JPH10330897A - Production of aluminum base alloy sheet for deep drawing - Google Patents

Abstract

PROBLEM TO BE SOLVED: To obtain an aluminum base alloy sheet for deep drawing in which not only the earing ratio at the time of deep drawing can remarkably be reduced, but also neck earing is hard to occur even in the case the reduction rate of the neck is made high at the time of can making by using a reverse type hot rough rolling mill of a single mill in all stages of a hot rolling stage. SOLUTION: In (1) a soaking stage, an aluminum base alloy ingot is heated at 560 to 610 deg.C, in (2) a hot rolling stage, hot rolling is executed and its temp. upon the end of the hot rolling is regulated to 280 to 350 deg.C, and, in (3) a primary cold rolling stage, cold rolling is executed so as to regulate the rolling ratio to >=85%. Then, in (4) a primary process annealing stage, annealing is executed at 260 to 350 deg.C for 1 to 8 hr, in (5) a secondary process annealing stage, annealing is executed at 500 to 600 deg.C for 2 to 60 sec, and then, in a secondary cold rolling stage, final cold rolling is executed.

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing an aluminum-base alloy plate for deep drawing, which has high strength and high ductility and can significantly reduce the ear ratio in deep drawing of aluminum-based alloy cans and the like. About.

[0002]

2. Description of the Related Art With an increase in demand for canned beverages and the like, recently, so-called DI (Deep drawing & Ironing) cans made of an aluminum-based alloy suitable for the containers have been mass-produced. This DI made of aluminum base alloy
As a general method of manufacturing the main body of the can, an aluminum-based alloy plate is deep-drawn in multiple stages, then ironed to form the main body of the can, and after baking coating, the pressure resistance is improved and a relatively expensive lid is formed. Neck processing is performed to reduce the diameter in order to reduce the amount of material used for the member. The aluminum-based alloy sheet used here is required to have both sufficient strength after can making and formability to withstand multi-stage deep drawing and ironing.

In general, as an aluminum-based alloy for deep drawing, an Al-Mn-Mg-based alloy such as the American Aluminum Association Standard (AA) 3004 alloy is widely used. In order to produce a deep-drawing aluminum-based alloy sheet from this alloy, (a) first hot-roll an ingot of this alloy, and then (b) cold-roll to obtain a sheet material having an appropriate thickness. The sheet material after cold rolling is subjected to (c) intermediate annealing, and further subjected to (d) cold rolling hardening treatment according to the required strength.

In the manufacturing process of the aluminum-base alloy sheet for deep drawing, in order to improve the strength of the sheet material, it is necessary to increase the cold rolling rate in the cold rolling (d). However, when the degree of cold rolling is increased, a so-called rolling texture develops, anisotropy appears remarkably at the time of plastic deformation, and according to the rolling direction of the sheet material at the time of deep drawing, the shape of the formed can body is A phenomenon occurs in which the height of the upper edge changes in a valley-like manner. This part that has been deformed into a mountain valley is usually
They are called "ears". The can body after deep drawing is then ironed, and then trimmed to cut the opening horizontally to make the can height uniform in order to attach a lid member.
Ears are also removed during this trimming, so if the height of the ears is high, the amount of plate material to be removed (hereinafter referred to as "ear ratio") increases, the yield decreases, and the manufacturing cost increases. There was a problem of doing. Therefore, a plate material having a low ear ratio was required.

In general, when an aluminum-based alloy plate is cold-rolled, a rolled texture tends to develop in the direction of 45 to 60 ° with respect to the rolling direction. Therefore, in order to reduce the ear ratio, it is necessary to suppress the development of the rolling texture. It has been found that this can be achieved by controlling the state of formation of the recrystallized texture in the sheet material before cold rolling. That is, generally, before cold rolling, 0
A method of developing a recrystallized texture called "cubic orientation" that produces a deep drawing ear in a direction of ~ 90 ° is used. The development of the cubic orientation results in ears in the 0-90 ° direction, but the subsequent cold rolling does not develop much in the ears, while the development of the rolled texture producing the 45 ° ears is also suppressed. As a result, the peak of the ear at the periphery of the opening is leveled. According to this method, after cold rolling at a rolling degree of 80% or more, a slight
It has become possible to obtain a low-ear plate material in which 0 ° ears and 45 ° ears coexist.

