JPH04221036A - Aluminum two piece can body and its manufacture - Google Patents

Abstract

PURPOSE:To facilitate the recycling of a can body, to reduce the anisotropy in strength as to a cap material without damaging its formability and to provide it with high strength by using alloys in which, respectively, Mg, Cu, Mn, Fe, Si and Al are specified as a cap material and a barrel material. CONSTITUTION:As a cap material, an alloy constituted of, by weight, 1.3 to 3% Mg, 0.05 to 0.5% Cu, 0.8 to 1.4% Mn, 0.1 to 0.7% Fe, 1 to 1.8% Mn+Fe, 0.1 to O.7% Si and the balance Al is used. Furthermore, as a barrel material, an alloy constituted of, by weight, 0.8 to 1.5% Mg, 0.05 to 0.5% Cu, 0.8 to 1.4% Mn, 0.1 to 0.7% Fe, 0.1 to 0.7% Si, 1 to 1.8% Mn+Fe and the balance Al is used. Then, the cap material and the barrel material obtd. by rolling the above alloys under prescribed conditions are combined to manufacture a can body.

Description

[Detailed description of the invention]

0001

[Field of Industrial Application] This invention relates to a two-piece can body made of aluminum alloy and a method for manufacturing the same, and more particularly to a two-piece aluminum can body that has high strength and is easy to recycle, and a method for manufacturing the same. It is something.

0002

[Prior Art] As is well known, the can body of an aluminum two-piece can is assembled by a can body (DI can body) and a can lid (end) by DI processing, and in the case of a normal easy open end can lid. A tab is attached to the

Among these, can body materials are required to have excellent deep drawing properties, ironing properties, necking properties after DI processing and baking painting, flanging properties, etc. is Al-Mn based 3004 alloy H1
9 material and H39 material are used. With the recent demand for thinner walls, higher strength is also required for the body material, but even the conventional 3004 alloy can body material has a yield strength of 270 N/mm2 or more after baking painting. It is now possible to obtain it.

On the other hand, can body lid materials for beer and other carbonated beverages, that is, lid materials for can bodies used in applications where internal pressure is high, are prone to seizure due to the recent trend toward thinner walls. A high strength of 300 N/mm2 or more is required in terms of yield strength after painting, so Al-Mg-based 5182 alloy is generally used, and 5082 alloy and 5052 alloy are also used for lid materials that do not require particularly high strength. In addition, an Al-Mn based 3004 alloy may also be used.

[0005] Since the tab material is generally not baked and painted, it is not required to have particularly high strength, and the yield strength is 250N/mm.
2 or more and has excellent bendability; 5182 alloy,
All of the 5082 alloy, 5052 alloy, and 3004 alloy have the above-mentioned strength and have a low degree of workability, so there is no particular problem with bendability.

[0006]

[Problems to be Solved by the Invention] As mentioned above, the body material of conventional two-piece aluminum cans is generally made of Al-Mn-based 3004 alloy, and the lid material is made of Al-Mn alloy in applications where internal pressure is applied. Mg-based 5182 alloy is the mainstream. However, like this, 3004 alloy is used for the body material and 51 alloy is used for the lid material.
82 alloy, when the can body after use is collected, remelted, and used again as a material for two-piece can bodies (i.e., during recycling), the same 3004 can body used before recycling is used.
In order to melt the alloy and the 5182 alloy for can lids, it is inconvenient that a new pure aluminum ingot, a master alloy for adding Mg, and some other composition adjustment materials must be added to adjust the composition.

On the other hand, recently attempts have been made to create a so-called unialloy in which the can body and can lid are made of an alloy with the same composition, but the biggest problem in this case is that the can body is used for purposes where internal pressure is applied. It is the lid material. In other words, we are trying to achieve the high strength required for can body lid materials for applications where internal pressure is applied, by using an alloy with a composition that can exhibit good formability as required for DI processing of can bodies. In this case, the moldability as a lid material is significantly reduced. Specifically, 30
There have already been proposals to use 04 alloy for both can bodies and can lids, but in this case, it would be necessary to obtain a strength of 300 N/mm2 or more after baking coating, which is required for can lids that are subject to internal pressure. This required cold working equivalent to H19 or higher, and there was a problem in that the formability as a lid material was significantly inferior compared to conventional 5182 alloy. Therefore, in the past, it was actually difficult to achieve unialloying. Even if the can body is made into a unialloy using 3004 alloy in this way, there will be a loss of Mg melting when the can body is remelted for recycling, so it is necessary to adjust the composition by adding a master alloy for Mg addition. is necessary.

[0008] Furthermore, the 5182 alloy conventionally used as a lid material for can bodies in applications where internal pressure is applied has the following problems. In other words, 5000 series alloys such as 5182 alloy have strong anisotropy in strength, and the strength is in the L direction (rolling direction),
Among the C direction (direction perpendicular to the rolling direction) and the 45° direction (direction at 45° to the rolling direction), the maximum in the L direction is 45°
The strength difference is 20 N/mm2. Due to such in-plane strength differences, the shape fixability also differs depending on the direction, so for example, when forming a seal during the lid forming process, the peripheral tongue (anchor lip)
Problems arise such as the height of the anchor drop height (anchor drop height) differing depending on the direction, or the roundness of the rivet molded part for tab attachment becomes poor after the tab is attached. Additionally, the L direction yield strength is generally considered to be a guideline for lid material strength, but even materials with a yield strength of 300 N/mm2 or more in the L direction may have in-plane strength anisotropy as mentioned above in applications where internal pressure is applied, such as carbonated beverages. There was a risk that the tightening part from the body would come off at a 45° angle due to the nature of the product, and the contents would come out. In order to avoid this problem, it is conceivable to set the strength in the L direction to a proof stress of 320 N/mm2 or more, and to secure a proof stress of 300 N/mm2 or more in the 45° direction. It is difficult to apply this method in practice because it is necessary to significantly increase the degree of cold working, which significantly impairs formability.

The present invention was made against the background of the above circumstances, and an object thereof is to provide a two-piece aluminum can body that can be easily recycled without impairing the strength and formability of the lid material and the body material, and a method for manufacturing the same. That is.

0010

[Means for Solving the Problem] As a means to increase the strength of 3004 alloy, which has been conventionally used as the body material of can bodies, and to make it applicable to the lid material,
The present inventors considered increasing the Mg content. It is true that the Mg content is 1.3w based on 3004 alloy.
If the Mg content is about t% or more, the strength necessary for the lid material can be obtained, and even if the Mg content exceeds about 1.5wt%, DI processing for can body formation is possible, but if the Mg content is Burning patterns such as black streaks become noticeable from around 1.5 wt%. This is caused by increased work hardening due to ironing during DI processing for forming can bodies, and seizure during ironing.If the amount of Mg further increases, this work hardening will cause can breakage. I'll wake you up. Therefore, while leaving the components other than Mg in the 3004 alloy as is, M
It is difficult to create a uni-alloy by using an alloy whose g content has been increased to about 1.5% or more for both the lid material and the body material.

