WO2015140833A1 - Feuille d'alliage d'aluminium pour corps de boîte métallique dr et son procédé de production - Google Patents

Feuille d'alliage d'aluminium pour corps de boîte métallique dr et son procédé de production Download PDF

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WO2015140833A1
WO2015140833A1 PCT/JP2014/001635 JP2014001635W WO2015140833A1 WO 2015140833 A1 WO2015140833 A1 WO 2015140833A1 JP 2014001635 W JP2014001635 W JP 2014001635W WO 2015140833 A1 WO2015140833 A1 WO 2015140833A1
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aluminum alloy
plate
annealing
temperature
hot
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PCT/JP2014/001635
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English (en)
Japanese (ja)
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聖誠 田添
鈴木　覚
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株式会社Uacj
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Priority to CN201480077133.7A priority Critical patent/CN106103760B/zh
Priority to JP2016508302A priority patent/JP6326485B2/ja
Priority to PCT/JP2014/001635 priority patent/WO2015140833A1/fr
Publication of WO2015140833A1 publication Critical patent/WO2015140833A1/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
    • 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

Definitions

  • the present invention relates to an aluminum alloy for a DR can body having excellent deep drawability and a low ear rate, and a method for producing the same.
  • Aluminum alloys such as A3004 and A3104 in JIS standards are used as body materials for aluminum cans because they have excellent formability and corrosion resistance.
  • the ear rate will be described.
  • a cup after deep drawing has a high portion (mountain) and a low portion (valley) at the upper end of the circumferential portion.
  • the difference between the average value of the peak height and the average value of the valley height divided by the average value of the valley height is referred to as the ear rate.
  • the productivity is adversely affected, for example, a defective portion is generated at the time of winding with the can lid, or the trimming amount is increased and the yield is lowered.
  • the shape of the ear there are a 0/90 degree ear with a mountain in the 0/90 degree direction with respect to the rolling direction and a 45 degree ear with a mountain in the 45 degree direction with respect to the rolling direction.
  • Each ear has a correlation with the texture, and the Cube orientation: (001) ⁇ 100> is known to develop 0/90 degree ears, and the ⁇ fiber, which is a rolled texture, is known to develop 45 degree ears. ing. When the cold rolling rate increases, the ⁇ fiber develops and the 45-degree ear becomes prominent.
  • a good balance between the Cube orientation and the rolling texture particularly the S and R orientations: ⁇ 123 ⁇ ⁇ 634> is required.
  • the DR can body is mainly used for food containers, and demand is expected to increase as the world population increases.
  • the DR can body is currently manufactured by a manufacturing method including an intermediate annealing process.
  • a manufacturing method including an intermediate annealing process.
  • a box-type annealing furnace hereinafter referred to as “batch furnace”
  • CAL continuous annealing furnace
  • the manufacturing cost of CAL increases, and the capital investment for increasing the production capacity is large. Therefore, in order to reduce the cost, it is necessary to manufacture in a batch furnace, but there is a problem that ear control is more strict and 45-degree ears are more easily developed than CAL.
  • the DR can body is formed only by deep drawing, a high degree of deep drawing formability is required. Specifically, high deep drawability and reduction of wrinkles during deep drawing. Deep drawability is evaluated by the limit draw ratio. If the deep drawability is not good, cracks are likely to occur during molding. In addition, when wrinkles occur during deep drawing, the surface quality of the product is significantly reduced. In recent years, the demand for surface quality has become increasingly severe.
  • Patent Document 1 describes a method for producing an aluminum alloy sheet for packaging having deep drawability and redrawability.
  • Patent Document 2 describes a method for producing a packaging aluminum alloy having high strength and low directionality.
  • Patent Documents 3 to 5 describe aluminum alloy sheets having a low ear ratio that define the hot-rolled sheet, the intermediate annealed sheet, the Cube orientation of the final sheet, and the rolled texture as a technique related to the texture described above. Yes.
  • Patent Document 1 the ear is controlled by the homogenization treatment and the cold rolling rate, but it is not possible to obtain a sufficiently low ear rate when intermediate annealing is performed in a batch furnace. Moreover, in the aluminum alloy of patent document 2, since there exists high intensity
  • Patent Documents 3 to 5 control the metal structure
  • the use is limited to DI cans.
  • DI can applications a high cold rolling rate is achieved without using an intermediate annealing process. Since the super hard material used has a high yield strength, wrinkles are likely to occur during deep drawing, and it is not suitable for DR cans.
