JPH11189836A - Al-mg-si aluminum alloy sheet to be formed excellent in surface properties - Google Patents

Abstract

PROBLEM TO BE SOLVED: To obtain the alloy sheet without the surface properties being deteriorated due to the generation of a ridging mark or further an orange peel effect, etc., under more severe forming conditions by specifying the cube orientation at the surface-layer part and specified region of an Al-Mg-Si aluminum alloy sheet of specified composition. SOLUTION: This Al-Mg-Si Al alloy sheet contains, by weight, 0.2-1.8% Si and 0.2-1.6% Mg and with the accumulation degree of the cube orientation controlled to 2-5 at the surface-layer part and to <=7, preferably <=6, at the 1/4 thickness region of the sheet. The cube orientation means 100} <100> orientation and is formed when the rolled sheet with a rolling texture formed is recrystallized. Besides, the alloy may contain, as required, 0.005-1.0% each of Zn and Cu, 0.001-0.1% Ti, 1-300 ppm B, 1-100 ppm Be and further >=1 kind among <=1.0% Mn, <=0.3% Cr and <=0.15% each of Zr and V, and the crystal grain diameter on the sheet surface is preferably controlled to <=45 μm.

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to moldings suitable for use in building materials such as roofs, interiors, curtain walls, etc., equipment, electric parts, optical equipment, transportation equipment such as automobiles, railway vehicles and aircraft, and general machine parts. The present invention relates to an Al-Mg-Si-based aluminum alloy sheet material for forming which has excellent surface properties after processing.

[0002]

2. Description of the Related Art A 6000 (Al-Mg-Si) aluminum alloy sheet is relatively excellent in corrosion resistance and formability at room temperature, and has high strength by artificial aging. It is suitable for applications requiring thinning. Al-Mg-Si based alloy sheet materials are usually
After the homogenization treatment, hot rolling is performed, followed by intermediate annealing, and then, if necessary, cold rolling is performed to obtain a sheet having a predetermined thickness, which is then subjected to solution quenching, and then, if necessary, a skin pass and a cold pass. It is manufactured by performing rolling, stretching and the like.

However, when a forming process is performed on an Al-Mg-Si alloy sheet material, a ridging mark is formed on the surface of the sheet as described in JP-A-7-228956 or JP-A-8-23252. The problem is that surface roughness called "surface roughness" occurs. When this ridging mark is generated, it cannot be used as a poor appearance for applications such as interiors, camera cases, automobile outer panel panels etc. where the surface is required to be extremely beautiful. To be particularly noticeable,
After the molding process, it proceeds to the painting process without being noticed, and may be recognized for the first time after painting. In other words, it has the troublesome characteristic that it sometimes appears only when it is a product.

[0004] In order to prevent deterioration of the surface properties due to ridging marks or the like generated on the plate surface during the forming process, it is necessary to change the product shape and perform the forming process under milder conditions. In general, the radius of curvature of a portion where the forming conditions are severe is reduced, and the desired product shape cannot be realized with this. On the other hand, if the surface properties are deteriorated during molding, the surface properties can be corrected to some extent by polishing the plate surface with paper or the like, but the number of manufacturing steps increases and the cost increases.

[0005]

SUMMARY OF THE INVENTION The above-mentioned JP-A-7-228
In Japanese Unexamined Patent Publication No. 956 and Japanese Unexamined Patent Publication No. Hei 8-23252,
In each case, the hot rolling temperature is set lower, and at the same time, the processing conditions of each of the other steps are strictly controlled, and fine and crystallographic orientations are generated at random to prevent the generation of ridging marks. ing. However, JP-A-7-2
Japanese Patent Application Laid-Open No. 8-9556 does not disclose the amount of deformation of press working which is considered to have no ridging mark.
Japanese Patent No. 232052 discloses a simulation of press working in which only 2% of tensile deformation is performed (that is, it is intended to prevent ridging marks generated by forming processing corresponding to at most 2% of tensile deformation). Only).

[0006] In view of the growing demand for molded products having excellent design properties and the situation in which molding processing conditions are going to be more severe than ever, the present invention provides a ridging mark and orange peel under more severe processing conditions. Al for molding without deterioration of surface properties due to generation of
An object is to provide a Mg-Si-based aluminum alloy sheet.

