WO2012043582A1 - Feuille d'alliage d'aluminium laminée à froid pour une canette - Google Patents

Feuille d'alliage d'aluminium laminée à froid pour une canette Download PDF

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WO2012043582A1
WO2012043582A1 PCT/JP2011/072116 JP2011072116W WO2012043582A1 WO 2012043582 A1 WO2012043582 A1 WO 2012043582A1 JP 2011072116 W JP2011072116 W JP 2011072116W WO 2012043582 A1 WO2012043582 A1 WO 2012043582A1
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phase
hot
mass
rolling
cold
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PCT/JP2011/072116
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English (en)
Japanese (ja)
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有賀　康博
松本　克史
淳人 鶴田
良治 正田
祐志 井上
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株式会社神戸製鋼所
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Priority to CN201180047269.XA priority Critical patent/CN103140593B/zh
Priority to KR1020137008080A priority patent/KR20130051488A/ko
Priority to AU2011309067A priority patent/AU2011309067B2/en
Publication of WO2012043582A1 publication Critical patent/WO2012043582A1/fr

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
    • C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/047—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with magnesium as the next major constituent

Definitions

  • the present invention relates to a material plate for bottle cans, and more particularly to an aluminum alloy cold-rolled plate for bottle cans.
  • the aluminum cold-rolled alloy sheet in the present invention is a rolled sheet (cold-rolled sheet) that has been rolled through hot rolling-cold rolling, and has been cold-rolled or further subjected to heat treatment. It is a tempered board.
  • the aluminum alloy is also referred to as an Al alloy.
  • a two-piece aluminum can obtained by seaming a can body and a can lid (can end) is often used.
  • the can body is made by DI processing (Drawing and Ironing) of an aluminum cold-rolled plate, trimming to a predetermined size, degreasing and washing, and painting and printing.
  • the can body is baked (baked), and the can body edge is necked and flanged.
  • DI processing Drawing and Ironing
  • JIS 3004 alloy and 3104 alloy which are Al—Mg—Mn alloys
  • JIS 3004 alloy and 3104 alloy are excellent in ironing workability, and exhibit relatively good formability even when cold rolling is performed at a high rolling rate in order to increase the strength. From these facts, these alloys are considered suitable as materials for DI can bodies.
  • a resin coating (resin coating or film laminating) is carried out on an aluminum alloy plate after a ground treatment (chromate, etc.). ). Subsequently, the aluminum alloy plate with the resin coating is punched into a circular blank and formed into a cup shape.
  • the manufacturing process of the bottle can (three-piece type described later) was slightly different from the manufacturing process of the DI can, and a thermoplastic resin coating layer (resin coating or film lamination) was formed on both surfaces of the aluminum alloy plate. Done above.
  • bottle cans are manufactured through each process of drawing ironing, top dome molding, trimming, printing and painting, screw / curl molding, and neck flange molding.
  • DI process drawing and ironing process
  • the cup-shaped molded product is redrawn and stretched or ironed to reduce the body diameter, thereby reducing the thickness of the bottomed cylindrical can. Is formed.
  • the bottom side of the bottomed cylindrical can is drawn a plurality of times to form a shoulder portion and an unopened mouth portion.
  • the printing / coating on the can body is performed after washing and trimming.
  • the curl portion and the screw portion are formed (screw / curl molding).
  • neck-in process and the flange process are performed on the part on the opposite side of the screw part (neck flange molding)
  • a bottle can is obtained by tightening a separately formed bottom lid with a seamer (Patent Document) 1).
  • the wall thickness of both bottle cans and DI cans is about 110 ⁇ m, and there is a demand for further thinning to reduce weight.
  • a low earing during ironing is also strongly required. By reducing the ear rate at the time of ironing, the yield at the time of ironing can be increased, and furthermore, the can body can be prevented from being broken due to the ear cut of the can body.
  • can blanks are respectively collected from a plurality of different positions (portions) in the plate width direction of an aluminum alloy plate as a material (original plate).
  • a plate having uniform characteristics in the plate width direction is not always obtained.
  • variations in characteristics often occur in the plate width direction. Therefore, even if the ear rate of the material plate is low on average, the size of the ear rate may vary at each position in the plate width direction. Thus, it becomes difficult to obtain a can body having a high yield.
  • Patent Document 2 proposes a technique for reducing the ear ratio of an aluminum alloy plate for a can body by sufficiently generating a texture in which the cube orientation is prioritized in hot rolling. For this reason, it is proposed in Patent Document 2 to perform a homogenization heat treatment at a high temperature of 530 to 630 ° C., and particularly the hot finish rolling conditions are defined in detail.
  • Patent Document 3 describes that ears are generated due to the crystallographic anisotropy of the rolled material. Patent Document 3 further describes a texture component (mainly 0 ° -90 ° ears) of cubic-oriented crystal grains formed by recrystallization that proceeds after hot rolling and a rolling texture formed by cold rolling. It is described that the height of the ear is determined by the balance between the component (45 ° ear). In this patent document 3, in order to realize the reduction in the ear rate that is strictly required as the can diameter is reduced, it is assumed that the soaking condition as the upper process is important in addition to the hot rolling condition, 560 to 620 A method for producing an aluminum alloy cold-rolled sheet for can bodies that has been subjected to soaking at a relatively high temperature of 0 ° C. has been proposed.
  • a texture component mainly 0 ° -90 ° ears
  • Patent Document 4 the ingot is subjected to homogenization heat treatment at a high temperature of 540 to 610 ° C. This is because if the temperature of the homogenization heat treatment is less than 540 ° C., the distribution of precipitates becomes dense and the structure becomes difficult to recrystallize after hot rolling. Moreover, in patent document 4, it is proposed that the completion
  • Patent Document 4 in order to reduce the ear rate itself by developing a proper cubic orientation during intermediate annealing in the middle of cold rolling after the hot rolling, and in a recrystallized state after hot rolling.
  • the finishing temperature of finish rolling is in the range of 330 to 360 ° C.
  • Patent Document 5 by reducing the difference in the area ratio of the Cube-oriented crystal grains in the region from the plate surface to the plate thickness center in the cross section of the aluminum alloy hot rolled plate, the ear rate is stabilized in the plate width direction. It has been proposed to obtain good materials. For this reason, Patent Document 5 provides a homogenization treatment at a high temperature of about 600 to 620 ° C. to provide Al—Mn—Fe—Si intermetallic compound phases and nucleus of Cube orientation crystal grains in a hot rolling process. The non-precipitation zone (PFZ) is distributed uniformly.