  • the hot-rolled sheet structure of Patent Document 5 is a partially recrystallized structure, a partially recrystallized structure cannot be obtained unless the sheet temperature is low. Therefore, the rolling speed, which is one of the manufacturing conditions, must be reduced, and there is a problem that the productivity is lowered and the manufacturing cost is increased.
  • JP-A 63-145758 Japanese Unexamined Patent Publication No. 1-198454 JP 2001-40461 A JP 2004-244701 A JP 2004-263253 A
  • the present inventors have successfully developed the S orientation in the matrix in the metal structure before the intermediate annealing step to suppress precipitation at the time of recrystallization. It has been found that an aluminum alloy plate having an excellent ear ratio can be obtained. That is, it is known that the Cube orientation and the S orientation have a rotational relationship of 40 degrees around the ⁇ 111> axis as the crystal orientation, and the Cube orientation is easy to grow in the S orientation matrix. Therefore, by developing the S orientation, the Cube orientation is easily grown. In addition, the precipitate inhibits recrystallization, suppresses the formation of the Cube orientation, and promotes the formation of the R orientation. Therefore, by sufficiently developing the S orientation and suppressing the number of precipitated particles, an excellent ear ratio was obtained even in the intermediate annealing process using a batch furnace.
  • the presence or absence of wrinkles during deep drawing is due to the yield strength after baking.
  • the yield strength after baking is reduced, the generation of wrinkles is suppressed, but since the tensile strength is also reduced, the deep drawability is also inferior.
  • the present invention is an aluminum alloy found on the basis of the above knowledge, has a low ear ratio even when a batch furnace is used, and has an excellent deep drawability, an aluminum alloy for DR can body, In addition, an object is to provide a manufacturing method thereof.
  • the present invention is characterized in that the primary cold rolling rate is appropriately controlled.
  • the primary cold rolling rate is appropriately controlled.
  • the S orientation can be developed.
  • PSN that is recrystallized from around the crystallized product becomes prominent, and the metal structure becomes a random structure with a reduced Cube orientation density.
  • the primary cold rolling rate is appropriately controlled.
  • the S orientation is developed into a structure before the intermediate annealing process, and the number of precipitated particles in the structure before the intermediate annealing process and the precipitation during recrystallization are suppressed. It is.
  • the growth of the Cube orientation in the annealing process can be promoted. That is, the development of the 0/90 degree ear is promoted, and an excellent ear rate is obtained by a good balance with the secondary cold rolling process. Further, in the secondary cold rolling process, by controlling appropriate proof stress and tensile strength, good deep drawability and aesthetics that can withstand high surface quality can be obtained.
  • Si 0.10 to 0.60 mass%, Fe: 0.10 to 0.80 mass%, Cu: 0.05 to 0.25 mass%, Mn: 0.80 to 1.50 mass %, Mg: 0.80 to 1.30 mass%, and is made of an aluminum alloy composed of the balance Al and inevitable impurities, and the final plate is obtained from the aluminum alloy ingot through at least a hot rolled plate and an intermediate annealed plate.
  • the hot-rolled sheet has a conductivity of 36.0 to 43.0% IACS.
  • the Cube orientation density (CubeO) in the intermediate annealing plate is 4.00 or more times the random orientation density, and the CubeO and the R orientation density (RO). And the ratio (CubeO / RO) to 1.00 or more.
  • the present invention provides the method for producing an aluminum alloy plate for a DR can body according to any one of claims 1 to 3, wherein Si: 0.10 to 0.60 mass%, Fe: 0.00. Contains 10 to 0.80 mass%, Cu: 0.05 to 0.25 mass%, Mn: 0.80 to 1.50 mass%, Mg: 0.80 to 1.30 mass%, and is composed of the balance Al and inevitable impurities.
  • a casting process for casting an aluminum alloy, a homogenization process for homogenizing the ingot, a hot rolling process for hot rolling the homogenized ingot, and a primary cold rolling process for the hot rolled plate A method for producing an aluminum alloy plate for a DR can body, comprising: an intermediate annealing step for annealing the primary cold rolled plate; and a secondary cold rolling step for the intermediate annealed plate.
  • the ingot is treated at 580 to 620 ° C. for 1 to 12 hours, and the hot rolling step is performed at a start temperature of 450 to 610 ° C. It consists of a hot rough rolling stage at 450 to 550 ° C. and a hot finish rolling stage at an end temperature of 330 to 380 ° C., and the rolling rate of the primary cold rolling process is 85 to 95%.
