JP2513559B2 - Manufacturing method of aluminum alloy plate with excellent mold galling resistance, scratch resistance and corrosion resistance - Google Patents

Description

Detailed Description of the Invention

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing an aluminum alloy sheet for forming, which is used for parts of various land transportation vehicles typified by automobile body sheets and parts of electric equipment. The present invention relates to a method for producing an aluminum alloy plate which has excellent galling property and scratch resistance and also has good corrosion resistance after painting.

[0002]

2. Description of the Related Art In the past, cold-rolled steel sheets were often used for automobile body sheets, but recently, studies have been conducted on the use of rolled aluminum alloy sheets mainly due to the demand for weight reduction of vehicle bodies. Further, in recent years, the demand for aluminum alloy rolled plates in parts of land vehicles such as automobiles other than body sheets and parts of electric devices such as chassis and panels has been increasing. The rolled aluminum alloy plate used for such forming processing has not only excellent formability, but also good strength, corrosion resistance (especially corrosion resistance after coating), and further pretreatment before coating. Is required,
Not only that, but especially when molding is performed in a mass production system, it is less likely to be scratched during transportation or molding, that is, it has good scratch resistance, and mold galling is less likely to occur during press molding. That is, good mold galling resistance is a very important issue.

By the way, conventionally, as an aluminum alloy for forming for the above-mentioned applications, Al-Mg based JIS 5 is used.
182 alloy O material and 5082 alloy O material are widely known, and in connection therewith, JP-A-62-27544,
JP-A-62-207850, JP-A-1-225783
No. 2, JP-A-2-118049, JP-A No. 2-11805
No. 0, JP-A-55-152160, JP-A-63-17
No. 9043, JP-A-1-198456, JP-A 1-2
19139, JP-A-2-47234, JP-A-2-5
In 7655 and JP-A-2-57656, Al-Mg-is used as an aluminum alloy for molding for similar applications.
Cu-based, Al-Mg-based, and Al-Mg-Cu-Zn-based alloys have been proposed.

[0004]

The above-mentioned 5182 is to be solved.
The alloy O material, the 5082 alloy O material, and each alloy as proposed in the above publication have good moldability and strength, corrosion resistance, and coating undercoating property, but they have excellent scratch resistance and mold galling resistance. I had to say that the points were still insufficient. That is, in the production line of automobile body sheets, aluminum alloy plates are often transported or handled on the same line as the processing line for steel plates, but when transported on the same line as steel plates and handled, they are easily scratched, Therefore, rework is required, which is a cause of hindering improvement in productivity. Since aluminum alloy has a lower Young's modulus and a higher dynamic friction coefficient than steel plates, aluminum sticks to the die when it is pressed by the die, causing galling, which may damage the surface appearance or shape. There was a problem of causing defects and cracks.

The present invention has been made in view of the above circumstances, and as an aluminum alloy plate for molding used for applications such as land transportation vehicles and electric equipment parts, it is particularly resistant to mold galling and scratches as compared with conventional materials. It is an object of the present invention to provide an aluminum alloy sheet which has excellent properties, is as good as the conventional material in terms of moldability and strength, and is also excellent in corrosion resistance after coating.

[0006]

[Means for Solving the Problems] In order to solve the above-mentioned problems, the inventors of the present invention have conducted extensive experiments and researches, and as a result, Zn is basically formed on the surface of an aluminum alloy plate based on Al--Mg system. The plating containing is performed, and then appropriate heat treatment is performed to diffuse Zn into the surface layer of the Al-Mg-based alloy plate to form only the surface layer of the plate as an Al-Mg-Zn-based alloy layer, and By making the Al-Mg-Zn alloy layer into a so-called T4 treated state, and further in a T6 treated state, it is possible to obtain excellent mold galling resistance and flaw resistance, and at the same time, in terms of moldability, strength, and corrosion resistance after coating. The inventors have found that an excellent aluminum alloy plate can be obtained, and have completed the present invention. It has been conventionally practiced to subject the surface of an aluminum alloy for forming to Zn plating, mainly for the purpose of improving the coating undercoating property.
There is a problem that flaking or mold galling that peels off the n-plating is likely to occur, and thus is not a fundamental solution. According to the present invention, not only Zn plating but also Zn plating is followed by appropriate heat treatment.
n is diffused, and the surface layer is treated with T4 or T
It was found that the 6-treatment state can improve the mold galling resistance and the scratch resistance without causing flaking during press molding.