By the way, as mentioned above, the advantage of using an alloy with the same composition for the body material and the lid material to make it a unialloy is that it is easy to recycle, but even in this case, Mg is generally added during recycling. It is necessary to do this. In other words, when remelting aluminum cans, Mg
There is a melting loss of at least 10% and an average of about 20%,
Therefore, in order to restore the original amount of Mg, it is necessary to add Mg. Even when unialloyed like this, M
Considering that it is necessary to add Mg, even if the Mg content of the lid material and the body material are different, from the point of view of ease of recycling, it should be equivalent to or even more advantageous than the case of uni-alloying. I can do it. In other words, if a low Mg alloy is used for the body material and a high Mg alloy is used for the lid material, as will be explained later, it is often sufficient to only add Mg to the lid material during recycling, and even in the worst case, the lid material Since it is only necessary to add Mg to both the material and the body material,
From the point of view of ease of recycling, it is equivalent to or even more advantageous than unialloying. On the other hand, by making the Mg contents of the body material and the lid material different in this way, it is possible to provide each with optimal characteristics. Therefore, in this invention, basically, an alloy with a low Mg content corresponding to the properties required for the shell material is used, an alloy with a high Mg content corresponding to the properties required for the lid material is used, This makes it easy to recycle and at the same time allows both the body material and the lid material to exhibit excellent performance.

On the other hand, especially for the lid material, it is simply a matter of high M.
It is possible to further improve formability and reduce strength anisotropy by not only creating an alloy with a weight of It has now become possible to solve the above-mentioned problem regarding the lid material.

Specifically, the invention according to claim 1 of the present application provides a combination of the composition of the can lid material and the composition of the can body material in a two-piece aluminum can body,
Mg1.3~3.0wt%, Cu0.05~0.5
wt%, Mn 0.8-1.4wt%, Fe 0.1
~0.7wt%, Si 0.1~0.7wt%, and the total amount of Mn and Fe is 1.0~1.8w
The lid material is an aluminum alloy in which Mg 0 is within the range of Mg 0
．． 8-1.5wt%, Cu0.05-0.5wt%
, Mn 0.8-1.4wt%, Fe 0.1-0
．． 7 wt%, Si 0.1 to 0.7 wt%, the total amount of Mn and Fe is within the range of 1.0 to 1.8 wt%, and the balance is Al and inevitable impurities. It is characterized by being made of wood.

[0014] Furthermore, the invention according to claim 2 of the present application specifies a method for manufacturing a two-piece aluminum can body, particularly a manufacturing process for a can lid material.
0wt%, Cu0.05-0.5wt%, Mn 0.
8 to 1.4 wt%, Fe 0.1 to 0.7 wt%,
Contains 0.1 to 0.7 wt% of Si, and also contains Mn and Fe.
The total amount of is within the range of 1.0 to 1.8 wt%,
After casting an aluminum alloy, the balance of which is Al and unavoidable impurities, by a DC casting method, the ingot is cast at 560~
Heating at a temperature within the range of 630°C for 2 hours or more, the area of the precipitate-free zone in the ingot occupies 40% or more in terms of the average area ratio of the cross section of the ingot, and the average diameter of the precipitates in the precipitate zone is 0.3～
Adjust the thickness to be within the range of 0.8 μm, then roll it to the required thickness, and then heat it to a temperature range of 500 to 620 °C at a temperature increase rate of 1 °C/sec or more immediately or for 2 minutes. After holding at a temperature within
After that, cold rolling is performed at a rolling rate of 40% or more to obtain a lid material,
After that, Mg 0.8-1.5wt%, Cu0.05
~0.5wt%, Mn 0.8~1.4wt%, F
e 0.1~0.7wt%, Si 0.1~0.7
wt%, and the total amount of Mn and Fe is 1.0~
It is characterized in that the can body is manufactured by combining the lid material and a body material made of an aluminum alloy in which the content of aluminum is within the range of 1.8 wt %, and the remainder is Al and unavoidable impurities.

[0015] Furthermore, the invention according to claim 3 of the present application specifies a method for manufacturing an aluminum two-piece can body, in particular a process for manufacturing a can body material, which includes Mg 0.8 to
1.5wt%, Cu0.05-0.5wt%, Mn
0.8~1.4wt%, Fe 0.1~0.7w
t%, Si 0.1-0.7wt%, and Mn
After casting an aluminum alloy in which the total amount of aluminum and Fe is in the range of 1.0 to 1.8 wt% and the balance is Al and unavoidable impurities by the DC casting method, the ingot is
Heating at a temperature within the range of 00 to 630°C for 2 hours or more,
After rolling to the required thickness, 1℃/se
Immediately after heating to a temperature range of 380 to 600℃ at a temperature increase rate of 1℃/se or after holding for less than 2 minutes
Intermediate annealing is performed using a continuous annealing furnace that cools at a cooling rate of 300 to 550°C, or intermediate annealing is performed using a box-type annealing furnace that heats the product to a temperature within the range of 300 to 550°C and holds it for 30 minutes to 10 hours, and then the rolling reduction A body material is obtained by performing cold rolling of 40% or more, and then Mg 1.3 to 3.0 wt%,
Cu 0.05~0.5wt%, Mn 0.8~
1.4wt%, Fe 0.1-0.7wt%, Si
0.1 to 0.7 wt%, the total amount of Mn and Fe is within the range of 1.0 to 1.8 wt%, and the remainder is Al and inevitable impurities. The present invention is characterized in that a can body is manufactured by combining the above-mentioned body material.

