JP2018123376A - Aluminum alloy sheet and manufacturing method therefor - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide an aluminum alloy sheet capable of reducing variation of flange length and a manufacturing method therefor.SOLUTION: There is provided an aluminum alloy sheet containing 0.05 to 0.60 mass% of Si, 0.05 to 0.80 mass% of Fe, 0.05 to 0.25 mass% of Cu, 0.80 to 1.50 mass% of Mn, 0.80 to 1.50 mass% of Mg, Al and inevitable impurities, 45° ear rate of a primary contraction cup in the aluminum alloy sheet is 2.0% or less, and value deducting the 45° ear rate from 0-180° ear rate of the primary cup in the aluminum alloy sheet is -1.0% to 2.0%.SELECTED DRAWING: None

Description

  The present disclosure relates to an aluminum alloy plate and a manufacturing method thereof.

  The aluminum alloy plate for DI molded can bodies is used for beverage cans and the like. An aluminum alloy plate for a DI molded can body is usually manufactured by subjecting an aluminum alloy ingot specified in JIS 3004 or JIS 3104 to a homogenization treatment, hot rolling, and cold rolling in this order. After the cold rolling, if necessary, further degreasing, cupping lubricant application, etc. are performed.

  The ear ratio is a ratio of the height difference (ear) between the convex portion and the concave portion generated at the peripheral edge when the rolled disc is squeezed into a cup shape to the cup height. When the ear rate is large, various problems occur. Problems include (1) pinholes and tear-off (fuselage cracking) during ironing due to the chip that peels off from the tip of the ear during cup molding, and (2) reduced dimensional accuracy of the can after flange molding (3) The problem that it is necessary to increase the trimming amount after molding the can body, and (4) the problem that the recesses at the peripheral edge of the can cannot be completely removed even after trimming.

  In addition, with the recent reduction in diameter of cans, ears also occur after necking, and this ear causes a new problem that the flange length varies in the subsequent flange processing and the can lid cannot be tightened well. Yes.

  The magnitude of the ear ratio in the aluminum alloy plate is affected by the crystallographic anisotropy of the aluminum alloy plate. More specifically, a balance between a cubic orientation recrystallized texture component (0-90 ° ears) formed after the end of hot rolling and a cold-rolled texture component (45 ° ears) formed by cold rolling. The ear rate is small when there is a lot of. In recent years, since the cold working degree is increased to increase the strength of the can in response to the thinning of the can body, the rolling texture component tends to increase.

  The technique described in Patent Document 1 proposes a method of preferentially growing cubic orientation recrystallized grains by regulating the homogenization, temperature conditions of hot rolling, etc., controlling the dispersion state of precipitates.

JP-A-11-140576

With the recent reduction in diameter of cans, there is a strict demand for reducing variations in flange length. In the prior art, it has been difficult to sufficiently reduce the variation in flange length.
An object of one aspect of the present disclosure is to provide an aluminum alloy plate that can reduce variations in flange length and a method for manufacturing the same.

  One embodiment of the present disclosure includes 0.05 to 0.60 mass% Si, 0.05 to 0.80 mass% Fe, 0.05 to 0.25 mass% Cu, and 0.80 to 0.80 mass%. 1. An aluminum alloy plate containing 50% by mass of Mn, 0.80 to 1.50% by mass of Mg, Al, and inevitable impurities, wherein 45 of the primary drawn cup in the aluminum alloy plate The ear ratio is 2.0% or less, and the value obtained by subtracting the 45 ° ear ratio from the 0-180 ° ear ratio of the primary drawn cup in the aluminum alloy plate is −1.0% or more and 2.0%. It is the following aluminum alloy plate.