  • the intermediate annealing process The primary cold-rolled sheet is heated to an annealing temperature of 300 to 450 ° C. at an average heating rate of 10 to 100 ° C./hour in a temperature range of 200 ° C. or higher, and then held at the annealing temperature for 1 to 4 hours.
  • the rolling rate in the secondary cold rolling process was 20 to 40%.
  • the method according to the fourth or fifth aspect further includes a final annealing step of annealing the secondary cold rolled sheet after the secondary cold rolling step.
  • the present invention is as described in claim 6, wherein in the final annealing step, the secondary cold-rolled sheet is annealed at 140 to 190 ° C. with an average temperature increase rate of 10 to 80 ° C./hour in a temperature range of 200 ° C. or higher. The temperature was raised to a temperature and then held at the annealing temperature for 2 to 4 hours.
  • an aluminum alloy for a DR can body having a low ear ratio and excellent deep drawability even when a batch furnace is used can be obtained.
  • Aluminum alloy plate for DR can body The aluminum alloy plate for DR can body according to the present invention is made of an aluminum alloy having a predetermined alloy composition, and the final plate has a characteristic of a specific orientation density (CubeO). Later, it has a predetermined strength.
  • CubeO specific orientation density
  • Si 0.10 to 0.60 mass%
  • Mg 2 Si-based particles are precipitated during final annealing and coating baking, thereby contributing to an increase in strength. If the Si content is less than 0.10 mass% (hereinafter referred to as “%”), this effect cannot be obtained, and high-purity metal must be used at the time of casting, which increases raw material costs. On the other hand, if it exceeds 0.60%, the precipitated particles increase, so that recrystallization is hindered in the hot rolling process and the intermediate annealing process. As a result, the formation of the Cube orientation is suppressed, and the ear rate of the final plate is deteriorated.
  • a preferable content of Si is 0.20 to 0.50%.
  • Fe 0.10 to 0.80%
  • the solid solution precipitation state of Mn is controlled by the inclusion of Fe, and the deep drawability is improved by uniformly dispersing the Mn-based crystallized product. If the Fe content is less than 0.10%, this effect cannot be obtained, and high-purity ingots must be used at the time of casting, which increases raw material costs. On the other hand, when it exceeds 0.80%, coarse Al—Fe—Mn—Si based crystallized substances increase, and recrystallization in a high dislocation density region around the crystallized substances called PSN becomes dominant. As a result, the Cube orientation density is lowered, and the ear rate of the final plate is deteriorated.
  • a preferable content of Fe is 0.30 to 0.60%.
  • Cu 0.05 to 0.25% Due to the inclusion of Cu, Al—Cu—Mg and Al—Cu—Mg—Si particles are deposited during final annealing and paint baking, contributing to an increase in strength. If the Cu content is less than 0.05%, this effect cannot be obtained, and if it exceeds 0.25%, the strength becomes too high and the deep drawability deteriorates. A preferable content of Cu is 0.10 to 0.25%.
  • Mn 0.80 to 1.50% Containing Mn contributes to an increase in strength. If the Mn content is less than 0.80%, sufficient strength cannot be obtained. On the other hand, if it exceeds 1.50%, the strength becomes too high and the deep drawability deteriorates. A preferable content of Mn is 0.80 to 1.10%.
  • Mg 0.80 to 1.30% Containing Mg contributes to an increase in strength due to solid solution. Further, the formation of Si and Mg 2 Si-based particles contributes to an increase in strength during final annealing and paint baking. If the Mg content is less than 0.80%, this effect cannot be obtained. On the other hand, if it exceeds 1.30%, the strength becomes too high and the deep drawability deteriorates. A preferable content of Mg is 0.90 to 1.25%.
  • the aluminum alloy may contain 0.05% or less of Ti, B, V, etc. as inevitable impurities, and 0.15% or less as a whole.
  • the Cube orientation density (hereinafter referred to as “CubeO”) in the final plate is 2.00 times or more than the random orientation density
  • CubeO and S orientation density (hereinafter referred to as “SO”) Ratio (CubeO / SO) is defined as 0.40 to 1.00.
  • the shape of the ear is determined by CubeO and the balance between CubeO and the rolling texture.
  • CubeO is less than 2.00 times the random orientation, or CubeO / SO is less than 0.40, the 45-degree ear develops and the ear rate deteriorates.