  • PFZ non-precipitation zone
  • a second homogenizing heat treatment is performed, which is once cooled and reheated to a temperature equal to or slightly higher than the hot rough rolling start temperature and held for several hours. It is recommended to perform two homogenization heat treatments called soaking twice.
  • the average solid solution amount of Mn in the hot-rolled sheet is controlled in the range of 0.12 to 0.38% by mass
  • the average solid solution amount of Cu is controlled in the range of 0.01 to 0.3% by mass, and the like. It has been proposed to do. Thereby, in patent document 6, even if it manufactures a cold rolled sheet without carrying out intermediate annealing, the ear rate when this cold rolled sheet is DI-formed is made small. According to the same literature, if the average solid solution amount of Mn and Cu increases, the Cube orientation (cube orientation) tends to develop during recrystallization, and the average ear ratio of the hot-rolled sheet tends to decrease. It is a thing.
  • the ear rate was stabilized by temporarily canceling the variation in the internal structure by the intermediate annealing.
  • the average ear rate can be stabilized without performing the above.
  • the homogenization heat treatment temperature is still relatively high at about 550 to 650 ° C., and this homogenization heat treatment is performed in a plurality of stages such as twice soaking.
  • Patent Document 7 it is proposed to perform homogenization at a high temperature of about 550 to 650 ° C., then cool and then reheat and then perform hot soaking twice.
  • the Mn average solid solution amount and crystal grain size of the hot-rolled sheet are controlled within a predetermined range, and the ear ratio of the hot-rolled sheet is stably -3 to -6%.
  • the hot rolled sheet is cold rolled without intermediate annealing so that the obtained cold rolled sheet has a stable ear ratio of 0 to 2%. Yes.
  • Patent Document 8 ⁇ 6 which is an Al 6 (Mn, Fe) phase crystallized product produced at the time of casting at a high homogenization temperature of 600 to 640 ° C. It has also been proposed to increase the area ratio of the ⁇ phase to 50% or more by transforming the phase into an ⁇ phase (Al—Mn—Fe—Si compound). In Patent Document 8, this ⁇ phase is used to prevent seizure at the time of ironing on a DI can.
  • a two-piece bottle can (“two-piece type” consisting of an integrally formed can body and cap) manufactured by coating the inner and outer surfaces of a molded aluminum plate
  • three-piece bottle cans (“three-piece type” composed of a can body, a bottom lid, and a cap) manufactured by forming a film-laminated material into a can body.
  • the present invention is a technique applied to the latter.
  • the flange of the bottom part of the bottom of the can body remaining at the time of forming the cup-shaped can body in the previous stage is left during the ironing process for further forming the drinking mouth part on the upper part of the can body formed in the cup shape. It is processed as follows. And after shaping
  • the amount of flange removed by trimming can be reduced.
  • the yield of materials can be improved.
  • in order to reduce the thickness of the bottle can for weight reduction not only the improvement of the characteristics to suppress the variation of the ear rate in the plate width direction but also the production cost of the material plate is reduced. It is also necessary to reduce it.
  • the above-mentioned conventional technology cannot respond to the required issues of reducing the manufacturing cost and improving the ear rate.
  • it has also been proposed to cold-roll a hot-rolled sheet without intermediate annealing.
  • the temperature at which the homogenization heat treatment is performed remains the same as the high temperature, and the earring rate of the can material cold-rolled plate is reduced, such as the homogenization heat treatment being performed twice. This has not led to a full-scale reduction in manufacturing cost while suppressing variations in the plate width direction.
  • the present invention has been made in view of such problems, and aims to reduce the manufacturing cost of an aluminum alloy cold-rolled sheet, which is a material of a bottle can, and to suppress variations in the edge ratio in the sheet width direction.
  • the gist of the aluminum alloy cold-rolled sheet for bottle cans of the present invention is as follows. (1) Mn: 0.3 to 1.2% by mass, Mg: 1.0 to 3.0% by mass, Fe: 0.3 to 0.7% by mass, Si: 0.1 to 0.5% by mass An aluminum alloy for a bottle can having a composition in which the mass composition ratio of Fe and Mn (Fe / Mn) is in the range of 0.45 to 1.5, and the balance is composed of Al and inevitable impurities.
  • a plate In the structure of the aluminum alloy cold-rolled sheet for bottle cans, the average number density of dispersed particles having a gravity center diameter of less than 1 ⁇ m that can be measured with a transmission electron microscope at a magnification of 20000 is less than 3 / mm 2 , A ⁇ phase that is an Al 6 (Fe, Mn) intermetallic compound, and an ⁇ phase that is an Al—Fe—Mn—Si intermetallic compound,
  • the maximum height H ⁇ of the X-ray diffraction peak in the range of 2 ⁇ 20.5 to 21.5 °, which can be regarded as the diffraction peak of the ⁇ phase, measured by the X-ray diffraction analyzer, and the diffraction peak of the ⁇ phase
  • the ratio (H ⁇ / H ⁇ ) of the maximum height H ⁇ of the X-ray diffraction peak in the range of 2 ⁇ 25.5 to 26.5 °, which can be regarded as 2 ⁇ , is 0.50 or more
  • Aluminum alloy cold-rolled sheet for bottle cans (2) One or more selected from Cu: 0.05 to 0.5% by mass, Cr: 0.001 to 0.3% by mass, Zn: 0.05 to 0.5% by mass (1) ) Aluminum alloy cold-rolled sheet for bottle cans. (3) Aluminum for bottle can according to (1) or (2), further containing Ti: 0.005 to 0.2% by mass alone or in combination with B: 0.0001 to 0.05% by mass Alloy cold rolled sheet.
  • the dispersed particles ( ⁇ phase, ⁇ phase) of the ingot structure after soaking and before hot rolling is about.
  • These dispersed particles depend on the production conditions, but within the production conditions of the present invention, even after hot rolling or cold rolling, the state of the ingot structure after soaking is maintained as it is, There is almost no change even with rolled or cold rolled sheets. Therefore, in the present invention, the ingot structure after soaking and before hot rolling is not an intermediate product such as an ingot or hot-rolled plate that is difficult to analyze, but is a cold-rolled material that is the final bottle can material that is easy to analyze. It defines the board.
  • the present invention is the same as the conventional one in that it guarantees uniform recrystallization in the sheet width direction of the hot-rolled sheet structure in order to suppress variation in the edge ratio in the sheet width direction.
  • the soaking temperature is set as low as possible. That is, the present invention is characteristic in that a certain amount of coarse dispersed particles that promote recrystallization are present in the ingot structure after soaking and before hot rolling.