The aluminum alloy plate that is one embodiment of the present disclosure can reduce variations in flange length.
Another aspect of the present disclosure includes 0.05 to 0.60 wt% Si, 0.05 to 0.80 wt% Fe, 0.05 to 0.25 wt% Cu, and 0.80. ~ 1.50 mass% Mn, 0.80 to 1.50 mass% Mg, Al, and an ingot of aluminum alloy containing inevitable impurities are homogenized, and a reversing mill is used. The hot rough rolling was performed under the conditions that the end temperature was 400 to 500 ° C., the last pass rolling reduction was 5 to 40%, and the strain rate of the last pass was 5 to 30 s ^−1. Is a method for producing an aluminum alloy sheet, in which hot finish rolling is performed and cold rolling is performed under a condition where the rolling reduction is 80 to 90%.

  According to the method for manufacturing an aluminum alloy plate according to another aspect of the present disclosure, variations in flange length in the manufactured aluminum alloy plate can be reduced.

An embodiment of the present disclosure will be described.
1. Aluminum alloy plate (1) Alloy component of aluminum alloy plate The aluminum alloy plate is composed of 0.05 to 0.60 mass% Si, 0.05 to 0.80 mass% Fe, and 0.05 to 0.25. It contains Cu of mass%, 0.80 to 1.50 mass% of Mn, 0.80 to 1.50 mass% of Mg, Al, and unavoidable impurities.

  Si causes a phase transformation in the Al—Mn—Fe-based crystallized product to form an Al—Mn—Fe—Si-based compound with higher hardness. The Al—Mn—Fe—Si based compound has a solid lubricating action. By forming the Al—Mn—Fe—Si based compound, ironing processability is improved.

By containing an appropriate amount of Si, when DI molding is performed, build-up due to adhesion between the alloy mold and the mold can be suppressed.
When the Si content is 0.05% by mass or more, the effect of suppressing the build-up is even higher. Moreover, when the content of Si is 0.05% by mass or more, it is not necessary to excessively increase the purity of the aluminum ingot, and the cost can be reduced.

  When the Si content is 0.60% by mass or less, the ear ratio can be further reduced. The reason is as follows. When the content of Si is 0.60% by mass or less, precipitation of a fine α-AlMnFeSi phase during hot rolling can be suppressed. The α-AlMnFeSi phase has an effect of inhibiting recrystallization after the end of hot rolling. By suppressing the precipitation of the α-AlMnFeSi phase, recrystallization after the end of hot rolling is promoted, and the ear ratio can be further reduced.

  Fe promotes crystallization of Mn and makes the distribution state uniform to improve ironing workability. The reason why Fe improves ironing workability is that Fe forms a compound such as an Al—Mn—Fe type or Al—Mn—Fe—Si type having a solid lubricating action.

  When the Fe content is 0.05% by mass or more, the ironing workability is further improved. Moreover, when content of Fe is 0.05 mass% or more, it is not necessary to raise the purity of an aluminum ingot excessively, and cost reduction is realizable.

  When the content of Fe is 0.80% by mass or less, it is possible to suppress the generation of a huge Al—Mn—Fe primary crystal compound by combining Fe and Mn during melt casting. As a result, it is possible to prevent the huge Al—Mn—Fe primary crystal compound from remaining after rolling and generating cracks and pinholes during DI molding.

  Cu contributes to improving the strength of the aluminum alloy plate. When the Cu content is 0.05% by mass or more, the strength of the aluminum alloy plate is further improved. If the strength of the aluminum alloy plate is further improved, sufficient pressure strength can be obtained in DI molding.

  When content of Cu is 0.25 mass% or less, it can suppress that the intensity | strength of an aluminum alloy plate becomes high too much. As a result, the ironing workability of the aluminum alloy plate can be further improved.

  Mn is an element that contributes to the improvement of the strength of the aluminum alloy plate and the formation of the crystallized matter described above, and contributes to the improvement of ironing workability. When the Mn content is 0.80% by mass or more, the ironing workability of the aluminum alloy plate is further improved. Moreover, when content of Mn is 0.80 mass% or more, the intensity | strength of an aluminum alloy plate improves further. If the strength of the aluminum alloy plate is further improved, sufficient pressure strength can be obtained in DI molding.

