Uncoated aluminum alloy sheet for can lids

Abstract

Provided is an uncoated aluminum alloy sheet for can lids, which, while incorporating scrap starting material derived from can materials, can achieve both high strength and high toughness. An embodiment of the present disclosure is an uncoated aluminum alloy sheet for can lids, wherein Si is at least 0.27 mass% and not more than 0.39 mass%, Fe is at least 0.35 mass% and not more than 0.55 mass%, Cu is at least 0.17 mass% and not more than 0.25 mass%, Mn is at least 0.75 mass% and not more than 0.95 mass%, and Mg is at least 2.2 mass% and not more than 2.8 mass%. An evaluation value S -- calculated with formula (1) using, for the 0° direction with respect to the rolling direction, the 0.2% proof stress σ0.2, tensile strength σB, and average value σfm of the 0.2% proof stress and tensile strength -- is at least 410 mPa and not more than 450 MPa.　(1): S = σfm / (σ0.2 / σB)

Description

Unpainted aluminum alloy sheet for can lids CROSS-REFERENCE TO RELATED APPLICATIONS

[0001] This international application claims the benefit of Japanese Patent Application No. 2023-223497, filed with the Japan Patent Office on December 28, 2023, the entire disclosure of which is incorporated herein by reference.

[0002] The present disclosure relates to an unpainted aluminum alloy sheet for can ends.

[0003] In recent years, with the rise of environmental awareness, CO ２ There is a demand for aluminum alloy sheets with low CO emissions. ２ The compounding of new aluminum ingots in the casting process indirectly contributes significantly to these emissions.

[0004] The production of primary aluminum ingots uses a large amount of electricity during the smelting process and produces a large amount of CO ２ Therefore, reducing the amount of virgin aluminum used and increasing the horizontal recycling rate will reduce CO emissions in the manufacture of aluminum alloy sheets. ２ This will lead to reduced emissions.

[0005] Generally, CO generated when aluminum scrap is remelted and cast ２ It is said that waste emissions can be reduced to about one-thirtieth of that when producing virgin aluminum ingots. In particular, the production volume of aluminum alloy sheets for beverage cans used worldwide is extremely large, and further improving the horizontal recycling rate for these cans will have a significant impact on reducing the environmental impact.

[0006] Among these, can ends made of 5182 aluminum alloy (AA5182 alloy) have lower upper limits for the compositional specifications of Si, Fe, Cu, Mn, etc. than can bodies made of 3104 aluminum alloy (AA3104 alloy), making it difficult to incorporate scrap derived from can stock containing 3104 aluminum alloy.

[0007] For example, if can scrap (UBC: Used Beverage Can) generated in the market is blended as is, the weight ratio of the can body to the can lid will result in a higher content of 3104 aluminum alloy components, which will likely exceed the upper limit of the content of 5182 aluminum alloy, making it necessary to dilute the components with virgin metal.

[0008] Therefore, compared with the aluminum alloy sheet for can bodies, the aluminum alloy sheet for can ends uses a larger amount of virgin metal to adjust the composition to that of 5182 aluminum alloy, resulting in a low recyclability. Therefore, by changing the can ends to an alloy whose composition is easily blended with 3104 aluminum alloy, the virgin metal usage rate for can ends can be significantly reduced.

[0009] Patent Documents 1 to 5 disclose aluminum alloy sheets for can lids that have compositions relatively close to those of 3104 aluminum alloy, which has excellent recyclability.

[0010] Japanese Patent Application Laid-Open No. 2001-73106 Japanese Patent Application Laid-Open No. 9-070925 Japanese Patent Application Laid-Open No. 11-269594 Japanese Patent Application Laid-Open No. 2000-160273 Japanese Patent Application Laid-Open No. 2016-160511

[0011] The problem of using an alloy for can lids with a composition similar to that of 3104 aluminum alloy is that it reduces the pressure resistance of the can lid and the toughness of the material. The pressure resistance of a can lid is the internal pressure value when the can lid is inverted against the pressure inside the can, and is the resistance value when the internal pressure of the can increases unexpectedly due to a change in the external environment.

[0012] In particular, positively pressurized cans for beer and carbonated beverages require high pressure resistance. Generally, the stronger the material and the thicker the plate, the greater the pressure resistance. For this reason, the lids of positively pressurized cans are made of high-strength 5182 aluminum alloy, which contains a large amount of magnesium, a component that contributes to increased strength.

[0013] In contrast, if conventional 3104 aluminum alloy is used for can lids, the pressure resistance is significantly reduced, and there is a high risk that the lid will invert and leak contents if the internal pressure of the can suddenly increases. Furthermore, if the plate thickness is increased to increase the pressure resistance, this will result in an increase in the weight and cost of the lid.

[0014] Furthermore, the toughness of the material affects the formability and openability of the lid. If the material has low toughness, cracks may occur during molding, especially at the rivet and countersink areas of the lid. Also, if the internal pressure of the can suddenly increases, cracks may occur at the score area, increasing the risk of the can contents leaking. These cracks occur particularly along the rolling direction. Therefore, the material must have toughness against tensile stress and bending stress in directions perpendicular to the rolling direction.

