JP2011094202A - Resin-coated aluminum alloy sheet for beverage can barrel, and method for producing the same - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a resin-coated aluminum alloy sheet which has excellent strength and formability and is suitable for a beverage can barrel subjected to DI forming and coating/baking, and to provide a method for producing the same. <P>SOLUTION: The resin-coated aluminum alloy sheet has a composition comprising, by mass, 0.4 to 0.8% Mg, >0.5 to 1.5% Si, 0.01 to 0.4% Cu and 0.01 to <0.4% Mn, and the balance Al with inevitable impurities, and in which tensile strength after being subjected to cold rolling to a final sheet thickness is 270 to 380 MPa, and also, electric conductivity is 40 to 50%IACS. The production method uses the same. <P>COPYRIGHT: (C)2011,JPO&INPIT

Description

  The present invention relates to a resin-coated aluminum alloy plate suitable for beverage can bodies and the like, and a method for producing the same.

  For beverage cans, etc., oil is applied to an aluminum alloy plate, cupping and DI (Drawing and Ironing) molding is performed to form a can body, trimming, washing, drying, outer and inner surface baking treatment, necking In addition, two-piece cans that have been subjected to flange processing, beverage filling, and can lid tightening are often used. Recently, for the purpose of improving productivity and working environment, a method of coating an aluminum alloy plate before DI molding with a resin film and omitting the steps of cleaning, drying, outer surface and inner surface coating baking after DI molding, and so on. It is supposed to be. The aluminum alloy plate is manufactured by subjecting an aluminum alloy ingot to homogenization, hot rolling, annealing as necessary, and then cold rolling. (Hereinafter, an aluminum alloy plate cold-rolled to the final thickness is referred to as a base plate.)

  In recent years, aluminum alloy plates for beverage can bodies have been made thinner and higher in strength because of the need for cost reduction of beverage cans. In addition, characteristics such as good moldability at the time of molding, and no reduction in strength due to heating at the time of paint baking are required.

  Conventionally, non-heat-treatable aluminum alloys such as Al-Mn-Mg-based JIS3004 alloy have been used for the above applications. However, in the case of JIS3004 alloy, the strength is reduced by heating due to the coating baking process, and if the strength of the base plate is increased in order to ensure the strength after the coating baking process, there will be a problem in the formability during the molding process. There were some disadvantages.

  On the other hand, as shown in Patent Documents 1 to 4, proposals have been made on aluminum alloy plates for can bodies using Al-Mg-Si alloys that can improve the strength after baking treatment by age hardening. .

  In Patent Document 2, in addition to Mg and Si, the content of alloy elements that contribute to the improvement of formability or strength such as Mn, Zn, Fe, Ti, Cu, and B is specified, and further, the solution treatment temperature and the final rolling rate The aluminum alloy plate which prescribes | regulates and the manufacturing method are shown. Further, Patent Document 3 discloses a method for producing an aluminum alloy plate in which conditions for precipitation treatment after solution treatment are defined in order to improve formability, and Patent Document 4 describes an intermediate method for improving formability. A method for producing an aluminum alloy sheet in which the cold rolling conditions after annealing are defined is shown.

  However, none of the methods of Patent Literatures 1 to 4 strictly defines the solid solution and precipitation state of the alloy elements in the aluminum alloy plate. Even the methods of Patent Literature 3 and Patent Literature 4 do not fix the solid plate. Since a specific index indicating the precipitation state is not disclosed, there is still room for improvement because it is still insufficient for obtaining an aluminum alloy sheet excellent in both strength and formability.

JP-A-56-139646 JP-A 63-149349 Japanese Laid-Open Patent Publication No. 02-093049 JP-A 61-261466

  In view of the above problems in the prior art, the present invention provides a resin-coated aluminum alloy plate excellent in strength and formability suitable for a beverage can body subjected to paint baking after DI molding and a method for producing the same. Objective.

