JP2000256774A - Hot rolled sheet for aluminum can body material, and can body sheet using the same - Google Patents

Abstract

PROBLEM TO BE SOLVED: To obtain a DI can body material securely and stably reduced in earing rate at deep drawing and excellent in external appearance quality by regulating the area ratio of rolled structure in the section of a sheet to a specific value or above and also regulating the orientation density of the cubic orientation and the orientation density of the rolling texture in the central part in a sheet-thickness direction to a specific value or above, respectively. SOLUTION: This sheet is composed of an Al alloy which has a composition consisting of, by weight, 0.5-2.0% Mg, 0.5-2.0% Mn, 0.1-0.7% Fe, 0.05-0.5% Si, and the balance Al with inevitable impurities and containing, if necessary, 0.005-0.20% Ti independently or in combination with 0.001-0.05% B. The area ratio of the rolled structure in the section of the sheet is regulated to >=80%. Further, the orientation density of cubic orientation is regulated to >=3 times that of random orientation over the whole region of the sheet thickness. Moreover, the orientation density of the rolling texture in the central part in the sheet-thickness direction is regulated to >=2 times the orientation density of the rolling texture in the sheet surface.

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

The present invention relates to DI processing (drawing).
Hot-rolled sheet used for the production of a can body for a two-piece aluminum can by ironing, and a sheet material for an aluminum can body using the same, ie, Al-Mg for a DI can body
The present invention relates to a hot-rolled plate and a can body plate made of a Mn-based aluminum alloy, and more particularly to a hot-rolled plate and a can body plate having low deep drawing ears and excellent appearance quality.

[0002]

2. Description of the Related Art In general, as a manufacturing process of a two-piece aluminum can, a can body material is subjected to DI forming by deep drawing and ironing to form a can body, and then trimmed to a predetermined size to be degreased.・ Washing process,
Further painting and printing and baking (baking)
And then necking the can body edge,
Usually, flanging is performed, and thereafter, a can is formed by performing seaming together with a separately formed can lid (can end).

[0003] As a raw material (can body material) of the DI can thus manufactured, a hard plate of JIS 3004 alloy, which is an Al-Mg-Mn alloy, has been widely used. This 3004 alloy is excellent in ironing workability, and shows relatively good formability even when cold-rolled at a high rolling ratio in order to increase strength, so that it is suitable as a DI can body. Have been.

[0004] As a method for producing such a 3004 alloy hard plate for a DI can body, after casting by a DC casting method or the like, the ingot is subjected to a homogenization treatment, and further subjected to hot rolling and cold rolling. Generally, a method is used in which a predetermined thickness is set and intermediate annealing is performed before or during cold rolling in the process.

[0005] By the way, it is strongly desired that the DI can body be made thinner mainly for the purpose of material cost reduction and weight reduction. In order to reduce the wall thickness in this way, it is important to increase the strength of the material in order to avoid the problem of reduction in buckling strength of the can caused by the reduction in the wall thickness. Furthermore, regarding the material for DI cans, not only the demand for high strength to achieve the thinning as described above,
It is strongly desired that the ear ratio at the time of DI molding is low. That is, a low ear ratio at the time of DI molding is extremely important from the viewpoint of improving the yield at the time of DI molding and preventing breakage of the can body due to the cut end of the can body. In addition, flange formability (mouth expansion) and ironing (can openability) during the production of DI cans are also required. In particular, it is difficult to control the ear ratio among these required characteristics. Therefore, in order to improve the balance of these various characteristics, appropriate control of the ear ratio is extremely important.

On the other hand, recently, the appearance quality of DI cans has been regarded as important due to consumers' high-grade orientation and the like.
The development of I can body materials has been strongly desired.