[0015] However, aluminum alloy sheets for can lids, which have chemical compositions relatively close to those of the conventional 3104 aluminum alloy, do not satisfy either or both of the above-mentioned two problems, i.e., material strength (i.e., pressure resistance of the lid) and toughness (i.e., formability and openability).

[0016] One aspect of the present disclosure is to provide an unpainted aluminum alloy sheet for can ends that contains scrap raw materials derived from can stock and yet has both high strength and high toughness after paint baking.

[0017] In one embodiment of the present disclosure, the silicon (Si) content is 0.27% by mass or more and 0.39% by mass or less, the iron (Fe) content is 0.35% by mass or more and 0.55% by mass or less, the copper (Cu) content is 0.17% by mass or more and 0.25% by mass or less, the manganese (Mn) content is 0.75% by mass or more and 0.95% by mass or less, the magnesium (Mg) content is 2.2% by mass or more and 2.8% by mass or less, and the balance is aluminum (Al) and unavoidable impurities or contains aluminum (Al) and unavoidable impurities, and in a direction of 0° relative to the rolling direction, a 0.2% proof stress σ ０．２ , tensile strength σ Ｂ , and the average value σ of 0.2% proof stress and tensile strength ｆｍ The unpainted aluminum alloy sheet for can ends has an evaluation value S calculated by the following formula (1) using

[0018] S = σ ｆｍ / (σ ０．２ / σ Ｂ) ... (1) According to this configuration, it is possible to achieve both high strength and high toughness in the aluminum alloy sheet after paint baking while blending scrap raw material derived from can stock. That is, it is possible to blend a certain amount of 3104 aluminum alloy scrap for can bodies, reduce the usage rate of new metal, and reduce CO ２ Furthermore, it is possible to obtain an unpainted aluminum alloy sheet for can ends that has high formability and can be used for positive pressure can ends, which require high pressure resistance.

[0019] The "unpainted aluminum alloy sheet for can ends" of the present disclosure is an alloy sheet (i.e., a bare material) that is to be used as an aluminum alloy sheet for can ends after painting. That is, the "aluminum alloy sheet for can ends" is obtained by painting the "unpainted aluminum alloy sheet for can ends" of the present disclosure.

[0020] Fig. 1 is a schematic diagram of a repeated bending test, and Fig. 2 is an explanatory diagram of an L-ST cross section.

[0021] Hereinafter, embodiments to which the present disclosure is applied will be described with reference to the drawings.

[0022] [1. First embodiment] [1-1. Configuration] The unpainted aluminum alloy sheet for can ends of the present disclosure may be continuously painted as a coil on a painting line, or may be cut into sheets and then painted or laminated to form into lids. The unpainted aluminum alloy sheet for can ends of the present disclosure can be used for any application. Furthermore, the unpainted aluminum alloy sheet for can ends is not limited to applications as beverage can lids, and can be widely used for food can lids, etc.

[0023] <Composition> The unpainted aluminum alloy sheet for can ends (hereinafter also simply referred to as "alloy sheet") of the present disclosure contains aluminum (Al), silicon (Si), iron (Fe), copper (Cu), manganese (Mn), and magnesium (Mg).

[0024] The lower limit of the Si content is 0.27% by mass, preferably 0.30% by mass. If the Si content is less than 0.27% by mass, the amount of Si precipitated during the processing heat of hot rolling and cold rolling after solution treatment may decrease, and the strength of the alloy sheet after paint baking may be insufficient.

[0025] The average Si content of 3104 aluminum alloy specified in JIS-H-4000: 2014 is 0.30% by mass. Therefore, by setting the Si content to 0.27% by mass or more, preferably 0.30% by mass or more, a large amount of 3104 aluminum alloy scrap can be blended.

[0026] The upper limit of the Si content is 0.39 mass%, preferably 0.35 mass%. If the Si content exceeds 0.39 mass%, Mg ２ The amount of Si particles increases, and the toughness of the alloy sheet after paint baking decreases.

[0027] The lower limit of the Fe content is 0.35% by mass, preferably 0.40% by mass. The average Fe content of the 3104 aluminum alloy is 0.40% by mass. Therefore, by setting the Fe content to 0.35% by mass or more, preferably 0.40% by mass or more, a large amount of 3104 aluminum alloy scrap can be blended.

[0028] The upper limit of the Fe content is 0.55% by mass. If the Fe content exceeds 0.55% by mass, the amount of Al-Fe-Mn or Al-Fe-Mn-Si intermetallic compounds (i.e., second phase particles) increases. As a result, crack propagation paths are created, and the toughness of the alloy sheet after paint baking decreases.