  When the content of Mn is 1.40% by mass or less, it is possible to suppress the generation of a huge Al—Mn—Fe primary crystal compound by combining Fe and Mn during melt casting. As a result, it is possible to prevent the huge Al—Mn—Fe primary crystal compound from remaining after rolling and generating cracks and pinholes during DI molding.

  Mg contributes to improving the strength of the aluminum alloy plate. When the Mg content is 0.80% by mass or more, the strength of the aluminum alloy plate is further improved. If the strength of the aluminum alloy plate is further improved, sufficient pressure strength can be obtained in DI molding.

When the content of Mg is 1.50% by mass or less, the aluminum alloy plate is difficult to work harden. As a result, the frequency of occurrence of cracking is reduced by ironing during DI molding.
Al is the main component of the aluminum alloy plate. For example, Al is a balance other than Si, Fe, Cu, Mn, Mg, and unavoidable impurities in an aluminum alloy plate.

(2) Ear rate As ear rates, there are a 45 ° ear rate of the primary iris cup and a 0-180 ° ear rate of the primary iris cup. These ear ratios affect the flange width variation (hereinafter sometimes simply referred to as flange width variation) in a can body formed by DI molding and neck molding of an aluminum alloy plate.

  When the 45 ° ear ratio of the primary throttle cup is 2.0% or less, the variation in the flange width can be further reduced. When the value obtained by subtracting the 45 ° ear rate from 0-180 ° ear rate is −1.0% or more, the variation in the flange width can be further reduced.

  When the value obtained by subtracting the 45 ° ear rate from the 0-180 ° ear rate is 2.0% or less, the pin is pinned by a chip that peels off from the ear tip when the DI can is cup-molded due to the 0-180 ° ear standing too much. It is possible to suppress the occurrence of tear-off (fuselage cracking) during hole or ironing.

  When the can height of the can body formed by DI molding and neck molding of the aluminum alloy plate is measured over the entire circumference, the difference between the maximum value and the minimum value in the can height is preferably 0.080 mm or less. In that case, the variation in the flange width is suppressed, and the winding with the can lid can be performed well. The difference between the maximum value and the minimum value is a variation in neck height in an embodiment described later.

2. Manufacturing method of aluminum alloy plate (1) Outline of manufacturing method In the manufacturing method of an aluminum alloy plate of the present disclosure, an ingot of an aluminum alloy is homogenized, and hot rough rolling is performed using a reversing mill. Hot finish rolling is performed using a hot rolling mill, and cold rolling is performed.

(2) Aluminum alloy ingot An aluminum alloy ingot can be produced, for example, by a DC casting method (semi-continuous casting method). The aluminum alloy ingot is composed of 0.05 to 0.60 mass% Si, 0.05 to 0.80 mass% Fe, 0.05 to 0.25 mass% Cu, and 0.80 to 0.80 mass%. 1.50 mass% Mn, 0.80-1.50 mass% Mg, Al, and an unavoidable impurity are contained. The composition of the ingot is the same as that of the aluminum alloy plate described above, for example.

(3) Homogenization process It is preferable to perform a homogenization process for 2 to 48 hours, for example at the temperature of 580-610 degreeC. When the temperature is 580 ° C. or higher and the time is 2 hours or longer, homogenization can be sufficiently performed. As a result, the progress of recrystallization after the end of hot rolling is hardly inhibited, and the 45 ° ear of the cold-rolled sheet can be prevented from becoming too high.

  When the temperature is 610 ° C. or lower, it is possible to suppress the occurrence of streak pattern defects (defects called “flow marks”) visually recognized on the outer surface of the can side wall after DI molding. The flow mark is caused by swelling on the surface of the ingot, and the defects remain up to the cold rolled sheet. When the time is within 48 hours, the productivity of the aluminum alloy plate is improved and the manufacturing cost is reduced.

(4) Hot rough rolling It is preferable that the end temperature of hot rough rolling is 400-550 degreeC, for example. When it is 400 ° C. or higher, the amount of the rolling texture brought into the hot finish rolling is suppressed, and the 0-90 ° ear of the hot rolled sheet is suppressed. When it is 550 ° C. or lower, it can be suppressed that the surface of the hot-rolled sheet is oxidized and the surface quality is deteriorated. As a result, it can suppress that a flow mark arises on a can side wall. Moreover, when it is 550 degrees C or less, the rolling texture brought in by hot finish rolling increases.