  As a result of intensive research to achieve the above object, the inventors have achieved excellent strength and formability by using an Al—Mg—Si heat-treatable aluminum alloy, and further have a paint baking treatment compared to conventional alloys. The present inventors have found a resin-coated aluminum alloy plate excellent in strength later and a method for producing the same, and have arrived at the present invention.

  That is, the invention of claim 1 is a resin-coated aluminum alloy plate, wherein Mg is 0.4 mass% or more and 0.8 mass% or less, Si is more than 0.5 mass% and 1.5 mass% or less, and Cu is 0.01 mass% or more. 0.4 mass% or less, Mn 0.01 mass% or more and less than 0.4 mass%, consisting of the balance Al and unavoidable impurities, tensile strength at the final plate thickness of 270 MPa or more and 380 MPa or less, and electrical conductivity of 40 It is a resin-coated aluminum alloy plate characterized by being from% IACS to 50% IACS.

  The invention according to claim 2 is the method for producing an aluminum alloy plate according to claim 1, wherein the ingot having the alloy composition is homogenized at a temperature of 500 ° C. to 560 ° C. for 1 hour to 48 hours. After the treatment, hot rough rolling is performed, followed by hot finish rolling with a rolling end temperature of less than 280 ° C., cold rolling, and cold rolling after the hot finish rolling. It is characterized in that a solution treatment is performed for 2 minutes or less at a temperature of 450 ° C. or more and 580 ° C. or less in the middle of cold rolling, and a resin film is coated on an aluminum alloy plate having a final thickness. This is a method for producing a resin-coated aluminum alloy plate.

  The aluminum alloy in the present invention contains Mg, Si, and Cu in appropriate amounts, so that the Mg-Si compound or Mg-Cu compound is finely precipitated in the aluminum alloy plate by the coating baking process after DI molding, and the coating baking is performed. A can body having excellent strength can be obtained after the treatment. Moreover, in this invention, the resin-coated aluminum alloy plate excellent in the balance of intensity | strength and a moldability is obtained by prescribing | regulating the tensile strength and electrical conductivity in a base plate.

  First, the reasons for limiting the component composition of the aluminum alloy in the present invention will be described.

  Mg is dissolved in the Al matrix to increase the strength of the base plate, and has the effect of improving the strength of the base plate by precipitating Mg-Si compounds or Mg-Cu compounds in the presence of Si and Cu. . In applications where the coating baking treatment is performed as in the present invention, it is soft at the time of molding before the coating baking treatment, and the Mg-Si compound or Mg-Cu compound is finely precipitated by heating due to the coating baking treatment after molding, and the strength is increased. Increase. If the Mg content is less than 0.4 mass%, there is little effect for strengthening, and if it exceeds 0.8 mass%, the strength of the base plate becomes too high, and the work hardening becomes too strong and the formability is lowered.

  Si has an effect of improving the strength of the base plate by precipitating Mg—Si based compounds together with Mg. When the Si content is 0.5 mass% or less, there is little effect for strengthening, and when it exceeds 1.5 mass%, in addition to the Mg-Si-based compound, single Si that does not form a compound precipitates. The strength becomes too high and the moldability is lowered.

  Cu has the effect of improving the strength of the base plate by precipitating a Mg—Cu compound by coexistence with Mg. If the Cu content is less than 0.01 mass%, a sufficient effect cannot be obtained. If the Cu content exceeds 0.4 mass%, the strength of the base plate becomes too high to inhibit the formability and the corrosion resistance deteriorates.

  Mn contributes to strength improvement and is an effective element for improving moldability by recrystallized grain refinement. If the Mn content is less than 0.01 mass%, a sufficient effect cannot be obtained. If the Mn content is 0.4 mass% or more, the amount of crystal precipitates increases so as to inhibit the formability and Si precipitates to form crystal precipitates. Is consumed, and the amount of Si dissolved in the matrix decreases, so that it is not possible to improve the strength by age hardening.