Furthermore, the invention according to claim 4 of the present application defines a method for manufacturing a two-piece aluminum can body, in particular, a manufacturing process for a can body material and a manufacturing process for a can lid material. 1.3-3.0wt%, Cu0.
05~0.5wt%, Mn 0.8~1.4wt%
, Fe0.1-0.7wt%, Si 0.1-0.
7wt%, and the total amount of Mn and Fe is 1.0
After casting an aluminum alloy in the range of 1.8 wt% with the balance consisting of Al and unavoidable impurities by the DC casting method, the ingot is heated at a temperature in the range of 560 to 630°C for 2 hours or more. , the area of the precipitate-free zone in the ingot occupies 40% or more of the average area ratio of the cross section of the ingot, and the average diameter of the precipitates in the precipitate zone is 0.3 to 0.8 μm.
After that, the plate is rolled to the required thickness, and then the temperature is increased at a rate of 1℃/sec or more.
Immediately after heating to a temperature range of 500 to 620°C or holding for within 2 minutes, intermediate annealing is performed in a continuous annealing furnace in which the material is cooled at a cooling rate of 1°C/sec or more, followed by cold rolling at a rolling reduction of 40% or more. was applied to obtain a lid material, while Mg
0.8-1.5wt%, Cu0.05-0.5wt%
, Mn 0.8-1.4wt%, Fe 0.1-0
．． 7 wt%, Si 0.1 to 0.7 wt%,
After casting an aluminum alloy in which the total amount of Mn and Fe is within the range of 1.0 to 1.8 wt% and the balance is Al and unavoidable impurities by DC casting, the ingot is heated at 500 to 630°C. After heating at a temperature within the range for 2 hours or more and then rolling to the required thickness, 1
Immediately after heating to a temperature range of 380 to 600°C at a temperature increase rate of ℃/sec or more or after holding for within 2 minutes 1
Intermediate annealing in a continuous annealing furnace that cools at a cooling rate of ℃/sec or more, or intermediate annealing in a box-type annealing furnace that heats to a temperature within the range of 300 to 550 degrees Celsius and holds it for 30 minutes to 10 hours, and then It is characterized in that a body material is obtained by performing cold rolling at a rolling rate of 40% or more, and a can body is manufactured by combining the lid material and the body material.

[0017]

[Operation] Basically, in this invention, a relatively low Mg Al-Mg-Mn alloy with an Mg content of 0.8 to 1.5 wt% is used as the shell material, and an Mg content is used as the lid material. Al-Mg with relatively high Mg of 1.3 to 3.0 wt%
-Mn-based alloy is used. Even when the body material and lid material are used differently depending on the Mg content in this way, the ease of recycling of aluminum cans is equivalent to that of unialloy aluminum cans.

That is, as already mentioned, when recycling aluminum cans, it is necessary to melt the entire can body as one piece, but since Mg is easily oxidized, an average of about 20% is lost during melting. On the other hand, the most popular two-piece aluminum can is the 350ml can, in which the weight ratio of the body material to the lid material is approximately 3:1. Therefore, Mg
Body material with an amount of 0.8 to 1.5 wt% and Mg amount of 1
．． The total Mg content of a two-piece can consisting of 3 to 3.0 wt% of the lid is approximately 0.9 to 3.0 wt%, based on body material: lid = 3:1.
It becomes 1.9wt%. If such a can is melted and the amount of Mg is lost by 20%, the amount of Mg in the ingot (regenerated ingot) after melting will be about 0.7 to 1.5 wt%. This amount of Mg is approximately the same level as the amount of Mg in the body material, so when manufacturing the body material from the recycled ingot, Mg
The addition of Mg becomes unnecessary, and although the amount of Mg is often insufficient when producing a lid material from the recycled lump, in that case as well, only the addition of Mg is sufficient. Furthermore, 500ml cans are used in the second largest amount after 350ml cans, but in this case the ratio of body material in the can is higher than in 350ml cans, so the Mg content in the recycled mass is lower than in the case of 350ml cans. 35 regarding the manufacture of can lid materials.
As in the case of 0 ml cans, only Mg is added, and when producing the can body material, it is sufficient to decide whether to add Mg or not depending on the Mg content of the recycled mass. In any case, the entire amount of recycled ingots from two-piece aluminum cans can be used for the production of can stock, and in that case, there is no need to add pure aluminum ingots, and only for the production of lid materials, or for the production of lid materials. Since it is only necessary to add Mg to both the shell material and the shell material, the ease of recycling is more advantageous than or equal to that of unialloying.

In the present invention, as described above, by making the lid material and the body material have different amounts of Mg, it is possible to obtain component compositions that fully satisfy the characteristics required for each material. In other words, the amount of Mg in the body material is
By setting the content to 0.8 to 1.5 wt% and appropriately adjusting other alloy components, it is possible to achieve excellent deep drawability and ironing performance in DI forming, as well as necking workability and flanging workability after baking painting. At the same time, the yield strength after baking coating is over 270N/mm2. In addition, by setting the Mg content to 1.3 to 3.0 wt% and appropriately adjusting other alloy components, the lid material can achieve high strength of 300 N/mm2 or more, which is desired for applications where internal pressure is applied, and at the same time, the lid material can be Formability for material processing can also be ensured.

[0020] In particular, regarding the lid material, not only the component composition is specified as described above, but also the dispersion state of the intermetallic compound is appropriately controlled at the ingot stage in the manufacturing process to obtain the desired lid material. Yield strength after baking coating
It is possible to ensure better moldability while ensuring 300 N/mm2 or more. That is, in the invention of claim 2, the area of the precipitate-free zone in the ingot by heating the ingot occupies 40% or more of the cross section of the ingot in terms of average area ratio, and the average diameter of the precipitates in the precipitate zone is It is adjusted to fall within the range of 0.3 to 0.8 μm.

[0021] Here, adjusting the precipitate-free zone in the ingot to account for 40% means widening the area in the matrix where no intermetallic compounds exist, and this allows the material to be formed during forming. There are fewer obstructions to the flow of water. Furthermore, the average particle size of precipitates (intermetallic compounds) in the precipitate zone is 0.
If the thickness is within the range of 3 to 0.8 μm, the presence of these intermetallic compounds will be relatively less likely to impede the flow of the material. Therefore, by applying these precipitate-free zone conditions and precipitate zone conditions, good formability can be obtained. Such precipitation conditions in the cross section of the ingot can be achieved by heating the ingot at 560 to 630°C for 2 hours or more.

[0022] The conditions for the precipitate zone in the ingot are basically such that the average grain size is 0.3 to 0.8 as described above.
Good formability can be obtained if the precipitate zone is within the range of 0.5 μm, but it is especially important to ensure that the total area of precipitates with a diameter of 0.5 μm or less in the precipitate zone is 15% or less of the area occupied by all precipitates. If adjusted, the flow of the material during molding will be even better, and moldability will be further improved.

Furthermore, regarding the final plate of the lid material, the maximum diameter (maximum length) of the intermetallic compound on the surface is 30 μm.
If the diameter exceeds the above, the large-diameter intermetallic compound is likely to become a starting point for cracks during bending or stretching, making it unsuitable for processing that requires local elongation. Therefore, the maximum diameter of the intermetallic compound in the final plate is 30 μm. It is desirable to set it to below, especially 20
It is preferable to set it to below micrometer. As mentioned above, setting the maximum diameter of the intermetallic compound in the final plate to 30 μm or less means that in normal DC casting, the total amount of Fe and Mn must be 1.
This can be achieved by setting the content to 8 wt% or less.