Specifically, the manufacturing method of the invention of claim 1 is
It is for obtaining an aluminum alloy plate for forming that has a surface layer in the T4 state finally, and is an essential alloy.
Al-M containing 2.0 to 8.0% Mg as a component
A plating layer containing Zn in an amount of 5% or more is formed on the surface of the g-based aluminum alloy plate in an amount of Zn of 0.1 g / m ² or more,
Then, heat to 400-580 ° C within 1440 minutes, and
It is characterized by cooling at a cooling rate of 0 ° C./minute or more. The method of the invention of claim 2 is also finally surface layer is used to obtain a molded aluminum alloy plate has a T4 processing state, the same Al-Mg
A plating layer containing Zn in an amount of 5% or more is formed on the surface of the aluminum- based aluminum alloy plate in an amount of Zn of 0.1 g / m ² or more, and then heated to 400 to 580 ° C. within 1440 minutes to obtain 50
Cooling at a cooling rate of less than C / min, and further 350-580
The final annealing is performed by heating to a temperature in the range of 0 ° C. and cooling at a cooling rate of 50 ° C./min or more.

On the other hand, the manufacturing method of the invention of claim 3 is for obtaining an aluminum alloy plate for forming, in which the surface layer is finally in a T6 treated state .
On the surface of the Mg-based aluminum alloy plate, a plating layer containing Zn in an amount of 5% or more is formed in a Zn amount of 0.1 g / m ² or more, and then heated to 400 to 580 ° C. within 1440 minutes, and 50 ° C./minute. After cooling at the above cooling rate, 80 ~
It is characterized in that it is subjected to an artificial aging treatment in which it is heated to a temperature of 200 ° C. for 1 to 40 hours. The method according to claim 4 also is for obtaining a molded aluminum alloy sheet for finally surface layer is in the T6 treatment condition, the
Zn on the surface of a similar Al-Mg-based aluminum alloy plate
The Zn content of the plating layer containing 5% or more is 0.1 g / m
² or more, and then heated to 400 to 580 ° C. within 1440 minutes, cooled at a cooling rate of less than 50 ° C./min, and further heated to a temperature in the range of 350 to 580 ° C. to 50 ° C. /
After performing the final annealing to cool at a cooling rate of more than 5 minutes,
It is characterized in that it is subjected to an artificial aging treatment in which it is heated to a temperature of 0 to 200 ° C. for 1 to 48 hours.

[0009]

In the aluminum alloy sheet of the present invention, the base aluminum sheet (hereinafter referred to as the substrate) includes JIS 5000 series alloys which are excellent in formability and strength as non-heat treatment type alloys for forming use. Al-Mg-based alloy , that is, Mg as an essential alloy component is 2.0 to 8.0.
% Al-Mg based alloy is used. Then, after forming a plating layer containing 5% or more of Zn on the surface of the substrate with a Zn amount of 0.1 g / m ² or more,
Heat treatment is performed by heating at 580 ° C. for 1440 minutes or less. By this heat treatment, Zn in the plating layer is diffused into the surface layer of the substrate, and the plating layer is integrated with the substrate surface layer. Therefore, only the surface layer is equivalent to JIS 7000 series A
A plate made of an 1-Zn-Mg-based alloy and having an Al-Mg-based alloy whose interior corresponds to the No. 5000 series can be obtained. When cooling after the heat treatment for such Zn diffusion is performed at 50 ° C./min or more, the heat treatment also serves as solution treatment-quenching of the Al—Zn—Mg-based alloy of the surface layer. Therefore, if it is aged at room temperature as it is, T for Al-Zn-Mg-based alloy of the surface layer
4 will be in the state of being processed. If the cooling rate after the heat treatment for Zn diffusion is less than 50 ° C / min, then heat to 350 to 580 ° C and perform solution treatment-quenching at 50 ° C / min or more, and perform aging at room temperature. It suffices that the T4 with respect to the Al-Zn-Mg based alloy of the surface layer
It will be in a state where it has been processed.