[0007]

Among the various performances required for the DI can body as described above, regarding the reduction of the ear ratio, the recrystallization in the (100) [001] orientation, that is, the so-called cube orientation. It is known that the grains contribute to the reduction of the ear ratio during deep drawing. Therefore, in the manufacturing process of the DI can body, the cube orientation in the final recrystallization process such as intermediate annealing after hot rolling is also considered. Generating a recrystallized grain texture is effective in reducing ear ratio. For that purpose, it is considered that forming as many sub-crystal grains or re-crystal grains as possible in the cube orientation in the hot rolling step or the subsequent cooling step is advantageous for reducing the ear ratio. However, since the growth rate of the sub-crystal grains in the cube orientation is faster than the growth rate of the sub-crystal grains in other orientations, the recrystallized grains completely recrystallized in the subsequent intermediate annealing tend to be coarse. Is shown. If such coarse recrystallized grains are present on the plate surface, it is difficult to remove the influence even if the final cold rolling is performed. This causes deterioration of the appearance quality of the can.

Therefore, it has conventionally been difficult to simultaneously achieve a reduction in the deep drawing ear ratio and an improvement in the appearance quality of the DI can body material.

The present invention has been made in view of the above circumstances, and a hot-rolled sheet and a hot-rolled sheet optimal for obtaining a DI can body material having a stable, low deep drawing ear ratio and a good appearance quality. An object of the present invention is to provide a sheet material for a DI can body using a hot-rolled sheet.

[0010]

Means for Solving the Problems In order to solve the above-mentioned problems, the present inventors have conducted intensive experiments and studies, and as a result, the cube orientation density in the DI can body plate in a completely recrystallized state was determined. It has been found that by appropriately controlling each part in the thickness direction, it is possible to simultaneously secure a low ear ratio and improve the appearance quality. Further, as described above, in order to appropriately control the cube orientation density in the sheet thickness direction in the completely recrystallized state, in the state of the hot-rolled sheet, the area ratio of the work structure in the sheet cross section and the orientation density of the cube orientation The present inventors have found that it is necessary to appropriately control the orientation density of the rolling texture in the sheet thickness direction at the same time as controlling the orientation density of each part in the sheet thickness direction, and have accomplished the present invention.

More specifically, the invention of claim 1 specifies a hot-rolled sheet for DI can body, and
0.5-2.0%, Mn 0.5-2.0%, Fe0.1
-0.7%, Si 0.05-0.5%, and if necessary, 0.005-0.20% Ti alone or in combination with 0.0001-0.05% B A hot-rolled plate for an aluminum can body comprising an aluminum alloy containing Al and unavoidable impurities, wherein the area ratio of the rolled structure in the cross section of the plate is 80%.
And the azimuth density of the cube orientation is at least three times the random orientation over the entire thickness, and the azimuth density of the rolled texture at the center in the thickness direction is 2% of the azimuth density of the rolled texture on the sheet surface. It is characterized by being twice or more.

The invention of claim 2 also defines a hot-rolled plate for DI can body, wherein Mg is 0.5 to 2.0 mm.
%, Mn 0.5-2.0%, Fe 0.1-0.7%, S
i containing 0.05-0.5% and Cu 0.05-
0.5%, Cr 0.05-0.3%, Zn 0.05-
One or more of 0.5%, and if necessary, 0.005 to 0.20% Ti alone or in combination with 0.0001 to 0.05% B A hot-rolled plate for an aluminum can body made of an aluminum alloy containing Al and unavoidable impurities, wherein the area ratio of the rolled structure in the cross section of the plate is 80%.
And the azimuth density of the cube orientation is at least three times the random orientation over the entire thickness, and the azimuth density of the rolled texture at the center in the thickness direction is 2% of the azimuth density of the rolled texture on the sheet surface. It is characterized by being twice or more.

[0013] The invention of claim 3 further specifies a plate material for a can body using the hot-rolled plate described in claim 1 or 2. That is, the plate material for an aluminum can body of the invention according to claim 3 is a plate material for an aluminum can body obtained by completely recrystallizing the structure of the hot-rolled plate using the hot-rolled plate according to claim 1 or 2. Therefore, the orientation density of the cube orientation is 30 times or less of the random orientation in the surface layer region from the plate surface to a position of 10% of the total plate thickness, and furthermore, from the position of 10% from the plate surface to the center in the plate thickness direction. In the central region, the density exceeds 15 times the random direction and is higher than the cube direction density in the surface region.

