WO2022239694A1 - Feuille d'alliage d'aluminium pour capuchons à anneau de tirage et son procédé de production - Google Patents

Feuille d'alliage d'aluminium pour capuchons à anneau de tirage et son procédé de production Download PDF

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WO2022239694A1
WO2022239694A1 PCT/JP2022/019507 JP2022019507W WO2022239694A1 WO 2022239694 A1 WO2022239694 A1 WO 2022239694A1 JP 2022019507 W JP2022019507 W JP 2022019507W WO 2022239694 A1 WO2022239694 A1 WO 2022239694A1
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aluminum alloy
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俊作 上田
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株式会社Uacj
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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
    • 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
    • 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
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02W—CLIMATE CHANGE MITIGATION TECHNOLOGIES RELATED TO WASTEWATER TREATMENT OR WASTE MANAGEMENT
    • Y02W30/00—Technologies for solid waste management
    • Y02W30/50—Reuse, recycling or recovery technologies
    • Y02W30/80—Packaging reuse or recycling, e.g. of multilayer packaging

Definitions

  • the present invention relates to an aluminum alloy plate suitable for manufacturing ring-pull caps, particularly maxicaps, and a method for manufacturing the same.
  • maxicaps include those in which the pull ring is made of plastic.
  • a ring-pull cap (especially maxicap) is opened by pulling the ring tab and tearing the cap from the hem (side) of the cap along the score (notch line, groove) provided on the top surface.
  • Ring-pull caps are widely used for beverages and the like because they are easy to open, have high airtightness and TE (tamper resistance).
  • the current mainstream plate thickness is 0.2 mm to 0.3 mm, and it is required to be less than 0.2 mm.
  • the thickness of the score portion thickness of the aluminum alloy plate immediately below the score
  • the airtightness may deteriorate.
  • it becomes difficult to tear the cap along the score and there is a possibility that the easy-to-open property may deteriorate.
  • blow-off refers to the phenomenon in which the cap flings off (flys) from the mouth of the container at the beginning of opening, before tearing off the hem of the cap and releasing pressure within the container. The reason for this is that the hem of the cap does not have enough force to restrain the mouth of the container. There is also concern that the thinning of the cap will reduce the blow-off resistance.
  • the cap can be recycled together with aluminum bottles, beverage cans, and the like.
  • alloys with different compositions are used depending on the application, which is an obstacle to efficient recycling.
  • the content of Mg, Mn, Fe, Si and Cu in the composition of aluminum alloys, the range of earing ratio, and the grain size are limited, and furthermore, the tensile strength after a predetermined heat treatment is limited.
  • the composition of the aluminum alloy is, on a mass basis, Mg: 2.2 to 2.8%, Mn: 0.20 to 0.50%, Fe: 0.20 to 0.40%, Si: 0.05 to 0. .20%, Cu: 0.01 to 0.15%, and the balance is aluminum and unavoidable impurities. It is said that the composition of the aluminum alloy may further contain Ti: 0.01% to 0.10% on a mass basis.
  • the aluminum alloy described in Patent Document 1 has high blow-off resistance, but further improvement is required.
  • the internal pressure of the container is high, so the cap is required to have high blow-off resistance.
  • the cap is subjected to high internal pressure for a long period of time, and the shape of the cap may change over time. That is, if stored at high temperatures for a long period of time, there is a risk that the blow-off resistance will decrease.
  • it is required to improve the property (long-term creep resistance) that does not deform even when stress is applied for a long period of time at high temperatures.
  • the present invention provides an aluminum alloy plate for a ring-pull cap that is excellent in blow-off resistance, easy-openability, recyclability and long-term creep resistance even when the thickness is reduced, and a method for producing such an aluminum alloy plate. intended to provide
  • solutions are provided in the following items.
  • Item 1 Based on mass, Mn: 0.50% or more and 1.10% or less, Mg: 2.85% or more and less than 3.48%, Fe: 0.20% or more and 0.40% or less, Si: 0.05% or more 0.20% or less, Cu: 0.01% or more and 0.15% or less, an alloy composition containing Ti as an optional element with an upper limit of 0.10% on a mass basis, and the balance being aluminum and unavoidable impurities A rolled plate, The tensile strength in the rolling direction after heat treatment at 190 ° C.