[0029] The lower limit of the Cu content is 0.17 mass%, more preferably 0.20 mass%. If the Cu content is less than 0.17 mass%, the amount of Cu that increases strength by solid solution or precipitation is insufficient, resulting in a decrease in the strength of the alloy sheet. Note that by precipitating Cu during the cold rolling process after hot rolling and solution treatment, the strength of the alloy sheet after paint baking is significantly increased.

[0030] The average Cu content of the 3104 aluminum alloy is 0.15% by mass, so by making the Cu content 0.17% by mass or more, it is possible to blend a large amount of 3104 aluminum alloy scrap.

[0031] The upper limit of the Cu content is 0.25 mass %. If the Cu content exceeds 0.25 mass %, the toughness of the alloy sheet after paint baking decreases.

[0032] The lower limit of the Mn content is 0.75 mass%, preferably 0.80 mass%. If the Mn content is less than 0.75 mass%, the amount of Mn that increases strength by solid solution or precipitation will be insufficient, and the average strength of the alloy sheet after paint baking will decrease.

[0033] The average Mn content of the 3104 aluminum alloy is 1.1 mass% and the average Mn content of the 5182 aluminum alloy is 0.35 mass%. Therefore, by setting the Mn content to 0.75 mass% or more, it is possible to blend more 3104 aluminum alloy scrap than in the conventional 5182 aluminum alloy.

[0034] The upper limit of the Mn content is 0.95% by mass, preferably 0.90% by mass. If the Mn content exceeds 0.95% by mass, the amount of Al-Fe-Mn or Al-Fe-Mn-Si intermetallic compounds (i.e., second phase particles) increases. As a result, crack propagation paths are created, and the toughness of the alloy sheet after paint baking decreases.

[0035] The lower limit of the Mg content is 2.2% by mass. If the Mg content is less than 2.2% by mass, there will be insufficient Mg, which increases strength through solid solution, and the average strength of the alloy sheet will decrease. Note that, by precipitating Mg during the cold rolling process after hot rolling and solution treatment, the strength of the alloy sheet after paint baking will be significantly increased.

[0036] The upper limit of the Mg content is 2.8% by mass. The average Mg content standard for 3104 aluminum alloy is 1.05% by mass, and the average Mg content standard for 5182 aluminum alloy is 4.5% by mass. Therefore, by setting the Mg content to 2.8% by mass or less, it is possible to incorporate a large amount of 3104 aluminum alloy scrap while reducing the amount of additional Mg-containing raw material.

[0037] The alloy plate may contain titanium (Ti). The upper limit of the Ti content is preferably 0.10 mass%. By including Ti, the ingot structure of the alloy plate is refined. The alloy plate may also contain zinc (Zn). The upper limit of the Zn content is preferably 0.25 mass%. Furthermore, the alloy plate may also contain chromium (Cr). The upper limit of the Cr content is preferably 0.10 mass%.

[0038] The alloy plate may contain unavoidable impurities to the extent that the performance of the alloy plate is not significantly impaired. That is, the alloy plate contains Si, Fe, Cu, Mn, Mg, Ti, Zn, and Cr within the respective ranges described above, with the balance consisting of aluminum and unavoidable impurities. The balance may be understood to include aluminum and unavoidable impurities. The balance may include substances other than aluminum and unavoidable impurities. The upper limit of the total amount of unavoidable impurities is preferably 0.15% by mass.

[0039] <Material strength and pressure resistance> Rolled aluminum alloy sheets have material anisotropy, and their strength varies in the 0°, 45°, and 90° directions relative to the rolling direction. When the pressure inside the can increases, deformation begins in the direction with the lowest strength.

[0040] Therefore, the alloy sheet of the present disclosure has a 0.2% yield strength σ in the direction of 0° relative to the rolling direction. ０．２ , tensile strength σ Ｂ , and the average value σ of 0.2% proof stress and tensile strength ｆｍ The evaluation value S0° calculated by the following formula (1) using the above formula is 410 MPa or more and 450 MPa or less.

[0041] S = σ ｆｍ / (σ ０．２ / σ Ｂ ) ... (1) Furthermore, the alloy plate of the present disclosure has a 0.2% yield strength σ after heat treatment at 260°C for 25 seconds in each of the 0°, 45°, and 90° directions relative to the rolling direction. ０．２ , tensile strength σ Ｂ , and the average value σ of 0.2% proof stress and tensile strength ｆｍ The minimum evaluation value S is the minimum value of the evaluation values ​​S (S0°, S45°, and S90°) calculated by the above formula (1) usingｍｉｎ (=min(S0°, S45°, S90°)) is preferably 370 MPa or more and 410 MPa or less.

[0042] The pressure resistance value of the lid made of aluminum alloy plate is empirically the minimum evaluation value S after painting and baking. ｍｉｎ and the plate thickness t, there is a strong positive correlation with the value V of the following formula (2).

[0043] V = t ２．２７ ×S ｍｉｎ ... (2) Therefore, by setting the evaluation value S0° of the alloy plate to 410 MPa or more, it is possible to form a lid having sufficient pressure resistance without increasing the plate thickness. Furthermore, the minimum evaluation value S of the alloy plate after heat treatment at 260°C for 25 seconds is ｍｉｎ When the pressure resistance is 370 MPa or more, the effect of improving the pressure resistance is enhanced.