[0014]

DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS First, the reasons for limiting the composition of the aluminum alloy used in the hot rolled sheet for can body or the sheet for can body of the present invention will be described.

Mg: The addition of Mg is effective in improving the strength by solid solution of Mg itself, and the solid solution of Mg has a large interaction with dislocations, so that the strength can be expected to be improved by work hardening. It can also be expected to improve the strength by aging precipitation of Mg ₂ Si due to coexistence with Mg. Therefore, Mg is an indispensable element for obtaining the necessary strength as a can body. However, if the Mg content is less than 0.5%, the above-mentioned effects are small, while if it exceeds 2.0%, high strength can be easily obtained, but deformation resistance during DI processing increases, and drawability and galling resistance are increased. And worsen ironing properties. Therefore, the Mg content is set in the range of 0.5 to 2.0%.

Mn: Mn is an effective element that contributes to improvement in strength and formability. In particular, in the can body material, which is the intended use of the present invention, ironing is added during DI molding, and therefore Mn is particularly important. Emulsion type lubricants are usually used for ironing aluminum plates, but when the amount of Mn-based crystals is small, lubricating ability is insufficient with only emulsion type lubricants even if they have the same strength. However, appearance defects such as abrasion and seizure called "goling" may occur.
It is known that galling is affected by the size, amount, and type of a crystallized substance, and Mn is an essential element for forming the crystallized substance. If the Mn content is less than 0.5%, the solid lubricating effect of the Mn-based compound cannot be obtained, while if the Mn content exceeds 2.0%, a primary intermetallic giant compound of Al ₆ Mn is generated, resulting in remarkable molding. Impair the nature. Therefore, the Mn content is set in the range of 0.5 to 2.0%.

Fe: Fe is an element required to promote crystallization and precipitation of Mn and to control the amount of Mn solid solution in the aluminum matrix and the dispersion state of the Mn-based intermetallic compound. In order to obtain an appropriate compound dispersion state, it is necessary to add Fe according to the amount of Mn added. Fe content is 0.1%
If it is less than 10%, it is difficult to obtain an appropriate compound dispersion state. On the other hand, if the amount of Fe exceeds 0.7%, a primary crystal giant intermetallic compound is easily generated with the addition of Mn, and the formability is significantly impaired. . Therefore, the range of the amount of Fe is 0.1 to 0.7.
%.

Si: The addition of Si contributes to the improvement of the strength of the can body material through age hardening due to precipitation of the Mg ₂ Si-based compound. Si is an element necessary for generating an Al-Mn-Fe-Si-based intermetallic compound and controlling the dispersion state of the Mn-based intermetallic compound. If the Si content is less than 0.05%, the above effects cannot be obtained, while if it exceeds 0.5%, the material becomes too hard due to age hardening, and the formability is impaired.
Therefore, the range of the amount of Si is set to 0.05 to 0.5%.

Ti, B: In ordinary aluminum alloys, a small amount of Ti or Ti and B is added to refine ingot crystal grains. In the present invention, trace amounts are added as necessary. May be added alone or in combination with B. However, if the amount of Ti is 0.00
If it is less than 5%, the effect cannot be obtained, and if it exceeds 0.20%, a huge Al-Ti intermetallic compound is crystallized and the formability is impaired.
It was in the range of 5 to 0.20%. If B is added together with Ti, the effect of refining the ingot crystal grains is improved.
When B is added together with B, the effect is not obtained if the amount of B is less than 0.0001%, and if it exceeds 0.05%, coarse particles of Ti-B series are mixed and formability is impaired. When B is added, the amount of B is 0.0001 to 0.0.
It was within the range of 5%.