  • the creep strain rate for 60 hours or more and 80 hours or less from the start of the test is 3.0 ⁇ 10 -4 % h -1 or less.
  • aluminum alloy plate for ring-pull type cap aluminum alloy plate for ring-pull type cap.
  • the alloy composition may contain, on a mass basis, Mn: more than 0.50% and 1.06% or less, and Mg: 2.90% or more and 3.09% or less.
  • the creep strain rate may be 2.6 ⁇ 10 ⁇ 4 %h ⁇ 1 or less.
  • a method for producing an aluminum alloy plate according to any one of items 1 to 3, A step A of heating an ingot made of an aluminum alloy having the alloy composition so that the temperature rise rate is 30° C./hour or more in a temperature range of at least 400° C. or higher and 460° C. or lower; After the step A, a step B of performing a homogenization treatment by holding the ingot at a first temperature of 460° C. or more and 540° C. or less for 2 hours or more and 24 hours or less; After the step B, hot rough rolling is performed at a second temperature of 460° C. or more and 540° C. or less at a rolling rate of 5% or more and 35% or less for each pass so as to be completed within 15 minutes.
  • a step C After the step C, a step D of obtaining a hot rolled sheet by performing hot finish rolling so that the finishing temperature is a third temperature of 300 ° C. or more and 350 ° C. or less; A step E of cooling the hot-rolled plate obtained in the step D at a cooling rate of 20° C./hour or less; After the step E, a step F of cold rolling the hot-rolled plate at a rolling reduction of 70% or more and 93% or less without performing intermediate annealing; and a step G of performing a stabilization heat treatment after the step F at a fourth temperature of 180° C. or higher and 240° C. or lower for 1 hour or longer and 5 hours or shorter.
  • an aluminum alloy plate for a ring-pull cap that is excellent in blow-off resistance, easy-openability, recyclability and long-term creep resistance even when the thickness is reduced, and production of such an aluminum alloy plate A method is provided.
  • FIG. 2 is a plan view of the test piece for explaining the test piece used in the creep test.
  • An aluminum alloy plate for a ring-pull cap and a method for manufacturing the same according to an embodiment of the present invention will be described below with reference to the drawings.
  • the aluminum alloy plate for ring-pull caps and the method for manufacturing the same according to the embodiments of the present invention are not limited to those exemplified below.
  • the inventors investigated an alloy composition that can improve long-term creep resistance without impairing the blow-off resistance, easy-openability, and recyclability of the aluminum alloy plate described in Patent Document 1.
  • an alloy composition that can improve long-term creep resistance without impairing the blow-off resistance, easy-openability, and recyclability of the aluminum alloy plate described in Patent Document 1.
  • Mn manganese
  • Mg manganesium
  • the aluminum alloy plate according to the embodiment of the present invention has Mn: 0.50% or more and 1.10% or less, Mg: 2.85% or more and less than 3.48%, and Fe: 0.20% or more and 0.20% or more, based on mass. 40% or less, Si: 0.05% or more and 0.20% or less, Cu: 0.01% or more and 0.15% or less, Ti as an optional element with an upper limit of 0.10% on the mass basis, and the balance has an alloy composition in which is aluminum and unavoidable impurities.
  • the alloy composition may contain Mn: more than 0.50% and 1.06% or less and Mg: 2.90% or more and 3.09% or less on a mass basis. Also, the alloy composition may contain Ti: 0.01% or more on a mass basis. Cr contained in the inevitable impurities is preferably less than 0.01% by mass.
  • the aluminum alloy plate according to the embodiment of the present invention is a rolled plate having the above alloy composition, and has a tensile strength in the rolling direction after heat treatment at 190 ° C. for 10 minutes of 280 MPa or more and 320 MPa or less.
  • the difference is 35 MPa or more
  • the conductivity is 25% IACS or more and 34% IACS or less
  • the material temperature is 80 ° C.