As a specific method for developing the recrystallized texture having the cubic orientation, various conditions during hot rolling are adjusted, and the coil wound after hot rolling is cooled or cooled. Method for controlling recrystallization generated when annealing a coil taken (Japanese Patent Laid-Open No. 5-125500)
It has been known. At present, the thickness of the sheet material mainly used for DI cans is about 0.3 mm, so when applying this method to make the final cold rolling reduction 80 to 90%, the heat It is necessary to perform rolling so that the sheet thickness becomes 1.5 to 3 mm by cold rolling. Therefore, usually, using a reverse type hot rolling mill, and further rolling using a tandem type finishing hot rolling mill or a reverse type hot finishing mill equipped with a coil winding device on both sides of the rolling mill. A method is used. However, these hot finishing mills are large-scale and expensive, and the use of these hot rolls imposes a heavy burden on manufacturing costs. Furthermore, as the thickness of the material for cans becomes thinner, the effect of the temperature drop between the rolling rolls and passes increases, and it is necessary to further increase the equipment capacity in order to maintain appropriate hot rolling conditions. Tended to increase.

Therefore, a method using only a single-mill reverse hot rough rolling mill in all the steps of hot rolling was studied. However, when trying to produce a thin plate using this rough rolling mill, the temperature between passes is remarkably reduced, and it is extremely difficult to maintain hot rolling conditions that balance strength and formability. As a means to solve this problem, an element that imparts age hardening property to the aluminum-based alloy is added, and the solution is made into a solution by performing intermediate annealing at a relatively high temperature, and sufficient strength is obtained even when the rolling degree of cold rolling is reduced. The resulting method has been proposed (JP-B-60-35242).

According to this method, since crystals are precipitated by heating the baking coating after forming the DI can body, softening due to heating during annealing is suppressed, and sufficient strength is obtained even if the cold rolling reduction is reduced. Can be obtained. Therefore, even if the cubic texture is not sufficiently developed after the intermediate annealing (c), the rolling reduction of the cold rolling can be reduced, so that the development of the rolled texture becomes light and the DI ratio at a practical level where the ear ratio is relatively low is reduced. Cans are now available. This method has a slightly higher ear ratio than in the case of using a finishing hot rolling mill, and therefore has a large amount of trim, but can be applied without using an expensive finishing hot rolling mill with high equipment cost. As a result, this is an advantageous method.

[0009]

However, recently, the demand for reducing the diameter of the lid member in the DI can has increased due to economical and design requirements, and as a result, the neck diameter reduction rate has increased. . However, when the diameter reduction ratio of the neck is increased, a new problem arises in that the can height changes in the opening due to the anisotropy of the material in the neck forming step as well as in the case of the deep drawing forming, and ears are generated. .
The height variation of the opening caused by the neck forming is called "neck ear".

The opening of the main body of the can is formed into a flange after the neck is formed. This flange is used for tightening with the lid member. Problems such as a change in the shape of the portion depending on the direction occur, which complicates the processing step and adversely affects the appearance. Therefore, there has been a demand for an aluminum-based alloy plate for deep drawing which hardly causes a neck ear even when the diameter reduction ratio of the neck is increased.

SUMMARY OF THE INVENTION The present invention has been made to solve the above-mentioned problems, and accordingly, it is an object of the present invention to provide a deep drawing using a single-mill reverse hot rough rolling mill in all of the hot rolling processes. An object of the present invention is to provide a method of manufacturing an aluminum-based alloy plate for deep drawing, which can significantly reduce ear ratio during forming.

[0012]

SUMMARY OF THE INVENTION In order to solve the above-mentioned problems, the present invention relates to a method for manufacturing an aluminum-based alloy plate from an aluminum-based alloy ingot, wherein the aluminum-based alloy From 560 to 61
Heating to a homogenization temperature in the range of 0 ° C. to homogenize, and in a hot rolling step, the homogenized aluminum-based alloy ingot is hot-rolled to form a sheet, and the sheet is not recrystallized. As shown in FIG.
The temperature is adjusted within the range of 50 ° C., and in the first cold rolling step, the sheet material after the completion of the hot rolling is subjected to a rolling reduction of 85 to 95%.
%, And in the first intermediate annealing step, the cold-rolled sheet material is subjected to an annealing temperature of 26%.
Annealing is performed in the range of 0 to 350 ° C. and the annealing time is in the range of 1 to 8 hours, and in the second intermediate annealing step, the sheet material after annealing is subjected to annealing at a temperature of 500 to 600 ° C. Production of an aluminum base alloy sheet for deep drawing in which annealing is performed for a time within a range of 2 to 60 seconds, and then in the second cold rolling step, the annealed sheet material is cold-rolled so as to have a desired thickness. Provide a way.