[0007]

The Al-Mg-Si-based aluminum alloy sheet for forming according to the present invention comprises Si:
An Al-Mg-Si-based aluminum alloy sheet material containing 0.2 to 1.8% and Mg: 0.2 to 1.6%. 1/4 thickness
7 or less at the portion, preferably 2 to 4 at the plate surface portion, and 6 or less at the 1/4 thickness portion.

[0008] The cube orientation means the {100} <100> orientation, and is formed when a rolled sheet having a rolled texture is recrystallized. In an aluminum alloy, the recrystallized grains having the cube orientation are not arranged randomly in the plate surface, but are easily arranged side by side in the rolling direction. These are phenomena common to not only rolled materials but also extruded materials. The present inventors have found that, when such an aluminum alloy sheet material is formed, the region where the recrystallized grains having the cube orientation are arranged in the rolling direction and the other regions where the recrystallized grains are not arranged in the rolling direction are deformed and deformed. Due to the different orientations, regions where recrystallized grains having a cube orientation are aligned in the rolling direction are easily observed as streaks on the plate surface after forming, and particularly such regions are long and numerous in the rolling direction. In this case, it was found that a remarkable streak pattern was observed in the rolling direction on the plate surface after the forming process. This is the ridging mark.

[0009] Based on such knowledge, the present inventors have conceived that if the degree of integration of the cube orientation is reduced, the ridging marks generated on the plate surface during the forming process can be improved. In other words, if the degree of integration of the cube orientation decreases, the row of the recrystallized grains having the cube orientation arranged in the rolling direction is divided, and the length of the row of the individual recrystallized grains decreases. In addition, the number of rows of recrystallized grains in the cube orientation is reduced. As a result, the length of the streaks generated during the forming process is short, and the number of the streaks is also reduced, the degree of the ridging mark is reduced, and the ridging mark cannot be observed with the naked eye. In addition, the occurrence of the ridging mark is affected not only by the degree of integration of the cube orientation in the surface layer of the plate, but also by the degree of integration of the cube orientation in the interior of the plate. In many cases (especially when the intermediate annealing is omitted), it is understood that it is necessary to reduce the degree of integration of the cube orientation in each of the surface layer portion and the inside of the plate (particularly, a 1/4 thickness portion). Was.

Si: 0.2-1.8%, Mg: 0.2-
In an Al-Mg-Si-based aluminum alloy sheet material containing 1.6%, in order to prevent the occurrence of ridging marks on the sheet surface after forming, the degree of integration of cube orientation is 5 or less at the sheet surface portion and the sheet thickness. It is necessary to set it to 7 or less at a ４ site. The degree of integration of cube orientation is 5 at the plate surface
Or, when the thickness exceeds 7 at a 厚 portion of the plate thickness, a remarkable ridging mark is generated on the plate surface during molding. Furthermore, in order to prevent the occurrence of ridging marks even under more severe forming conditions such as a plane strain state and an equibiaxial tension state, the degree of integration of cube orientation is 4 or less at the surface layer of the plate and the plate thickness is 1/4.
It is desirable that the number be 6 or less at the site.

As described above, in order to reduce ridging marks, it is desirable to reduce the degree of integration of cube orientations. However, it was found that when the degree of integration of the cube orientation was low, cracks such as cracks were likely to occur on the plate surface when bending was performed in the rolling direction (the bending line was perpendicular to the rolling direction). This is because when the degree of integration of the cube orientation decreases, the row of the recrystallized grains having the cube orientation arranged in the rolling direction is divided, and the length of the row of the individual recrystallized grains becomes shorter. In an Al-Mg-Si-based aluminum alloy sheet material containing 0.8% and Mg: 0.2 to 1.6%, if the degree of integration of the cube orientation is less than 2, the divided parts are likely to be arranged at right angles to the rolling direction, This is because when bending is performed in the rolling direction, the deformation tends to concentrate on such a divided portion, and cracks easily occur on the plate surface.

The influence of the degree of accumulation of cube orientation on the likelihood of cracking during bending is smaller in the interior of the sheet than in the surface layer of the sheet. It may be specified. That is, the cube orientation is 2 or more in the plate surface layer. Therefore, Al
In order to prevent the occurrence of ridging marks and to prevent cracking during bending in an Mg-Si based aluminum alloy sheet, the degree of integration of the cube orientation should be 2 to 5 at the sheet surface layer.
And at a plate thickness portion of 7 or less, desirably, the degree of integration of cube orientation is 2 to 4 at the plate surface layer portion and 6 or less at a plate thickness of 1/4 portion.