  • the load on the test piece is 100 MPa.
  • the creep strain rate for 80 hours or less is 3.0 ⁇ 10 ⁇ 4 %h ⁇ 1 or less.
  • the aluminum alloy plate according to the embodiment of the present invention can be obtained by at least the following method. can be manufactured by
  • the manufacturing method according to the embodiment of the present invention is a step of heating an ingot made of an aluminum alloy having the above alloy composition so that the temperature rise rate is 30 ° C./hour or more in a temperature range of at least 400 ° C. or higher and 460 ° C. or lower.
  • a step B of performing a homogenization treatment by holding the ingot at a first temperature of 460 ° C. or higher and 540 ° C. or lower for 2 hours or more and 24 hours or less
  • a pass A step C in which hot rough rolling is performed at a second rolling temperature of 460 ° C. to 540 ° C. within 15 minutes with a rolling reduction of 5% to 35% for each step, and step C.
  • a step of holding the hot-rolled sheet obtained in step D at a temperature of 300° C. or higher for 1 hour or longer may be further included.
  • Mn exhibits the effect of improving creep resistance, and that an aluminum alloy sheet containing 0.50% by mass or more of Mn has excellent long-term creep resistance.
  • the content of Mn is preferably 1.10% by mass or less. If the Mn content exceeds 1.10% by mass, it forms a huge intermetallic compound with elements such as Fe (iron) during casting, which may cause cracks during molding.
  • the Mn content is more preferably more than 0.50% by mass and 1.06% or less, and more preferably 0.70% by mass or more from the viewpoint of strength.
  • the Mg exerts the effect of improving strength (pressure resistance and blow-off resistance) and easy opening while maintaining moldability.
  • the content of Mg is preferably 2.85% by mass or more and less than 3.48% by mass. If the Mg content is 3.48% by mass or more, the aging softening at room temperature increases, and there is a risk that the blow-off resistance when the cap is opened after long-term storage will decrease. From the viewpoint of increasing strength and suppressing aging softening, the Mg content is preferably 2.90% by mass or more and 3.09% by mass or less.
  • Fe (iron) forms an intermetallic compound with Mn or the like, has the effect of refining the recrystallized grains after hot rolling, and exhibits the effect of improving the ease of opening.
  • the Fe content is preferably 0.20% by mass or more and 0.40% by mass or less. If the Fe content is less than 0.20% by mass, it is difficult to obtain the above effects. In addition, it is necessary to increase the purity of the base metal, and the recycled material cannot be used as it is. If the Fe content exceeds 0.40% by mass, a huge intermetallic compound is formed, which may cause cracks during molding.
  • the Fe content is preferably 0.20% by mass or more and 0.35% by mass or less.
  • Si is one of the impurity elements.
  • the Si content is preferably 0.10% by mass or more.
  • the Si content of Si exceeds 0.20% by mass, it forms an intermetallic compound with Mg or Mn and Fe, reduces the solid solution amount of Mg or Mn, and reduces the above effects of Mg or Mn. may cause Therefore, the Si content is preferably 0.20% by mass or less.
  • Cu copper contributes to improving the strength of the cap.
  • the Cu content is preferably 0.01% by mass or more and 0.15% by mass or less. If it is less than 0.01% by mass, the effect of Cu may not be exhibited, and if it exceeds 0.15% by mass, the strength may become too high and the formability may deteriorate.
  • Ti titanium
  • Ti is an optional element and may not be contained, but may be contained with an upper limit of 0.10% by mass.
  • Ti has the effect of reducing micro-segregation in the aluminum alloy ingot during production and finely dispersing the intermetallic compound, thereby refining the crystal grains and making the structure uniform.
  • the Ti content is preferably 0.01% by mass or more.
  • Al aluminum
  • Al-Ti compound a huge intermetallic compound
  • the alloy composition of the aluminum alloy according to the embodiment of the present invention consists of Al and unavoidable impurities as the balance other than the above elements.
  • Unavoidable impurities are inevitably mixed in during the preparation of the intended aluminum alloy, and the content is controlled so that they exist at a known impurity content.