The above-mentioned aluminum-based alloy contains Si: 0.
1 to 0.4% by weight, Fe: 0.3 to 0.6% by weight, C
u: 0.05 to 0.4% by weight, Mn: 0.8 to 1.5% by weight and Mg: 0.8 to 1.5% by weight, with the balance being Al and unavoidable impurities Preferably, it is This aluminum-based alloy further contains Cr: 0.25% by weight or less and Zn: 0.
It is preferable that the composition contains one or more of 0.05 to 0.25% by weight and Ti: 0.2% by weight or less.

In the above soaking step, the homogenizing temperature is in the range of 580 to 610 ° C., and the homogenizing heating rate is 100 ° C.
/ Hr or less, and the homogenization time is preferably 1 hour or more. In the hot rolling step, it is preferable to use a single-mill reverse hot rough rolling mill in all the steps of hot rolling. In this step, the hot rolling start temperature is 5
It is preferable that the rolling ratio in the final pass of hot rolling is set to 50% or more. In the first cold rolling step, the rolling ratio is preferably in the range of 90 to 95%. In the first intermediate annealing step, the annealing heating rate is preferably set to 1 ° C./second or less. In the second intermediate annealing step, the annealing heating rate is 10 to 200 ° C /
Within the range of seconds, the annealing temperature is preferably in the range of 550 to 600 ° C. In the second cold rolling step, the rolling ratio is preferably in the range of 35% to 55%.

[0015]

Embodiments of the present invention will be described below in detail. The method for producing an aluminum-based alloy sheet for deep drawing (hereinafter, referred to as “the present alloy sheet”) of the present invention (hereinafter, referred to as “the present production method”) basically uses an ingot of an aluminum-based alloy as a base material, It is configured by sequentially passing through the soaking process, hot rolling process, first cold rolling process, first intermediate annealing process, second intermediate annealing process, and second cold rolling process set under specific conditions. Is done.

According to the present production method, a single-mill reverse hot rough rolling mill alone is used in all of the hot rolling steps, and the present alloy sheet having both strength and formability can be obtained. When used as a plate material for manufacturing deep drawn cans, the ear ratio is reduced as compared with conventional plate materials, and the neck ears are reduced even when molding DI cans with a large neck diameter reduction ratio, which reduces the deformation of the can body. This can improve the yield.

The aluminum-based alloy composition (hereinafter referred to as "the present composition") used in the present production method is basically based on Al, containing 0.1 to 0.4% by weight of Si and 0.3% by weight of Fe. ~
A material containing 0.6% by weight, 0.05 to 0.4% by weight of Cu, 0.8 to 1.5% by weight of Mn, and 0.8 to 1.5% by weight of Mg is used. Among them, Si easily forms a compound with simultaneously contained Mg, has a solid solution hardening action, a dispersion hardening action, and a precipitation hardening action, and contributes to age hardening. If the content is less than 0.1% by weight, desired age hardening characteristics cannot be secured, and if it exceeds 0.4% by weight, workability is deteriorated and disadvantageously. Fe has an effect of miniaturizing the crystal and preventing seizure on a die during ironing. If the content is less than 0.3% by weight, the desired effect cannot be obtained, and if it exceeds 0.6% by weight, the workability is deteriorated. Cu easily forms a compound with Mg,
It contributes to solid solution hardening, dispersion hardening and precipitation hardening. If the content is less than 0.05% by weight, the desired effect cannot be obtained, and if it exceeds 0.4% by weight, the workability is deteriorated. Mn
Easily forms a compound with Fe, Si, Al, etc., and mainly exhibits a dispersion hardening effect as a crystallized phase and a dispersed phase.
If the content is less than 0.8% by weight, desired curing properties cannot be obtained, and if it exceeds 1.5% by weight, processability is deteriorated.
Mg has a solid solution strengthening effect, enhances work hardenability by rolling, and exhibits a precipitation hardening effect by coexisting with Si and Cu described later. Its content is 0.
If the amount is less than 8% by weight, the desired effect cannot be obtained.
If it exceeds, the effect will be reduced again.