  • CubeO / SO exceeds 1.00, a good balance between the 0/90 degree ear and the 45 degree ear cannot be obtained, and the ear rate is similarly deteriorated.
  • CubeO is preferably 3.00 or more times the random orientation density.
  • the upper limit value of the magnification is not particularly specified, but is naturally determined by the composition and manufacturing conditions of the aluminum alloy, and in the present invention, the upper limit value is set to 7.00 times.
  • CubeO / SO is preferably 0.50 to 1.00.
  • the strength of the aluminum alloy plate for DR can body according to the present invention is defined as having a yield strength of 180 to 220 MPa and a tensile strength of 230 MPa or more after baking.
  • the yield strength after baking is less than 180 MPa, the strength of the DR can body is insufficient.
  • the yield strength after baking is over 220 MPa, wrinkles are generated during deep drawing and surface quality is deteriorated.
  • the yield strength after baking is preferably 190 to 210 MPa.
  • the limit drawing ratio is lowered and the deep drawability is poor.
  • the tensile strength after baking is 235 MPa or more.
  • the upper limit value of the tensile strength after baking is not particularly specified, but it is naturally determined by the composition and manufacturing conditions of the aluminum alloy, and the upper limit value is set to 255 MPa in the present invention.
  • CubeO in the intermediate annealed plate is 4.00 times or more than the random orientation density
  • the ratio (CubeO / RO) between CubeO and R orientation density (hereinafter referred to as “RO”) is 1.
  • it is defined as 00 or more.
  • CubeO is preferably 4.50 or more times the random orientation density.
  • the upper limit value of the magnification is not particularly specified, but is naturally determined by the composition of the aluminum alloy and the manufacturing conditions, and the upper limit value is set to 10 times in the present invention.
  • CubeO / RO is preferably 1.00 or more. Although the upper limit value of CubeO / RO is not particularly defined, it is naturally determined by the composition and manufacturing conditions of the aluminum alloy, and in the present invention, the upper limit value is set to 5.00.
  • the aluminum alloy plate for DR can body according to the present invention includes a casting step of casting the aluminum alloy having the above-mentioned predetermined composition; a homogenization treatment step of homogenizing the ingot; A hot rolling step for hot rolling the homogenized ingot; a primary cold rolling step for the hot rolled plate; an intermediate annealing step for annealing the primary cold rolled plate at 300 to 450 ° C; and an intermediate annealed plate A secondary cold rolling step.
  • the ingot cast in the casting step is preferably subjected to heat treatment at a temperature of 580 to 620 ° C. for 1 to 12 hours.
  • the treatment temperature is less than 580 ° C. and the treatment time is less than 1 hour, the homogenization effect is insufficient.
  • the number of precipitated particles during the hot rolling process increases, recrystallization after the hot rolling process is hindered.
  • CubeO also decreases in the recrystallized grains. Since CubeO of this hot-rolled sheet becomes one of the nuclei of Cube-oriented grains during intermediate annealing, it is important not to lower it.
  • the temperature of the homogenization treatment step is more preferably 580 to 610 ° C., and the treatment time is further preferably 1 to 4 hours.
  • Hot rolling process After the homogenization process, the ingot is subjected to a hot rolling process.
  • the hot rolling process includes a hot rough rolling stage and a hot finish rolling stage.
  • the start temperature is 450 to 610 ° C.
  • the end temperature is 450 to 550 ° C.
  • the starting temperature is less than 450 ° C.
  • precipitation of intermetallic compounds occurs and the temperature of the rolled sheet decreases.
  • the rolled structure remains in the structure after the hot finish rolling, and the 45-degree ears of the final plate are developed.
  • the starting temperature exceeds 610 ° C.
  • the surface of the rolled sheet is oxidized, and a defect occurs on the surface of the rolled sheet during rolling, resulting in a deterioration in quality.
  • the end temperature is less than 450 ° C.
  • seizure occurs on the surface of the rolled sheet, and the surface quality deteriorates.
  • the rolling time in the hot rough rolling stage and the hot finish rolling stage is not particularly limited, but is preferably within 20 minutes. It is more preferable that the start temperature of the hot rough rolling step is 470 to 580 ° C. and the end temperature is 450 to 530 ° C.
  • the rolled plate is subjected to the hot finish rolling stage.
  • the end temperature is preferably set to 330 to 380 ° C.