  • Zn (zinc), Cr (chromium), and the like may be contained as unavoidable impurities, but if each is 0.10% by mass or less, the above-described characteristics are not impaired, and the inclusion of these components is also permitted. Also, within this range, recyclability is not impaired.
  • the Zn and Cr contents are preferably less than 0.01% by mass each.
  • the total content of inevitable impurities is preferably 0.10% by mass or less.
  • the aluminum alloy plate according to the embodiment of the present invention has a rolling direction tensile strength of 280 MPa or more and 320 MPa or less after heat treatment at 190°C for 10 minutes, and a difference between tensile strength and yield strength of 35 MPa or more. If the tensile strength is less than 280 MPa, pressure resistance may be insufficient. On the other hand, if it exceeds 320 MPa, wrinkles may occur during the drawing process, and there is a risk that sufficient sealing performance may not be obtained, and the ease of opening the plug may deteriorate.
  • the aluminum alloy plate according to the embodiment of the present invention has a creep strain rate of 3.0 for 60 hours or more and 80 hours or less from the start of the creep test under the conditions of a material temperature of 80 ° C. and a load on the test piece of 100 MPa. ⁇ 10 ⁇ 4 % h ⁇ 1 or less.
  • the creep strain amount is Test times exceeded 1000 days to reach 0.3%.
  • the creep strain rate decreases as the test time elapses, in the creep test under the above conditions, if the creep rate for 60 hours or more and 80 hours or less from the start of the test is 3.0 ⁇ 10 -4 % h -1 or less, The test time required for the creep strain amount to reach 0.3% must exceed 1000 days. Blow-off may occur, for example, when the amount of creep strain reaches 0.3%. Then, the aluminum alloy plate that satisfies the above conditions has excellent long-term creep resistance, and can provide a cap that suppresses a decrease in blow-off resistance due to long-term storage as compared to conventional caps.
  • the electrical conductivity of the rolled sheet after stabilization treatment is preferably 25% IACS or more and 34% IACS or less. If the conductivity is less than 25% IACS or more than 34% IACS, it may not be possible to maintain sufficient binding force at the bottom of the cap. If the aluminum alloy contains a large amount of solute elements (particularly Mn and Mg) in solid solution, the electrical conductivity is lowered, work hardening is likely to occur, and the moldability of the cap may be lowered. On the other hand, if the solid solution amount of the solute elements (especially Mn and Mg) is small, the electrical conductivity may increase, the strength may decrease, and the binding force may decrease.
  • solute elements especially Mn and Mg
  • the aluminum alloy plate according to the embodiment of the present invention can be manufactured by a manufacturing method including steps A to G described above.
  • casting is performed according to a conventional method to obtain an ingot made of an aluminum alloy having the above alloy composition.
  • predetermined homogenization treatment step B
  • hot rough rolling step C
  • hot finish rolling step D
  • cooling step E
  • cold rolling step F
  • stabilization heat treatment Step G
  • cold rolling step F
  • intermediate annealing refers to heat treatment performed before cold rolling or between passes of cold rolling.
  • an aluminum alloy having a slab thickness of about 450 mm to 600 mm obtained by casting by a known casting method such as semi-continuous casting (DC casting) Use an ingot.
  • the temperature range of at least 400° C. to 460° C. is raised at a rate of 30° C./hour or more.
  • the ingot is homogenized by holding it at a first temperature of 460° C. or more and 540° C. or less for 2 hours or more and 24 hours or less.
  • the first temperature need not be constant over 2 hours or more and 24 hours or less, and may vary in the range of 460° C. or more and 540° C. or less.
  • Such a homogenization treatment enables the size and distribution of precipitates to be effective in suppressing the growth of the Cube orientation, which is the recrystallization texture formed during recrystallization of the hot-rolled sheet.
  • precipitates are Al--Mn-based compounds and Al--Mn--Si-based compounds, which precipitate most at around 480.degree.
  • Such a compound has a higher interfacial energy with the parent phase than other intermetallic compounds, and is precipitated in a fine spherical shape, so that it exerts an effect of suppressing the growth of the Cube orientation.