Regarding the cube orientation, for example, Japanese Patent Application Laid-Open No. 5-263203 discloses that an aluminum alloy sheet material having a strong cube orientation by recrystallization has strong anisotropy and lowers deep drawability. Have been. However, that the degree of accumulation of cube orientations affects the occurrence of ridging marks, and that the occurrence of ridging marks can be prevented by defining the degree of accumulation of cube orientations on both the surface layer and the inside of the plate to a predetermined value or less. However, there is no disclosure suggesting the findings of the present inventors, such as that if the degree of integration of the cube orientation is excessively reduced, cracks are likely to occur during bending.

Further, in order to prevent the occurrence of orange peel, the crystal grain size on the plate surface is desirably 45 μm or less. As described above, it is possible to obtain an aluminum alloy sheet material for forming work which is excellent in sheet surface properties and does not cause ridging marks, cracks, and orange peel during forming.

[0015]

BEST MODE FOR CARRYING OUT THE INVENTION In terms of the composition of components, the present invention relates to the following: Si: 0.2 to 1.8%, Mg: 0.2 to 1.6%
, An aluminum alloy containing the balance of Al and unavoidable impurities, and if necessary, further Zn: 0.00
5 to 1.0%, Cu: 0.005 to 1.0%, Ti:
0.001-0.1%, B: 1-300 ppm, B
e: 0.1 to 100 ppm, Mn: 1.0% or less, C
r: 0.3% or less, Zr: 0.15% or less, V: 0.1
One or more of 5% or less of a total of 0.01
Si: 0.2 to 1.8%, such as an aluminum alloy containing any one or a combination thereof.
Mg: Applicable to all Al-Mg-Si-based aluminum alloys containing 0.2-1.6%. Al-Mg-Si
The reasons for defining the composition of the system alloy as described above are as follows.

Mg: Mg is an element that imparts strength together with Si, but if it is less than 0.2%, sufficient strength cannot be obtained by artificial aging, whereas if it exceeds 1.6%, formability decreases. Therefore, the Mg content is in the range of 0.2 to 1.6%. Si: Si is an element that imparts strength together with Mg, but if it is less than 0.2%, sufficient strength cannot be obtained by artificial aging, while if it exceeds 1.8%, elongation decreases and moldability decreases. I do. Therefore, the Si content is in the range of 0.2 to 1.8%. In order to obtain high strength by artificial aging, M
It is desirable that the ratio of the content of g and Si be Si / Mg ≧ 0.65.

Zn: Zn is MgZn during artificial aging.
₂ is finely and densely deposited to achieve high strength.
However, if less than 0.005%, sufficient strength cannot be obtained,
On the other hand, if it exceeds 1.0%, the corrosion resistance is significantly reduced,
The content is in the range of 0.005 to 1.0%. Cu: Cu precipitates Mg ₂ Si finely and at high density during artificial aging, and realizes high strength. However, 0.0
If it is less than 05%, there is no effect, while if it exceeds 1.0%, the corrosion resistance and weldability are remarkably reduced.
005 to 1.0%. Ti: Ti is an element added for refining the crystal grains of the ingot and improving formability. However, if it is less than 0.001%, there is no effect, and if it exceeds 0.1%, it is not effective. It forms coarse crystals and lowers moldability. For this reason,
The Ti content is in the range of 0.001 to 0.1%.

B: Similar to Ti, B is an alloy added for refining the crystal grains of the ingot and improving formability. However, if less than 1 ppm is added, there is no effect.
If contained in excess of the above, a coarse crystallized product is formed and the moldability is reduced. Therefore, the B content is in the range of 1 to 300 ppm. Be: Be is contained in an amount of 0.1 ppm or more, if necessary, to prevent reoxidation of the aluminum melt in the air. However, if the content exceeds 100 ppm, the hardness of the material increases and the formability decreases.
ppm range.

Mn, Cr, Zr, V: These components are Al ₂₀ Cu ₂ M during the homogenizing heat treatment and during the subsequent hot rolling.
Dispersed particles such as n ₃ , Al ₁₂ Mg ₂ Cr, Al ₃ Zr, and Al ₂ Mg ₃ Zn ₃ are generated. Since these dispersed particles have an effect of hindering the movement of the grain boundary after recrystallization, fine crystal grains can be obtained. However, excessive addition tends to generate a coarse insoluble intermetallic compound at the time of melting casting, becomes a starting point of destruction at the time of forming, and causes a reduction in formability. Also, excessive addition of Zr tends to make the microstructure needle-like,
Fracture toughness and fatigue properties in a specific direction, as well as formability are deteriorated. Therefore, the addition amounts of Mn, Cr, Zr, and V are 1.0%, 0.30%, 0.15%, and 0.15%, respectively.
% Or less.

