 0.02% or more and 0.2% or less, and more preferably in the range of 0.02% or more and 0.15% or less.

[Fe]

Fe (iron) exists mainly in the form of second-phase particles (Al-Fe-based compound, etc.), and acts as nucleation sites for recrystallization nuclei, thereby having an effect of refining the crystal grains. By setting the Fe content in the aluminum alloy to 0.02% or more, an effect of making crystal grains finer can be obtained.

However, if the content of Fe in the aluminum alloy exceeds 0.5%, coarse second phase particles are formed in large amounts, and there is a concern that the elongation at break of the produced aluminum alloy material is reduced. Therefore, the content of Fe in the aluminum alloy is preferably in the range of 0.02% to 0.25%, more preferably in the range of 0.02% to 0.2%.

[Cu]

Cu (copper) exists mainly in the form of solute element, and has an effect of improving strength. By setting the Cu content in the aluminum alloy to 0.05% or more, the effect of improving the strength can be sufficiently obtained.

However, if the Cu content in the aluminum alloy exceeds 1.0%, cracking may occur during hot rolling, which may make manufacturing difficult. Therefore, the Cu content in the aluminum alloy is preferably in the range of 0.05% to 0.5%, more preferably in the range of 0.10% to 0.3%.

[Mn]

Mn (manganese) exists mainly in the form of second phase particles (Al-Mn-based compound) and acts as nucleation sites for recrystallization nuclei, thereby having an effect of refining the crystal grains. Specifically, by setting the Mn content in the aluminum alloy to 0.05% or more, the effect of making the crystal grains fine can be sufficiently obtained.

However, if the Mn content in the aluminum alloy exceeds 1.0%, coarse second phase particles are formed in large amounts, and there is a concern that the elongation at break of the produced aluminum alloy material is reduced. Therefore, the Mn content in the aluminum alloy is preferably in the range of 0.1% to 0.5%, more preferably in the range of 0.15% to 0.3%.

[Cr、V、Zr]

Cr (chromium), V (vanadium), zr (zirconium) are mainly present as second phase particles (Al-Fe-Mn-based compound, al-Cr-based compound, al-V-based compound, al-Zr-based compound, etc.), and act as nucleation sites for recrystallized nuclei, thereby having an effect of refining the crystal grains. Specifically, the effect of making the crystal grains finer can be obtained sufficiently by setting the content of Cr and V in the aluminum alloy to 0.05% or more or setting the content of Zr to 0.02% or more.

However, if the Cr and V content exceeds 0.3% or the Zr content exceeds 0.2% in the aluminum alloy, coarse second phase particles are formed in large amounts, and the elongation at break of the produced aluminum alloy material may be reduced.

Therefore, the content of Cr and V in the aluminum alloy is preferably 0.2% or less. The Zr content in the aluminum alloy is preferably 0.1%.

The content of Cr, V, zr in the aluminum alloy is not limited to the above, and at least one of Cr, V, zr may be contained in the aluminum alloy.

[Ti]

Ti (titanium) has an effect of suppressing the growth of a solidified aluminum phase formed during casting and reducing the size of a cast structure, thereby suppressing defects such as cracking during casting. However, if the Ti content in the aluminum alloy is too large, the second phase particles may coarsen, and the elongation at break of the produced aluminum alloy material may be reduced.

Therefore, by setting the Ti content in the aluminum alloy to 0.2% or less, the reduction in elongation at break of the manufactured aluminum alloy material can be suppressed. The Ti content in the aluminum alloy is more preferably 0.1% or less. Besides the above elements, al and unavoidable impurities (unavoidable impurities) are basically used.

(tensile Strength and elongation at Break)

In this embodiment, by subjecting an aluminum alloy having the above composition to a production process described below, an aluminum alloy material (H-state material) having a tensile strength of 500MPa or more and an elongation at break of 3% or more and less than 10% can be produced. This prevents the tensile strength from being lower than 500MPa and the strength of the final product from becoming insufficient. In addition, the elongation at break of less than 3% can be prevented from causing defects such as cracking during processing of the final product.

Further, the tensile strength of the aluminum alloy material is more preferably 550MPa or more. The elongation at break of the aluminum alloy material is more preferably 5% or more and less than 10%.

(strength anisotropy)

As shown in fig. 1, the aluminum alloy material 1 of the present embodiment is set so that the standard deviation of the tensile strength in the direction of 0 ° from the rolling direction toward the sheet width direction, the direction of 45 ° from the rolling direction toward the sheet width direction, and the direction of 90 ° from the rolling direction toward the sheet width direction (sheet width direction) on the plane formed by the rolling direction (final machine direction) and the sheet width direction in which the final rolling is performed by the pair of rolls 2 is 20[ mpa ] or less. This is because if the standard deviation of the tensile strength exceeds 20[ MPa ], the strength anisotropy is too high, and the strength of the final product in a specific direction is lowered, and the reliability may be lowered. Here, the standard deviation of the tensile strength is calculated according to the formula (1) described below.