  • the cause of variation in the edge width ratio of the ear ratio is variation in the progress of recrystallization after the hot rolling (hot rolling) of the can material plate is completed.
  • recrystallization proceeds on the end side in the plate width direction of the can raw material plate (hot rolled plate) with a relatively high strain introduced, whereas the strain introduced is low. Recrystallization is less likely to occur at the center in the plate width direction of the can material plate (hot rolled plate), particularly at the center of the plate thickness. This phenomenon influences after the subsequent cold rolling, resulting in a large variation as the ear of the final plate (molded can).
  • the dispersed particle state of the ingot after the homogenization heat treatment (soaking) and before hot rolling is controlled.
  • the proportion of the ⁇ phase which is a relatively coarse Al 6 (Fe, Mn) intermetallic compound that promotes recrystallization, is increased, and a relatively fine Al—Fe—Mn—Si that inhibits recrystallization.
  • Reduce the abundance ratio of ⁇ -phase which is an intermetallic compound.
  • the ⁇ phase is increased, and the center portion in the plate width direction of the above-described can material plate (hot rolled plate), in particular, the central portion of the plate thickness is restored. Crystallization is promoted, the recrystallization rate in the plate width direction of the hot-rolled plate is made uniform, and as a result, the variation in the ear rate of the final plate in the plate width direction is reduced. At the same time, the fine ⁇ -phase is restricted, but the relatively coarse ⁇ -phase should not be too small.
  • the soaking temperature is as low as possible below 550 ° C., and the hot rolling (particularly rough rolling) conditions are adjusted.
  • the existence ratio of the fine ⁇ phase that inhibits recrystallization is increased while the existence ratio of the ⁇ phase that promotes recrystallization is increased by devising the manufacturing process of the hot-rolled sheet in particular. Control to reduce.
  • Patent Document 4 is directed to a structure that is easily recrystallized, and despite the attempt to prevent a structure that is difficult to recrystallize with a dense distribution of precipitates, it is 540 to 610 ° C. with respect to the ingot. Homogenized heat treatment is performed at high temperature.
  • the homogenization treatment temperature is set to a high temperature of 600 to 640 ° C., and the ⁇ phase generated during casting is positively transformed into the ⁇ phase so that a large amount of the ⁇ phase is present.
  • the amount of dissolved Mn is also increasing, and a structure that is difficult to recrystallize is obtained.
  • the manufacturing cost of the material plate is reduced by omitting the process such as performing the homogenization heat treatment only once and lowering the soaking temperature, and the ear rate of the can material plate itself. It is impossible to achieve both reduction and suppression of variation in the width direction of the ear rate. As a result, the conventional manufacturing method cannot reduce the amount (trimming amount) of the flange of the bottom portion of the bottom of the can body remaining in the can body molding of the three-piece type can among the bottle cans.
  • the process is omitted such as performing the homogenization heat treatment only once, and the soaking temperature is lowered to reduce the manufacturing cost of the material plate.
  • the rate itself can be reduced, and variations in the ear rate in the plate width direction can be suppressed. As a result, it is possible to reduce the amount of trimming when molding a three-piece type can body among bottle cans.
  • Al alloy cold-rolled sheet composition First, the chemical component composition of the aluminum alloy cold-rolled sheet (ingot) according to the present invention will be described below, including reasons for limiting each element.
  • the chemical component composition of the aluminum alloy cold-rolled sheet in the present invention satisfies the necessary characteristics such as formability and strength to the above-mentioned can as a material for a bottle can, and the structure specified by the present invention has a chemical component composition. It is necessary to satisfy from the point of. For this reason, the aluminum alloy cold-rolled sheet according to the present invention has Mn: 0.3 to 1.2% by mass, Mg: 1.0 to 3.0% by mass, Fe: 0.3 to 0.7% by mass, Si: 0.1 to 0.5% by mass, the mass composition ratio of Fe and Mn (Fe / Mn) is in the range of 0.45 to 1.5, and the balance is from Al and inevitable impurities. It has the composition which becomes.
  • the aluminum alloy cold rolled sheet according to the present invention has Cu: 0.05 to 0.5 mass%, Cr: 0.001 to 0.3 mass%, Zn: 0.05 to 0.5 mass%.
  • One or more selected from mass% and / or 0.005 to 0.2 mass% Ti alone or in combination with 0.0001 to 0.05 mass% B may be further contained. good. The significance of the definition of each element will be described below in order.
  • Mn is an effective element that contributes to improvement in strength and further contributes to improvement in formability.
  • Mn is extremely important because ironing is performed during DI molding.
  • Mn forms various Mn-based intermetallic compounds such as a coarse ⁇ phase.
  • the coarse compound contributes to the promotion of recrystallization of the hot-rolled sheet and is also effective for increasing the strength of the product sheet. If the Mn content is too small, the above effect cannot be exhibited. For this reason, content of Mn is 0.3 mass% or more, Preferably it is 0.4 mass% or more.
  • the upper limit of the Mn content is 1.2% by mass, preferably 1.1% by mass, and more preferably 1.0% by mass.
  • Mg 1.0-3.0% by mass
  • Mg is effective in that the strength can be improved by solid solution strengthening alone.
  • the Mg content is low, the amount of MgSi compound generated decreases and Si remains excessively, so that the amount of Al—Fe—Mn—Si intermetallic compound ( ⁇ phase) increases.
  • the Mg content for this purpose is 1.0% by mass or more, preferably 1.2% by mass or more.
  • the upper limit of the amount of Mg is 3.0% by mass, preferably 2.5% by mass.
  • Fe has the effect of refining crystal grains, and further increases the amount of coarse ⁇ phase formed, contributing to the promotion of recrystallization of hot-rolled sheets. Fe is also useful in that it promotes crystallization and precipitation of Mn, and controls the Mn average solid solution amount in the aluminum matrix and the dispersion state of the Mn-based intermetallic compound. For this reason, content of Fe is 0.3 mass% or more, Preferably it is 0.4 mass% or more. On the other hand, when the Fe content is excessive, a huge primary intermetallic compound having a diameter exceeding 15 ⁇ m is likely to be generated, and the moldability is lowered. Therefore, the upper limit of the Fe content is 0.7% by mass, preferably 0.6% by mass.
  • the mass composition ratio of Fe and Mn (Fe / Mn) is set to 0.45 to 1.5, preferably 0.6 to 1.4.