  • the temperature increase rate in the temperature range of 400 ° C. or higher and 460 ° C. or lower in the heating step has a particularly large effect on the precipitation behavior of the intermetallic compound described above.
  • the size of precipitates remains as fine as 0.5 ⁇ m or less.
  • a sufficient recrystallized structure may not be obtained at the end of hot rolling.
  • the strength of the cap material may become excessively high and/or the selvage rate may become excessively large.
  • the upper limit of this temperature increase rate is, for example, 200° C./hour.
  • the homogenization treatment is carried out by maintaining the temperature in the temperature range of 460°C or higher and 540°C or lower after the above heating process. If the holding temperature is lower than 460° C., the diffusion speed becomes slow, so that the size of the compound becomes too fine as 0.5 ⁇ m or less, and a sufficient recrystallized structure may not be obtained at the end of hot rolling. If the holding temperature exceeds 540° C., the amount of the compound existing in the equilibrium state decreases, so the amount of precipitation may become insufficient. Furthermore, the interfacial energy with the matrix phase is relatively low, the precipitate size tends to increase, and the effect of suppressing the growth of the Cube orientation after hot rolling may be reduced. Further, when the holding time in the temperature range of 460° C.
  • Rough hot rolling performed after the homogenization treatment is completed within 15 minutes at a second rolling temperature of 460° C. or higher and 540° C. or lower with a rolling rate of 5% or higher and 35% or lower for each pass. It is done as follows.
  • the second temperature does not need to be constant, and may vary within a range of 460°C or higher and 540°C or lower.
  • the second temperature is set independently of the first temperature.
  • Rough hot rolling can be performed using a known rolling mill, but it is preferable to use, for example, a reverse type rough rolling mill.
  • the material may adhere to the rolling rolls, resulting in a deterioration of the surface quality of the material.
  • precipitation sites for intermetallic compounds are successively introduced, so they can be densely precipitated even in a short period of time.
  • the compound may precipitate finely and a sufficient recrystallized structure may not be obtained after the hot rolling is finished.
  • the rolling reduction is less than 5%, the amount of heat generated during processing decreases, and the rolling temperature may drop below 460°C. Temperatures may exceed 540°C.
  • Hot rough rolling is preferably completed within 15 minutes, and if it exceeds 15 minutes, the time for fine precipitation of precipitates increases similarly to the above, so that a sufficient recrystallized structure is obtained after hot rolling. Sometimes I can't.
  • hot rough rolling for example, a hot rough rolled sheet having a thickness of about 22 mm to 32 mm is obtained.
  • Hot finish rolling is performed so that the finishing temperature is a third temperature of 300°C or higher and 350°C or lower to obtain a hot rolled sheet.
  • Hot finish rolling can be performed using various known hot rolling mills, but it is preferable to use, for example, a tandem hot rolling mill with three or more stands.
  • the finishing temperature In hot finish rolling, if the finishing temperature is lower than 300°C, a sufficient recrystallized structure cannot be obtained, and the lugs in the 45° direction of the product plate become too large, causing transportation troubles during cap production. The undulations at the edge of the mouth become large, and a sufficient seal may not be obtained.
  • the finishing temperature exceeds 350° C., part of the material to be rolled will adhere to the rolling rolls, possibly leading to deterioration of the surface quality of the hot-rolled sheet. In this hot finishing rolling, the draft is generally about 88% to 94%. If the rolling reduction is too low, the amount of strain accumulated during hot finish rolling may be small, and recrystallization after the completion of rolling may be insufficient.
  • a hot-rolled sheet having a thickness of about 1.8 mm to 2.8 mm is obtained.
  • the hot-rolled sheet immediately after hot finish rolling is cooled from the hot state at the hot-rolling end temperature to around normal temperature of 50°C or less at a cooling rate of 20°C/hour or less.
  • recrystallization in the hot-rolled sheet proceeds sufficiently to obtain a suitable ear ratio.
  • the sheet immediately after hot finish rolling may be held at a temperature of 300° C. or higher for one hour or more (holding step).