The composition of the present invention contains Si, Fe, Cu, M
0.25% by weight of Cr in addition to n and Mg
Hereinafter, 0.05 to 0.25% by weight of Zn and 0.2% of Ti
It is preferable that the content be contained within the range of not more than weight%. Of which C
r has the effect of suppressing recrystallization after hot rolling. However, if its content exceeds 0.25% by weight, it will rather decrease. Zn has an effect of promoting precipitation of Mg, Si, and Cu. If the content is less than 0.05% by weight, the desired effect cannot be obtained, and if it exceeds 0.25% by weight, the corrosion resistance deteriorates. Ti has the effect of making crystal grains finer and improving workability. However, when the content exceeds 0.2% by weight, a coarse compound is formed and processability is deteriorated.

In producing the present alloy sheet from the present composition, first, an ingot is cast from a molten metal of the present composition according to a conventional method. The solidification rate at this time is usually 5 to 20 ° C./sec. The size of the ingot is, for example, 1.5mx 0.5mx
4 to 5 m. Next, the surface of the ingot is cut by 1-2 mm.
Grind about 5 mm to create a chamfer with a smooth surface.

This chamfer is then sent to the soaking step of the present invention. In general, this soaking process is used to homogenize microsegregation caused by solidification of molten metal, precipitate supersaturated solid solution elements,
This is performed for the purpose of, for example, transferring a metastable phase formed by solidification to an equilibrium phase. In this soaking step, the homogenization temperature is set to 560 to 610 ° C, more preferably 580 to 61 ° C.
It is important to keep it at 0 ° C. When the homogenization temperature is lower than 560 ° C., the effect of the second intermediate annealing cannot be obtained, and the ear ratio becomes high. If the temperature exceeds 610 ° C., the ingot melts.

In the above-mentioned soaking process, it is preferable to heat the chamfered body to a homogenizing temperature at a heating rate of 100 ° C./hour or less. When the heating rate exceeds 100 ° C / hour,
There is a risk of partial melting. But the heating rate is
If it is too slow, production efficiency will decrease. From this viewpoint, a preferable heating rate is in the range of 10 to 100 ° C./hour.

In the above soaking step, the time for maintaining the temperature at the homogenization temperature (homogenization time) is preferably 1 hour or more. If the homogenization time is less than 1 hour, the homogenization may not proceed sufficiently. However, if it is too long, there is no effect and the production efficiency is reduced. From this point of view, the preferred homogenization time is in the range of 1 to 24 hours. This soaking step is usually carried out in a batch mode in a furnace due to the relatively long homogenization time.

The hot rolling step is performed to hot-roll the homogenized aluminum-based alloy ingot to form a sheet material. In the present invention, it is preferable to use a single-mill reverse hot rough rolling mill in the hot rolling step. This rolling mill is generally provided as a hot rough rolling mill in which a seat is provided before and after a single-base type hot rolling roll, and a thin plate is gradually thinned by repeatedly passing an ingot between the hot rolling rolls. This is the device used.

In the hot rolling step, it is particularly important to prevent the sheet material wound as a coil from recrystallizing after the completion of the rolling. For this purpose, the temperature of the coil immediately after the end of the hot rolling is adjusted to be in the range of 280 to 350 ° C. When this finishing temperature is cooled to less than 280 ° C., the sheet material becomes hard and cracks are likely to occur during the subsequent cold rolling. After winding on a coil,
If it exceeds 50 ° C., recrystallization occurs in the wound plate material.

In the hot rolling step, the rolling start temperature is preferably set to 500 ° C. or higher. If the rolling start temperature is lower than 500 ° C., the rolling load increases, the number of required passes increases, the efficiency decreases, and it becomes difficult to maintain the allowable temperature range immediately after the end of the hot rolling. Also,
The starting temperature of the final hot rolling pass is preferably 400 ° C. or higher. The rolling rate in the final pass of hot rolling is 50%
As described above, the strain rate is preferably in the range of ¹ to 50 sec ^-1 . The higher the starting temperature, rolling ratio and strain rate of the final hot rolling pass, the higher the production efficiency, but the sheet temperature immediately after hot rolling becomes higher than the specified temperature.
For this reason, it is preferable to forcibly cool the sheet material before being wound up into the coil after being drawn out from the rolling roll, and to adjust the temperature immediately after winding up into the coil to 280 to 350 ° C.