Fe: Fe contained as impurities is Al
₇ Cu ₂ Fe, Al ₁₂ (Fe, Mn) ₃ Cu ₂ , (Fe, M
n) Produce crystallized substances such as Al ₆ . These crystals are harmful to the fracture toughness and the fatigue properties. If the Fe content exceeds 0.5%, the fracture toughness, the fatigue properties and the formability are remarkably reduced. 5% or less.
In addition, as a crystallized substance, Al ₂ Cu ₂ Mg other than Fe-based,
There are soluble ones such as Al ₂ Cu ₂ and Mg ₂ Si, and it is desirable that these are sufficiently re-dissolved in an Al matrix by solution treatment and quenching. Other impurities: Ni is limited to 0.05% or less.

Next, the Al-Mg for forming according to the present invention is used.
As an example of a method for producing a Si-based aluminum alloy sheet material, first, an ingot is formed by melting and casting in accordance with a conventional method, then homogenized and heat-treated, hot-rolled, and if necessary, subjected to intermediate annealing, and then cold-rolled. Finally, solution treatment and quenching are performed to obtain a product plate. Hereinafter, each step of the exemplified manufacturing method will be described in more detail together with preferable conditions.

Hot Rolling Through rough hot rolling and finish hot rolling, the rolling start temperature is set to be equal to or lower than the soaking temperature (for example, 470 to 540 ° C.), and the rolling end temperature is set to 350 to 450 ° C. The distortion speed at the time of the final pass is set to 9000 to 20000% / sec. As a result, at least the sheet thickness 1 / from the surface layer of the sheet material after hot rolling.
The metallographic structure of up to four sites can be made into fine recrystallized grains to eliminate the fibrous structure that causes the recrystallized grains having the cube orientation to be aligned in the rolling direction in the final product sheet. In the plate, the occurrence of ridging marks during molding can be prevented. Also, in the final product sheet, the rows of recrystallized grains in the cube orientation are divided, the rows of individual crystal grains are shortened, and the cube orientation is not reduced to such an extent that the divided portions are aligned in a direction perpendicular to the rolling direction. Thereby, it is possible to suppress the occurrence of cracks on the plate surface (where the plate is deformed so as to extend in the rolling direction) when the bending process is performed in the rolling direction, and it is possible to improve bending workability in the rolling direction. In other words, in the final product plate, the degree of integration of the cube orientation is 2 to 5 at the plate surface layer portion and 7 or less at the 1/4 thickness portion, preferably 2 to 4, 6 or less, respectively, to prevent the occurrence of ridging marks, Bending workability can be improved. Here, the strain rate is defined as: strain rate = rolling rate (%) by final roll / time (second) that the sheet passes through the final roll.

Intermediate Annealing The microstructure near the leading end of the coil at the start of hot rolling and near the trailing end of the coil at the end of hot rolling is a fixed part (coil) where hot rolling is stably performed. (Central portion in the longitudinal direction) in many cases. It is necessary to stably maintain the degree of integration of the cube orientation of 2 to 5 at the surface of the plate and 7 or less at the 1/4 plate thickness, regardless of where the product plate is collected from the coil. Intermediate annealing may be performed according to. Intermediate annealing is also effective for subdividing the row of recrystallized grains in the cube orientation and reducing the number, especially when priority is given to reducing ridging marks. Preferred intermediate annealing conditions are as follows: heating rate: up to 400 ° C., 30 ° C./min to 500 ° C./sec, 40 ° C.
0 to 500 ° C. at 10 to 100 ° C./min, holding condition: 500
５580 ° C. × 10 seconds to 10 minutes, cooling rate: 30 ° C./min or more from the holding temperature to 50 ° C. In the case of performing the intermediate annealing, the rolling end temperature of the hot rolling can be set lower than the temperature range previously described in the hot rolling (for example, 150 ° C. to 450 ° C.). Further, the strain rate at the final pass after hot rolling can be set low (for example, 7000 to 2000).
0% / sec).