Similarly, regarding the final plate of the lid material, it is preferable that the number of intermetallic compound precipitates of 1 μm or more observed on the plate surface is within the range of 800 to 2000 per 0.2 mm2, and furthermore, the average particle size is 2~6μm
It is preferable to set it within the range of. By adjusting in this way, it is possible to obtain a material with less strength anisotropy while maintaining good formability. In other words, strength anisotropy occurs due to the presence of a specific slip plane during tension in each direction of the cold-worked material, but the slip is dispersed due to the distribution of intermetallic compound precipitates, reducing the strength anisotropy and increasing the total strength. A material having high strength in all directions can be obtained, and shape fixability during press molding is also the same in all directions. Especially 1μm
The number of intermetallic compounds is 800/0.2mm2
The effect can be obtained in the above cases. On the other hand, 2000 pieces/
If it exceeds 0.2 mm2, the strength anisotropy will decrease, but the material itself will become brittle and have little elongation, impairing formability. And this effect also occurs when the average particle size is 2μ
On the other hand, if the average particle size is less than 6 μm, a large number of intermetallic compounds of about 10 to 20 μm will inevitably occupy a considerable number, and such large intermetallic compounds will cause cracks to occur. It tends to become a starting point, impairing local elongation and reducing formability.

On the other hand, for the shell material as well, it is preferable not only to specify the component composition as described above, but also to set the maximum diameter (maximum length) of the intermetallic compound on the surface of the final plate to 30 μm or less. If the maximum diameter of the intermetallic compound exceeds 30 μm, the intermetallic compound is likely to become a starting point for cracks during molding. By setting the maximum diameter to 30 μm or less, it is possible to prevent the flange from cracking during molding, as in the case of the lid material, and to reduce the thickness of the side wall of the can as the can stock becomes thinner.
Even when the wall is as thin as 00 μm, the intermetallic compound
It is possible to prevent can breakage from becoming a starting point during I processing. In this way, reducing the intermetallic compound thickness of the final shell plate to 30 μm or less can be achieved by controlling the total content of Fe and Mn to 1.8 wt% or less in a normal DC casting method.

Similarly, for the final plate of the body material, the number of intermetallic compound precipitates of 1 μm or more observed on the plate surface was 800 to 2000 per 0.2 mm2.
It is preferable that the number of By doing so, ironing workability in DI processing can be improved. Note that such conditions can be achieved by a normal DC casting method when the total content of Fe and Mn is 1.0 wt% or more.

[0027] In addition, the features and effects of each invention of the present application will become clear from the explanation of the reasons for limiting the ingredients and the manufacturing process described below.

Next, the reason for limiting the ingredients in this invention will be explained.

Mg: Mg contributes to improving strength, and also contributes to developing shear bands during rolling and making recrystallized grains finer. In the case of a body material, if the Mg amount is less than 0.8 wt%, sufficient strength as a body material cannot be obtained; on the other hand, if the Mg amount is less than 1.
If it exceeds 5 wt%, there is a risk of tool seizure during ironing in DI forming, so the Mg content of the body material was set within the range of 0.8 to 1.5 wt%. In the case of lid materials, if the Mg content is less than 1.3 wt%, sufficient strength as a lid material cannot be obtained, whereas if the Mg amount exceeds 3.0 wt%, the ingot must be heated to a high temperature to form an appropriate intermetallic material. When trying to obtain a dispersed state of compounds, surface oxidation becomes severe, which is undesirable, and the Mg content of the regenerated lump increases during recycling, making it necessary to add new pure Al ingot to adjust the composition. Therefore, the Mg content of the lid material should be 1.3 to 3.0wt.
It was set within the range of %.

Cu: Like Mg, Cu also contributes to improving strength. In particular, when Cu is added, hardening can be expected due to aging precipitation of GPB zone, S' phase, etc., so even a small amount of Cu is effective. Especially like a continuous baking painting line 22
When baking at a high temperature of 0 to 400°C, solution treatment by continuous annealing is effective and effective in reducing strength loss after baking. Both lid and body materials are Cu
If the amount is less than 0.05 wt%, it is difficult to obtain sufficient strength. On the other hand, if the Cu content exceeds 0.5wt%, the DI for the body material
The ironing properties during molding and the formability of the flange portion are reduced, and the formability of the lid material is also reduced. Therefore, the amount of Cu for both the lid material and the body material is 0.05 to 0.
．． It was set within the range of 5 wt%.

Mn: Mn not only contributes to improving the strength, but also plays an important role together with Fe to obtain a suitable dispersion state of the intermetallic compound as described above. Here, the effect of an appropriate dispersion state of intermetallic compounds is, for example, in the case of the lid material, it contributes to improving formability by controlling the precipitate-free zone in the Al matrix, and in the case of the shell material, it contributes to improving formability. (1 μm or more) Solid lubricating ability is obtained by dispersing the intermetallic compound, which brings about effects such as contributing to improving the ironing workability of DI forming. In either case of the lid material or the body material, if the amount of Mn is less than 0.8wt%, an appropriate dispersion state of the intermetallic compound cannot be obtained; on the other hand, if the amount of Mn is 1.4w
If it exceeds t%, there is a possibility that giant crystallized substances will be formed due to the relationship with the Fe content, resulting in a significant decrease in formability. Therefore, the Mn content of both the lid material and the body material was set within the range of 0.8 to 1.4 wt%.

[0032] Fe: Similar to Mn, Fe plays an important role in obtaining an appropriate dispersion state of the intermetallic compound. The amount of Fe is
If it is less than 0.1wt%, the effect cannot be obtained, and 0.7w
If it exceeds t%, the moldability deteriorates, so the Fe amount for both the lid material and the body material was set within the range of 0.1 to 0.7 wt%.

[0033] Mn+Fe: The amount of Mn and the amount of Fe are individually as described above, but since it is necessary for both to coexist in order to generate an intermetallic compound, an appropriate dispersion state of the intermetallic compound can be obtained. In order to achieve this, it is necessary to consider the total content of both. If the total amount of Mn + Fe is less than 1.0 wt%, an appropriate dispersion state of the intermetallic compound cannot be obtained, while if the total amount exceeds 1.8 wt%, the formability will be deteriorated, so it is important to consider whether the lid material or the body material is Also in the case of Mn+Fe
It needs to be within the range of 1.0 to 1.8 wt%.

Si: Si contributes to improving strength by forming fine precipitates such as Mg2Si, but in the case of this invention, F
It promotes the precipitation of e and Mn and contributes to obtaining an appropriate dispersion state of the intermetallic compound. If the amount of Si is less than 0.1 wt%, this effect cannot be obtained, while if it exceeds 0.7 wt%, the effect is saturated. Further, the smaller the Fe/Si ratio is, the smaller the deep drawing selvage ratio is, and it is particularly preferable to suppress the Fe/Si ratio to 3 or less, and the Si amount is 0.1 to 0.
7 wt% can usually satisfy this requirement. Therefore, the amount of Si is 0.1 to 0.7 for both the lid material and the body material.
It was set within the range of wt%.