As described above, only the surface layer of the heat treatment type A
By using the 1-Zn-Mg-based alloy and performing the treatment corresponding to the T4 treatment, only the surface layer is hardened. That is, the Al-Zn-Mg-based alloy of the surface layer is G at room temperature aging from the supersaturated solid solution by solution treatment-quenching.
A P zone is created, which contributes to curing. The aluminum alloy plate having the surface layer thus hardened has excellent scratch resistance and mold galling resistance during molding, and also has good corrosion resistance. On the other hand, the inside remains a non-heat treatment type Al-Mg alloy, and even if the solution treatment-quenching and normal temperature aging are performed as described above, no remarkable hardening due to the formation of the GP zone occurs, and therefore, the formability is high. Etc. are secured similarly to the conventional Al-Mg-based alloy.

Further, after the above-mentioned processing, 80-2
If you give artificial aging treatment by heating at 00 ℃ for 1-48 hours,
The T6 treatment is applied to the Al-Zn-Mg-based alloy of the surface layer. That is, the Al-Zn-Mg-based alloy of the surface layer contains an intermediate phase (η 'phase, T' phase, and Cu, which has a large contribution to the strength due to artificial aging, from the supersaturated solid solution by solution treatment-quenching, through the GP zone. S ′ phase) is generated, and these η ′ phase, T ′
The phase and S'phase further harden the surface layer to further improve mold galling resistance and scratch resistance.

The method for producing the aluminum alloy plate of the present invention will be described in more detail.

As described above, the aluminum plate serving as the substrate basically contains Mg2.0 to 8.0 as an essential alloy component.
%, An Al-Mg-based aluminum alloy may be used, but if necessary, Cu 0.05 to 1.5
%, Zn 0.05 to 2.5%, one or two of
It may be contained, and if necessary, Mn of 0.05 to 0.
6%, Cr 0.05 to 0.3%, Zr 0.05 to 0.3
You may contain 1 type (s) or 2 or more types of%. Less than
The reasons for adding these elements are described in.

Mg: Mg is an alloying element that is a basic Al-Mg alloy for forming and contributes to the improvement of strength and formability. If the amount of Mg is less than 2.0%, sufficient strength and formability cannot be obtained, while if it exceeds 8.0%, the rollability deteriorates and rolling becomes difficult, so Mg is 2.0-8.
It was set within the range of 0%.

[0015] Cu, Zn: These are elements effective in both improving the strength, may be added if necessary either or both. Cu
Is less than 0.05% and Zn is less than 0.05%, the effect of improving strength cannot be sufficiently obtained, while if Cu is more than 1.5% and Zn is more than 2.5%, corrosion resistance is deteriorated. Since the formability decreases, the Cu addition amount is 0.05 to 1.
5%, Zn addition amount is in the range of 0.05 to 2.5%
It is preferable. In addition, less than 0.05% of C as an impurity
u, may contain less than 0.05% Zn
Of course .

Mn, Cr, Zr: Each of these is an element having an effect of refining and stabilizing crystal grains, and if necessary, one kind or two or more kinds are added.
You may add . If the content of Mn is less than 0.05%, the above effect cannot be obtained. On the other hand, if the content of Mn exceeds 0.6% and the content of Cr and Zr exceeds 0.3%, the formability decreases.
Addition amount is within the range of 0.05-0.6%, Cr addition amount, Z
The amount of addition of r is in the range of 0.05 to 0.3% in all cases.
It is preferable. M less than 0.05% as an impurity
n, less than 0.05% Cr, less than 0.05% Zr
Of course, there are cases where it is included .