Further, in a general aluminum alloy, a small amount of Ti or Ti and B may be added in order to refine the cast structure. In the present invention, a small amount of Ti or Ti and B may be contained. However, when the Ti content is less than 0.0001 mass%, the effect cannot be obtained. When the Ti content exceeds 0.2 mass%, a coarse TiAl ₃ crystallized product is formed and the formability is inhibited, so the Ti content is 0. It is preferable to be within the range of .0001 mass% to 0.2 mass%. Also, when adding B with Ti for grain refining effect improved, the content of B can not be obtained, the effect is less than 0.0001Mass%, coarse particles exceeds 0.05 mass% TiB ₂ is Impairs moldability by mixing. Accordingly, the B content is preferably in the range of 0.0001 mass% to 0.05 mass%.

  In addition, in this invention, when Fe contains, it is set as 0.01 mass%-0.5 mass%. Further, other impurity elements may be included if they are each 0.1 mass% or less and a total of 0.5 mass% or less.

  The resin-coated aluminum alloy plate of the present invention defines not only the above component composition but also the tensile strength and conductivity of the base plate. The reasons for defining the tensile strength and conductivity will be described.

  The tensile strength of the base plate affects the moldability at the time of DI molding and the pressure resistance strength of the can body after the coating baking process. If the tensile strength is less than 270 MPa, the pressure resistance strength of the can body material cannot be ensured, and if it exceeds 380 MPa, the moldability during DI molding is lowered. Therefore, the tensile strength of the base plate is set to 270 MPa or more and 380 MPa or less. More preferably, it is 270 MPa or more and 380 MPa.

  The conductivity of the base plate affects the moldability during DI molding and the pressure resistance of the can body after the paint baking process. The electrical conductivity is related to the solid solution amount or precipitation amount of the alloy element in the Al matrix. The greater the solid solution amount or the smaller the precipitation amount, the lower the conductivity. In the present invention, Mg, Si and Cu are dissolved in the Al matrix by solution treatment. If the amount of these solid solutions is large, the compound of the element is deposited as a precipitate by heating during the coating baking process, Strength after paint baking is improved. That is, high age-hardening property can be obtained. When the electrical conductivity exceeds 50% IACS, the solid solution amount of the element is small, so that the strength increase after the baking treatment is small, and the age hardening is inferior. Moreover, since the amount of precipitates composed of the compound of the element is large, the moldability during DI molding is lowered. On the other hand, when the electrical conductivity is less than 40% IACS, the solid solution amount of the element increases, so that the strength of the base plate is too high and the formability is lowered by work hardening.

  Next, the manufacturing method of this invention alloy plate is demonstrated.

  First, DC casting (semi-continuous casting) of a molten aluminum alloy having the above alloy composition is performed according to a conventional method.

  The homogenization treatment has the purpose of homogenizing the segregation of the ingot. In particular, the present invention has an effect of promoting solid solution of Mg, Si, and Cu and facilitating the solution effect during the solution treatment. When the homogenization treatment temperature is less than 500 ° C., the solid solution of the element is insufficient and the compound composed of the element precipitates coarsely, so that the solid solution does not progress in the solution treatment in the subsequent step and the solution is sufficient. The effect cannot be obtained. If it exceeds 560 ° C., local eutectic melting occurs in the ingot, which is not preferable. Moreover, the said objective will not be achieved if the retention time of a homogenization process is less than 1 hour, and economical efficiency will deteriorate when it exceeds 48 hours. Therefore, the homogenization conditions are preferably a holding time of not less than 1 hour and not more than 48 hours in a temperature range of 500 ° C. to 560 ° C. More preferably, it is 3 hours or more and 6 hours or less.

After the homogenization treatment, hot rough rolling and hot finish rolling are performed. When the finish temperature of hot finish rolling is 280 ° C. or higher, the Mg—Si compound or Mg—Cu compound is coarsely precipitated by the residual heat at the end of hot rolling, so that it is dissolved in the solution treatment in the subsequent process. A sufficient solution effect cannot be obtained. Therefore, the finish temperature for hot finish rolling is preferably less than 280 ° C. However, considering the hot ductility, it is preferably 200 ° C. or higher. In addition, in order to make it into the said temperature range, the usage-amount of lubricating oil, distribution of a coolant and each rolling reduction, a rolling speed, etc. are adjusted.
Further, the plate thickness after hot finish rolling is preferably 10 mm or less in consideration of the winding property.