  • this ratio is smaller than 0.45, the content of Fe with respect to Mn is too small, so the amount of ⁇ -phase generated is reduced, and the number density of particles ( ⁇ -phase) having a diameter of less than 1 ⁇ m is increased.
  • this ratio exceeds 1.5, the amount of ⁇ -phase produced becomes too small, and the ironing processability is lowered.
  • Si forms an Al—Fe—Mn—Si intermetallic compound ( ⁇ phase).
  • ⁇ phase is appropriately distributed, the moldability is improved.
  • content of Si is 0.1 mass% or more, Preferably it is 0.2 mass% or more.
  • the upper limit of Si content is 0.5 mass%, Preferably it is 0.4 mass%.
  • Cu 0.05 to 0.5% by mass
  • the lower limit in the case of selectively containing Cu is 0.05% by mass or more, preferably 0.1% by mass or more.
  • the upper limit of Cu content is 0.5 mass%, preferably 0.4 mass%.
  • Cr 0.001 to 0.3% by mass
  • the amount of Cr is, for example, 0.001% by mass or more, preferably 0.002% by mass or more.
  • the upper limit of the Cr amount is, for example, about 0.3% by mass, preferably about 0.25% by mass.
  • Zn 0.05 to 0.5% by mass
  • Zn is also an element effective for improving the strength.
  • the amount of Zn is 0.05% by mass or more, preferably 0.06% by mass or more.
  • the upper limit of the Zn content is about 0.5% by mass, preferably about 0.45% by mass.
  • Ti 0.005 to 0.2% by mass
  • Ti is a grain refinement element. Therefore, Ti is preferably selectively contained when it is desired to exert the effect of crystal grain refinement.
  • the Ti content is 0.005% by mass or more, preferably 0.01% by mass or more.
  • the upper limit of the Ti content is 0.2% by mass, preferably 0.1% by mass.
  • Ti may be contained alone, but may be contained together with a small amount of B.
  • B When B is used in combination, the effect of crystal grain refinement is further improved. For this reason, the content of B when selectively contained is 0.0001% by mass or more, preferably 0.0005% by mass or more.
  • the upper limit of the B content is 0.05% by mass, preferably 0.01% by mass.
  • inevitable impurities are basically preferably low, but there is also a balance with refining costs for reducing impurities in the aluminum alloy melting step. Therefore, the inclusion of inevitable impurities up to the upper limit value of each element of the 3000 series aluminum alloy described in the JIS standard or the like is allowed within a range that does not impair the plate characteristics.
  • the cold rolled sheet structure of the present invention in addition to the component composition, in order to ensure uniform recrystallization in the sheet width direction of the hot-rolled sheet structure, the main elements (Mn, Fe, Cu) of the ingot after soaking and before hot-rolling are used. ) And the amount of ⁇ phase, which is coarse dispersed particles that promote recrystallization of the structure, are guaranteed in relation to the ⁇ phase to be regulated.
  • the structure of the ingot after soaking and before hot rolling As described above, in the present invention, these are defined in the state of cold-rolled sheets.
  • the ⁇ phase which is an intermetallic compound composed of Al 6 (Fe, Mn) as defined in the present invention, is a coarse crystallized product produced during casting, and the second phase during hot rolling. It becomes a recrystallization nucleation site as dispersed particles and promotes recrystallization of the hot-rolled sheet structure.
  • the ⁇ phase which is an intermetallic compound composed of Al—FeMn—Si, has two types, one that transforms from the ⁇ phase during the soaking (coarse) and one that newly nucleates and precipitates (fine). is there.
  • the soaking temperature under the optimum production conditions of the present invention is low (less than 550 ° C.)
  • the ⁇ phase in the structure after soaking (cold rolled sheet) in the present invention is transformed from the ⁇ phase during soaking. It is thought that there are few, and many are fine particles that are newly nucleated and precipitated during soaking.
  • the ⁇ phase is a coarse crystallized product, and there is no fine one having a center of gravity diameter of less than 1 ⁇ m. Therefore, when the cold-rolled sheet structure in the present invention is observed with a transmission electron microscope, the observed particles having a center-of-gravity diameter of less than 1 ⁇ m are considered to be ⁇ phases that are newly nucleated and precipitated during soaking. It is done.
  • this average number density is defined as less than 3 / mm 2 in order to regulate fine dispersed particles having a large effect of inhibiting recrystallization of hot-rolled sheets and having a center of gravity diameter of less than 1 ⁇ m.
  • Most of the fine dispersed particles having a diameter of the center of gravity of less than 1 ⁇ m are ⁇ phases newly nucleated and precipitated during soaking or hot rolling. The phase is substantially defined.
  • the recrystallization rate in the plate width direction of the plate is made uniform, and as a result, variation in the ear rate of the final plate in the plate width direction is reduced. If this average number density is 3 pieces / mm 2 or more, particularly fine ⁇ phase is increased, recrystallization of the hot-rolled sheet is hindered, and variation in the edge width ratio of the final sheet cannot be reduced. .
  • the number of fine dispersed particles having a center-of-gravity diameter (size) of less than 1 ⁇ m is specified.
  • the transmission-type electron microscope hereinafter referred to as “Transmission Electron Microscope”
  • TEM transmission Electron Microscope
  • the range may include finely dispersed particles that cannot be observed or measured.
  • the lower limit of the center-of-gravity diameter (size) of the dispersed particles that can be objectively measured with good reproducibility using a TEM with a magnification of 20000 times is about 30 nm.
  • the atomic diffusion rate is large and the growth rate of the dispersed particles is large. Therefore, fine particles of 30 nm or less at the time of recrystallization in hot rolling. Is very unlikely to be dispersed. Therefore, in the present invention, actually, fine dispersed particles having a centroid diameter of 30 nm or more and less than 1 ⁇ m are measured and defined.
  • the average number density of dispersed particles is usually defined per mm 3 considering the volume of the thin film sample.
  • the average number density of dispersed particles is defined per mm 2 .
  • the reason for this is that while the TEM observation sample is a thin film having a thickness of about 100 ⁇ m, the dispersed particles (precipitates) targeted by the present invention observed in the TEM image are three-dimensionally formed on the entire thin film. Due to being dispersed. For this reason, even if a plurality of particles are dispersed in a state of being overlapped in the thickness direction of the thin film, only a single particle is seen (not observed) in the TEM image, and thus the number of particles that are three-dimensionally accurate is counted.
  • the thickness of the thin film is not necessarily completely the same over the observation visual field. Therefore, in the present invention, for the sake of convenience, the number of dispersed particles per mm 2 is calculated, and this number is defined as the number density of dispersed particles.