In the first cold rolling step, the sheet material after the completion of the hot rolling step is cold-rolled so that the rolling ratio falls within a range of 85 to 95%. The rolling reduction in this step is 85
If it is less than%, the ear ratio becomes large. The higher the rolling reduction, the more cubic orientation structures having 0-90 ° ears are generated in the second intermediate annealing step. However, when the rolling ratio exceeds 95%, the ear ratio is conversely increased and side cracks also occur.
From this viewpoint, the rolling reduction is preferably in the range of 90 to 95%.

In the first intermediate annealing step, the cold-rolled sheet material is annealed at an annealing temperature of 260 to 350 ° C. and an annealing time of 1 to 8 hours. This step is a step of almost completely recrystallizing the plate material. Annealing temperature is 2
If the temperature is less than 60 ° C. or the annealing time is less than 1 hour, sufficient recrystallization cannot be obtained, and the ear ratio becomes high. Even if the annealing temperature exceeds 350 ° C. or the annealing time exceeds 8 hours, the ear rate does not improve,
Evils such as surface oxidation are likely to occur. Since a long time is required for annealing, it is preferable to use a batch type annealing furnace.
The heating rate for annealing is preferably 1 ° C./sec or less. If the heating rate exceeds 1 ° C./sec, the entire coil cannot be heated uniformly.

In the second intermediate annealing step, the sheet material having undergone the first intermediate annealing step is subjected to an annealing temperature in the range of 500 to 600 ° C. higher than that of the first intermediate annealing step, more preferably in the range of 550 to 600 ° C. Within and an annealing time of 2 to 6
Annealing is performed within a range of 0 seconds. This step has the effect of further increasing the generation of the cubic orientation structure by annealing by raising the annealing temperature to a higher annealing temperature subsequent to the first intermediate annealing step, and increasing the 0-90 ° ear, which is particularly important in the present invention. Process. If the annealing temperature is 500 ° C. or the annealing time is less than 2 seconds, the effect of the annealing is insufficient, sufficient strength cannot be obtained, and the ear rate improving effect is low. Annealing temperature is 6
If the temperature exceeds 00 ° C. or the annealing time exceeds 60 seconds, the ear ratio is low and the strength is large, but work hardening is likely to occur during neck molding. This step is preferably performed using a continuous annealing apparatus because the annealing time is short.

The annealing heating rate in the second intermediate annealing step is preferably in the range of 10 to 200 ° C./sec.
If the heating rate is less than 10 ° C./sec, the heating takes a long time and the production efficiency is reduced. On the other hand, if the heating rate exceeds 200 ° C./second, the plate material is likely to be distorted.

In the second cold rolling step, which is the final step,
Rolling is performed so that the rolling ratio is in the range of 35 to 55%.
After this step, the plate material is wound into a coil as a main alloy plate having a predetermined thickness and commercialized. In this manufacturing method,
Since the rolling rate is increased in the first cold rolling step, the rolling rate in this step for obtaining a desired product thickness is reduced to a range of 35 to 55%. When the rolling ratio is less than 35%, the ear ratio decreases, but the strength also decreases. Increasing the processing temperature in the second intermediate annealing step can compensate for the decrease in strength. However, in this case, work hardening is likely to occur during neck forming, and it is necessary to balance the two properties by the neck forming method. When the rolling ratio exceeds 55%, the ear ratio increases.

[0031]

Next, the present invention will be described in more detail with reference to examples. In the following Examples and Comparative Examples, an aluminum-based alloy having the following composition was used as a raw material. Si: 0.30 wt% Fe: 0.45 wt% Cu: 0.28 wt% Mn: 1.00 wt% Mg: 1.25 wt% Cr: 0.02 wt% Zn: 0.15 wt% Ti : 0.03% by weight Al: Remaining amount