[0044] Furthermore, if the evaluation value S0° exceeds 450 MPa, the material strength becomes excessively high, resulting in a decrease in the toughness of the material. In other words, shear bands are more likely to occur due to the tensile stress and bending stress that occur in the material during forming, making it more likely that forming cracks will occur. By setting the evaluation value S0° to 450 MPa or less, it is possible to achieve both the strength of the material (i.e., the pressure resistance of the lid) and the toughness (i.e., formability and openability). Furthermore, the minimum evaluation value S of the alloy plate after heat treatment at 260°C for 25 seconds is 450 MPa. ｍｉｎ When the modulus of elasticity is 410 MPa or less, it is possible to improve the compatibility between strength and toughness.

[0045] 0.2% proof stress σ in formula (1) ０．２ and tensile strength σ Ｂ is measured by the method specified in JIS-Z-2241: 2011. The plate thickness t is measured, for example, with a microgauge.

[0046] The withstand pressure of an aluminum alloy plate is measured, for example, by the following procedure. First, a shell formed from a baked aluminum alloy plate is fixed to a jig and internal pressure is applied. Next, this internal pressure is gradually increased, and the internal pressure value when the shell inverts (i.e., buckles) is taken as the withstand pressure value.

[0047] Specifically, a φ204 full-form (B64) shell mold is used to mold the shell. Internal pressure values ​​are measured using a Versatile Technology DV036E buckle and missile measuring machine. Specifically, after fixing the molded shell in place with a dedicated jig, the internal pressure is increased using a program, and the internal pressure value is read when the shell inverts. For example, the internal pressure is increased at a rate of approximately 175 kPa / s, and when it reaches approximately 350 kPa to 400 kPa, the internal pressure is increased at a rate of 10 kPa / s.

[0048] <Toughness> It is known that the formability of the lid and the force required to open the score (i.e., opening force) are affected by the toughness of the aluminum alloy plate after paint baking.

[0049] (Number of repeated bending) A repeated bending test is one of the evaluation indices for the toughness of an aluminum alloy sheet. For a given sheet thickness, the more repeated bending times an aluminum alloy sheet can be subjected to, the more excellent its toughness.

[0050] The repeated bending test is carried out as follows. For example, as shown in Fig. 1, a test piece is heat-treated at 260°C for 25 seconds and cut into a strip shape with a width of 12.5 mm and a length of 200 mm, and is positioned so that the bending ridgeline R is parallel to the rolling direction D of the alloy plate. Both ends of this test piece are fixed with chucks, and a tension of 200 N is applied.

[0051] In this state, the test piece is repeatedly bent by rotating the other chuck 90° left and right, using a jig with a bending radius of 2.0 mm as a fulcrum, which is positioned 150 mm in the longitudinal direction of the test piece from the end of the test piece fixed to one of the immovable chucks, and the number of bends until the test piece breaks is measured.

[0052] The number of bending times is counted as one bending operation to either the left or right by 90° and one operation returning to the original position. If the wire breaks during bending, the angle Θ (0°-90°) is read and the number of repeated bending times N is calculated using the following formula (3). In formula (3), N ０ is the total number of times that the test piece was bent 90° to either the left or right and returned to the original 0° position from the 90° bent position until it broke.

[0053] N=N ０ +Θ / 90 ... (3) Repeated bending evaluation is more disadvantageous as the plate thickness increases, so it is necessary to consider it by correcting it with a standard plate thickness. Therefore, the normalized number of repeated bending times N is normalized by the following formula (4) using a plate thickness of 0.235 mm as the standard. ｓ where t (mm) is the thickness of the test piece.

[0054] N ｓ = N × t / 0.235 (4) The normalized number of repeated bending times N for the unpainted aluminum alloy sheet of the present disclosure ｓ The number of times is preferably 14.0 or more.

[0055] (Second-phase particles) Toughness is affected by strength and the distribution of second-phase particles. That is, the higher the strength and the higher the density of second-phase particles, the lower the toughness. In particular, when the contents of Mg and Si are high, the distribution of Mg ２ As a result, Mg ２ The Si particles act as crack initiation points and propagation paths, which reduces toughness.

[0056] In the unpainted aluminum alloy sheet of the present disclosure, the area of ​​the L-ST cross section in the width direction center part after heat treatment at 260 ° C for 25 seconds is 0.3 μm ２ More than Mg ２ The ratio of the total area of ​​the Si particles in the L-ST cross section is preferably 0.2% or less. In Fig. 2, L indicates the longitudinal direction, ST indicates the plate thickness direction, and LT indicates the width direction.