  • the end temperature is less than 330 ° C.
  • the driving force for recrystallization is insufficient.
  • the rolling texture remains on the rolled plate, and the 45 ° ears of the final plate develop and the ear rate deteriorates.
  • productivity also falls.
  • the end temperature exceeds 380 ° C., seizure occurs on the surface of the rolled sheet, and the surface quality deteriorates. It is more preferable that the end temperature of the hot finish rolling step is 330 to 370 ° C.
  • the electrical conductivity of the hot rolled sheet after the hot rolling step is preferably 36.0 to 43.0% IACS.
  • the electrical conductivity is less than 36.0% IACS, the solution is in a highly solid state, the deep drawability is lowered, and cracking occurs during can making.
  • the electrical conductivity exceeds 43.0% IACS precipitates in the hot-rolled sheet increase and the R orientation is preferentially formed during intermediate annealing, so the 45-degree ear development of the final sheet is remarkable. become.
  • the electrical conductivity of the hot rolled sheet is more preferably 36.0 to 42.0% IACS.
  • the total rolling rate in the entire hot rolling process is not particularly specified, but is preferably 80 to 95%. If it is less than 80%, the S orientation density in the hot-rolled sheet decreases, the 0/90 degree ear during self-annealing becomes weak, and if it exceeds 95%, the recrystallization driving force becomes too high and the ear becomes no-ear, This leads to a decrease in Cube orientation density during intermediate annealing.
  • the total rolling rate in the entire hot rolling process is more preferably 85 to 93%.
  • the rolling rate in the primary cold rolling process is preferably 85 to 95%.
  • the rolling rate in the primary cold rolling process is more preferably 87 to 93%.
  • Intermediate annealing step After the primary cold rolling, the cold rolled sheet is subjected to an intermediate annealing step.
  • the intermediate annealing step the primary cold-rolled sheet is first heated to an annealing temperature of 300 to 450 ° C. at an average heating rate of 10 to 100 ° C./hour in a temperature range of 200 ° C. or higher, and then at this annealing temperature. It is preferable to hold for 1 to 4 hours.
  • an intermediate annealing plate in which CubeO is 4 times or more with respect to the random orientation and CubeO / RO is 1 or more is obtained.
  • the average rate of temperature increase in the temperature range of 200 ° C. or higher is less than 10 ° C./hour.
  • competition between recrystallization and precipitation becomes remarkable, and the formation of the R orientation is rapidly promoted.
  • the temperature exceeds 100 ° C./hour a temperature gradient is generated between the inner winding and the outer winding of the coil to cause a difference in thermal expansion, and the overlapping plates are rubbed with each other to deteriorate the surface quality.
  • the reason why the temperature range is limited to 200 ° C. or more is that recrystallization and precipitation compete.
  • the average rate of temperature increase in the temperature range of 200 ° C. or higher is more preferably 15 to 80 ° C./hour.
  • the annealing temperature is less than 300 ° C. and the annealing time is less than 1 hour, a complete recrystallized structure cannot be obtained.
  • the annealing temperature exceeds 450 ° C.
  • the cold rolling oil is baked on the surface of the intermediate annealing plate and the surface quality is deteriorated.
  • the annealing time exceeds 4 hours, productivity deteriorates.
  • the annealing temperature is more preferably 330 to 400 ° C., and the annealing time is further preferably 2 to 4 hours.
  • Secondary cold rolling step The intermediate annealed plate after the intermediate annealing step is subjected to the secondary cold rolling step.
  • the rolling rate in the secondary cold rolling process is preferably 20 to 40%. When the rolling rate is less than 20%, the strength is insufficient. As a result, the strength of the can cannot be obtained, and cracks occur during deep drawing. When the rolling rate exceeds 40%, the yield strength becomes too high, and the ratio between the tensile strength and the yield strength becomes small. As a result, cracks and wrinkles occur during deep drawing. Further, when the rolling rate exceeds 40%, the rolling texture develops, so that the 45 degree ear becomes stronger.
  • a final annealing step of annealing the secondary cold rolled sheet may be further provided. Thereby, material strength and ductility can be adjusted, and it becomes possible to aim at the further improvement of a moldability.
  • the temperature is raised to an annealing temperature of 140 to 190 ° C. at an average temperature increase rate of 10 to 80 ° C./hour, and then held at the annealing temperature for 2 to 4 hours.
  • the productivity is deteriorated.
  • the productivity is deteriorated.