  • the center-of-gravity diameter is the equivalent circle diameter (equivalent circle diameter) when the maximum length of the irregularly dispersed particles is regarded as the diameter of the circle.
  • Japanese Patent Application Laid-Open No. 2009-191293 JP2009-215643, JP2009-228111, JP2009-242904, JP2008-266684, JP2007-126706 As disclosed in Japanese Laid-Open Patent Publication No. 2006-104561, Japanese Laid-Open Patent Publication No. 2005-240113, and the like, it is widely used as a definition of the size of dispersed particles and the like in the field of aluminum alloys.
  • the average number density of dispersed particles having a centroid diameter of less than 1 ⁇ m is measured by observing the cold-rolled plate structure with a transmission electron microscope. More specifically, the specimen at the center of the plate thickness and the upper surface of the rolling surface is mirror-polished, and the structure of the polished surface is observed with 10 fields of view with a transmission electron microscope of 20000 times, and the average number density per 1 ⁇ m 2 is calculated. did. At this time, the number of particles observed in a range of 8 ⁇ m ⁇ 8 ⁇ m was measured, and the number of particles per 1 ⁇ m 2 was calculated. Further, since the film thickness greatly affects the average number density, the film thickness at the time of TEM observation is constant at 100 nm, and the film thickness error is within an allowable range of ⁇ 20 nm.
  • the amount of ⁇ phase is increased to promote recrystallization of the hot rolled sheet.
  • the ⁇ phase that is generated by transformation from the ⁇ phase during soaking is also the ⁇ phase. Regulate in relation to That is, the amount of ⁇ phase is ensured by controlling the balance of the existence ratio of these ⁇ phase and ⁇ phase and relatively increasing the ⁇ phase.
  • the ⁇ phase transformed from the ⁇ phase is as coarse as the ⁇ phase, it is a dispersed particle having a centroid diameter of less than 1 ⁇ m, which is subject to the regulation, and is newly nucleated and precipitated during soaking. It is not included in the ⁇ phase.
  • the bottle can is slightly different from the manufacturing process of the DI can.
  • the bottle can is formed after forming a thermoplastic resin coating layer (resin coating or film lamination) on both sides of an aluminum alloy plate (cold rolled plate). Is done. For this reason, the moldability to the can is greatly improved by the role of the thermoplastic resin coating layer as a lubricant during molding.
  • the present invention minimizes the deterioration of the can moldability of the material plate by minimizing the relatively coarse ⁇ phase. is doing. That is, the prescription of the existence ratio of the ⁇ phase and the ⁇ phase according to the present invention is not to restrict only the ⁇ phase side or only the ⁇ phase side, but to suppress an excessive decrease of the ⁇ phase and By controlling the balance of the abundance ratio with the ⁇ phase, the can moldability is prevented from being lowered and the moldability of the can when the thermoplastic resin coating layer is formed before molding is ensured.
  • the diffraction peak intensity measured by the X-ray diffraction analyzer is used to define the abundance ratio (balance control) of these ⁇ phase and ⁇ phase.
  • Identification (qualification and quantification) of the type and amount of the compound (intermetallic compound, etc.) as the second phase particles in the metal matrix (structure) based on the position and height of the X-ray diffraction peak measured by X-ray diffraction analysis Possible). Therefore, the method using the diffraction peak intensity in the present invention is optimal for discrimination (distinguishment) and quantification of the ⁇ phase and the ⁇ phase as the second phase particles in the present invention, that is, for defining the existence ratio.
  • FIG. 1 shows the distribution of diffraction peaks of X-ray diffraction lines measured by an X-ray diffraction analyzer for the cold-rolled sheet of the present invention (Invention Example 7 in Table 2 in Examples described later).
  • the ⁇ phase as the second phase particle in the aluminum alloy structure by the position (horizontal axis position) of the diffraction peak shown in FIG. 1 and the height H (intensity (unit: CPS)) of the diffraction peak shown on the vertical axis.
  • the abundance ratio of the ⁇ phase can be identified.
  • the diffraction peak distribution is shown in the range where the measurement range 2 ⁇ on the horizontal axis is 10 ° to 100 °.
  • the diffraction peaks of the crystallized product and Al are shown as thin bar lines (bar graphs) for each position on the horizontal axis in order from the top. ing.
  • the crystallized substances on the right side are listed in order from the top, ⁇ phase (described as ( ⁇ -Al 12 (Fe, Mn) 3 Si)), ⁇ phase (Al 6 (Fe, Mn)).
  • an intermetallic compound denoteted as: Mg 2 Si
  • the bottommost is Al described as a base material component at the right end.
  • FIG. 1 it can be seen from the comparative comparison between the diffraction peak distribution and the bar graph that the large intensity peaks with 2 ⁇ of 45 ° or more are all Al of the base material component (matrix).
  • the ⁇ phase and the ⁇ phase can be seen from the comparative comparison of each diffraction peak distribution and each bar graph that the peaks overlap with each other at almost the horizontal axis position.
  • each X-ray diffraction peak (X-ray diffraction peak having the maximum height within the range) specified within the range indicated by the horizontal axis position described above defines the abundance of the ⁇ phase and the ⁇ phase, respectively.
  • the maximum height H ⁇ of the X-ray diffraction peak in the range of 2 ⁇ 20.5 to 21.5 °, which can be regarded as the diffraction peak of ⁇ phase, and the diffraction peak of the ⁇ phase can be regarded.
  • the maximum height H ⁇ of the X-ray diffraction peak in the range of 2 ⁇ 25.5 to 26.5 ° is used, and the ratio of ⁇ phase and ⁇ phase is defined by these ratios (H ⁇ / H ⁇ ). . This ensures the abundance of the ⁇ phase and ensures uniform recrystallization of the hot rolled sheet.
  • the lower limit of the X-ray diffraction peak height ratio H ⁇ / H ⁇ is 0.50 or more.
  • this ratio is less than 0.50, the ⁇ phase is too small, and the recrystallization suppression effect by the ⁇ phase is too large compared to the recrystallization promotion effect by the ⁇ phase. For this reason, it becomes impossible to guarantee uniform recrystallization in the plate width direction of the hot-rolled plate structure in order to suppress variations in the ear rate in the plate width direction.
  • too much ⁇ phase (too little ⁇ phase) is due not only to soaking conditions, but also to the time to start hot rough rolling and the steady speed in hot rough rolling, as will be described later. This is also due to manufacturing conditions.