From the melt of the above composition, a weight of 6 t and a thickness of 55
A 0 mm ingot was cast, and 12.5 mm face milling was performed to prepare a sample of the face milled ingot. For each of these samples,
Examples are sequentially shown in Table 1 and comparative examples are shown in Table 2, soaking step, hot rolling step, first cold rolling step, first intermediate annealing step, second intermediate annealing step, and second cold annealing step. A rolling process was performed to produce an aluminum-based alloy plate for deep drawing. Conditions of each step other than the notation were as follows for all samples. Soaking process: The heating rate is 50 ° C / hour on average, the homogenization temperature is ± 3 ° C in Tables 1 and 2, and the homogenization time is 8 to 10 hours. Hot rolling process: The sample after the soaking process is immediately started using a single-mill reverse hot rough rolling mill. Final pass rolling start temperature 450 ° C, reduction 62%. "Temperature immediately after hot rolling and winding" in Tables 1 and 2 is the temperature immediately after the final pass, and was adjusted by the rolling speed (the lower the rolling speed, the lower the finishing temperature). First intermediate annealing step: The average heating rate from (annealing temperature −100 ° C.) to (annealing temperature −10 ° C.) is 30 ° C./hour. After the completion of the annealing, cooling was performed in a furnace until the actual temperature reached about 250 ° C., and thereafter cooling was performed in the atmosphere. Second intermediate annealing step: Using a floating continuous annealing furnace, the average heating rate from normal temperature to (annealing temperature-100 ° C) is 30 to 50 ° C / sec. “Temperature” in Tables 1 and 2 indicates the maximum annealing temperature, and “Time” indicates the time (second) from 400 ° C. to the maximum annealing temperature. The cooling rate is
On average from the highest annealing temperature to 70 ° C, about 100 ° C
/ Sec. Second cold rolling (final) step: An aluminum-based alloy sheet for deep drawing having a thickness of 0.31 mm was manufactured according to the “final cold rolling rate” in Tables 1 and 2.

A deep drawing test was performed using the above-mentioned aluminum base alloy plate for deep drawing. The “ear ratio” was calculated from the following formula: ear ratio = ear height ÷ cup height × 100 (%) for a cup drawn by deep drawing. The yield strength corresponds to the baking conditions for baking the aluminum-based alloy plate for deep drawing.
After heating at 10 ° C. for 10 minutes, it was processed into a JIS No. 5 tensile test piece, and the 0.2% proof stress was determined according to JIS B7771. These results are shown in Table 1 (Example) and Table 2.
(Comparative Example)

[0034]

[Table 1]

[Table 2]

From the results of Tables 1 and 2, the aluminum base alloy sheets for deep drawing according to Examples 1 to 14 satisfying the conditions of the present invention (described in Table 1) all maintained excellent yield strength. As it was, a low ear ratio of 2.6 to 3.7% was shown.
On the other hand, in Table 2, Comparative Examples 1 and 15 in which the holding temperature in the soaking step deviated from the conditions of the present invention; Comparative Example 2 in which the rolling end temperature in the hot rolling step deviated from the conditions of the present invention. Comparative Example 5, Comparative Example 6, Comparative Example 8; Comparative Example 3, Comparative Example 4, Comparative Example 7 in which the rolling end temperature in the hot rolling step deviated from the conditions of the present invention and the first intermediate annealing step was omitted.
Comparative Example 9 in which the first intermediate annealing step was omitted; Comparative Example 1 in which the rolling ratio in the first cold rolling step was outside the conditions of the present invention.
0, Comparative Example 13; Comparative Examples 11 and 12 in which the holding temperature in the first intermediate annealing step was outside the conditions of the present invention; and Comparative Examples in which the rolling ratio in the second cold rolling step was outside the conditions of the present invention. 14 has an ear ratio of 3.8 to 5.2, which indicates that all are inferior to the examples. In the case of Comparative Example 10, side cracks occurred frequently because the rolling reduction in the first cold rolling step was too high at 96%.

[0036]

According to the method for producing an aluminum-based alloy plate for deep drawing according to the present invention, an aluminum-based alloy ingot is heated to 560 to 610 ° C. in a soaking step, and hot-rolled in a hot rolling step. The sheet material temperature at the end of hot rolling is adjusted to 280 to 350 ° C. so that the sheet material does not recrystallize,
In the first cold rolling step, cold rolling is performed so that the rolling ratio is in the range of 85 to 95%, and in the first intermediate annealing step, annealing is performed at 260 to 350 ° C for 1 to 8 hours,
500-600 ° C., 2-6 in the second intermediate annealing step
Annealing within the range of 0 seconds, and then cold rolling to a desired thickness in the second cold rolling step, the equipment cost for hot rolling is a single mill reverse hot Using only a rough rolling mill, not only can the ear ratio be greatly reduced during deep drawing, but also the aluminum base alloy plate for deep drawing can hardly cause neck ears even when the neck diameter reduction ratio is increased during can manufacturing. As a result, it is possible to reduce the manufacturing cost when manufacturing DI cans and the like, and to greatly improve the yield.