  • it exceeds 80 ° C./hour the amount of heat input becomes insufficient and the effect of annealing cannot be obtained sufficiently, and only the manufacturing cost increases.
  • the annealing temperature is less than 140 ° C. and the annealing time is less than 2 hours, the effect of annealing becomes insufficient.
  • the annealing temperature exceeds 190 ° C., the softening proceeds too much and the material strength decreases.
  • productivity deteriorates.
  • the annealing temperature is more preferably 160 to 180 ° C., and the annealing time is further preferably 2 to 3 hours.
  • An ingot was produced by DC casting using an aluminum alloy having the composition of A to U shown in Table 1 according to a conventional method.
  • the ingot was homogenized, hot rolled, primary cold rolled, intermediate annealed, secondary cold rolled, and final annealed under the conditions shown in Table 2 to produce a final product having a thickness of 0.22 mm.
  • tissue observation were performed.
  • the conductivity was measured using an eddy current conductivity measuring device and using copper as a reference sample.
  • the structure was observed by polishing the plate cross section (L-ST surface) using the Barker method.
  • the case where it was a complete recrystallized structure was evaluated as ⁇ , and the case where the rolled structure remained was evaluated as x.
  • the intermediate annealed plate was subjected to structure observation and texture evaluation.
  • the plate cross section (L-ST plane) was evaluated in the same manner as the hot-rolled plate.
  • the texture evaluation was performed by the SEM-EBSD method on the plate surface using OIM manufactured by TSL. CubeO and RO were evaluated without considering the tilt angle.
  • the final plate was further evaluated for strength, ear coverage, surface quality, and deep drawability.
  • intensity strength, it implemented in the rolling direction and the parallel direction using the JIS5 test piece, and measured the yield strength and tensile strength after baking.
  • the baking conditions were 205 ° C. ⁇ 10 minutes.
  • the ear ratio was calculated from the following equation by measuring a cup height in the rolling direction after forming a cup by squeezing a blank having a diameter of 57 mm with a 33 mm punch.
  • Ear rate (%) ⁇ (average mountain height ⁇ average valley height) / average cup height ⁇ ⁇ 100
  • ⁇ the others were regarded as unacceptable (x).
  • x the surface quality
  • the case where the DR could be continuously formed without cracking was determined to be acceptable ( ⁇ ), and the others were rejected.
  • Comparative Example 25 the Si content of the aluminum alloy was large, and the amount of intermetallic compound deposited was large. As a result, the formation of the Cube orientation was suppressed, leading to the development of 45-degree ears and the ear rate deteriorated.
  • Comparative Example 26 the Fe content of the aluminum alloy was large, and coarse crystals were increased. As a result, recrystallization around the crystallized substance became dominant at the time of recrystallization, leading to the development of 45-degree ears of the final plate, and the ear rate was deteriorated.
  • Comparative Example 44 the primary cold rolling rate is high, the recrystallization driving force before annealing is increased, the formation amount of the Cube orientation is decreased, and the 45-degree ear of the final plate is developed, leading to deterioration of the ear rate. Also, cracks occurred during deep drawing.

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Abstract

La présente invention concerne un alliage d'aluminium pour corps de boîte métallique DR, l'alliage ayant un faible taux de formation de cornes et d'excellentes propriétés d'emboutissage profond, même lorsqu'un four discontinu est utilisé, et un procédé procédé pour le fabriquer,. L'invention concerne une feuille d'alliage d'aluminium pour corps de boîtes métalliques DR et un procédé pour la fabriquer, la feuille d'alliage d'aluminium étant obtenue à partir d'un alliage d'aluminium contenant : Si : 0,10 à 0,60 % en masse (% ci-dessous), Fe : 0,10 à 0,80 %, Cu : 0,05 à 0,25 %, Mn : 0,80 -1,50 %, Mg : 0,80 à 1,30 % et le reste étant obtenu à partir de Al et des impuretés inévitables et la feuille d'alliage d'aluminium étant transformée en une feuille finale après conversion d'un lingot dudit alliage d'aluminium en une feuille laminée à chaud et en une feuille recuite de procédé. Dans la feuille finale, la densité d'orientation cubique (CubeO) est égale à 2,00 ou plus fois la densité d'orientation aléatoire et le rapport (CubeO/SO) de CubeO à la densité d'orientation S (SO) est de 0,40 - 1,00. Après cuisson, la feuille en alliage d'aluminium a une limite d'élasticité de 180 à 220 MPa et une résistance à la traction d'au moins 230 MPa.