  The last pass reduction ratio in the hot rough rolling is preferably 5.0 to 40%, for example. When it is 5.0% or more, recrystallization at the end of rolling is appropriately controlled, a desired rolling texture is brought into hot finish rolling, and the 0-90 ° ear of the hot rolled sheet becomes excessively high. Is suppressed. Moreover, when it is 5.0% or more, since the number of passes may be small, the productivity of the aluminum alloy plate is improved.

When it is 40% or less, the progress of recrystallization at the end of rough rolling is suppressed, the rolling texture brought into hot finish rolling is increased, and the 0-90 ° ear of the hot rolled sheet becomes high. .
The strain rate of the last path in hot rough rolling is preferably 5.0 to 30 s ⁻¹ . When it is 5.0 s ^-1 or more, recrystallization at the end of rolling is appropriately controlled, a desired rolling texture is brought into hot finish rolling, and the 0-90 ° ear of the hot rolled sheet becomes excessively high. It is suppressed. Moreover, when it is 5.0 s ^-1 or more, the rolling time can be suppressed, and the productivity of the aluminum alloy sheet is improved.

If it is 30 s ^-1 or less, the progress of recrystallization at the end of rough rolling is suppressed, the rolling texture brought into hot finish rolling increases, and the 0-90 ° ear of the hot rolled plate becomes high. , Variation in flange width is reduced. Hot rough rolling can be performed using, for example, a reversing mill.

(5) Hot finish rolling Hot finish rolling finishes an aluminum alloy sheet to a predetermined dimension. The structure after completion of hot finish rolling becomes a recrystallized structure by the self-annealing.

  In hot finish rolling, for example, a tandem hot rolling mill can be used. When a tandem hot rolling mill is used, the number of passes can be reduced as compared with a case where a reversing mill is used. Therefore, recrystallization that occurs between passes can be suppressed, and as a result, the 0-90 ° ear of the hot-rolled sheet can be sufficiently developed.

  The end temperature in hot finish rolling is preferably 300 to 400 ° C. When the temperature is 300 ° C. or higher, the recrystallization rate after cooling to room temperature can be further increased, and as a result, the shortage of recrystallized grains in the cubic orientation can be suppressed. When it is 400 ° C. or lower, seizure and rough skin can be suppressed, and the surface properties of the hot-rolled sheet can be improved. As a result, it can suppress that a flow mark arises on a can side wall.

  The total rolling reduction in hot finish rolling is preferably 80 to 95%. When it is 80% or more, the accumulation of the rolling texture can be promoted, the cube orientation density can be increased at the time of coiling up after hot finish rolling, and the 45 ° ear ratio can be reduced. When it is 95% or less, the 0-90 ° ear of the hot-rolled sheet can be prevented from becoming excessively high. Moreover, when it is 95% or less, it can suppress that a flow mark arises in a can side wall by improving the surface property of a hot-rolled sheet.

(6) Cold rolling
Cold rolling provides the strength required for a can body. The rolling reduction in cold rolling is preferably 80 to 90%. When it is 80% or more, the strength of the aluminum alloy plate is further improved. If the strength of the aluminum alloy plate is further improved, sufficient pressure strength can be obtained in DI molding.

  When it is 90% or less, the strength of the aluminum alloy plate is not excessively high, and therefore it is possible to suppress the occurrence of cupping cracks and can bottom cracks during DI molding. Moreover, when it is 90% or less, a 45 degree ear becomes low.

(7) Characteristics of manufactured aluminum alloy sheet An aluminum alloy sheet manufactured by the method for manufacturing an aluminum alloy sheet of the present disclosure has the following characteristics, for example.

(A) The 45 ° ear ratio of the primary drawn cup in the aluminum alloy plate is 2.0% or less.
(B) The value obtained by subtracting the 45 ° ear rate from the 0-180 ° ear rate of the primary drawn cup in the aluminum alloy plate is −1.0% or more and 2.0% or less.