The standard deviation of the tensile strength of the aluminum alloy material 1 is preferably 15[ MPa ] or less, more preferably 12[ MPa ] or less.

(texture)

In the aluminum alloy material of the present embodiment, the orientation density calculated using the crystal orientation distribution function (ODF: crystallite Orientation Distribution Function) is set so that {013} < 100 > and {011} < 100 > are 5 or less (for example, about 1). This is because if the orientation density of {013} < 100 > and {011} < 100 > exceeds 5, there is a concern that the strength anisotropy becomes remarkable and the strength in a specific direction of the final product is lowered.

In the aluminum alloy material of the present embodiment, the ratio of the orientation density {011} < 211 > calculated using the crystal Orientation Distribution Function (ODF) divided by the orientation density {112} < 111 > is set to 0.4 or more. This is because if the orientation density of {011} < 211 > is less than 0.4 times the orientation density of {112} < 111 >, there is a concern that the strength anisotropy becomes remarkable and the strength in a specific direction in the final product is lowered.

Here, a method of calculating the orientation density using the crystal Orientation Distribution Function (ODF) will be described in detail. In this embodiment, the orientation density of the produced aluminum alloy material was calculated by using a three-dimensional orientation analysis method (see light metal society, 1992, volume 42, page 6, page 358 to page 367) using a crystal Orientation Distribution Function (ODF). First, a cross section perpendicular to the machine direction (rolling direction) of the aluminum alloy material was measured by an X-ray diffraction method. In this case, the incomplete pole diagrams of the (111) plane, (220) plane and (200) plane were measured by the Schlz reflection method (see light metal society, 1983, volume 33, page 4, pages 230 to 239) in the range of 15 to 90 degrees of inclination angle. Next, the order expansion was performed to obtain a crystal Orientation Distribution Function (ODF). Thus, the orientation density in each direction was calculated as a ratio of the orientation density to the orientation density of the standard sample having a random texture.

(method for producing aluminum alloy Material)

Next, a method for producing the aluminum alloy material according to the present embodiment will be described. The aluminum alloy material according to the present embodiment is produced in the order of the casting step, the homogenizing step, the hot rolling step, the cold rolling step, and the annealing step. This manufacturing process is an example, and is not limited thereto.

First, in the casting step, a billet is cast by a semi-continuous casting method such as a Direct Chill (DC) casting method or a hot top method. In the casting step, the casting speed is preferably 20 mm/min to 100 mm/min in order to prevent coarse second phase particles from forming.

After the casting process is completed, a homogenization process is performed. The treatment temperature is set to 400 ℃ to 490 ℃. The reason for this is that: if the treatment temperature is lower than 400 ℃, there is a concern that sufficient homogenization may not be performed. If the treatment temperature exceeds 490 ℃, the al—mg compound remaining without re-solid solution may be dissolved, and defects such as cracking may occur during hot rolling. In addition, coarsening of the second phase particles progresses excessively, grains in a specific direction tend to preferentially grow during the subsequent recrystallization, and there is a concern that strength anisotropy decreases.

In the homogenization step of the present embodiment, two-stage homogenization treatment may be performed. In this case, the treatment temperature in the first stage is set to 400 ℃ or higher and 450 ℃ or lower. The reason for this is that: if the treatment temperature in the first stage is lower than 400 ℃, there is a possibility that homogenization may not be sufficiently performed. If the first-stage treatment temperature exceeds 450 ℃, the al—mg compound remaining without re-solid solution may be dissolved, and defects such as cracking may occur during hot rolling.

The treatment time in the first stage is set to be in the range of 5 hours to 20 hours. The reason for this is that: if the treatment time in the first stage is less than 5 hours, homogenization cannot be sufficiently performed. In addition, if the treatment time of the first stage exceeds 20 hours, productivity is lowered. As described above, by appropriately setting the treatment temperature and the treatment time, the first-stage homogenization treatment is performed, and the al—mg-based compound is solid-dissolved and homogenized at a higher temperature.

Then, the second stage treatment temperature is set to 450 ℃ to 490 ℃. The reason for this is that: if the second stage treatment temperature is less than 450 ℃, sufficient homogenization cannot be performed. If the second stage treatment temperature exceeds 490 ℃, oxidation of Mg occurs on the surface, and the Mg concentration on the surface layer may decrease.

The second stage treatment time is set to be in the range of 5 hours to 20 hours. The reason for this is that: if the second stage treatment time is less than 5 hours, homogenization cannot be performed sufficiently. In addition, if the second-stage treatment time exceeds 20 hours, coarsening of the second-phase particles excessively progresses, grains in a specific direction tend to preferentially grow in the subsequent recrystallization process, and there is a concern that strength anisotropy may be reduced.