  • the hot-rolled sheet that has undergone this holding step is cooled under the conditions described above, the recrystallization of the hot-rolled sheet can be further promoted, and the ear property can be further improved.
  • the upper limit of the holding temperature and holding time in the holding step can be appropriately selected in consideration of the effect, but for example, the upper limit of the holding temperature is about 350 ° C. and the upper limit of the holding time is about 5 hours. .
  • the cooled hot-rolled sheet is then further cold-rolled to obtain an aluminum alloy sheet with the desired thickness.
  • Cold rolling is preferably performed at a rolling reduction of 70% or more and 93% or less.
  • a rolled sheet having a thickness of about 0.2 mm to 0.7 mm is obtained.
  • the alloy composition of the aluminum alloy plate according to the embodiment of the present invention has a higher work hardenability than the alloy composition described in Patent Document 1 because it contains more Mg (and Mn). Therefore, the lower limit of the rolling reduction in cold rolling can be made lower (70% or more) than in Patent Document 1 (83% or more).
  • the rolling reduction In cold rolling, if the rolling reduction is lower than 70%, sufficient strength may not be obtained. In addition, the lugs in the 0° direction and 180° direction with respect to the rolling direction cannot be made sufficiently small, and the lugs in the 45° direction become small. It may reduce sexuality. Furthermore, after capping, the end portion of the mouth of the cap may be greatly undulated, and sufficient sealing performance may not be obtained. On the other hand, if the rolling reduction exceeds 93%, the work hardening of the resulting rolled sheet becomes significant, and the formability and blow-off resistance may deteriorate. Moreover, a desired selvage rate may not be obtained, resulting in a decrease in productivity.
  • intermediate annealing may be performed to control formability.
  • cold rolling is performed without performing intermediate annealing after the cooling step. I do. If intermediate annealing is performed, the solid solution amount of Mn may decrease, and the long-term creep resistance may decrease. In addition, by omitting the intermediate annealing, it is possible to contribute to the reduction of the environmental load.
  • the cold-rolled aluminum alloy plate is subjected to a stabilization heat treatment at a fourth temperature of 180°C or higher and 240°C or lower for 1 hour or longer and 5 hours or shorter.
  • the fourth temperature need not be constant over 1 hour or more and 5 hours or less, and may vary in the range of 180° C. or more and 240° C. or less.
  • the stabilization heat treatment the strain accumulated by cold rolling can be relaxed, the strain distribution on the surface of the rolled plate can be uniformed, and, for example, the occurrence of wicket marks during paint baking can be prevented.
  • the strain may not be sufficiently relaxed. Further, when the treatment time is less than 1 hour, a sufficient effect cannot be obtained, and when it exceeds 5 hours, the strength may be lowered. Moreover, lengthening the processing time is not preferable from the viewpoint of environmental load.
  • an aluminum alloy plate for a ring-pull cap that is excellent in blow-off resistance, easy-openability, recyclability and long-term creep resistance even when the thickness is reduced, and a method for producing the same are provided. can get.
  • Example 1 Aluminum alloys (Examples 1 to 4 and Comparative Examples 1 to 4) having various alloy compositions shown in Table 1 below were produced according to the production method described above. After soaking at 490° C. for 2 hours, hot rolling was performed, cold rolling was performed at room temperature, and stabilization heat treatment was performed at a temperature range of 215° C. or higher and 233° C. or lower for 2 hours. The alloy composition was analyzed by a cantometer (ARL4460, Thermo Fisher Scientific Co., Ltd.). Also, as a comparative material, an A5052 alloy material was tested. In addition, in Comparative Example 1, intermediate annealing was performed. The conditions for the intermediate annealing were a heating rate of 100° C./min or more and a condition of maintaining the temperature of the rolled sheet within the range of 400° C. or higher and 500° C. or lower for 10 minutes or less.