  • the upper limit of the X-ray diffraction peak height ratio (H ⁇ / H ⁇ ) is 1.8 in order to allow the presence of a certain ⁇ phase so that there is no reduction in can moldability until such a problem occurs.
  • the ⁇ phase there is an advantage that a decrease in can moldability due to the ⁇ phase can be minimized.
  • the ⁇ phase is excessive, such as when the X-ray diffraction peak height ratio (H ⁇ / H ⁇ ) exceeds the above upper limit, the can moldability is improved, while the ear ratio, which is the main object of the present invention. It itself goes down.
  • the definition based on the X-ray diffraction peak height ratio (H ⁇ / H ⁇ ) of the present invention that is, the definition of the abundance ratio of the ⁇ phase and the ⁇ phase of the present invention is not limited only to the ⁇ phase side. It is also meaningful to ensure can moldability by controlling the balance of the proportion of ⁇ phase and ⁇ phase while suppressing the decrease of ⁇ phase.
  • the method of identifying and defining the ⁇ phase and ⁇ phase as the second phase particles in the aluminum alloy structure with such X-ray diffraction peak height or height ratio by X-ray diffraction is as follows.
  • Japanese Unexamined Patent Publication No. 2010-116594 the proportion of ⁇ -phase crystallized material existing in an Al-Mg-Si-based Al-Mg-Si-based AA or JIS 6000-based aluminum alloy plate is increased, and the entire existing crystallized material is refined. And spheroidizing to improve bending workability (hem workability) under severe conditions for automobile panels.
  • the X-ray diffraction peak measurement method The X-ray diffractometer used to measure the X-ray diffraction peak height, H ⁇ and H ⁇ is, for example, a Rigaku Electric X-ray diffractometer (model: RAD-RU300), using a Co target, Measurement is performed at a voltage of 40 kV, a tube current of 200 mA, a scanning speed of 1 ° / min, a sampling width of 0.02 °, and a measurement range (2 ⁇ ) of 10 ° to 100 °.
  • a Rigaku Electric X-ray diffractometer model: RAD-RU300
  • Measurement is performed at a voltage of 40 kV, a tube current of 200 mA, a scanning speed of 1 ° / min, a sampling width of 0.02 °, and a measurement range (2 ⁇ ) of 10 ° to 100 °.
  • the maximum X-ray diffraction peak height H ⁇ (in the vicinity of 26 °) within the range of 25.5 to 26.5 ° is obtained.
  • Each of these maximum peak heights is determined by subtracting the background from the X-ray diffraction profile.
  • an aluminum alloy cold-rolled sheet which is a material for a bottle can in the present invention, it can be manufactured without greatly changing the conventional soaking, hot-rolling, and cold-rolling manufacturing processes, and the manufacturing cost is reduced. In addition, it is possible to suppress the variation of the ear rate in the plate width direction.
  • the aluminum alloy ingot having the above composition is subjected to homogenization heat treatment only once at a temperature of 450 ° C. or more and less than 550 ° C., and then the hot rough rolling is quickly started. And hot rough rolling is completed rapidly.
  • Soaking conditions In order to reduce the manufacturing cost, the soaking process is performed only once.
  • the soaking temperature at this time is in a relatively low temperature range of 450 ° C. or higher and lower than 550 ° C., preferably 460 ° C. or higher and lower than 530 ° C.
  • the presence state of the ⁇ phase of the ingot after the homogenization heat treatment (soaking) and before hot rolling is controlled in order to reduce the variation in the edge ratio of the final plate in the plate width direction. To do.
  • this ⁇ phase is maintained in a relatively coarse state without undergoing ⁇ transformation.
  • the temperature of the soaking is set as low as possible at a temperature lower than 550 ° C., so that the crystallized ⁇ phase is not so dissolved, and the ⁇ -phase transformation is suppressed.
  • This also reduces the amount of solid solution Fe and solid solution Mn, and positively increases the amount of ⁇ phase, which is a relatively coarse dispersed particle having a diameter of 2 to 15 ⁇ m, which serves as a nucleation site for recrystallization of the hot-rolled sheet. Increase.
  • the soaking process at a relatively high temperature of 520 ° C. or higher since the soaking process at a relatively high temperature of 520 ° C. or higher is performed, the soaking temperature is too high, the crystallized product is dissolved, or the ⁇ phase is transformed into ⁇ . Therefore, the relatively coarse dispersed particles that promote the recrystallization of the hot-rolled sheet as defined by the present invention are insufficient. Moreover, in the said prior art, the amount of solid solution Fe and the amount of solid solution Mn increase, and it becomes a structure
  • the soaking time is preferably as short as possible so that the ingot can be homogenized, for example, 12 hours or less, preferably 6 hours or less.
  • Hot rolling conditions The hot rolling is a rough rolling step of the ingot (slab) after the soaking performed according to the thickness of the rolled sheet, and a thickness of about 40 mm or less after the rough rolling is about 4 mm or less. And a finish rolling step of rolling to a maximum.
  • a reverse type or a tandem type rolling mill is used as appropriate, and rolling consisting of a plurality of passes is performed.
  • Hot rough rolling In the present invention, after the soaking process is completed, the soaking process is not performed twice or two steps so as to be cooled and reheated once, but the soaking process is performed only once. Therefore, in the present invention, hot rough rolling is started at a soaking temperature in a temperature range of 450 ° C. or higher and lower than 550 ° C. When this rough rolling start temperature is too lower than 450 ° C., recrystallization of the hot rolled sheet is suppressed. On the other hand, the upper limit of the rough rolling start temperature is determined by the soaking temperature (upper limit 550 ° C.). If hot rolling is started from a temperature of 550 ° C. or higher, seizure of the plate and the work roll occurs during hot rolling, and surface defects of the plate are likely to occur.
  • This hot rough rolling is performed promptly (without time delay) immediately after the soaking.
  • generation of particles ( ⁇ phase) having a diameter of less than 1 ⁇ m from the end of soaking to the start of hot rough rolling can be suppressed.
  • hot rough rolling is started within 15 minutes, preferably within 10 minutes, on the aluminum alloy sheet after the soaking.
  • the lowest steady speed is set to 50 m / min or more among all the steady speeds of a pass of several to several tens of times in the case of a reverse rolling mill.
  • the steady speed means a rolling speed (line speed) that is maximum and constant per pass. If the steady speed at which all the passes in hot rough rolling are the lowest is less than 50 m / min, the rolling time becomes longer, the amount of ⁇ -phase is increased, and the hot-rolled sheet is recrystallized. It is suppressed.
  • the end temperature of hot rough rolling is preferably 400 ° C. or higher.