Cold Rolling In order to reduce the grain size of the micro crystal grains (normal crystal grains) to 45 μm or less, preferably, the cold rolling rate is 50% or more.
When the above-described intermediate annealing is performed, the solid solubility is high, the work hardening degree in cold rolling is high, and the micro crystal grains in the final solution treatment are likely to be small. Therefore, the cold rolling rate is 3
0% or more is sufficient. Final solution treatment The preferred final solution treatment conditions are as follows: heating rate up to 400 ° C is 30 ° C / min or more, 400 to 530 ° C is 10 ° C / min or more, holding condition: 530 to 580 ° C × 10 seconds to 10 minutes, Cooling rate: 30 ° C./min or more from the holding temperature to 30 ° C.

The above is an example of the case where the Al—Mg—Si alloy is hot-rolled, intermediately-annealed if necessary, cold-rolled, and finally subjected to solution treatment and quenching. Although the preferred conditions and the like have been described, the present invention is not limited to this method or conditions, and is equally applicable to Al-Mg-Si-based aluminum alloy sheets generally manufactured by various methods. In short, a certain amount of Mg and S
In the Al-Mg-Si-based aluminum alloy sheet containing i, the degree of integration of the cube orientation may be 2 to 5 at the surface of the sheet and 7 or less at 1/4 thickness.

[0026]

Embodiments of the present invention will be described below. (Example 1) Mg 0.5%, Si 1.3%, Mn 0.0
5%, Fe 0.16%, Cr 0.25%, Ni 0.00
2%, Zn 0.05%, Cu 0.1%, Ti 0.06
%, B: 10 ppm, Be: 30 ppm, the balance A
melting and casting an aluminum alloy consisting of
After forming a 460 mm thick ingot, and then performing a soaking heat treatment at 540 ° C. for 4 hours, hot rolling was performed under various conditions shown in Table 1.
The plates were 2.0 mm and 2.5 mm thick. Subsequently, cold rolling was performed without intermediate annealing to obtain a 1.2 mm thick plate. The plate was heated to a solution temperature of 550 ° C., held for 20 seconds, and then water-quenched (cooling rate to 150 ° C. is about 50 ° C./s). Then, after leaving at room temperature for 3 months,
Sampling was performed from the center of the plate width to evaluate the material properties. The results are shown in Table 1.

[0027]

[Table 1]

The properties of each material in Table 1 were measured as follows. The degree of integration of the cube orientation Electrolytic polishing (Ra <0.1μ)
m), the {111} pole figure was measured by the Schulz reflection method using X-rays (CoKα rays), and the cube orientation {100} <1 was obtained from the obtained pole figure.
10> (the ratio of the random sample to the diffraction intensity at {111} (= random intensity)) was evaluated. In addition,
In order to measure the degree of integration of cube orientation at a 1/4 thickness, one side of the plate is emery paper (# 400 → # 800 → # 12
00 → # 1500) → OPS polishing → Polishing by diamond abrasive grains (6 μm → 1 μm) to 研磨 of the plate thickness, and then electropolishing.

After the surface of the plate is mechanically polished to about 0.05 to 0.1 mm,
It was electrolytically etched and observed using an optical microscope (using a polarizing plate). The grain size was measured on the LL plane in the rolling direction by a line intercept method. One measurement line length was 500 μm, and a total of five visual fields were observed with five lines per visual field. Tensile properties Based on JIS-Z2241, a tensile test was performed in the LT direction (90 ° direction with respect to the rolling direction) at a tensile speed of 5 mm / min using a JIS No. 5 test piece in a normal temperature atmosphere. Evaluation of ridging mark The product plate was cut into a size of w200 × l180 mm (w200 is parallel to the rolling direction), and then extended to a height of 10 mm using a φ50.8 mm ball-head punch. The other forming conditions were a rock bead state, the oil used was a lubricating oil for steel plates, and the punch speed was 250 mm / min. After the molding test, a plane strain processing region on the plate surface (the surface opposite to the punch contact side) was visually observed, and a case where a ridging mark was generated was evaluated as x, and a case where it was difficult to distinguish the ridging mark was evaluated as ○. Evaluation of Orange Peel In the tensile test, after 20% tensile deformation, a case where a matte pattern was remarkably observed on the plate surface was evaluated as x, and a case where the matte pattern was difficult to discriminate was evaluated as ○.