  • a strain gauge 12 was attached to the test piece 10 shown in FIG. 1 to measure the creep strain. Numerical values in FIG. 1 represent dimensions in mm. A test piece shown in FIG. 1 was taken from each sample in a direction forming an angle of 0° with respect to the rolling direction, and the creep strain was measured under conditions of an ambient temperature of 80° C. and an applied load of 100 MPa. Then, samples with a creep strain rate of 3.0 ⁇ 10 ⁇ 4 %h ⁇ 1 or less after 60 hours or more and 80 hours or less from the start of the test were evaluated as acceptable, and those other than this were determined as unacceptable. For the creep strain rate, the slope of the graph of creep strain against time was calculated by the least squares method in the range of 60 hours or more and 80 hours or less after the start of the test.
  • Table 2 shows the results of evaluating the tensile strength, yield strength, difference between tensile strength and yield strength, creep strain rate, and electrical conductivity. .
  • x x (NG) was given in the comprehensive judgment.
  • the "cold rolling rate” in Table 2 indicates the reduction rate during cold rolling. The rolling reduction in other rolling steps does not affect the properties.
  • Comparative Example 1 had the same alloy composition as Example 2, but did not have sufficient long-term creep resistance. It is considered that this is because the amount of solid solution of Mn decreased due to the intermediate annealing. Since Comparative Example 2 had a high Mg content, sufficient long-term creep resistance was not obtained. It is considered that this is because Mg has a high diffusion rate and softens with age. In Comparative Examples 3 and 4, since the Mn content was low, sufficient long-term creep resistance was not obtained. This is probably because when the content of Mn is low, the effect of reducing the movement speed of dislocations due to dissolved Mn cannot be obtained.
  • the aluminum alloy plate according to the embodiment of the present invention is suitable for, for example, ring-pull caps used for containers of carbonated beverages, and can provide blow-off resistance during long-term storage compared to conventional caps.

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Abstract

L'invention concerne une feuille d'alliage d'aluminium qui est une feuille laminée ayant une composition d'alliage qui contient, en pourcentage massique, de 0,50% à 1,10% de Mn, entre 2,85% et 3,48% de Mg, de 0,20% à 0,40% de Fe, de 0,05% à 0,20% de Si et de 0,01% à 0,15% de Cu, tout en contenant éventuellement un maximum de 0,10% de Ti en pourcentage massique, le reste étant constitué d'aluminium et d'impuretés inévitables. Concernant cette feuille d'alliage d'aluminium, la résistance à la traction dans la direction enroulée après un traitement thermique à 190 °C pendant 10 minutes est de 280 MPa à 320 MPa; la différence entre la résistance à la traction et la limite élastique conventionnelle est de 35 MPa ou plus; la conductivité est de 25% IACS à 34% IACS; et la vitesse de déformation au fluage après 60 à 80 heures à partir du début d'un essai de fluage à une température de matériau de 80°C avec une charge sur une pièce d'essai de 100 MPa est de 3.0 × 10-4% h-1 ou moins.
PCT/JP2022/019507 2021-05-12 2022-05-02 Feuille d'alliage d'aluminium pour capuchons à anneau de tirage et son procédé de production WO2022239694A1 (fr)

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Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0586444A (ja) * 1991-06-27 1993-04-06 Sumitomo Light Metal Ind Ltd 異方性及び耐軟化性に優れたアルミニウム合金硬質板の製造方法
JPH09291331A (ja) * 1996-02-27 1997-11-11 Kobe Steel Ltd リングプル型キャップ用アルミニウム合金板及びその製造方法
JP2011132592A (ja) * 2009-12-25 2011-07-07 Sumitomo Light Metal Ind Ltd リングプル型キャップ用アルミニウム合金板及びその製造方法

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0586444A (ja) * 1991-06-27 1993-04-06 Sumitomo Light Metal Ind Ltd 異方性及び耐軟化性に優れたアルミニウム合金硬質板の製造方法
JPH09291331A (ja) * 1996-02-27 1997-11-11 Kobe Steel Ltd リングプル型キャップ用アルミニウム合金板及びその製造方法
JP2011132592A (ja) * 2009-12-25 2011-07-07 Sumitomo Light Metal Ind Ltd リングプル型キャップ用アルミニウム合金板及びその製造方法

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