  (C) When the can height of the can body formed by DI molding and neck molding of the aluminum alloy plate is measured over the entire circumference, the difference between the maximum value and the minimum value in the can height is 0.080 mm or less. The difference between the maximum value and the minimum value is a variation in neck height in an embodiment described later.

  The reason why the aluminum alloy plate has the above-mentioned characteristics is presumed as follows. The inventor of the present invention has found that the rolling texture during the hot rolling promotes the growth of recrystallized grains in the cubic orientation in a process called “self-annealing” in which recrystallization proceeds after hot rolling. It was. The above-described ingot homogenization treatment conditions, hot rolling conditions, and the like are conditions that facilitate the development of the rolling texture by hot rolling. According to the manufacturing method of the present disclosure, the variation in the flange length can be reduced by developing the rolling texture component after hot rolling and increasing the density of the cube orientation component during self-annealing.

(8) Use of aluminum alloy plate The aluminum alloy plate of the present disclosure can be, for example, an aluminum alloy plate for a DI molded can body. Moreover, you may use the aluminum alloy plate of this indication for another use.

3. Examples Hereinafter, the present disclosure will be described in detail by way of examples. In addition, this indication is not limited to this Example.

(1) Manufacture of aluminum alloy plate The alloy components shown in Table 1 were melted and cast by a conventional method to obtain alloys (plate-shaped ingots) A to D having a thickness of 500 mm. Next, the alloys A to D were chamfered to a thickness of 470 mm.

Next, using these alloys A to D, a homogenization treatment, hot rough rolling, hot finish rolling, and cold rolling were sequentially performed.
Table 2 shows the conditions for homogenization, hot rough rolling, hot finish rolling, and cold rolling (hereinafter referred to as production conditions). Production conditions include a to j. The following matters are common to all manufacturing conditions. The hot rough rolling was performed using a single reverse mill having a work roll diameter of 930 mm. Hot finish rolling was performed using a 4-stand tandem rolling mill. Cold rolling was performed by a conventional method.

  The strain rate of the last pass in the hot rough rolling in Table 2 is a value calculated in Equation (1).

  V in Formula (1) is a rolling speed (mm / s). The equivalent strain ε in equation (1) is a value represented by equation (2).

  R in Formula (1) is a work roll radius (mm). The plate thickness t ′ before the last pass in equation (1) is a value represented by equation (3).

T in Formula (1) and Formula (3) is the rough heat extension side plate thickness (mm). In Equation (3), r is the last path reduction rate (%).
Table 3 shows combinations of alloy types and manufacturing conditions. Hereinafter, a combination of the type of alloy and manufacturing conditions is referred to as a manufacturing method. In the manufacturing method, No. There are 1-24.

No. Cold rolled sheets having a thickness of 0.29 mm were obtained by the manufacturing methods 1 to 24, respectively. This cold-rolled plate corresponds to an aluminum alloy plate.
(2) Evaluation of aluminum alloy sheet About the manufactured cold rolled sheet, the ear rate, the neck height variation, the ironing formability, the pressure strength, and the surface property were evaluated. The evaluation methods and evaluation criteria are as follows.

(2-1) Ear ratio A sample having a blank diameter of 57 mm was deep-drawn with an Erichsen tester. The diameter of the punch is 33 mm and the shoulder R of the punch is 2.5 mm. The wrinkle holding force was 300 kgf. The height of the cup was measured every 22.5 ° with respect to the rolling direction.

A 45 ° ear rate and a 0-180 ° ear rate were calculated according to the following equations.
45 ° ear rate (%) = (45 ° position height average−average height) / average height × 100
0-180 ° ear rate (%) = (0 ° position / 180 ° position height average−average height) / average height × 100
In addition, "45 degree position height" means the cup ear height which appears in the position which makes an angle of 45 degrees from the rolling direction among Eriksen cup ears. “45 ° position height average” means an average value of four “45 ° position height” appearing in one cup. “Average height” means an average value of 16 cup heights obtained by measuring the height of the Erichsen cup in increments of 22.5 ° from the rolling direction. “Average of 0 ° position / 180 ° position height” means the average value of the heights of two cup ears appearing at the positions of 0 ° and 180 ° from the rolling direction.