[0057] Mg ２ The area ratio of Si particles can be measured, for example, by the following method. First, a measurement sample is cut, and the surface to be measured (i.e., the L-ST cross section) is mechanically polished to a mirror finish. Next, the polished surface (i.e., the L-ST cross section) is observed using a SEM (scanning electron microscope) to obtain 10 fields of view. The acceleration voltage of the SEM is 15 kV, the magnification is 500 times, and the range of one field of view is 0.049 mm. ２ The image is taken as is, and a COMPO (backscattered electron composition) image is obtained.

[0058] The captured COMPO image is analyzed using the image analysis software "ImageJ." The threshold value must be set appropriately when setting the contrast during SEM observation. From the histogram of the image brightness in 256 gradations, Mg ２ The threshold value for distinguishing between Si particles and Al-Fe-Mn compound particles is calculated. ２ In an image in which Si particles and Al-Fe-Mn compound particles are present, there are three peaks in the brightness histogram. The peak with the most frequent value corresponds to the peak of the aluminum matrix, and the brightness of this peak is designated as P1. The peaks in the region of brightness lower than the peak of the aluminum matrix are Mg ２ The peak brightness of this peak is designated as P2. Particles with a brightness lower than the average of P1 and P2 are designated as Mg ２ It is determined to be a Si particle.

[0059] Determined Mg ２ Among the Si particles, 0.3 μm ２ The total area of ​​particles with an area of ​​0.3 μm or more was calculated and divided by the photographed area of ​​10 fields of view (i.e., the total photographed area), resulting in an area of ​​0.3 μm ２ More than Mg ２ The percentage of the total area of ​​the Si particles in the L-ST cross section is calculated.

[0060] <Strength Anisotropy> It is known that a material with a low cold rolling ratio (hereinafter abbreviated as cold rolling ratio) has high toughness, and a material with a high cold rolling ratio has high strength. In addition, the higher the cold rolling ratio, the greater the 0.2% proof stress σ in the direction at 90° to the rolling direction. ０．２＿９０° , 0.2% proof stress σ in the 0° direction ０．２＿０° Therefore, the difference in 0.2% yield strength between the 0° direction and the 90° direction with respect to the rolling direction, that is, the strength anisotropy, can be associated with the cold rolling rate of the material.

[0061] In order to achieve toughness that can ensure formability of the lid, the alloy plate of the present disclosure has a 0.2% yield strength σ in the direction of 0° to the rolling direction after heat treatment at 260°C for 25 seconds, as calculated by formula (5). ０．２＿０° From the above, after heat treatment at 260 ° C for 25 seconds, the 0.2% proof stress σ in the direction at 90 ° to the rolling direction ０．２＿９０°It is preferable that the value D obtained by subtracting ΔN is -20 MPa or more. However, if the value D is -10 MPa or more, the cold rolling rate will be low and the strength may be insufficient. Therefore, it is preferable that the value D of the strength anisotropy is -10 MPa or less.

[0062] D = σ ０．２＿０° -σ ０．２＿９０° ... (5) 0.2% proof stress σ in the 0° direction relative to the rolling direction after heat treatment at 260 ° C. for 25 seconds ０．２＿０° From the above, after heat treatment at 260 ° C for 25 seconds, the 0.2% proof stress σ in the direction at 90 ° to the rolling direction ０．２＿９０° The material structure meaning of the strength anisotropy minus can be explained as follows.

[0063] After hot rolling or annealing, the material is in a recrystallized state, with a high concentration of isotropic Cube orientation. From this point, plastic deformation by cold rolling transforms the Cube orientation into a rolling texture with anisotropy in the rolling direction. Furthermore, the larger the cold rolling rate, the more the crystal grains are elongated in the rolling direction, so the diameter of the crystal grains along the 0° direction relative to the rolling direction increases, while the change in the diameter of the crystal grains along the 90° direction relative to the rolling direction becomes smaller than in the 0° direction.

[0064] The structural changes caused by these rolling processes and the 0.2% yield strength σ ０．２ The relationship between these two is expressed by the Hall-Petch equation as shown in Equation (6): In Equation (6), κ is the resistance to sliding of the grain boundary, and d is the grain size.

[0065] σ ０．２ ∝κ×d−½ (6) The resistance κ has different values ​​when tension is applied in the 0° direction or 90° direction relative to the rolling direction. This is because the degree of integration of the rolling texture, which is anisotropic in the rolling direction, increases with an increase in the cold reduction ratio, and the resistance to sliding of the grain boundaries changes depending on the tension direction.

[0066] In addition, in the direction of 0° from the rolling direction, the grains elongate and their diameters increase with increasing cold rolling, whereas in the direction of 90° from the rolling direction, the change in grain size with increasing cold rolling is relatively small. The cumulative effect of these effects results in strength anisotropy with increasing cold rolling.

[0067] <Method for producing aluminum alloy sheet> The unpainted aluminum alloy sheet of the present disclosure can be produced, for example, as follows: First, an aluminum alloy having the composition of the unpainted aluminum alloy sheet of the present disclosure is subjected to a semi-continuous casting method (i.e., DC casting) according to a conventional method to produce an ingot.