Cu, Cr, Zn: These are all elements that contribute to strength improvement, and one or more selected from these are added as necessary. Each of these elements will be further described.

Cu: Cu is dissolved in an aluminum matrix at the time of annealing, and Al-Cu-
It contributes to strength improvement utilizing precipitation hardening by precipitation as Mg-based precipitates. When the Cu content is less than 0.05%, the effect cannot be obtained. On the other hand, when Cu is added in excess of 0.5%, age hardening can be easily obtained, but it becomes too hard and impairs moldability. In addition, the corrosion resistance also deteriorates. Therefore, the range of the amount of Cu is set to 0.05 to 0.5%.

Cr: Cr is also an element effective for improving the strength, but if less than 0.05%, the effect is small, and 0.3%
Exceeding the range is not preferred because the formation of giant crystals causes a reduction in moldability. Therefore, the range of the amount of Cr is 0.05 to
0.3%.

Zn: The addition of Zn contributes to the improvement of the strength due to the aging precipitation of the Al—Mg—Zn-based particles.
If it is less than 0.5%, the effect cannot be obtained, and if it exceeds 0.5%, the corrosion resistance is deteriorated. Therefore, the range of the amount of Zn is 0.05-0.
5%.

The balance of each of the above elements may be Al and inevitable impurities.

Next, the structure conditions of the hot-rolled sheet of the present invention and the sheet material for DI can body using the hot-rolled sheet will be described in detail.

In the hot-rolled sheet, first, the orientation density of sub-crystal grains having a cube orientation (which may partially include recrystallized grains), that is, the cube orientation density is determined by the random orientation over the entire thickness of the sheet. Must be at least three times That is, if the cube orientation density of the sub-crystal grains is not at least three times the random orientation at the stage of the hot-rolled sheet, then the recrystallization process such as intermediate annealing will sufficiently form the cube-oriented recrystallized grains. However, it is difficult to achieve a sufficiently low ear ratio in the final board. Here, the ratio of the cube orientation density to the random orientation can be determined as the X-ray diffraction intensity ratio of the cube orientation to a random orientation sample (generally a powder sample) having no orientation by performing X-ray diffraction.

The second structure condition of the hot-rolled sheet is that the area ratio of the processed structure is 8% in the cross section of the hot-rolled sheet.
It must be present at 0% or more. That is, when the area ratio of the processed structure in the cross section of the plate is less than 80% at the stage of the hot-rolled plate, the sub-crystal grains having the cube orientation are grown in the subsequent complete recrystallization treatment such as intermediate annealing to recrystallize the cube orientation. It becomes difficult to sufficiently develop the rolled texture that contributes to the generation of the grain structure in the center in the thickness direction, and as a result, it becomes difficult to obtain a completely recrystallized grain structure having a high cube orientation density. It is difficult to reduce the rate. Here, the area ratio of the processed structure can be determined from an optical micrograph using an image analyzer.

Further, as a third structural condition of the hot-rolled sheet, with respect to the orientation density of the rolling texture, the orientation density of the rolling texture at the center in the thickness direction is at least twice the orientation density of the rolling texture on the sheet surface. It is necessary to be. This means that, conversely, the azimuth density of the rolled texture on the sheet surface is 1 / th of the azimuth density of the rolled texture at the center in the sheet thickness direction.
It is the same as being 2 or less. As described above, by setting the orientation density of the rolled texture on the sheet surface to 中央 or less of the central part in the thickness direction, the cube orientation near the surface of the sheet (surface layer region) in the subsequent complete recrystallization treatment such as intermediate annealing. While suppressing the coarse growth of recrystallized grains, the central part in the thickness direction promotes the growth of recrystallized grains in the cube orientation to satisfy the microstructure condition of the can body plate after complete recrystallization described later. As a result, a plate material for a DI can body having good surface appearance quality and a low ear ratio can be obtained as will be described again. Here, the orientation density ratio of the rolled texture can be obtained by the same method as the orientation density ratio of the cube orientation.