[0035] In ordinary aluminum alloys,
In order to refine the ingot crystal grains, a small amount of Ti alone or in combination with B may be added, and the addition of a small amount of Ti or Ti and B is also allowed in this invention. However, when adding Ti, the amount added is 0.01wt.
If it is less than %, the effect of refining the ingot crystal grains cannot be obtained;
If it exceeds 0.3 wt%, the moldability will be impaired, so Ti is 0.
．． It is preferably within the range of 0.01 to 0.3 wt%. Further, when B is added together with Ti, if B is less than 1 ppm, there is no effect, while if it exceeds 500 ppm, moldability is impaired, so B is preferably within the range of 1 to 500 ppm.

In addition, if each of Cr, Zr, and V is up to about 0.3 wt %, they contribute to improving the strength without losing the effects of the present invention. Also, Zn 1.
If it is up to about 0 wt%, it contributes to improving the strength without losing the effects of the present invention.

Next, the manufacturing process of the present invention, that is, the manufacturing process of the lid material and the manufacturing process of the body material will be explained in order.

First, as for the lid material, an aluminum alloy ingot having the above-mentioned composition was D.
Cast using the C casting method (semi-continuous casting method).

Next, the ingot is subjected to heating as a homogenization treatment and then preheated before hot rolling, or preheated before hot rolling which also serves as homogenization. In such ingot heating, the area of the precipitate-free zone where intermetallic compound precipitates are not substantially precipitated should occupy 40% or more of the average area ratio of the ingot cross section. The average diameter of the precipitates in the precipitate band is such that the area of the band is less than 60% in terms of the average area ratio of the cross section of the ingot.
Adjust so that it is within the range of 0.3 to 0.8 μm.

[0040] Here, to explain a little about the area ratio of the precipitate-free zone, intermetallic compounds are dispersed and precipitated during the temperature raising process of heating the ingot, but by heating at high temperature for a long time, the precipitates are gradually dissolves into the matrix, and as schematically shown in Fig. 1, there is a region where precipitates remain in groups, that is, a precipitate zone 1, and a region where the precipitates dissolve into the Al matrix and substantially precipitates exist. It separates into a precipitate-free zone 2 where no precipitation occurs. In this invention, the average area ratio of the precipitate-free zone is controlled to 40% or more depending on the conditions during ingot heating, and the average particle size of precipitates in the precipitate zone is 0.3 to 0.3. It is controlled within a range of 0.8 μm. For this purpose, it is necessary to set the ingot heating conditions to 560 to 630°C for 2 hours or more. If the ingot heating temperature is less than 560°C, such a distribution state cannot be obtained, and even if the ingot heating time is less than 2 hours, it is difficult to obtain such a distribution state. On the other hand, the ingot heating temperature is 630
If the temperature exceeds ℃, local melting of the ingot may occur. Although there is no particular upper limit to the ingot heating time, it is usually within 24 hours from the economic point of view.

The area ratio occupied by the precipitate-free zone in the cross section of the ingot was determined by direct observation using a transmission electron microscope.
Although there is a method of directly examining the occupancy of the precipitate-free zone in a region including the precipitate-free zone of ~20 visual fields, the following method is simple and can eliminate individual differences in measurement. That is, the cross section of the ingot to be measured is micropolished by diamond paste polishing or magomet finish polishing,
Using an etching solution made by diluting Keller's solution with pure water about 40 times, immersion etching was performed at room temperature for about 60 to 80 seconds, followed by washing and etching.
After drying, the cross-sectional structure image taken with an optical microscope is processed using an image analysis device to erase the crystallized parts and to binarize the precipitate-free zone and the precipitate zone, and calculate the occupancy of the precipitate-free zone by area. Find it as a percentage. FIG. 2 shows an example in which a cross-sectional tissue image obtained by an optical microscope is binarized using an image processing device. FIG. 2 shows an example of processing the cross-sectional structure image shown in FIG. It can be seen that it is binarized.

After adjusting the area ratio of the precipitate-free zone and the average grain size of the precipitate zone in the cross section of the ingot by heating the ingot as described above, the ingot is rolled in a conventional manner to obtain an intermediate plate thickness. . This rolling may be carried out only by hot rolling, or by a combination of hot rolling and cold rolling,
Furthermore, it may be carried out only by cold rolling.

After rolling, the plate having an intermediate thickness is subjected to intermediate annealing in a continuous annealing furnace. This intermediate annealing is performed by heating to a temperature within the range of 500 to 620°C at a temperature increase rate of 1°C/sec or more, without holding or holding for less than 2 minutes, and then cooling at a temperature decreasing rate of 1°C/sec or more. . This intermediate annealing using a continuous annealing furnace is effective for obtaining a solution treatment effect and improving strength through subsequent age hardening. Here, the temperature increase rate and temperature decrease rate of intermediate annealing are 1°C/se.
If the heating temperature is less than 500°C, sufficient solution effect cannot be obtained, and if the heating temperature is less than 620°C.
If the holding time exceeds 2 minutes, there is a risk of local melting, and if the holding time exceeds 2 minutes, there is a risk of surface oxidation. Therefore, each condition was determined as described above.

After the intermediate annealing, final cold rolling is performed, and this final cold rolling must be performed at a rolling ratio of 40% or more. If the rolling ratio is less than 40%, it will be difficult to obtain a yield strength of 300 N/mm2 or more after baking coating in the direction where the strength is minimum. There is no particular upper limit to the final cold rolling rate, but if it exceeds 90%, formability will deteriorate, so 4.
It is preferably within the range of 0 to 90%.

[0045] The rolled plate having the final thickness obtained by the final cold rolling may be used as it is for forming can lids, but 10
If the final annealing is performed at a temperature in the range of 0 to 200° C. for about 30 minutes to 10 hours, aging precipitation can be promoted and strength loss due to paint baking treatment can be reduced. Specifically, by performing the final annealing, the yield strength after the paint baking treatment can be increased by about 20 N/mm2 at the maximum.

As for the state of dispersion of intermetallic compounds in the final plate of the lid material thus obtained, as described above, the intermetallic compounds with a size of 1 μm or more were observed on the plate surface to be 0.0.
800 to 2000 particles are dispersed per 2 mm2, and the average particle size of the intermetallic compound is within the range of 2 to 6 μm, and the maximum diameter of the intermetallic compound is 30 μm or less, more preferably 2
It is desirable that the thickness is 0 μm or less.