Other than the above, basically Al and C
Inevitable impurities other than u, Zn, Mn, Cr, and Zr may be used. Here, Fe and Si are typical examples of unavoidable impurities in an aluminum alloy.
Since e forms an Al-Fe (-Si) -based intermetallic compound and causes deterioration of moldability, Fe is preferably less than 0.20%. Si also coexists with Fe
Si is desirable to be less than 0.20% because it produces an l-Fe-Si based intermetallic compound and deteriorates formability, particularly elongation and bendability.

In general aluminum alloys, a small amount of Ti alone or a small amount of T is used for refining ingot crystal grains.
i may be added in combination with a trace amount of B, and addition of Ti, or Ti and B is allowed in the present invention as well. However, if the Ti addition amount exceeds 0.15%, coarse primary crystal TiAl ₃ particles are generated, so that the Ti addition amount is 0.1.
15% or less is desirable, and B together with Ti
When B is added, the amount of B is preferably 500 ppm or less because coarse TiB ₂ particles are generated when the amount of B added exceeds 500 ppm. Further, in the case of an aluminum alloy containing about 2% or more of Mg, a small amount of Be may be added to prevent the oxidation of the molten metal. In the case of the present invention, however, if Be is added in an amount of 500 ppm or less, other performances are It does not deteriorate.

Next, each process of the manufacturing method of the present invention will be described.

The process of forming an aluminum alloy having the above-described composition into a substrate having a required product thickness, that is, Z
The process up to the point of applying the plating containing n is the conventional Al
-The process applied to the Mg-based alloy may be applied. That is, the aluminum alloy having the above-mentioned composition is
Casting may be performed by a C casting method (semi-continuous casting method) or the like, and the obtained ingot may be homogenized, and then hot-rolled and cold-rolled to obtain a required plate thickness. Then, intermediate annealing may be performed between the hot rolling and the cold rolling or in the middle of the cold rolling.

The homogenization treatment is carried out to eliminate inhomogeneity of the ingot to improve the formability and stabilize the recrystallized grains, and at a temperature in the range of 400 to 570 ° C. It is desirable to keep heating for 0.5 to 48 hours. If the homogenization temperature is lower than 450 ° C, the above-mentioned effects cannot be sufficiently obtained, while if it exceeds 570 ° C, eutectic melting may occur. Further, if the heating time of the homogenization treatment is less than 0.5 hours, the above-mentioned effects cannot be sufficiently obtained, while if it exceeds 48 hours, the economical efficiency is only impaired. In addition, intermediate annealing performed as necessary between hot rolling and cold rolling or in the middle of cold rolling is effective in improving cold rolling property by recrystallizing and controlling crystal grains, Either a batch type annealing furnace or a continuous annealing furnace may be used, but in the case of a batch type annealing, it is preferable to perform heating and holding at 300 to 450 ° C. for 0.5 to 24 hours. In this case, if the heating temperature is less than 300 ° C. or the holding time is less than 0.5 hours, recrystallization does not occur. On the other hand, if the heating temperature exceeds 450 ° C., high-temperature oxidation of Mg becomes severe, deteriorating the surface properties and economical efficiency. Is worse, and even if the holding time exceeds 24 hours, it is economically wasteful. 3 if intermediate annealing is performed by continuous annealing
It is preferable to heat to 50 to 580 ° C. and set the condition of no holding or holding within 5 minutes. In this case, if the heating temperature is less than 350 ° C, recrystallization does not occur, and if it exceeds 580 ° C, M
There is a possibility that eutectic melting may occur as a result of violent high-temperature oxidation of g and the eutectic melting. Further, if the holding time exceeds 5 minutes, the crystal grains become coarse and the economical efficiency deteriorates.