[0068] Next, the four sides of the ingot, excluding the front and rear ends, are chamfered. The ingot is then placed in a soaking furnace for homogenization. The temperature in the homogenization is preferably, for example, 470°C or higher and 620°C or lower. The time for the homogenization is preferably, for example, 1 hour or higher and 20 hours or lower.

[0069] When the homogenization temperature is 400°C or higher, segregation of the ingot structure is easily eliminated. Furthermore, when the homogenization temperature is 450°C or higher, Mg ２ The homogenization temperature is 470°C or higher, preferably 550°C or higher, and the Mg ２ The re-dissolution of Si particles is promoted, and the strength and toughness of the alloy plate can be further improved. On the other hand, if the temperature in the homogenization treatment is 620°C or less, local melting of the aluminum alloy is unlikely to occur.

[0070] When the homogenization treatment time is 1 hour or more, the temperature of the entire slab becomes uniform, segregation of the ingot structure is easily eliminated, and Mg ２ The longer the homogenization time, the easier it is to redissolve the Si particles. ２ The Si particles can be redissolved. However, if the homogenization treatment time exceeds 20 hours, the effect of the homogenization treatment becomes saturated.

[0071] After the homogenization treatment, the ingot is subjected to hot rolling. The hot rolling process includes a rough rolling process and a finish rolling process. In the rough rolling process, the ingot is processed into a plate material having a thickness of about several tens of mm by reverse rolling. In the finish rolling process, the thickness of the plate material is reduced to about several mm by, for example, tandem rolling, and the plate material is wound into a coil to form a hot-rolled coil.

[0072] If the total reduction rate of the finish rolling is high, a recrystallized structure is formed after coiling, and the concentration of the Cube orientation can be increased. If the coiling temperature of the finish rolling is high, a recrystallized structure is formed after coiling, and the concentration of the Cube orientation can be increased.

[0073] Furthermore, a high-strength alloy sheet can be obtained by subjecting a hot-rolled coil to solution treatment to redissolve Mg, etc. For example, the strength of the alloy sheet can be effectively increased by performing heat treatment (i.e., annealing) at a target solid temperature of 440°C or higher for 30 seconds or longer using a continuous annealing furnace (CAL), followed by forced cooling by air cooling or the like.

[0074] Following the hot rolling, the plate material is cold rolled. In the cold rolling, the hot rolled coil is rolled until the product plate thickness is reached. The cold rolling may be either single rolling or tandem rolling. In the cold rolling by single rolling, it is preferable to perform the rolling in two or more passes.

[0075] Furthermore, by setting the finishing temperature of cold rolling in intermediate passes other than the final pass to 120°C or higher, Si, Cu, and Mg are finely precipitated and age-hardened, thereby increasing the strength of the alloy sheet. Furthermore, by setting the finishing temperature to 130°C or higher, the strength of the alloy sheet can be further increased.

[0076] The cold rolling rate (i.e., the target total rolling reduction rate) is preferably 80% or more. When the cold rolling rate is 80% or more, the strength of the alloy sheet can be increased. Furthermore, the lower the cold rolling rate, the more the Cube orientation remains, so the cold rolling rate is preferably 92% or less.

[0077] The cold rolling rate R (%) is the thickness t after hot rolling or solution treatment. ０ (mm), product thickness after cold rolling t １ (mm) is calculated using the following formula (7).

[0078] R = (t ０ -t １ ) / t ０× 100 (7) The product plate thickness can be appropriately selected so as to obtain a desired pressure resistance. As shown in the above formula (2), the pressure resistance improves as the plate thickness increases. The product plate thickness can be selected according to the value V in formula (2), and it is preferable that the value V is 13.0 or more, preferably 14.0 or more, after heat treatment at 260°C for 25 seconds. As described above, the unpainted aluminum alloy plate of the present disclosure can suppress an increase in plate thickness to maintain high pressure resistance.

[0079] By such a rolling treatment, an unpainted aluminum alloy sheet is obtained. The obtained unpainted aluminum alloy sheet (i.e., a coil cold-rolled to a product thickness) is subjected to painting including pre-coating in a painting line or the like to obtain a painted aluminum alloy sheet. The surface of the cold-rolled coil is degreased, washed, and subjected to a chemical conversion treatment, and then painted, followed by a paint baking treatment.

[0080] Chemical solutions such as chromate-based and zirconium-based solutions are used in chemical conversion treatments. Epoxy-based and polyester-based paints are used. These can be selected according to the application. In the paint baking process, the coil is heated to a peak metal temperature (PMT) of 220°C to 270°C for approximately 30 seconds or less. The lower the PMT, the more the recovery of the material is suppressed, and the higher the strength of the alloy plate can be maintained.

[0081] [1-2. Effects] According to the embodiment described above in detail, the following effects can be obtained.