────────────────────────────────────────────────── ─── front page continued (51) Int.Cl. ⁶ identifications FI C22F 1/00 623 C22F 1/00 623 630 630K 682 682 683 683 684 684A 685 685Z 686 686B 691 691B 691C 691A 694 694A 694B (72) Inventor Mitsuru Saito 85 Hiramatsu, Susono-shi, Shizuoka Pref. Mitsubishi Aluminum Corporation Technology Development Center (72) Inventor Toshihiro Harada 85-Hiramatsu, Susono-shi Shizuoka Pref.

Claims (13)

[Claims] When producing an aluminum-based alloy plate from an ingot of an aluminum-based alloy, the aluminum-based alloy ingot is successively subjected to a soaking process.
Heating to a homogenization temperature in the range of 560 to 610 ° C. to homogenize, and in a hot rolling step, the homogenized aluminum-based alloy ingot is hot-rolled to form a sheet, and this sheet is recycled. The sheet temperature at the end of hot rolling is set at 28 to prevent crystallization.
The temperature is adjusted within the range of 0 to 350 ° C., and in the first cold rolling step, the sheet material after the completion of the hot rolling is cold-rolled so that the rolling ratio falls within the range of 85 to 95%. In the intermediate annealing step, the cold-rolled sheet material is annealed at an annealing temperature in the range of 260 to 350 ° C. and an annealing time in the range of 1 to 8 hours. In the second intermediate annealing step, Of the sheet material having an annealing temperature in the range of 500 to 600 ° C. and an annealing time of 2
Annealed in a range of 60 seconds to 60 seconds, and then, in a second cold rolling step, the sheet material after the annealing is cold-rolled so as to have a desired thickness. Manufacturing method. 2. An aluminum-based alloy comprising: Si: 0.1 to 0.4% by weight; Fe: 0.3 to 0.6% by weight; Cu: 0.05 to 0.4% by weight; 2. The deep drawing according to claim 1, comprising 8 to 1.5% by weight and Mg: 0.8 to 1.5% by weight, with the balance having a composition consisting of Al and unavoidable impurities. A method for producing an aluminum-based alloy sheet for forming. 3. An aluminum-based alloy comprising: Si: 0.1 to 0.4% by weight; Fe: 0.3 to 0.6% by weight; Cu: 0.05 to 0.4% by weight; 8 to 1.5% by weight and Mg: 0.8 to 1.5% by weight, Cr: 0.25% by weight or less Zn: 0.05 to 0.25% by weight, Ti: 0.2 The aluminum-based alloy sheet for deep drawing according to claim 1, characterized in that it contains one or more of the following by weight and has a composition consisting of Al and inevitable impurities. Method. 4. The method for producing an aluminum-based alloy plate for deep drawing according to claim 1, wherein the homogenization temperature in the soaking step is in a range of 580 to 610 ° C. 5. The deep drawing aluminum base according to claim 1, wherein in the heat equalizing step, the homogenizing heating rate is 100 ° C./hour or less and the homogenizing time is 1 hour or more. Manufacturing method of alloy sheet. 6. The aluminum base alloy sheet for deep drawing according to claim 1, wherein in the hot rolling step, a single-mill reverse hot rough rolling mill of a single mill is used in all steps of the hot rolling. Manufacturing method. 7. The method for producing an aluminum-based alloy plate for deep drawing according to claim 1, wherein in the hot rolling step, a hot rolling start temperature is set to 500 ° C. or higher. 8. The method for producing an aluminum-based alloy sheet for deep drawing according to claim 1, wherein in the hot rolling step, a rolling reduction in a final hot rolling pass is set to 50% or more. 9. The method for producing an aluminum-based alloy sheet for deep drawing according to claim 1, wherein a rolling reduction is in a range of 90 to 95% in the first cold rolling step. 10. The method for producing an aluminum-based alloy sheet for deep drawing according to claim 1, wherein in the first intermediate annealing step, an annealing heating rate is set to 1 ° C./sec or less. 11. The method for producing an aluminum-based alloy sheet for deep drawing according to claim 1, wherein in the second intermediate annealing step, an annealing heating rate is in a range of 10 to 200 ° C./sec. . 12. The method according to claim 1, wherein in the second intermediate annealing step, the annealing temperature is in a range of 550 to 600 ° C. 13. The method for producing an aluminum-based alloy plate for deep drawing according to claim 1, wherein in the second cold rolling step, a rolling reduction is in a range of 35 to 55%.