[0047] When manufacturing a two-piece aluminum can body using the above-mentioned lid material, baking painting is usually performed. This baking coating is either a batch type with low temperature and long time (100 to 220℃ x 10 to 60 minutes) or high temperature and short time (220 to 400℃ x 5 to 60 minutes).
180 seconds) continuous baking painting is generally applied,
In the case of the lid material of the present invention obtained as described above, the yield strength after baking coating is 300 N/mm in all cases.
Strength of 2 or more can be definitely obtained. In other words, the conventional 3
In the case of 004 alloy, it was possible to obtain a yield strength of 300 N/mm2 by applying continuous annealing as an intermediate annealing in the case of low-temperature, long-time baking coating, but 220
Baking coating at a high temperature of ℃ or higher for a short period of time caused a sudden decrease in strength, and it was not possible to secure a yield strength of 300 N/mm2 or more. On the other hand, in the case of the lid material of this invention,
Even with baking coating at a high temperature of 220°C or more for a short time, there is no sudden drop in yield strength, and a yield strength of 300N/mm2 or more can be maintained.

Next, to explain the manufacturing process of the shell material, in this case as well, an aluminum alloy ingot having a predetermined composition is cast by the DC casting method (semi-continuous casting method) according to the conventional method. .

Next, the ingot is subjected to heating as a homogenization treatment and then preheated before hot rolling, or preheated before hot rolling which also serves as homogenization. Such ingot heating is carried out according to a conventional method at a temperature of 500 to 630
The treatment may be carried out at a temperature within the range of .degree. C. for 2 hours or more, preferably 24 hours or less.

After heating the ingot, it is rolled according to a conventional method to obtain an intermediate thickness. This rolling may be performed by hot rolling alone, by a combination of hot rolling and cold rolling, or by cold rolling alone.

[0051] After rolling, the plate having an intermediate thickness is subjected to intermediate annealing. This intermediate annealing may be performed using a box-type annealing furnace or a continuous annealing furnace. In the case of batch annealing using a box type annealing furnace, the temperature is 300 to 550℃.
It is sufficient to heat to a temperature within the range of 30 minutes to 10 hours, and if continuous annealing is used, 1℃/sec
After heating to a temperature within the range of 380 to 600°C at the above temperature increase rate and holding it for no longer than 2 minutes or less, it may be cooled at a temperature decrease rate of 1°C/sec or more.

After the intermediate annealing, final cold rolling is performed, and this final cold rolling must be performed at a rolling rate of 40% or more in order to ensure strength. The upper limit of the final cold rolling rate is not particularly determined, but if it exceeds 90%, the formability will deteriorate, so it is preferably 90% or less.

[0053] The rolled plate having the final thickness obtained by the final cold rolling may be used as it is to form a can body, but 10
Final annealing may be performed at a temperature in the range of 0 to 200°C for about 30 minutes to 10 hours, and in this case, the decrease in strength due to the paint baking process can be further reduced.

As for the dispersion state of intermetallic compounds in the final plate of the body material obtained in this way, the maximum diameter of the intermetallic compounds observed on the plate surface is 30 μm or less, and the maximum diameter of 1 μm or more is determined as described above. The number of intermetallic compounds is 0.2
It is desirable that the number be within the range of 800 to 2000 pieces per mm2.

[0055] Regarding the final plate of the shell material, reapply lubricating oil after rolling (after final annealing if final annealing is performed).
It is desirable to re-oil). That is, 50 to 500 mmg/m2 of lubricating oil is applied after rolling or final annealing.
By reapplying oil to a certain extent, the lubricity during DI molding becomes good, and it is possible to reduce the occurrence of seizure patterns such as black streaks during DI molding.

[0056] The lid material and body material obtained as described above may be molded and assembled to form a two-piece can body, but the specific method at that stage is a conventionally known method. Just apply.

[0057] Although there are no particular limitations on the tab material,
An alloy having the same composition as the lid material or body material described above can be used.

[0058]

[Example] Example 1: As the lid material, alloys A to D in Table 1 were used.
was used. That is, the alloys A to D in Table 1 were DC cast according to the conventional method, and the resulting ingots were heated and hot rolled. After performing inter-rolling, intermediate annealing was performed, and final cold rolling was performed to obtain a final plate thickness of 0.285 mm, and some of the sheets were further subjected to final annealing. The conditions of each step are shown in production numbers 1 to 7 in Table 2.

The obtained lid material was subjected to heat treatment equivalent to continuous coating baking at 270°C x 2 in an oil bath.
Heat treatment was performed for 0 seconds. Table 3 shows the results of examining the yield strength after this heat treatment and the Erichsen value, local elongation, and bendability as formability evaluations. We also investigated the average area ratio of the precipitate-free zone in the cross section of the ingot immediately after heating the ingot, and the average diameter of the intermetallic compound in the precipitate zone in the cross section of the ingot after heating the ingot. The maximum diameter was investigated and the results are also shown in Table 3. The average area ratio of the precipitate-free zone in the cross section of the ingot was investigated using the method described above. In addition, local elongation is
It represents the comprehensive evaluation of rivet forming, dimple forming, and bending forming, and as shown in Figure 3, the diameter φ = 2
Using a punch 5 with a tip curvature R of 1 mm, press forming was carried out by placing the test material 7 on a die plate 6, and changing the punch length L in 10 steps from rank 1 to rank 10 (however, the punch length L was changed in 10 steps from rank 1 to rank 10) The length increases sequentially from rank 1 to rank 10), and the rank one step before the stage at which cracking occurs is listed in Table 3. Therefore, the larger the rank value, the better the local elongation.

[0060]

[Table 1]

[0061]

[Table 2]

[0062]

[Table 3]

As shown in Tables 1 to 3 above, the manufacturing process of the lid material obtained by production number 1 is within the scope of the present invention, but the alloy composition is outside the scope of the present invention, especially the Mg content. In this case, in order to obtain a yield strength of 300 N/mm2 or more after baking coating, the rolling ratio of the final cold rolling had to be increased to 90.5%, resulting in poor formability. The lid material obtained by production number 2 is within the scope of this invention in terms of manufacturing process and alloy composition, and is different from the conventional lid material (5182 alloy material: production number 7).
The same level of performance was obtained. The lid material obtained by production number 3 is also within the scope of the present invention in terms of manufacturing process and alloy composition, but final annealing is performed to improve the strength, so in order to obtain the required strength, The final cold rolling reduction could be made relatively small, resulting in excellent formability. The lid material according to production number 4 has an alloy composition within the scope of the present invention, but the manufacturing process is outside the scope of the present invention, and the area ratio of the precipitate-free zone of the ingot and the average precipitate diameter of the precipitate zone are However, the conditions of this invention were not met, and the moldability was slightly inferior in this case. The lid material according to production number 5 is within the scope of the present invention in terms of alloy composition and manufacturing process, and since it has a particularly large amount of Mg, it is possible to obtain the required strength by lowering the final cold rolling rate. Therefore, excellent moldability could be obtained. The lid material according to production number 6 has an alloy composition within the scope of the present invention, but the manufacturing process deviates from the conditions of the present invention.
Batch annealing was performed in a box-type annealing furnace as intermediate annealing, but in this case, no improvement in strength due to the solution effect during intermediate annealing could be expected, so final cold annealing was required to obtain the required strength. The rolling rate must be increased, resulting in poor formability. The lid material with serial number 7 is
It was manufactured using 5182 alloy, which has been conventionally used as a lid material, through a conventional process that applied continuous annealing.