As described above, for the hot-rolled sheet, the condition of the cube orientation density by X-ray diffraction, the condition of the area ratio of the processed structure in the sheet cross section, and the condition of the direction density ratio of the rolled texture at the center of the sheet surface and the sheet thickness direction It is necessary to satisfy the following three conditions. Simultaneously satisfying these three conditions makes it possible to satisfy the following conditions as a can body plate after a complete recrystallization treatment such as intermediate annealing. is there.

The texture condition of the can body plate after the complete recrystallization treatment is as follows: the azimuth density of the cube orientation is 30 times the random orientation in the region (surface layer region) from the plate surface to a position of 10% of the total plate thickness. In addition, it is necessary that in the region (central region) in the central portion in the plate thickness direction from the position of 10% of the total plate thickness, it exceeds 15 times the random orientation and is higher than the cube orientation density in the surface layer region. is there. These conditions are necessary in order to ensure a low ear ratio and to obtain a can body material excellent in appearance quality which is less likely to cause skin roughness and flow lines during can manufacturing.

Here, the cube orientation density of the surface layer from the plate surface to the position of 10% of the total plate thickness is 3% of the random orientation.
If it exceeds 0 times, there is a possibility that rough skin or flow lines may occur at the time of can-making, leading to deterioration in appearance quality. On the other hand, when the cube orientation density in the central region from the position of 10% of the total thickness to the central portion in the thickness direction is 15 times or less of the random orientation or lower than the cube orientation density in the surface layer region, the low ear ratio is reduced. It is difficult to achieve. The cube azimuth density in the central region may be more than 15 times the random azimuth, but it is more preferably more than 30 times the random azimuth in order to obtain a low ear ratio reliably and stably, more preferably. Preferably, it exceeds 50 times.

The entire process itself for producing a hot-rolled plate and a plate for a can body that satisfies the above-mentioned structural conditions may be the same as the conventional process. That is, an ingot such as a slab obtained by a DC casting method or the like is subjected to a homogenization treatment and then hot-rolled to obtain a hot-rolled plate. In addition,
In order to obtain a sheet material for a can body, a hot-rolled sheet is immediately or firstly subjected to cold rolling, and then subjected to batch annealing or continuous annealing as a complete recrystallization treatment, followed by final annealing. Cold rolling is performed to obtain a sheet thickness required for a sheet material for a can body. Further, if necessary, in order to improve DI formability, final annealing may be performed at a temperature lower than the recrystallization temperature.

The process conditions during such a manufacturing process may be selected so as to satisfy the above-mentioned organizational conditions. Of course, specific process conditions are different depending on the composition of the alloy and other process conditions, and thus cannot be unconditionally determined. However, the following conditions are usually preferable.

That is, the homogenization process for the ingot is performed
The reaction is performed at a temperature within the range of 0 to 630 ° C. for 1 hour or more, preferably 48 hours or less. Next, hot rough rolling is performed for 350 to 5
Starting in the range of 80 ° C., and subsequently performing hot finish rolling, the rolling temperature in each pass of the finish rolling is set to a range of 280 to 350 ° C. excluding the final pass,
The final pass rolling temperature of hot finish rolling is 200-330 ° C
It is preferable to finish to a plate thickness of 1.0 to 7.0 mm. 200-330 immediately after the end of hot rolling
The average cooling rate from a temperature in the range of
C./hour or less is preferable. The hot-rolled sheet thus obtained is subjected to cold rolling at a rolling ratio of 2 to 60% as primary cold rolling, and then to intermediate annealing (continuous recrystallization treatment) by continuous annealing or batch annealing. ) Is preferred. When continuous annealing is applied to the intermediate annealing, the continuous annealing is performed by heating at a temperature in the range of 330 to 620 ° C. at an average heating rate in the range of 1 to 100 ° C./sec, and without holding or 10 minutes or less. After holding, 1-10
Preferably, the cooling is performed at an average cooling rate within the range of 0 ° C./sec. On the other hand, when batch annealing is applied as the intermediate annealing after the primary cold rolling, the average heating rate is 0.1 ° C. /
Heated to a temperature in the range of 250 to 500 ° C. in seconds or less, held at a temperature in the range for 0.5 to 24 hours,
It is preferable to cool at an average cooling rate of 0.1 ° C./second or less.