As can be seen from Table 1, the degree of integration of the cube orientation is within the range specified in the present invention. 1 to No.
3, No. 7-No. 8 has no ridging mark,
In particular, No. 4 having a microcrystal grain size of 45 μm or less. 1 to No.
3 has no orange peel. On the other hand, when the degree of integration of the cube orientation is out of the range specified in the present invention, No. 4-No.
In No. 6, ridging marks are generated, and it can be seen that the degree of surface texture after the forming is low.

Example 2 The same aluminum alloy as in Example 1 was melt-cast to form a 460 mm thick ingot.
After performing soaking at 0 ° C. × 4 hr, hot rolling was performed under various conditions shown in Table 2 to obtain a 2.5 mm thick plate. continue,
After performing intermediate annealing at a heating rate shown in Table 2 and holding at 520 ° C. for 20 seconds, cooling was performed to room temperature at 50 ° C./min.
It was cold rolled into a 1 mm thick plate. The plate was heated to a solution temperature of 550 ° C., held for 20 seconds, and then water-quenched (cooling rate to 150 ° C. is about 50 ° C./s). Then, after leaving at room temperature for 3 months, sampling was performed from the center of the plate width to evaluate the material properties. Table 2 shows the results.
Shown along with. The evaluation of the bendability was performed as follows. Evaluation of bendability Specimen cut into a JIS-Z-2204 No. 4 test piece shape (W25 x 1200 mm, 120 mm is in the rolling direction)
And a bending test according to the method specified in JIS-Z-2248.
(80 degree bending). The case where cracks were observed on the bending surface after the bending test was evaluated as x, and the case where no cracks were observed was evaluated as ○.

[0032]

[Table 2]

As can be seen from Table 2, the degree of integration of the cube orientation is within the range specified in the present invention. 10 to N
o. No. 13 has no ridging mark and no orange peel. On the other hand, when the integration degree of the cube orientation is higher than the range defined in the present invention, 14-No. In No. 15, a ridging mark was generated, the degree of surface texture after forming was low, and the degree of integration of the surface layer portion of the plate was low. 16 shows that bending property is inferior.

[0034]

According to the present invention, it is possible to obtain an Al-Mg-Si-based aluminum alloy sheet material for forming which does not generate ridging marks, has excellent bendability, and does not generate orange peel.

──────────────────────────────────────────────────続 き Continued on the front page (51) Int.Cl. ⁶ Identification code FI C22F 1/00 623 C22F 1/00 623 630 630K

Claims (5)

[Claims] 1. Al-Mg containing Si: 0.2 to 1.8% (% by weight, the same applies hereinafter) and Mg: 0.2 to 1.6%.
-In the Si-based aluminum alloy sheet material, the degree of integration in the cube orientation is 2 to 5 at the surface layer of the sheet and 7 at the 1/4 sheet thickness portion.
An Al-Mg-Si-based aluminum alloy sheet for forming and processing having excellent surface properties, characterized in that: 2. Si: 0.2-1.8%, Mg: 0.2
To 1.6%, Zn: 0.005 to 1.0%, Cu: 0.
005 to 1.0%, Ti: 0.001 to 0.1%, B:
1 to 300 ppm, Be: 0.1 to 100 ppm, Mn: 1.0% or less, Cr: 0.3% or less,
Zr: 0.15% or less, V: One or more of 0.15% or less contained in a total of 0.01 to 1.5%,
In an Al-Mg-Si-based aluminum alloy sheet material comprising the remaining Al and unavoidable impurities, the degree of integration of cube orientation is 2 to 5 in the surface layer portion of the plate and 7 or less in a 1/4 thickness region. Al- for molding with excellent properties
Mg-Si based aluminum alloy sheet material. 3. The degree of integration of the cube orientation is 2 to 3 at the surface layer of the plate.
The Al-Mg-Si-based aluminum alloy sheet material for forming according to claim 1 or 2, wherein the sheet material has a surface thickness of 4 or less and a thickness of 1/4 or less. 4. The Al-Mg-Si based aluminum alloy sheet material for forming according to claim 1, wherein the micro crystal grains have a particle size of 45 μm or less. 5. The Al-Mg-Si-based aluminum alloy sheet which has been subjected to hot rolling, intermediate annealing as required, and then cold rolling. Al-Mg for forming process excellent in the described surface properties
-Si-based aluminum alloy sheet material.