On the other hand, as the shell material, an alloy shown in alloy code A in Table 1, that is, 3004, which has been conventionally used for the shell material, is used.
Alloy (within the composition range of the shell material specified in this invention)
DC casting, ingot heating, hot rolling, cold rolling, intermediate annealing, and final cold rolling were performed under conditions that satisfied the manufacturing method conditions for the shell material stipulated in this invention, and the plate thickness was reduced to 0. 3m
The body material was m.

[0065] When a 350 ml two-piece can is made by combining this body material and a lid material made of each of the alloys A to D described above, the Mg of the regenerated lump when the can is remelted for recycling. Table 4 shows the results of calculating the amounts. The loss of Mg amount during remelting is expected to be 20%, and the thickness of the body material is 0.
3 mm, and the cover material was calculated assuming a plate thickness of 0.285 mm.

[0066]

[Table 4]

In the case of the conventional example (d), when manufacturing the lid material from the recycled ingot, it is sufficient to add Mg, but when manufacturing the shell material, it is necessary to add a considerable amount of new Al ingot. Although not shown in the table, Mn, Fe, Cu,
It is also necessary to adjust Si, etc. In addition, in the case of the conventional Unialloy concept in (a), when manufacturing lid material from recycled lumps,
Similarly, it is necessary to add Mg in any case where a shell material is manufactured from a recycled lump. On the other hand, (b) of this invention,
In the case of (c), the recycled lump can be used as is as the shell material, and Mg only needs to be added to the lid material, so it can be said that recycling is easier than in the case of the conventional unialloy concept.

Example 2: Alloy code E in Table 5 was used as the lid material.
An alloy having the composition shown in ~K is DC cast according to a conventional method, the obtained ingot is heated, and after further hot rolling, some of the ingots are cold rolled. The intermediate plate thickness was obtained. However, some of the sheets were directly cold-rolled to an intermediate thickness without hot rolling. Next, after performing intermediate annealing in a continuous annealing furnace, final cold rolling is performed to obtain the final plate thickness.
It was finished to 0.3 mm, and some of them were subjected to final annealing. The conditions for each step are manufacturing numbers 8 to 17 in Table 6.
Shown below. In production number 9, the ingot had a thickness of 80 mm, and the other ingots had a thickness of 500 mm.

[0069] Regarding the lid material obtained as described above,
As heat treatment equivalent to continuous paint baking, heat treatment was performed in an oil bath at 270°C for 20 seconds. After this heat treatment, each plate was examined for yield strength in each direction, local elongation and Erichsen value as evaluation of formability, and further examined for anisotropy of shape fixability, and the results are shown in Table 7. Note that the proof stress value here is determined by examining the proof stress in the direction of 45° to the rolling direction, that is, the direction where the proof stress is generally the minimum, and also by calculating the difference between the maximum proof stress value and the minimum proof stress value among the proof stress values in each direction in the plane. I looked into it. In addition, the local elongation was 1 as in Example 1.
Evaluation was made by a run based on a 0-level evaluation.

In addition, the area ratio of the precipitate-free zone on the cross section of the ingot immediately after heating the ingot was investigated, and the area ratio of the precipitate-free zone on the surface of the final plate was also investigated.
The number of intermetallic compounds of 1 μm or more per 0.2 mm 2 , the maximum particle size, and the average particle size of the intermetallic compounds were investigated, and the results are also shown in Table 7.

[0071]

[Table 5]

[0072]

[Table 6]

[0073]

[Table 7]

[0074] In Tables 5 to 7, the lid material obtained by production number 8 has an alloy composition within the scope of the present invention, but the manufacturing process conditions are out of range, especially the ingot heating temperature is low. In this case, the area ratio of the precipitate-free zone in the ingot cross section is as small as 20%, and the final plate has poor local elongation. In addition, production number 11 uses comparative alloy F in which the total amount of Fe and Mn exceeds 1.8 wt% as alloy components, and in this case, the maximum diameter of the intermetallic compound in the final plate is as large as 50 μm. Local elongation is poor. Production number 12 has a total amount of Fe and Mn as alloy components of 1.0
In this case, the number of intermetallic compounds in the final plate is small, the difference between the maximum and minimum yield strength becomes large, and the strength anisotropy becomes significant. Ta. Furthermore, for production number 16, a comparison process was applied in which the ingot heating temperature was relatively low for comparative alloy J, which had a high Mg content of 4.50 wt%, which was as high as the conventional 5182 alloy, and a high Fe and Mn content, as high as this invention. In this case, the area ratio of the precipitate-free zone in the ingot is low, and the local elongation of the final plate is poor. Furthermore, serial number 17 is a comparison process (a process in which the ingot heating temperature is relatively low) for the 5182 alloy traditionally used for lid materials, and in this case, the maximum yield strength and minimum yield strength are The difference was significantly large, and the strength anisotropy was strong, as was the anisotropy of shape freezing.

[0075] On the other hand, serial numbers 9, 10, 13, 14
, 15 are all produced by applying the manufacturing process conditions of this invention to alloys within the composition range of this invention, and all of them have good local elongation, excellent formability, and strength anisotropy. It is clear that there is little anisotropy in properties and shape fixability. It should be noted that the minimum proof stress value of all cases was 300/Nmm2 or more, which is required for lid materials.

[0076]

[Effects of the Invention] As is clear from the above examples, when recycling the two-piece aluminum can of the present invention, the composition of the regenerated lump after remelting is the same as the composition of the shell material. or close to that, when manufacturing a shell material from a recycled lump, it can be used as it is without adding anything, or it is sufficient to add a small amount of Mg, and when manufacturing a lid material from a recycled lump, M
Since it is sufficient to add only g, and therefore there is no need to use new Al ingots, recycling is easy, and in particular, it can be said that recycling is as easy as or better than the conventional idea of unialloying. Furthermore, the lid material for the two-piece aluminum can body of the present invention has a proof stress of 300 N/mm2 after baking coating, which is required for can bodies that are subject to internal pressure.
A lid material that can sufficiently ensure the above, has excellent formability such as local elongation, and has low strength anisotropy and shape fixability anisotropy by appropriately controlling the dispersion state of intermetallic compounds. It can be done. Furthermore, the body material of the two-piece aluminum can body of the present invention also has a proof strength after baking coating that is required for can bodies that are subjected to internal pressure.
70 N/mm2 or more can be sufficiently ensured, and the molding processability in DI molding, flange formability, etc. are also excellent.