The final cold rolling after the intermediate annealing by the continuous annealing or the batch annealing is performed by 50%
It is preferable to apply at the above rolling ratio.

The sheet after final cold rolling may be used as it is as a final sheet for DI forming. However, if necessary, the sheet after final cold rolling may be subjected to 80 to 20 to improve formability.
The final annealing may be performed at a temperature within the range of 0 ° C. for 0.5 to 24 hours. Even when the final annealing is not actively performed, the same effect as the final annealing can be obtained by utilizing the processing heat generated by performing the final cold rolling at a high speed.

[0037]

EXAMPLES As examples of the present invention, alloy symbols A to D shown in Table 1 are used.
Each alloy was cast into a slab by a DC casting method according to a conventional method, then subjected to a homogenization treatment at 520 to 630 ° C. for 1 hour or more, and then subjected to hot rolling. Hot rolling is 3
Start hot rough rolling at a temperature within the range of 50 to 580 ° C,
Thereafter, hot finish rolling is performed in 5 passes, and the rolling temperature is 280 to 350 ° C. until the first to fourth passes of the finish rolling.
In the fifth pass, the rolling temperature was adjusted to 200 to 330 ° C. to obtain a hot-rolled sheet having a sheet thickness of 2.0 mm. Further, the rolling rate of the hot-rolled sheet after cooling to room temperature is 10%.
After the first cold rolling, continuous annealing (heating rate and cooling rate of 1 to 100 ° C./second, ultimate temperature of heating of 330 to 620 ° C., holding 0 to 10 minutes) or batch annealing (intermediate annealing) Speed and cooling rate of 0.1 ° C./sec or less, heating temperature of 250 to 500 ° C., holding 0.5 to 24 hours), and then final cold rolling at a rolling reduction of 83%.

As a comparative example, the alloy symbol E shown in Table 1 was used.
Each of the alloys Nos. To G was cast into a slab by a DC casting method according to a conventional method, and then subjected to a homogenization treatment at 520 to 630 ° C. for 1 hour or more, followed by hot rolling. Hot rolling starts hot rough rolling at a temperature in the range of 450 to 580 ° C., then performs hot finish rolling in 5 passes, and a rolling temperature of 360 to 1 to 5 passes of the finish rolling. 41
The fifth pass was performed at a rolling temperature of 260 to 390 ° C. Thereafter, primary cold rolling, intermediate annealing, and final cold rolling were performed in the same manner as in the above-described examples of the present invention.

In the above-mentioned examples of the present invention and comparative examples, for the hot-rolled sheet after hot rolling, the area ratio of the processed structure in the cross section, the orientation density ratio of the cube orientation to the random orientation by X-ray diffraction, and the Table 2 shows the results of examining the orientation density ratio of the rolled texture at the center in the sheet thickness direction to the rolled texture. Further, with respect to the sheet material after the intermediate annealing as a complete recrystallization treatment, the orientation density ratio of the cube orientation in the surface layer region from the sheet surface to the position of 10% of the total sheet thickness with respect to the random orientation and the 10% of the total sheet thickness are determined. Table 2 also shows the result of examining the azimuth density ratio of the cube azimuth in the central region from the position to the center in the thickness direction.

Further, each of the can body plates obtained after the final cold rolling, obtained as described above, was subjected to DI molding to examine the ear ratio, and the appearance of the can after can production was examined. Table 3 shows the results. Note that an ear rate of 2.5% or less can be determined to be acceptable. On the other hand, the appearance of the can was evaluated on a five-point scale of ranks "1" to "5". In this five-step evaluation, the higher the numerical value of the rank, the better, and a pass of "3" or higher was evaluated.