(2-2) Neck Height Variation A disc having a blank diameter of 140 mm was DI molded so that the inner diameter of the can body was 66 mm. Next, the ears of the opening were trimmed. Next, neck molding in which the neck inner diameter was 57 mm was performed. The height of the can after neck formation was measured every 22.5 °. In addition, said blank diameter, can cylinder inner diameter, and neck inner diameter were determined based on the shape of the can cylinder generally used in Japan. Among the averages of 0 °, 22.5 °, 45 °, 67.5 °, and 90 ° position height, the difference between the maximum value and the minimum value was defined as the neck height variation. Neck height variation is an index of flange width variation. The neck height variation is preferably 0.080 mm or less.

(2-3) Ironing formability A disc having a blank diameter of 140 mm was DI molded so as to have an inner diameter of 66 mm. At this time, a severe ironing molding test was performed in which a punch whose outer diameter increases as it approaches the can opening from the bottom of the can and forcibly causes the can to run out. The limit ironing rate was calculated from the average value of the can side wall thickness when the can was cut in the 10 can test. The limiting ironing rate is an index of ironing formability.

Limit ironing rate (%) = (original plate thickness-can side wall thickness when the can is cut) / original plate thickness x 100
A mark with a marginal ironing ratio of 46% or more was rated as ○. Moreover, the limit ironing rate was less than 46%, or the case where the can molding could not be performed due to the occurrence of the cupping crack or the can bottom crack during the DI molding was evaluated as x.

(2-4) Compressive strength The DI molded can was baked at 200 ° C. for 20 minutes. Next, the pressure at which the bottom of the dome-shaped can material buckled with an air pressure tester was measured. A sample having a pressure of 6.0 kgf / cm ² or more was evaluated as “◯”, and a sample having a pressure less than 6.0 kgf / cm ^{2 was} evaluated as “X”.

(2-5) Surface properties The strength of the flow mark was determined by visual observation, and the case where no defect was visually recognized was evaluated as ◯, and the case where the defect was easily visually recognized was evaluated as x.

The evaluation results for each item are shown in Table 3 above.
In No. 1-10, all of the ear rate, the neck height variation, the ironing formability, the pressure strength, and the surface properties were good. The aluminum alloy plate manufactured by No. 1-10 had a suitable texture.

  The aluminum alloy plates manufactured in Nos. 1 to 10 have small variations in flange length, and can be tightly wound on the can lid. Moreover, the aluminum alloy plate manufactured by No. 1-10 has the characteristic desirable as an object for can bodies in a pressure-resistant strength, ironing formability, surface properties, and the like. The manufacturing method of No. 1-10 can be easily implemented by a conventional method by limiting hot rolling conditions. Therefore, there is an industrially significant effect.

  In No. 11, since the amount of Si was excessive, the recrystallization rate of the hot-rolled sheet was low, the strength was high, and the ironing formability was deteriorated. Also, the 45 ° ear rate was high, and the neck height variation was large.

In No. 12, since the amount of Fe was excessive, a huge crystallized product was generated, and the ironing moldability deteriorated.
In No. 13, since the amount of Cu was too small, the strength was low and the pressure strength deteriorated.

In No. 14, since the amount of Cu was excessive, the strength became too high and the ironing formability deteriorated.
In No. 15, since the amount of Mn was too small, the strength was insufficient and the pressure strength was deteriorated.

In No. 16, since the amount of Mn was excessive, the strength was too high and the ironing moldability was poor.
In No. 17, since the amount of Mg was too small, the strength was insufficient and the pressure strength deteriorated.