  Solution treatment is performed after hot finish rolling and before cold rolling or during cold rolling. In the solution treatment, the heating temperature is preferably 450 ° C. or higher and 580 ° C. or lower in order to promote solid solution of Mg, Si and Cu in the alloy. If it is less than 450 ° C., Mg, Si and Cu are not sufficiently dissolved and do not contribute to improvement of strength, and age hardening is reduced by heating during the coating baking process. On the other hand, when the temperature exceeds 580 ° C., local melting of Mg due to burning occurs, and the strength after the coating baking process becomes too high, and the moldability is lowered. The heating and holding time is preferably within 2 minutes. Even if holding for more than 2 minutes, the effect of the solution treatment is saturated, which is uneconomical. Further, if the holding time is excessively long, problems such as deterioration of the appearance of the final plate or deterioration of formability may occur due to the coarsening of crystal grains. As the solution treatment method, rapid heating and rapid cooling and continuous annealing are desirable from the viewpoint of improving formability and improving productivity by refining crystal grains. Also, cooling to 100 ° C. or less at a cooling rate of 1 ° C./sec or more from the standpoint of preventing the precipitation of Mg—Si compound or Mg—Cu compound in the cooling process after solution heating and ensuring the strength of the final plate. Is preferred.

  In the cold rolling after the solution treatment, the rolling rate up to the final thickness is preferably 30% or more. If it is less than 30%, sufficient work hardening cannot be obtained and the strength cannot be ensured.

  A resin film is coated on the aluminum alloy plate that has been cold-rolled to the final thickness. In the present invention, the resin film is preferably a polyester, polyolefin, or polyamide system that releases less harmful environmental hormones such as bisphenol A. In general, since a resin film has excellent workability, it can be applied in advance to an aluminum alloy plate before can body molding, and improvement in DI moldability can also be expected. Compared with the case where anticorrosive protective coating is applied after can body molding, the efficiency and simplification of the coating process can be achieved, which is desirable from the viewpoint of improving productivity.

  As a pretreatment for resin coating, coating with a chemical conversion film or an anodized film improves the adhesion to the resin film. In particular, the chemical conversion film can be formed with simple equipment and is advantageous in terms of cost. The chemical conversion film is formed by chemical conversion treatment such as zinc phosphate method, boehmite method, MBV method, EW method (alkali-chromate system), allodyne method (chromate system, phosphate-chromate system), etc. . The anodized film is formed by anodizing using an electrolytic solution such as sulfuric acid, oxalic acid, chromic acid, or organic acid.

  The coating method is preferably a method in which the resin film is heated to the melting point or higher and thermocompression bonded. If the thermocompression bonding temperature is less than 200 ° C., sufficient adhesion cannot be obtained, and peeling may occur during DI molding. On the other hand, at a temperature exceeding 300 ° C., the resin film is altered. Therefore, the temperature for thermocompression bonding the resin film is preferably 200 ° C. or higher and 300 ° C. or lower.

  In the present invention, fine precipitation of the Mg—Si-based compound or Mg—Cu-based compound occurs by heating at the time of thermocompression bonding of the resin film, and an improvement in strength due to age hardening can be expected. In addition, even if the strength before DI molding is somewhat increased due to the age hardening, the resin-coated aluminum alloy plate is DI molded because the moldability during DI molding is improved by coating the resin film as described above. In this case, the moldability is not impaired. Therefore, by coating the resin film, it is possible to realize a can barrel having a higher strength and a thinner wall.

  If the thickness of the resin film is less than 10 μm, the film thickness is too thin and may be broken during the molding process, and if it exceeds 30 μm, the cost increases. For this reason, as for the thickness of a resin film, 10-30 micrometers is desirable.