[0082] (1a) While blending scrap raw materials derived from can stock, it is possible to achieve both high strength and high toughness of the aluminum alloy sheet after paint baking. That is, it is possible to blend a certain amount of 3104 aluminum alloy scrap for can bodies, reduce the usage rate of virgin metal, and reduce CO ２ Furthermore, it is possible to obtain an aluminum alloy sheet for can ends after baking that has high formability and can be used for positive pressure can ends, which require high pressure resistance.

[0083] [2. Other Embodiments] Although the embodiments of the present disclosure have been described above, it goes without saying that the present disclosure is not limited to the above-described embodiments and can take on various forms.

[0084] (2a) In addition to the unpainted aluminum alloy plate of the above embodiment, the present disclosure also includes various forms such as a member made of this unpainted aluminum alloy plate and a method for manufacturing this unpainted aluminum alloy plate.

[0085] (2b) The function of one component in the above embodiments may be distributed among multiple components, or the functions of multiple components may be integrated into one component. Also, part of the configuration of the above embodiments may be omitted. Furthermore, at least part of the configuration of the above embodiments may be added to, replaced with, or the like, the configuration of another of the above embodiments. Note that all aspects included in the technical idea identified by the wording of the claims are embodiments of the present disclosure.

[0086] 3. Examples The following describes the details of tests conducted to confirm the effects of the present disclosure and the evaluation results thereof.

[0087] <Production of Unpainted Aluminum Alloy Sheets> As examples and comparative examples, unpainted aluminum alloy sheets S1 to S4 shown in Tables 1 and 2 were produced. Specific production procedures are described below.

[0088] First, an ingot containing the components (mass %) of Alloy Nos. 1-4 shown in Table 3, with the balance consisting of aluminum and unavoidable impurities, was produced by semi-continuous casting. The ingot contained 0.10 mass % or less of Ti, 0.25 mass % or less of Zn, 0.10 mass % or less of Cr, and 0.15 mass % or less of unavoidable impurities. The balance may be understood to include aluminum and unavoidable impurities. The balance may also include substances other than aluminum and unavoidable impurities.

[0089] Next, the four sides of the ingot, excluding the front and rear ends, were chamfered. The ingot was then placed in a furnace and subjected to homogenization treatment. The homogenization treatment temperature is shown in Table 1. After the homogenization treatment, the ingot was removed from the furnace, and immediately hot rolling was started to produce a rolled sheet.

[0090] Furthermore, for S1, S2, and S4, the rolled sheets after hot rolling were cold rolled until they reached the CAL thickness shown in Table 1. Thereafter, the rolled sheets having the CAL thickness were annealed in a continuous annealing furnace (CAL). The CAL temperature during annealing is as shown in Table 1. After annealing, the rolled sheets were cooled to room temperature by air cooling. After cooling, the rolled sheets were cold rolled again. The target cold reduction ratios in the cold rolling after annealing are as shown in Table 1.

[0091] For S3, the hot-rolled sheet was subjected to cold rolling without annealing. The target cold rolling reduction ratios are shown in Table 1.

[0092] The unpainted aluminum alloy sheets S1-S4 were obtained by the above-mentioned treatment. The product thickness after cold rolling in S1-S4 (i.e., t １ ) was in the range of approximately 0.235±0.03 mm. Table 1 shows the thicknesses of the unpainted aluminum alloy sheets S1 to S4 measured with a microgauge (i.e., product thicknesses).

[0093]

[0094]

[0095] <Evaluation of unpainted aluminum alloy sheets> (Tensile properties) Three No. 5 test pieces defined in JIS-Z-2241: 2011 were prepared from each of the unpainted aluminum alloy sheets S1 to S4 by milling. The longitudinal directions of the three test pieces extended in directions forming angles of 0°, 45°, and 90° with respect to the rolling direction, respectively.

[0096] These test pieces were subjected to a heat treatment at 260°C for 25 seconds, which is a heat treatment simulating paint baking, and then a tensile test was carried out in accordance with JIS-Z-2241:2011 to measure the 0.2% proof stress and tensile strength. For the test pieces in the 0° direction relative to the rolling direction, the 0.2% proof stress and tensile strength were measured even before the heat treatment. In addition, the 0.2% proof stress σ ０．２ and tensile strength σ ＢThe measurement results of the evaluation values ​​S (S0°, S45°, and S90°) calculated from the formula (1), and the minimum evaluation value S ｍｉｎ The results are shown in Tables 1 and 2.

[0097] (Toughness) In the unpainted aluminum alloy plates of S1 to S4, the area after heat treatment at 260°C for 25 seconds was 0.3 μm by the measurement method described in the embodiment. ２ More than Mg ２ The ratio of the total area (area ratio) of the Si particles in the L-ST cross section was calculated. The measurement results are shown in Table 2.

[0098] For the unpainted aluminum alloy plates S1 to S4, the number of repeated bendings and the normalized number of repeated bendings after heat treatment at 260°C for 25 seconds were calculated using the measurement method described in the embodiment and equations (3) and (4). The results are shown in Table 2.