[0041]

[Table 1]

[0042]

[Table 2]

[0043]

[Table 3]

In Tables 1 to 3, the production numbers 1 to 4 are all within the scope of the present invention. In these cases, the ear ratio is as low as 2.5% or less, and the appearance quality is good. Was. On the other hand, in the case of the production number 5, the area ratio of the processed structure in the cross section of the hot-rolled sheet is as low as 55%, and the orientation density ratio of the cube orientation in the central region of the completely recrystallized sheet after the intermediate annealing is 14; In this case, the appearance quality was excellent, but the ear ratio was high at 3.6%.
Production number 6 is an example using an alloy having a Mg content higher than the range specified in the present invention. In this case, the microstructure of the hot-rolled sheet satisfies the range specified in the present invention, and the intermediate annealing is performed. Although the cube orientation density in the surface region of the later completely recrystallized plate is within the range specified in the present invention, the cube orientation density in the central region is low and the ear ratio is 4.3.
%. Furthermore, the production number 7 is such that the orientation density of the rolling texture at the center in the thickness direction of the hot-rolled sheet is 0.8 times lower than the orientation density of the rolling texture on the sheet surface,
In this case, the cube orientation density of the surface layer region in the completely recrystallized plate after the intermediate annealing is too high and the cube orientation density of the central region is low. As a result, not only the ear ratio is as high as 2.9%, but also the surface appearance quality. Was also inferior.

[0045]

According to the hot-rolled sheet of the present invention and the sheet material for a can body using the same, the ear ratio after DI forming is reliably and stably reduced by appropriately setting the structure conditions. At the same time, it is possible to obtain a can having good appearance quality by preventing the occurrence of rough skin and flow lines during DI molding.

Claims (3)

[Claims] 1. Mg 0.5-2.0% (weight%, the same applies hereinafter), Mn 0.5-2.0%, Fe 0.1-0.7%,
0.05 to 0.5% of Si, and if necessary, 0.005 to 0.20% of Ti alone or 0.0
001-0.05% B in combination with the balance being Al
And a hot-rolled plate for an aluminum can body made of an aluminum alloy comprising unavoidable impurities, wherein the area ratio of the rolled structure in the cross section of the plate is 80% or more, and the azimuth density of the cube orientation is the entire thickness of the plate. Aluminum can body material characterized in that the orientation density of the rolled texture in the central part in the thickness direction is at least twice the orientation density of the rolled texture on the sheet surface. For hot rolled plate. 2. Mg 0.5-2.0%, Mn 0.5-
2.0%, Fe 0.1-0.7%, Si 0.05-0.
5%, Cu 0.05-0.5%, Cr0.
0.05 to 0.3% and Zn 0.05 to 0.5%, and if necessary, 0.002% or more.
5 to 0.20% Ti alone or 0.0001 to
A hot-rolled plate for an aluminum can body made of an aluminum alloy containing 0.05% of B in combination with the balance being Al and inevitable impurities, wherein the area ratio of the rolled structure in the cross section of the plate is 80%. % Or more, and the azimuth density of the cube orientation is at least three times the random orientation over the entire thickness, and the azimuth density of the rolled texture at the center in the thickness direction is the azimuth density of the rolled texture at the plate surface. A hot-rolled sheet for aluminum can body, characterized in that it is twice or more. 3. A plate material for an aluminum can body obtained by completely recrystallizing the structure of the hot-rolled plate using the hot-rolled plate according to claim 1 or 2, wherein the cube orientation has an orientation density of: In the surface layer region from the plate surface to the position of 10% of the total plate thickness, the random orientation is 30 times or less, and in the central region from the position of 10% from the plate surface to the center in the plate thickness direction, the random direction is 15 times. A plate material for an aluminum can body, which exceeds the cube orientation density in the surface region.