  • hot rolling is divided into rough rolling and finish rolling, and these are carried out continuously, so if the end temperature of hot rough rolling becomes too low, in the hot finish rolling of the next step The rolling temperature is lowered and edge cracking is likely to occur.
  • the end temperature of hot rough rolling is too low, the self-heating necessary for recrystallization after finish rolling tends to be insufficient, so it becomes unnecessary to recrystallize the hot-rolled sheet, and recrystallization in the sheet width direction. The uniformity of is impaired.
  • Hot finish rolling For the aluminum alloy sheet that has been subjected to hot rough rolling, hot finish rolling is performed, for example, continuously and quickly (immediately without any time delay). By rapid hot finish rolling, it is possible to prevent the strain accumulated in the hot rough rolling from recovering, and the strength of the cold-rolled sheet obtained thereafter can be increased. As a measure of this point, it is preferable to hot finish and roll the aluminum alloy sheet after the hot rough rolling within 5 minutes, preferably within 3 minutes.
  • the finishing temperature of hot finish rolling is preferably 300 to 360 ° C.
  • the hot finish rolling step is a step of finishing the plate to a predetermined size. Since the structure after the end of rolling becomes a recrystallized structure due to self-heating, the end temperature affects the recrystallized structure. If the finish temperature of hot finish rolling is 300 ° C. or higher, the structure of the final plate can be easily made into a uniform recrystallized structure in the plate width direction together with the subsequent cold rolling conditions. When the finish temperature of hot finish rolling is less than 300 ° C., it is difficult to obtain the structure of the present invention.
  • the finish temperature of hot finish rolling exceeds 360 ° C., a coarse MgSi compound or the like precipitates to hinder formability, and further, the crystal grains become coarse and the plate surface becomes rough. Therefore, the lower limit of the finish temperature of hot finish rolling is 300 ° C. or higher, preferably 310 ° C. or higher. Moreover, the upper limit of the finish temperature of hot finish rolling is 360 ° C. or lower, preferably 350 ° C. or lower.
  • the hot finish rolling mill it is preferable to use a tandem hot rolling mill having three or more stands.
  • the number of stands is 3 or more, the rolling rate per stand can be reduced, and strain can be accumulated while maintaining the surface properties of the hot-rolled sheet. For this reason, the intensity
  • the thickness of the alloy plate after hot (finish) rolling is desirably about 1.8 to 3 mm. If the plate thickness after the end of hot (finish) rolling is 1.8 mm or more, the surface properties (seizure, rough surface, etc.) of the hot-rolled plate and deterioration of the plate thickness profile can be prevented.
  • the rolling rate when manufacturing a cold rolled sheet becomes too high. Can be prevented, and the ear rate after DI molding can be suppressed.
  • Cold rolling In the cold rolling process, it is desirable that rolling is performed directly by a plurality of passes without intermediate annealing, and the total rolling ratio is 77 to 90%.
  • the plate thickness after cold rolling is about 0.28 to 0.35 mm in terms of forming into a bottle can.
  • a tempering treatment such as finish annealing (final annealing) at a temperature lower than the recrystallization temperature may be performed as necessary.
  • finish annealing final annealing
  • cold rolling by the tandem rolling mill described above can generate subgrains at a lower temperature and continuously, so that such finish annealing is basically unnecessary.
  • the ingot having such a component composition was subjected to soaking and hot rolling according to the conditions shown in Table 2.
  • the soaking process was performed only once, and each treatment temperature shown in Table 2 was held for 4 hours in common with each ingot of each example.
  • hot rolling was performed.
  • a reverse hot rough rolling mill with one stand was used for hot rough rolling, and a tandem hot rolling mill with four stands was used for hot finish rolling.
  • the start temperature of hot rough rolling the time from the end of soaking to the start of hot rough rolling, the lowest steady time in all passes of hot rough rolling (the lowest in all passes) Steady time), hot rough rolling finish temperature (approximately equal to hot finish rolling start temperature), hot finish rolling finish temperature, and the like were variously changed. In this way, an aluminum alloy hot-rolled sheet having a thickness of 2.5 mm in common after hot finish rolling was obtained.
  • the rolling reduction was changed according to the plate thickness.
  • the reduction is relatively light.
  • the number of passes is 4 in each example.
  • the obtained hot-rolled sheet was cold-rolled (directly-rolled) with only one pass through a two-stage tandem rolling mill without intermediate annealing.
  • a plate material for a bottle can body (cold rolled plate) having a final plate thickness of 0.3 mm is manufactured.
  • the test piece mentioned later was extract
  • collected from the cold rolled sheet (coil) for bottle can bodies after cold rolling. And the mechanical characteristic of the test piece was measured with the above-mentioned measuring method. Further, in the measurement method described above, the average number density (particles / mm 2 ) of dispersed particles having a centroid diameter of less than 1 ⁇ m as the structure of the test piece, and 2 ⁇ 20.5 to 21 which can be regarded as a ⁇ -phase diffraction peak.
  • the tensile test for measuring the mechanical properties is performed according to JIS Z 2201, and the test piece shape is a JIS No. 5 test piece, and the longitudinal direction of the test piece coincides with the rolling direction.
  • a test piece was prepared as described above.
  • the crosshead speed was 5 mm / min, and a tensile test was performed at a constant speed until the test piece broke.
  • the average ear rate is in the range of 0% to + 3.5%.
  • the calculation of the average ear rate was performed by a known method disclosed in the prior art based on the developed view of the cup obtained by DI molding a plate material for a bottle can body. That is, the height of the ears (T1, T2, T3, T4; referred to as minus ears) measured in the directions of 0 °, 90 °, 180 °, and 270 ° is measured with the rolling direction of the development view of the cup as 0 °. In addition, the heights of the ears (Y1, Y2, Y3, Y4; referred to as plus ears) occurring in the 45 °, 135 °, 225 °, and 315 ° directions are measured.
  • the heights Y1 to Y4 and T1 to T4 are heights from the bottom of the cup. Then, the average ear rate is calculated from each measured value based on the following equation.
  • Average Ear Ratio (%) [ ⁇ (Y1 + Y2 + Y3 + Y4) ⁇ (T1 + T2 + T3 + T4) ⁇ / ⁇ 1/2 ⁇ (Y1 + Y2 + Y3 + Y4 + T1 + T2 + T3 + T4) ⁇ ] ⁇ 100
  • Invention Examples 1 to 12 in Table 2 have the composition of the present invention (Alloy Nos. 1 to 10 in Table 1), and are TEMs having a magnification of 20000 times in the cold rolled sheet structure of Invention Examples 1 to 12.