The aluminum plate as a substrate having the required plate thickness as described above is then electroplated,
Z by hot dip plating, chemical plating (electroless plating), etc.
A plating layer containing 5% or more of n is formed. This plated layer need only contain 5% or more of Zn. Therefore, in addition to a pure Zn plated layer, a Zn-Fe alloy plated layer, a Zn-Ni alloy plated layer, a Zn-Mn alloy plated layer, etc. Is also good. In the case of a Zn-Fe alloy plating layer, Fe is 10-80.
%, And in the case of a Zn—Ni alloy plated layer, Ni is preferably in the range of 1 to 20%, and in the case of a Zn—Mn plated layer, Mn is also 1 to 10%. It is preferably within the range. Here, if the Zn content of the plating layer is less than 5%, the Zn content of the surface layer after diffusion is too small to sufficiently harden the surface by heat treatment (or further artificial aging treatment), Therefore, mold galling resistance and scratch resistance are not sufficiently improved. In addition, this plating layer has an adhesion amount (thickness) of Zn
The amount should be 0.1 g / m ² or more.
If the amount of adhesion is less than 0.1 g / m ² , the Zn content of the surface layer after diffusion is too small to sufficiently harden the plate surface as described above, resulting in sufficient mold galling resistance and scratch resistance. I can not get sex. Before the plating containing 5% or more of Zn in this way, an arbitrary pretreatment such as a zincate treatment may be performed in advance on the substrate surface.

After plating, Zn in the plating layer is diffused into the surface layer of the substrate, and a heat treatment for forming an Al-Zn-Mg-based alloy layer is performed. This heat treatment is 400-580
Perform at 1440C for 1440 minutes or less. If the temperature is lower than 400 ° C, the diffusion is insufficient and the surface of the plate is insufficiently cured. On the other hand, if the temperature is higher than 580 ° C or the heat treatment time is longer than 1440 minutes, the diffusion is excessive and the inside of the plate is cured. As a result, the formability decreases, the entire plate becomes brittle, and the corrosion resistance also decreases. Here, the diffusion layer, that is, Al-Z
It is desirable that the thickness of the surface layer made of the n-Mg-based alloy be within 20% of the plate thickness per one side. The heat treatment may be performed in a batch type furnace or a continuous furnace such as a continuous annealing furnace. When using a batch type furnace, it is preferable to maintain the temperature at 10 minutes or more, and when using a continuous furnace, it is desirable to maintain the temperature at 460 ° C. or higher for 10 seconds or more and 10 minutes or less, but at a high temperature. If you don't hold it

If the cooling rate after the heat treatment for Zn diffusion as described above is less than 50 ° C./min, then 3 for solution treatment of the surface layer (Al--Zn--Mg alloy layer).
Final annealing is performed at 50 to 580 ° C, and rapid cooling (quenching) is performed at a cooling rate of 50 ° C / min or more. If the temperature of this final annealing is less than 350 ° C., solution treatment of Zn and Cu is insufficient, and finally sufficient hardness cannot be obtained. On the other hand, if it exceeds 580 ° C., not only the solutionizing effect is saturated, There is a risk of eutectic melting. If the cooling rate after the final annealing is less than 50 ° C / min,
Grain boundary precipitation of Cu and Zn occurs during cooling, which reduces strength and formability, particularly elongation corrosion resistance. The holding time is not particularly limited, but it is sufficient if it is within the time specified in JIS H6088.

On the other hand, when the cooling rate after the heat treatment for diffusion of Zn is rapid cooling of 50 ° C./min or more, the object of solution treatment-quenching is achieved by the heat treatment and the subsequent rapid cooling. It is not necessary to perform the final annealing again for the solution treatment as described above.

After forming the Zn-containing plated layer in this way, solution treatment-quenching is performed in combination with the heat treatment for Zn diffusion, or the solution is treated as a final annealing after the heat treatment for Zn diffusion. Chemical treatment-Altering the surface layer by quenching and aging at room temperature
The Zn-Mg-based alloy is in a state of being subjected to so-called T4 treatment. Even as it is, the surface layer is considerably hardened, so even if it is as it is, the mold galling resistance and the scratch resistance are superior to those of the conventional Al-Mg alloys for ordinary forming, but further artificial aging treatment should be performed. This makes it possible to further increase the hardness of the surface layer.