Next, a hot rolling process is performed. In the hot rolling step, the start temperature of hot rolling is set to be in the range of 350 ℃ to 480 ℃. The reason for this is that: if the treatment temperature of the hot rolling is less than 350 ℃, there is a concern that the rolling becomes difficult due to an excessively high deformation resistance. In addition, if the hot rolling treatment temperature exceeds 480 ℃, there is a fear that the material is partially melted to cause cracking. Further, the homogenization step may be omitted and the hot rolling step may be performed.

Then, after the hot rolling process is completed, a cold rolling process is performed. In the cold rolling step, cold rolling is performed so that the thickness from the end of the hot rolling step to the end of the cold rolling step (the ratio of the thickness after the processing to the thickness before the processing) is 50% or more. The degree of processing may be 50% or more, and may be appropriately changed.

In addition, the intermediate annealing may be performed before or during the cold rolling process. In this case, the cold rolling is performed so that the working ratio from the plate thickness at the end of the intermediate annealing to the plate thickness at the end of the cold rolling is 50% or more. The treatment temperature of the intermediate annealing is preferably in the range of 300 ℃ to 400 ℃. The holding time of the intermediate annealing is preferably in the range of 1 hour or more and 10 hours or less. The reason for this is that: if the intermediate annealing is performed at a high temperature for a long period of time, there is a concern that the surface is oxidized to deteriorate the appearance quality.

According to the aluminum alloy material of the present embodiment described above, by adjusting the composition and manufacturing process of the aluminum alloy and appropriately controlling the metallographic structure, an aluminum alloy material having high strength and suppressed strength anisotropy can be manufactured. Thus, the aluminum alloy material can be improved in manufacturability and the reliability of the final product can be improved.

Examples

Example 1 of the present embodiment will be described below with reference to tables 1 and 2.

(composition of aluminum alloy)

The composition of the aluminum alloy used in example 1 is shown in table 1.

TABLE 1

(Table 1)

As shown in table 1, the composition of the aluminum alloy of example 1 was within a predetermined range. Here, the predetermined range is a range in which Mg is 7.0% to 10.0% and Ca is 0.1% or less.

(manufacturing method)

An aluminum alloy having a composition shown in table 1 was dissolved and DC cast, and then subjected to a homogenization step, a hot rolling step, and a cold rolling step. After the completion of the cold rolling step, an aluminum alloy material having a sheet thickness of 1.0mm was produced.

In example 1, heating was performed at 465℃for 12 hours in the homogenization step prior to the hot rolling step. In the cold rolling step, the working ratio from the plate thickness at the end of hot rolling to the plate thickness at the end of cold rolling was set to 80%.

(Properties of aluminum alloy Material)

The strength characteristics, strength anisotropy, and manufacturability of the aluminum alloy materials produced by performing the above-described treatments on the aluminum alloy of example 1 having the composition shown in table 1 are summarized in table 2.

TABLE 2

(Table 2)

(tensile Strength and elongation at Break)

As shown in table 2, the tensile strength and elongation at break of the aluminum alloy material produced in example 1 were within the predetermined ranges. That is, the tensile strength of the aluminum alloy material produced in example 1 was 500MPa or more, and the elongation at break was in the range of 3% or more and less than 10%.

The tensile strength and elongation at break of the aluminum alloy material thus produced were measured in accordance with JIS standard Z-2241-2011. As shown in fig. 1, the tensile strength and elongation at break of the produced aluminum alloy material 1 were measured in a plane formed by the rolling direction (final machine direction) and the sheet width direction by a set of rolls 2, and the tensile strength and elongation at break in the direction of 0 ° as the rolling direction, the direction of 45 ° from the rolling direction toward the sheet width direction at 45 ° to the 0 ° direction, and the direction of 90 ° from the rolling direction toward the sheet width direction at 90 ° to the 0 ° direction were defined as average values.

(strength anisotropy)

The strength anisotropy is defined by measuring the tensile strength in a plane formed by the rolling direction (final machine direction) and the sheet width direction, in a direction of 0 ° as the rolling direction, in a direction of 45 ° from the rolling direction toward the sheet width direction at 45 ° to the 0 ° direction, and in a direction of 90 ° from the rolling direction toward the sheet width direction at 90 ° to the 0 ° direction, and by using the standard deviation [ MPa ] calculated by the following formula (1).

[ number 1]

Here, TS _i [MPa]Tensile strength in all directions. TS [ MPa ]]Is the average of the tensile strength in each direction. n is the total number of data for tensile strength.