In No. 18, since the amount of Mg was excessive, the strength became too high and the ironing moldability was poor.
In No. 19, the finish temperature of hot rough rolling was too low, and finish rolling was performed with a large amount of rolling texture remaining. As a result, the Cube orientation density became very high, and the final plate was 0-180 °. Ears were too high, and tear-off occurred during ironing.

  In No. 20, the end temperature of the hot rough rolling became too high, the recrystallization progressed at the end of the rough rolling, and the finish rolling was performed while the degree of accumulation of the rolling texture was low. The density was low, the 45 ° ear rate of the final plate was high, and the neck height variation was large. Moreover, the surface quality of the hot rolled sheet was poor, and a flow mark appeared on the can surface.

  In No. 21, the rolling reduction of the hot rough rolling last pass was too high, the recrystallization progressed at the end of the rough rolling, and the finish rolling was performed with little strain accumulation. The 45 ° ear rate of the final plate was high, and the neck height variation was large.

  In No. 22, the strain rate of the last pass of hot rough rolling was too high, the recrystallization progressed at the end of rough rolling, and the finish rolling was performed with little strain accumulation. The 45 ° ear rate of the final plate was high, and the neck height variation was large.

In No. 23, the total rolling reduction in cold rolling was too low, the strength was low, and the pressure strength was reduced.
In No. 24, the total rolling reduction in cold rolling was too high, the strength was high, and the ironing formability deteriorated. Further, the 45 ° ear rate of the final plate was high, and the neck height variation was large.

As mentioned above, although embodiment of this indication was described, this indication is not limited to the above-mentioned embodiment, and can carry out various modifications.
(1) A function of one component in each of the above embodiments may be shared by a plurality of components, or a function of a plurality of components may be exhibited by one component. Moreover, you may abbreviate | omit a part of structure of each said embodiment. In addition, at least a part of the configuration of each of the above embodiments may be added to or replaced with the configuration of the other above embodiments. In addition, all the aspects included in the technical idea specified from the wording described in the claims are embodiments of the present disclosure.

  (2) In addition to the above-described aluminum alloy plate, the present disclosure can also be realized in various forms such as a DI molded can body molded using the aluminum alloy plate and a method for manufacturing the DI molded can body.

Claims (5)

0.05-0.60 mass% Si, 0.05-0.80 mass% Fe, 0.05-0.25 mass% Cu, and 0.80-1.50 mass% Mn And an aluminum alloy plate containing 0.80 to 1.50 mass% Mg, Al, and unavoidable impurities,
The 45 ° ear ratio of the primary drawn cup in the aluminum alloy plate is 2.0% or less,
The aluminum alloy plate in which the value obtained by subtracting the 45 ° ear rate from the 0-180 ° ear rate of the primary drawn cup in the aluminum alloy plate is −1.0% or more and 2.0% or less. 0.05-0.60 mass% Si, 0.05-0.80 mass% Fe, 0.05-0.25 mass% Cu, and 0.80-1.50 mass% Mn And an ingot of aluminum alloy containing 0.80 to 1.50% by mass of Mg, Al, and inevitable impurities,
Conditions under which hot rough rolling using a reversing mill is completed, the end temperature is 400 to 550 ° C., the last path rolling reduction is 5.0 to 40%, and the strain rate of the last path is 5.0 to 30 s ^−1. Done in
Perform hot finish rolling using a tandem hot rolling mill,
A method for producing an aluminum alloy sheet, which is cold-rolled under a condition where the rolling reduction is 80 to 90%. It is a manufacturing method of the aluminum alloy plate according to claim 2,
The manufacturing method of the aluminum alloy plate which performs the said homogenization process for 2 to 48 hours at the temperature of 580-610 degreeC. It is a manufacturing method of the aluminum alloy plate according to claim 2 or 3,
The end temperature in the hot finish rolling is 300 to 400 ° C,
The manufacturing method of the aluminum alloy plate whose total rolling reduction in the said hot finish rolling is 80 to 95%. It is a manufacturing method of the aluminum alloy plate according to any one of claims 2 to 4,
The manufacturing method of the aluminum alloy plate which manufactures the aluminum alloy plate of Claim 1.