PCT/JP2014/001635 2014-03-20 2014-03-20 Feuille d'alliage d'aluminium pour corps de boîte métallique dr et son procédé de production WO2015140833A1 (fr)

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CN201480077133.7A CN106103760B (zh) 2014-03-20 2014-03-20 Dr罐体用铝合金板及其制造方法
JP2016508302A JP6326485B2 (ja) 2014-03-20 2014-03-20 Ｄｒ缶ボディ用アルミニウム合金板及びその製造方法
PCT/JP2014/001635 WO2015140833A1 (fr) 2014-03-20 2014-03-20 Feuille d'alliage d'aluminium pour corps de boîte métallique dr et son procédé de production

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Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN107532241A (zh) * 2015-12-17 2018-01-02 诺维尔里斯公司 用于高度塑形产品的铝微结构及相关联方法
JP2018123376A (ja) * 2017-02-01 2018-08-09 株式会社Uacj アルミニウム合金板及びその製造方法
JP2019518867A (ja) * 2016-05-02 2019-07-04 ノベリス・インコーポレイテッドＮｏｖｅｌｉｓ Ｉｎｃ． 向上した成形性を有するアルミニウム合金及び関連方法
EP3234208B1 (fr) 2014-12-19 2020-04-29 Novelis Inc. Alliage d'aluminium approprié pour la production à grande vitesse d'une bouteille en aluminium et procédé de fabrication associé
CN112122882A (zh) * 2019-06-25 2020-12-25 西南铝业（集团）有限责任公司 一种纯铝合金o态板材的生产工艺
EP3875629A1 (fr) * 2020-03-03 2021-09-08 Elvalhalcor Hellenic Copper and Aluminium Industry S.A. Procédé et installation pour la production d'une tôle de boîte d'aluminium
EP4050115A1 (fr) 2021-02-26 2022-08-31 Constellium Rolled Products Singen GmbH & Co.KG Tole mince durable en alliage d'aluminium pour applications décoratives

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JP6402229B1 (ja) * 2017-09-28 2018-10-10 株式会社Uacj 磁気ディスク用アルミニウム合金基板及びその製造方法、ならびに、当該磁気ディスク用アルミニウム合金基板を用いた磁気ディスク

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EP3234208B1 (fr) 2014-12-19 2020-04-29 Novelis Inc. Alliage d'aluminium approprié pour la production à grande vitesse d'une bouteille en aluminium et procédé de fabrication associé
CN107532241A (zh) * 2015-12-17 2018-01-02 诺维尔里斯公司 用于高度塑形产品的铝微结构及相关联方法
US10604826B2 (en) 2015-12-17 2020-03-31 Novelis Inc. Aluminum microstructure for highly shaped products and associated methods
JP2019518867A (ja) * 2016-05-02 2019-07-04 ノベリス・インコーポレイテッドＮｏｖｅｌｉｓ Ｉｎｃ． 向上した成形性を有するアルミニウム合金及び関連方法
JP2018123376A (ja) * 2017-02-01 2018-08-09 株式会社Uacj アルミニウム合金板及びその製造方法
JP7138396B2 (ja) 2017-02-01 2022-09-16 株式会社Uacj 缶胴体用アルミニウム合金板及びその製造方法
CN112122882A (zh) * 2019-06-25 2020-12-25 西南铝业（集团）有限责任公司 一种纯铝合金o态板材的生产工艺
EP3875629A1 (fr) * 2020-03-03 2021-09-08 Elvalhalcor Hellenic Copper and Aluminium Industry S.A. Procédé et installation pour la production d'une tôle de boîte d'aluminium
WO2021175761A1 (fr) 2020-03-03 2021-09-10 Elvalhalcor Hellenic Copper And Aluminium Industry S.A. Procédé et installation de production de feuille de canette d'aluminium
CN115151675A (zh) * 2020-03-03 2022-10-04 希腊金属研究中心公司 制造铝罐板的方法和设备
EP4050115A1 (fr) 2021-02-26 2022-08-31 Constellium Rolled Products Singen GmbH & Co.KG Tole mince durable en alliage d'aluminium pour applications décoratives
WO2022179856A1 (fr) 2021-02-26 2022-09-01 Constellium Rolled Products Singen Gmbh & Co.Kg Feuille d'alliage d'aluminium durable pour applications décoratives

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