This artificial aging treatment is carried out at 80-200 ° C. for 1-
The condition is 48 hours. If the temperature is less than 80 ° C. and the time is less than 1 hour, the surface layer is not sufficiently cured, while if the temperature exceeds 200 ° C., overaging causes a decrease in strength, a decrease in moldability, and an embrittlement. Even if the time exceeds 48 hours, it is economically wasted, and especially over 48 hours at a high temperature, overaging occurs. In addition, when the artificial aging treatment as described above is performed, before solution treatment-quenching to artificial aging. Room temperature between
By pre-aging at a low temperature of less than 80 ° C., it is possible to further harden the surface layer. This preliminary aging is preferably at least 1 day at room temperature, and 2 if heated.
It is preferably from 48 hours to 48 hours.

Further, after the solution treatment-quenching which also serves as the heat treatment for Zn diffusion as described above-the quenching, or the final annealing, the strain of the plate may be corrected if necessary. As such a correction process, any means such as stretching and leveling can be applied.

[0029]

Example Al-4.41 corresponding to JIS 5182
% Mg-0.02% Cu-0.18% Fe-0.15%
An alloy composed of Si-0.28% Mn was cast by DC casting, homogenized at 500 ° C. for 5 hours, hot-rolled to a thickness of 3 mm, and cold-rolled to a thickness of 1 mm.
mm. Then, a plating layer as shown in Table 1 was formed on the surface of this plate by ordinary electroplating, and then Zn
The heat treatment for diffusion was performed under the conditions shown in Table 1, and the final annealing (solution treatment) was also performed under the same conditions shown in Table 1 except for a part. Then, an artificial aging treatment was performed under the conditions shown in Table 1 except for some of them.

With respect to each plate after the above-mentioned treatment, the hardness of the surface of the rolled surface was measured, and the surface of the rolled surface was etched to obtain hardness at each position at a depth of 50 to 500 μm from the surface of the rolled surface. Was measured to examine the hardness distribution in the thickness direction.
The results are shown in Table 2. In addition, a bending test and an Erichsen test were performed as a formability evaluation. Bending test is 18
The 0 ° minimum bend radius was investigated. Furthermore, the mold galling resistance and the corrosion resistance after coating were examined. The mold galling resistance was determined by using a Z-5 lubricating oil manufactured by Nippon Machine Oil Co., Ltd. and conducting a cylindrical drawing test of 50 mmφ 50 times in succession to generate scratches and flaking due to mold galling on the die (plate surface layer It was evaluated based on the presence or absence of flaky peeling). Corrosion resistance after coating was evaluated by subjecting a plate that had been subjected to chemical conversion treatment with zinc phosphate as a coating base treatment, followed by electrodeposition coating and then baking coating to a thread rust test to determine the length of thread rust that occurred. It was evaluated by. Specifically, scratches were put on the baking coated surface with a cutter knife, a corrosion test was performed in accordance with ASTM, and the length of thread rust generated in the scratched portion was examined by a loupe. Table 3 shows the results. Table 3
Condition No. in As a reference example, 13 shows the results of examining each characteristic of the steel sheet.

[0031]

[Table 1]

[0032]

[Table 2]

[0033]

[Table 3]

As is apparent from Tables 2 and 3, the condition No. 1 according to the method of the present invention was used. 1-No. 4, No. In the case of No. 11, only the surface had a high hardness, and the moldability was good, and at the same time, the galling resistance was excellent as with the steel sheet, and the corrosion resistance after coating was also good. Although the scratch resistance was not particularly investigated, it is clear that the scratch resistance is also good because the surface is hard and the mold galling resistance is excellent.