  In the present invention, the base plate may be subjected to heat treatment at 100 ° C. or more and 250 ° C. or less for 1 hour or more and less than 24 hours before resin coating. This heat treatment is for fine precipitation of the Mg—Si based compound or the Mg—Cu based compound, and can further improve the strength of the final plate and obtain a desired strength after the coating baking treatment. If it is less than 100 ° C. or less than 1 hour, the effect of improving the strength cannot be sufficiently obtained. On the other hand, if it exceeds 250 ° C., the compound may be coarsened to impair moldability. Moreover, since the said effect will be saturated when it exceeds 24 hours, it is uneconomical. In addition, even if the strength is improved by age hardening by the heat treatment, since the resin is then coated, the moldability is not impaired during DI molding.

  In addition, in beverage cans and the like, it is usual to perform a paint baking process of heating at 150 ° C. or higher and 250 ° C. or lower for about 3 to 10 minutes after DI molding. Since Mg, Si, and Cu are sufficiently dissolved by the solution treatment, fine precipitation of Mg-Si compounds or Mg-Cu compounds occurs due to the coating baking process, and an improvement in strength due to age hardening is expected. it can.

  An aluminum alloy having a composition shown in Table 1 was formed into an ingot having a thickness of 500 mm by a DC casting method. Then, they were made into aluminum alloy plates according to the steps shown in Table 2. In addition, in the composition shown in Table 1, when the content of the component was less than 0.001 mass%, it was described as “−”.

The manufacturing process a shown in Table 2 is the second invention of the present invention, and after the homogenization treatment is performed at 560 ° C. for 6 hours on the alloy ingot, the finish temperature of hot finish rolling is 270 ° C. Rolled to a 2 mm plate, then rolled to a 0.6 mm thick plate by cold rolling, then subjected to a solution treatment at 550 ° C. for 2 minutes in a continuous annealing furnace, then cooled to 0.3 mm thick by air rolling and cold rolling. Roll to plate. Thereafter, both surfaces are subjected to alkali etching and phosphoric acid chromate treatment as a pretreatment to form Cr to a thickness of 15 mg / cm ² , and then a thermocompression bonding of a 15 μm thick resin film at 270 ° C. Manufactured.

  Moreover, the manufacturing process b is a process which performs a solution treatment prior to cold rolling after hot rolling. A solution treatment at 520 ° C. was performed in a continuous annealing furnace, and then air-cooled and then rolled into a 0.3 mm thick plate by cold rolling to produce a resin-coated aluminum alloy plate in the same manner as in the production step a.

  Moreover, the manufacturing process c is a process which heat-processes 120 degreeC x 2 hours to the aluminum alloy plate rolled to thickness 0.3mm as one aspect | mode of implementation of this invention. After the heat treatment, a resin-coated aluminum alloy plate was produced in the same manner as in production step a.

  Manufacturing steps d to g are manufacturing steps as comparative examples of the present invention. In the manufacturing process d, the homogenization temperature is as low as 480 ° C. In the manufacturing process e, the finishing temperature of hot finish rolling is as high as 300 ° C. In the manufacturing process f, the solution treatment temperature is as high as 590 ° C. The manufacturing process g is the same as the manufacturing process a until cold rolling is performed to the final plate thickness, but is a process that does not cover the resin film thereafter.

  As an alternative evaluation of the strength, electrical conductivity, and DI formability, the iron formability and the pressure strength were evaluated for the aluminum alloy plate composed of the above manufacturing process. The results are shown in Table 3. Each characteristic value was measured by the following method.

  Strength: A tensile test was performed using a JIS No. 5 test piece, and the tensile strength of the base plate (thickness 0.3 mm aluminum alloy plate before resin coating) was measured.

  Conductivity: The base plate was measured using an eddy current conductivity measuring apparatus with copper as a reference sample.

  Ironing formability: For resin-coated aluminum alloy plates, changing the inner diameter of the first ironing iron and the second ironing iron changes the ironing ratio of the third ironing iron, and limits the maximum ironing ratio that can be formed to the ironing ratio. did. Specifically, the ironing rate (%) = {1- (can barrel side wall thickness after third ironing) / (can barrel side wall thickness after second ironing)} × 100, and the limit ironing rate is 46. .5% or more is “◯”, and less than 46.5% is “x”.