[Brief explanation of the drawing]

FIG. 1 is a schematic diagram of a cross-sectional structure of an ingot for explaining a precipitate-free zone in a cross section of an ingot after heating an ingot.

[Figure 2] Image processing of the cross-sectional structure of the ingot in Figure 1
FIG. 2 is a schematic diagram of a value-converted state.

FIG. 3 is a schematic diagram showing a mode of press molding for evaluating local elongation in Examples.

Claims (4)

[Claims] [Claim 1] Mg 1.3-3.0wt%, Cu
0.05-0.5wt%, Mn 0.8-1.4wt
%, Fe 0.1~0.7wt%, Si 0.1~
0.7 wt%, and the total amount of Mn and Fe is 1
．． The lid material is made of an aluminum alloy in which the content is within the range of 0 to 1.8 wt%, the balance being Al and unavoidable impurities, and further contains 0.8 to 1.5 wt% of Mg and 0.05 to 1.5 wt% of Cu.
0.5wt%, Mn 0.8-1.4wt%, Fe
0.1~0.7wt%, Si 0.1~0.7w
t%, and the total amount of Mn and Fe is 1.0 to 1
．． 1. A two-piece aluminum can body, characterized in that the body material is an aluminum alloy in which the content is within the range of 8 wt %, and the remainder is Al and unavoidable impurities. [Claim 2] Mg 1.3-3.0wt%, Cu
0.05-0.5wt%, Mn 0.8-1.4wt
%, Fe 0.1~0.7wt%, Si 0.1~
0.7 wt%, and the total amount of Mn and Fe is 1
．． After casting an aluminum alloy in the range of 0 to 1.8 wt% with the balance consisting of Al and unavoidable impurities by the DC casting method, the ingot is heated at a temperature in the range of 560 to 630°C for 2 hours or more. The area of the precipitate-free zone in the ingot occupies 40% or more of the average area ratio of the cross section of the ingot, and the average diameter of the precipitates in the precipitate zone is 0.3 to 0.8 μm.
After that, the plate is rolled to the required thickness, and then the temperature is increased at a rate of 1℃/sec or more.
Immediately after heating to a temperature range of 500 to 620°C or holding for within 2 minutes, intermediate annealing is performed in a continuous annealing furnace in which the material is cooled at a cooling rate of 1°C/sec or more, followed by cold rolling at a rolling reduction of 40% or more. After that, M
g 0.8-1.5wt%, Cu0.05-0.5
wt%, Mn 0.8-1.4wt%, Fe 0.1
~0.7wt%, Si 0.1~0.7wt%, and the total amount of Mn and Fe is 1.0~1.8wt
%, and the remainder is Al and unavoidable impurities.
A method for manufacturing a piece can body. [Claim 3] Mg 0.8 to 1.5 wt%, Cu
0.05-0.5wt%, Mn 0.8-1.4wt
%, Fe 0.1~0.7wt%, Si 0.1~
0.7 wt%, and the total amount of Mn and Fe is 1
．． After casting an aluminum alloy in the range of 0 to 1.8 wt% with the balance consisting of Al and unavoidable impurities by the DC casting method, the ingot is heated at a temperature in the range of 500 to 630°C for 2 hours or more. , then rolled to the required thickness, then heated to a temperature range of 380 to 600°C at a temperature increase rate of 1°C/sec or more, and immediately or held within 2 minutes, then cooled at a cooling rate of 1°C/sec or more. Intermediate annealing in a continuous annealing furnace cooled at 300 ~
Intermediate annealing is performed in a box-type annealing furnace that is heated to a temperature within the range of 550°C and held for 30 minutes to 10 hours, and then cold rolled at a rolling rate of 40% or more to obtain a body material. 1.3~3.0wt%, Cu0.05~0
．． 5wt%, Mn 0.8-1.4wt%, Fe 0
．． 1~0.7wt%, Si 0.1~0.7wt%
and the total amount of Mn and Fe is 1.0 to 1.8
A method for manufacturing a two-piece aluminum can body, characterized in that the can body is manufactured by combining the body material with a lid material made of an aluminum alloy in which the aluminum alloy is within a range of wt% and the remainder is Al and unavoidable impurities. [Claim 4] Mg 1.3 to 3.0 wt%, Cu
0.05-0.5wt%, Mn 0.8-1.4wt
%, Fe 0.1~0.7wt%, Si 0.1~
0.7 wt%, and the total amount of Mn and Fe is 1
．． After casting an aluminum alloy in the range of 0 to 1.8 wt% with the balance consisting of Al and unavoidable impurities by the DC casting method, the ingot is heated at a temperature in the range of 560 to 630°C for 2 hours or more. The area of the precipitate-free zone in the ingot occupies 40% or more of the average area ratio of the cross section of the ingot, and the average diameter of the precipitates in the precipitate zone is 0.3 to 0.8 μm.
After that, the plate is rolled to the required thickness, and then the temperature is increased at a rate of 1℃/sec or more.
Immediately after heating to a temperature range of 500 to 620°C or holding for within 2 minutes, intermediate annealing is performed in a continuous annealing furnace in which the material is cooled at a cooling rate of 1°C/sec or more, followed by cold rolling at a rolling reduction of 40% or more. was applied to obtain a lid material, while Mg
0.8-1.5wt%, Cu 0.05-0.5
wt%, Mn 0.8-1.4wt%, Fe 0.1
~0.7wt%, Si 0.1~0.7wt%, and the total amount of Mn and Fe is 1.0~1.8wt
After casting an aluminum alloy using the DC casting method, the ingot is heated at a temperature within the range of 500 to 630°C for more than 2 hours, and then the required plate is formed. After rolling until thick,
380-600 at a heating rate of 1℃/sec or more
Intermediate annealing in a continuous annealing furnace in which the material is heated to a temperature range of 300 to 550 °C and cooled immediately or within 2 minutes after cooling at a cooling rate of 1 °C/sec or more, or heated to a temperature in the range of 300 to 550 °C for 30 minutes. Intermediate annealing is performed in a box-shaped annealing furnace that is heated and held for ~10 hours, followed by cold rolling at a rolling rate of 40% or more to obtain a body material, and the lid material and body material are combined to manufacture a can body. A manufacturing method for two-piece aluminum cans.