On the other hand, the condition No.
In No. 5, the moldability was good, but the surface was not sufficiently cured, the mold galling resistance was poor, and the corrosion resistance after coating was also poor. In addition, the condition No. In No. 6, the temperature of the heat treatment for diffusion of Zn was too low. In this case, the moldability and the corrosion resistance after coating were good, but since Zn was not sufficiently diffused in the surface layer, the surface was It was not sufficiently cured, the mold galling resistance was poor, and flaking also occurred.
Condition No. In No. 7, the heat treatment temperature for Zn diffusion was too high. In No. 8, the heating time for diffusion of Zn was too long, but in all of these cases, the interior was hardened, the moldability became poor, and the corrosion resistance after coating deteriorated. Condition No. In No. 9, the temperature of the artificial aging treatment was too high, but in this case, the hardness of the surface layer was lowered by the overaging, so that the mold galling resistance was deteriorated and the moldability was also lowered. Condition No. 10 is Zn
The cooling rate after the heat treatment for diffusion is slow, and further, the solution treatment as the final annealing-quenching is not performed, but in this case, the surface layer is not cured at all and the mold galling resistance is also high. It was bad. Further condition No. No. 12 has an adhesion amount of the plating layer of Fe-10% Zn alloy of 0.5 g / m
^{Since the} amount of Zn was ² and the amount of Zn was as small as 0.05 g / m ² , the surface was not sufficiently hardened, and the mold galling resistance and corrosion resistance were poor.

[0036]

As is clear from the examples, according to the manufacturing method of the present invention, the moldability and strength are not impaired.
It is possible to obtain an aluminum alloy plate for forming which is superior in die galling resistance during press working, scratch resistance and corrosion resistance after painting, compared to the Al-Mg alloy plate used for forming in the past. Therefore, it is most suitable for manufacturing aluminum alloy plates used for automobile body seats and other parts for land transportation vehicles, or as cases and chassis for various electric devices.

Claims (4)

(57) [Claims] 1. An essential alloying component of 2.0 to 8.0%
A plating layer containing 5% or more of Zn is formed on the surface of an Al-Mg-based aluminum alloy plate containing (wt%, the same applies hereinafter) Mg in a Zn amount of 0.1 g / m ² or more. Then, heat to 400 to 580 ° C within 1440 minutes to obtain 50 ° C /
A method for producing an aluminum alloy sheet having excellent mold galling resistance, scratch resistance, and corrosion resistance during press forming, which is characterized by cooling at a cooling rate of not less than a minute. 2. An essential alloying component of 2.0 to 8.0%
On the surface of the Al-Mg-based aluminum alloy plate containing Mg, a plating layer containing Zn in an amount of 5% or more was added in a Zn amount of 0.
1 g / m ² or more, and then at 400 to 580 ° C for 14
A final anneal of heating within 40 minutes, cooling at a cooling rate of less than 50 ° C./minute, further heating to a temperature in the range of 350 to 580 ° C. and cooling at a cooling rate of 50 ° C./minute or more is performed. A characteristic method of manufacturing aluminum alloy sheets with excellent mold galling resistance, scratch resistance, and corrosion resistance during press forming. 3. An essential alloying component of 2.0 to 8.0%
On the surface of the Al-Mg-based aluminum alloy plate containing Mg, a plating layer containing Zn in an amount of 5% or more was added in a Zn amount of 0.
1 g / m ² or more, and then at 400 to 580 ° C for 14
An artificial aging treatment of heating within 40 minutes, cooling at a cooling rate of 50 ° C./minute or more, and then heating at a temperature of 80 to 200 ° C. for 1 to 48 hours is performed. A method of manufacturing aluminum alloy sheets with excellent mold galling, scratch resistance, and corrosion resistance. 4. An essential alloy component of 2.0 to 8.0%
On the surface of the Al-Mg-based aluminum alloy plate containing Mg, a plating layer containing Zn in an amount of 5% or more was added in a Zn amount of 0.
1 g / m ² or more, and then at 400 to 580 ° C for 14
Heating within 40 minutes, cooling at a cooling rate of less than 50 ° C./min, further heating to a temperature in the range of 350 to 580 ° C. and cooling at a cooling rate of 50 ° C./min or more. A method for producing an aluminum alloy plate excellent in mold galling resistance, scratch resistance and corrosion resistance during press forming, characterized by performing artificial aging treatment of heating at a temperature of 80 to 200 ° C for 1 to 48 hours.