Pressure strength: A can formed by DI-molding a resin-coated aluminum alloy plate was subjected to a heat treatment equivalent to a coating baking process at 200 ° C. for 10 minutes (hereinafter referred to as “air baking”), and then formed into a dome using an air pressure tester. The pressure at which the bottom buckles was measured. Pressure "○" and 6.8kgf / cm ² or more of, and those less than 6.8kgf / cm ² as "×".

  As apparent from Table 3, the alloy composition falls within the scope of the present invention. Since the tensile strength and electrical conductivity of the alloy plates 1 to 10 were within the specified ranges, all of the iron formability and the pressure strength during DI molding were good.

In contrast, no. About the comparative examples of 11-21, the problem shown below generate | occur | produced.
No. No. 11 has a Mg content of less than 0.4% and is too small, so the yield strength after baking is low and the pressure strength is inferior.
No. In No. 12, the Mg content exceeds 0.8%, so that the tensile strength of the base plate is high and the ironing formability is inferior.
No. No. 13 has a Si content of less than 0.5% and is too small, so the yield strength after baking is low and the pressure strength is inferior.
No. No. 14 has an excess of Si exceeding 1.5%, so that the tensile strength of the base plate is high, and Si simple substance is precipitated, resulting in poor ironing formability.
No. No. 15 has an excessive Cu content exceeding 0.4%, so that the tensile strength of the base plate is high and the ironing formability is inferior.
No. In No. 16, the Mn content exceeds 0.4%, so that the tensile strength of the base plate is high and the ironing formability is inferior.
No. In No. 17, the Ti amount exceeds 0.2%, so that a coarse crystallized product is generated and the ironing formability is inferior.
No. No. 18 has a homogenization treatment temperature as low as less than 500 ° C., and a conductivity exceeding 50% IACS. For this reason, the age hardening is inferior and the yield strength after baking is reduced, so that the pressure strength is inferior. Moreover, since there are many precipitates, iron moldability is also inferior.
No. No. 19 has a hot finish rolling temperature higher than 280 ° C. and a conductivity exceeding 50% IACS. For this reason, the age-hardening property is inferior and the yield strength after baking is reduced, so that the pressure resistance is inferior. Moreover, since there are many precipitates, iron moldability is also inferior.
No. No. 20 has a solution treatment temperature of higher than 580 ° C. and an electrical conductivity of less than 40% IACS, which is too low.
No. No. 21 has the tensile strength and electrical conductivity of the base plate within the specified range of the present invention, but the iron film is inferior in formability because it does not cover the resin film.

  By using the aluminum alloy of the present invention for a beverage can body, it is possible to obtain a can body having an excellent balance between strength and formability and having an excellent strength after a paint baking process, and has a remarkable industrial effect.

Claims (2)

  In the resin-coated aluminum alloy plate, Mg is 0.4 mass% to 0.8 mass%, Si is more than 0.5 mass% to 1.5 mass%, Cu is 0.01 mass% to 0.4 mass%, and Mn is 0. .01 mass% or more and less than 0.4 mass%, the balance is Al and inevitable impurities, the tensile strength at the final plate thickness is 270 MPa or more and 380 MPa or less, and the conductivity is 40% IACS or more and 50% IACS or less. A resin-coated aluminum alloy plate characterized by the above.   The method for producing an aluminum alloy sheet according to claim 1, wherein the ingot having the alloy composition is subjected to homogenization treatment at a temperature of 500 ° C or higher and 560 ° C or lower for 1 hour or more and 48 hours or less, and then hot rough rolling is performed. Followed by hot finish rolling at a rolling end temperature of less than 280 ° C., followed by cold rolling and before cold rolling after the hot finish rolling, or in the middle of cold rolling, 450 A method for producing a resin-coated aluminum alloy plate, which comprises subjecting a solution treatment to be performed at a temperature of from ℃ to 580 ° C. within 2 minutes and further coating a resin film on the aluminum alloy plate having a final thickness.