  • the average number density of dispersed particles having a center of gravity diameter of less than 1 ⁇ m, which can be measured at 1 is less than 3 particles / mm 2 , and the ratio of the maximum height H ⁇ of the X-ray diffraction peaks of the ⁇ phase and the ⁇ phase ( (H ⁇ / H ⁇ ) is 0.50 or more.
  • the average ear rate itself is low even in a low-cost production method of only one time and low-temperature soaking and no intermediate annealing.
  • the variation in the ear rate in the width direction is small.
  • Comparative Examples 13 to 17 and 21 in Table 2 are manufactured under preferable manufacturing conditions as in the invention examples.
  • the aluminum alloy composition alloy Nos. 11 to 16 in Table 1
  • the structure deviates from the definition of the present invention.
  • the average ear rate itself is high and the variation in the ear rate in the plate width direction is also large.
  • the alloy no. 11 since the amount of Si is too large, the average number density of dispersed particles having a centroid diameter of less than 1 ⁇ m is too large, and the ratio between the maximum height H ⁇ of the X-ray diffraction peaks of the ⁇ phase and the ⁇ phase ( H ⁇ / H ⁇ ) is too low.
  • alloy no. As shown in FIG. 12, the amount of Fe is too small, and the mass composition ratio (Fe / Mn) between Fe and Mn is too low. For this reason, the ratio (H ⁇ / H ⁇ ) of the maximum height H ⁇ of the X-ray diffraction peak between the ⁇ phase and the ⁇ phase is too low.
  • alloy no As shown in FIG.
  • both the Fe amount and the Mn amount are too large. For this reason, the average number density of dispersed particles having a centroid diameter of less than 1 ⁇ m is too large, and the ratio (H ⁇ / H ⁇ ) of the maximum height H ⁇ of the X-ray diffraction peak between the ⁇ phase and the ⁇ phase is too low.
  • alloy no As shown in FIG. 14, the individual Fe and Mn amounts are within the scope of the present invention, but the mass composition ratio (Fe / Mn) between Fe and Mn is too low.
  • alloy no As shown in FIG. 15, the amount of Mg is too small. For this reason, the average number density of dispersed particles having a centroid diameter of less than 1 ⁇ m is too large, and the ratio (H ⁇ / H ⁇ ) of the maximum height H ⁇ of the X-ray diffraction peak between the ⁇ phase and the ⁇ phase is too low.
  • alloy no As shown in FIG. 15, the amount of Mg is too small. For this reason, the average number density of dispersed particles having a centroid diameter of less than 1 ⁇ m is too large, and the ratio (H ⁇ / H ⁇ ) of the maximum height H ⁇ of the X-ray diffraction peak between the ⁇ phase and the ⁇ phase is too low.
  • alloy no As shown in FIG.
  • the mass composition ratio (Fe / Mn) of Fe and Mn is too low, and only this condition deviates from the composition of the present invention. Nevertheless, since the Fe content with respect to Mn is too small, as described above, the amount of ⁇ -phase generated is reduced, and the number density of particles ( ⁇ -phase) having a centroid diameter of less than 1 ⁇ m is increased. As a result, as shown in Table 2, the average number density of dispersed particles having a centroid diameter of less than 1 ⁇ m is too large, and the ratio between the maximum height H ⁇ of the X-ray diffraction peaks of the ⁇ phase and the ⁇ phase (H ⁇ / H ⁇ ). Is too low.
  • Comparative Examples 18 to 21 have the composition of the present invention (alloy No. 2 in Table 1), the conditions such as the soaking temperature only once and the end temperature of hot rough rolling are the above-mentioned preferable conditions. In order to deviate, the organization deviates from the provisions of the present invention. As a result, in a low-cost manufacturing method in which low-temperature soaking and intermediate annealing are performed only once, the average ear rate itself is high, and the variation in the ear rate in the plate width direction is also large.
  • Comparative Example 18 since the soaking temperature was too low and hot rolling cracks occurred, the test was interrupted in the middle of hot rolling as shown by the hatched lines in Table 2.
  • the finish temperature of hot finish rolling was too high, and surface defects were caused by rough skin. Therefore, cold rolling after hot rolling was not performed as shown by the diagonal lines in Table 2.
  • the end temperature of hot rough rolling and the end temperature of hot finish rolling are too low, the average number density of dispersed particles having a centroid diameter of less than 1 ⁇ m is too high, and the ⁇ phase and ⁇ phase The ratio H ⁇ / H ⁇ to the maximum height H ⁇ of the X-ray diffraction peak is too low.
  • the soaking temperature was too high, and surface defects due to seizure occurred during hot rolling, so that cold rolling after hot rolling was not performed as shown by the oblique lines in Table 2.
  • the present invention it is possible to reduce the manufacturing cost of an aluminum alloy cold-rolled sheet, which is a material of a bottle can, and to suppress variations in the edge ratio in the sheet width direction. Further, in the three-piece type bottle can, the amount of the flange (trimming amount) to be removed particularly by trimming is reduced by lowering the ear rate itself and suppressing the variation of the ear rate in the plate width direction. Therefore, the yield of the material can be improved. Therefore, the present invention is suitable for use in manufacturing a three-piece type bottle can among the bottle cans.

Abstract

La présente invention réduit le coût de fabrication d'une feuille d'alliage d'aluminium laminée à froid qui doit être utilisée comme matériau des canettes et réduit le défaut de planéité des oreilles dans le sens de la largeur. Cette feuille d'alliage d'aluminium laminée à froid pour des canettes a une composition spécifique et présente une structure qui contient une faible quantité de particules dispersées ayant un diamètre au centre de gravité inférieur à 1 µm, qui représente une phase α et le rapport de la quantité de la phase β qui est un composé intermétallique Al6(Fe, Mn) sur la quantité de la phase α qui est un composé intermétallique Al-Fe-Mn-Si étant égal ou supérieur à 0,50 pour ce qui est du rapport de la hauteur maximale Hβ des pics de diffraction des rayons X sur la hauteur maximale Hα des pics de diffraction des rayons X, Hβ/Hα. Ainsi, la feuille laminée à chaud de l'invention présente un degré égal de recristallisation dans le sens de la largeur de la feuille et la feuille d'alliage d'aluminium laminée à froid présente un défaut de planéité des oreilles dans le sens de la largeur.
PCT/JP2011/072116 2010-09-30 2011-09-27 Feuille d'alliage d'aluminium laminée à froid pour une canette WO2012043582A1 (fr)

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