(texture)

For the aluminum alloy material of example 1, the orientation density was calculated by a three-dimensional orientation analysis method using the above-mentioned crystal Orientation Distribution Function (ODF). Specifically, a cross section perpendicular to the machine direction (rolling direction) of the aluminum alloy material was measured by an X-ray diffraction method for a part of the produced aluminum alloy material. In this case, the (111), (220) and (200) partial polar diagrams of the planes were measured by the Schlz reflection method in the range of 15 ° to 90 °, and then the crystal Orientation Distribution Function (ODF) was obtained by performing series expansion.

The orientation density in each direction thus obtained was calculated as a ratio with respect to the orientation density of a standard sample having a random texture. Table 2 shows the evaluation results of {013} < 100 > and {011} < 100 > with an orientation density of 5 or less as "O", and more than "5" as "X". The ratio (as the orientation density two) obtained by dividing the orientation density {011} < 211 > by the orientation density {112} < 111 > is 0.4 or more, and is "X" when it is smaller than 0.4.

As shown in table 2, it is found that in example 1, the strength anisotropy was well suppressed. In example 1, the manufacturability was not a problem.

Comparative example

As comparative examples with respect to example 1, the properties of aluminum alloy materials produced by performing the same treatments as in example 1 on aluminum alloys of examples 2 to 4 and comparative examples 4 to 5 having compositions shown in table 3 are summarized in table 4. In examples 2 to 4, the homogenization treatment was performed at 500℃for 8 hours.

TABLE 3

(Table 3)

TABLE 4

(Table 4)

In examples 2 to 4, each of the performances was excellent, and the manufacturability was excellent.

In comparative example 4, since Mg content was too large, cracking occurred at the time of hot rolling, and rolling was difficult, and thus it was impossible to manufacture.

In comparative example 5, since the content of Ca was too large, cracking occurred during hot rolling, and rolling was difficult, and thus, production was impossible.

The present invention is not limited to the above-described embodiments and examples, and various modifications can be made within the scope of the claims, and embodiments obtained by appropriately combining the technical means disclosed in the respective different embodiments are also included in the technical scope of the present invention.

An aluminum alloy material according to an aspect of the present invention contains Mg:7.0 to 10.0 mass%, the same as the following), ca: less than 0.1%, the remainder comprising aluminum and unavoidable impurities, and having a tensile strength of 500MPa or more and an elongation at break of 3% or more and less than 10%.

The aluminum alloy material according to the present invention further comprises Mg:5.0 to 7.0 mass percent of Ca:0.1 mass% or less, the remainder comprising aluminum and unavoidable impurities, the tensile strength being 350MPa or more, and the aluminum alloy material further comprising Mg:5.7 to 7.0 mass%.

The aluminum alloy material preferably contains Mn:0.05 to 1.0 percent.

In addition, the standard deviation of tensile strength of the aluminum alloy material in a plane formed by a final machine direction and a sheet width direction of the aluminum alloy material, the tensile strength being 0 ° direction as the final machine direction, 45 ° direction forming 45 ° with the 0 ° direction from the final machine direction toward the sheet width direction, and 90 ° direction forming 90 ° with the 0 ° direction from the final machine direction toward the sheet width direction, is preferably 20 or less.

The aluminum alloy material preferably has an orientation density of 5 or less, calculated using a crystal Orientation Distribution Function (ODF), of {013} < 100 > and {011} < 100 >.

The aluminum alloy material preferably has an orientation density {011} < 211 > calculated using a crystal Orientation Distribution Function (ODF) of 0.4 times or more the orientation density {112} < 111 >.

[ description of symbols ]

1: aluminum alloy material

2: and (3) a roller.

Claims

1. An aluminum alloy material characterized by comprising Mg:5.0 to 7.0 mass percent of Ca: at most 0.1 mass% of the total mass of the composition,

the remainder comprises aluminum and unavoidable impurities, and

the tensile strength is more than 350 MPa.

2. The aluminum alloy material according to claim 1, wherein Mg:5.7 to 7.0 mass%.

3. The aluminum alloy material according to claim 1 or 2, wherein the aluminum alloy material contains Mn:0.05 to 1.0 mass%.

4. The aluminum alloy material according to claim 1 or 2, wherein a standard deviation of tensile strength of the aluminum alloy material in a plane formed by a final machine direction and a sheet width direction of the aluminum alloy material, the direction being 0 ° of the final machine direction, the direction being 45 ° of 45 ° from the final machine direction toward the sheet width direction and the direction being 45 ° of the 0 ° direction, and the direction being 90 ° of 90 ° from the final machine direction toward the sheet width direction and the direction being 0 ° is 20 or less.

5. The aluminum alloy material according to claim 4, wherein {013} < 100 > and {011} < 100 > calculated using the crystal orientation distribution function ODF have an orientation density of 5 or less.

6. The aluminum alloy material according to claim 4 or 5, wherein {011} < 211 > calculated using the crystal orientation distribution function ODF has an orientation density of {112} < 111 > that is 0.4 times or more the orientation density.