[0099] (Scrap Blending Ratio) With respect to the compositions of the unpainted aluminum alloy plates S1 to S4, it was determined whether the possible blending ratio of 3104 aluminum alloy scrap was 50 mass % or more. The results are shown in Table 2.

[0100] In Table 2, unpainted aluminum alloy plates indicated as "≧50" can contain 50 mass% or more of 3104 aluminum alloy. The possible blending ratio of 3104 aluminum alloy scrap is determined based on Table 4.

[0101] Table 4 shows the relationship between the blending ratios of 3104 aluminum alloy and 5182 aluminum alloy and the average values ​​of the component specifications. The first row of Table 4 shows the average values ​​of the component specifications of 3104 aluminum alloy, and the second row shows the average values ​​of the component specifications of 5182 aluminum alloy.

[0102] For example, when the compounding ratio of 3104 aluminum alloy is 50 mass%, the average value of Si is 0.20 mass%, the average value of Fe is 0.29 mass%, the average value of Cu is 0.11 mass%, the average value of Mn is 0.7 mass%, and the average value of Mg is 2.8 mass%.

[0103] Therefore, when the proportions of each component of the unpainted aluminum alloy plate are equal to or greater than the above-mentioned values ​​of Si, Fe, Cu, Mn, and Mg, the possible blending ratio of 3104 aluminum alloy plate is 50% by mass or more. As the blending ratio of 3104 aluminum alloy increases, the contents of Si, Fe, Cu, and Mn increase and the content of Mg decreases. The unpainted aluminum alloy plate S1-S2 can blend 50% by mass or more of 3104 aluminum alloy scrap.

[0104] (Evaluation) The unpainted aluminum alloy plates S1-S2 had a lower Mg content than the unpainted aluminum alloy plate S4, but exhibited higher strength. That is, the unpainted aluminum alloy plates S1-S2 were able to achieve both strength and toughness compared to S4.

[0105] The unpainted aluminum alloy S1 was heat treated at 260°C for 25 seconds. ２ The area ratio of Si particles is small, 0.2% or less. Furthermore, the unpainted aluminum alloy sheet S1 has a higher number of repeated bending cycles after heat treatment at 260°C for 25 seconds than the unpainted aluminum alloy sheet S2.

Claims

1. An aluminum alloy sheet for an uncoated can lid, having a silicon (Si) content of 0.27% by mass or more and 0.39% by mass or less, an iron (Fe) content of 0.35% by mass or more and 0.55% by mass or less, a copper (Cu) content of 0.17% by mass or more and 0.25% by mass or less, a manganese (Mn) content of 0.75% by mass or more and 0.95% by mass or less, a magnesium (Mg) content of 2.2% by mass or more and 2.8% by mass or less, the balance being composed of aluminum (Al) and inevitable impurities or including the aluminum (Al) and the inevitable impurities, and at a 0° direction with respect to the rolling direction, the 0.2% proof stress σ ０．２ , the tensile strength σ Ｂ , and the average value σ of the 0.2% proof stress and the tensile strength ｆｍ are used, and the evaluation value S calculated by the following formula (1) is 410 MPa or more and 450 MPa or less. An aluminum alloy sheet for an uncoated can lid. S = σ ｆｍ / (σ ０．２ / σ Ｂ )... (1) 2. The aluminum alloy sheet for an uncoated can lid according to claim 1, wherein, in the 0°, 45°, and 90° directions with respect to the rolling direction, the 0.2% proof stress σ ０．２ , the tensile strength σ Ｂ , and the average value σ of the 0.2% proof stress and the tensile strength ｆｍ are used to calculate the evaluation value S by the formula (1), and the minimum evaluation value S ｍｉｎ , which is the minimum value, is 370 MPa or more and 410 MPa or less, and the 0.2% proof stress σ ０．２＿０° in the 0° direction with respect to the rolling direction after heat treatment at 260°C for 25 seconds, minus the 0.2% proof stress σ ０．２＿９０° in the 90° direction with respect to the rolling direction after heat treatment at 260°C for 25 seconds is -20 MPa or more and -10 MPa or less, and in the L-ST cross-section at the center of the width direction after heat treatment at 260°C for 25 seconds, the ratio of the total area of Mg ２ Si particles with an area of 0.3 μm ２ or more to the total area of the L-ST cross-section is 0.2% or less. An aluminum alloy sheet for an uncoated can lid.

3. An aluminum alloy sheet for an unpainted can lid according to claim 1 or claim 2, which has been heat-treated at 260° C. for 25 seconds, and when a bending operation of bending 90° and returning to the 0° position is repeated in a direction in which the bending ridge line is parallel to the rolling direction with respect to a test piece cut out in a strip shape having a width of 12.5 mm and a length of 200 mm, the number of repeated bending times N, which is the number of times of the bending operation until the test piece breaks, is normalized by the plate thickness t of the test piece and the following formula (2) to obtain the normalized repeated bending times N ｓ is 14.0 times or more, an aluminum alloy sheet for an unpainted can lid. N ｓ = N × t / 0.235 ··· (2)

Images