WO2014168147A1 - Feuille d'alliage d'aluminium pour formage à la presse, son procédé de fabrication et produit formé à la presse associé - Google Patents

Feuille d'alliage d'aluminium pour formage à la presse, son procédé de fabrication et produit formé à la presse associé Download PDF

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WO2014168147A1
WO2014168147A1 PCT/JP2014/060202 JP2014060202W WO2014168147A1 WO 2014168147 A1 WO2014168147 A1 WO 2014168147A1 JP 2014060202 W JP2014060202 W JP 2014060202W WO 2014168147 A1 WO2014168147 A1 WO 2014168147A1
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mass
aluminum alloy
less
press
temperature
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PCT/JP2014/060202
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English (en)
Japanese (ja)
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貴彦 中村
増田　哲也
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株式会社神戸製鋼所
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Priority to CN201480018802.3A priority Critical patent/CN105102645A/zh
Priority to MX2015014132A priority patent/MX2015014132A/es
Priority to US14/783,202 priority patent/US20160047021A1/en
Publication of WO2014168147A1 publication Critical patent/WO2014168147A1/fr

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    • 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
    • C22F1/05—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 of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions
    • 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
    • C22C21/02—Alloys based on aluminium with silicon 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
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/10—Alloys based on aluminium with zinc 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
    • 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
    • C22F1/043—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 silicon as the next major constituent

Definitions

  • the present invention relates to an aluminum alloy plate for press forming used for press forming, a manufacturing method thereof, and a press formed body thereof.
  • Al alloy materials In order to reduce the weight of transportation equipment such as automobiles, lighter aluminum alloy materials have been developed as exterior materials in place of steel materials that have been used conventionally, and are being put to practical use.
  • Patent Document 1 discloses an Al alloy plate for forming which is a 6000 series alloy and defines the particle size and density of an intermetallic compound.
  • Patent Document 2 discloses an Al alloy plate which is a 6000 series alloy and defines the texture inside the plate.
  • the present invention has been made in view of the above circumstances, and its object is to provide an aluminum alloy plate for press forming excellent in press formability that can be applied to deep press forming and a press formed body thereof. It is to be. Moreover, it is providing the manufacturing method of the aluminum alloy plate for press molding excellent in press moldability.
  • the present inventors have studied not only the composition of the Al alloy plate but also the structure of the alloy plate, etc. As a result, the direction of elongation of the plate material during press forming is in any direction. However, in order to be able to cope with this, it was thought that it is important that the stretchability is not direction-dependent, in other words, it has excellent isotropy during molding.
  • the ratio of the diagonal length of the indentation in the Vickers hardness tester is effective as an isotropic index in the formability of the Al alloy plate.
  • the Al alloy plate having excellent isotropy at the time of forming has not only a large overhang height in the overhang forming, but also a low ear rate and is difficult to generate ridging marks. Furthermore, it came to discover that it was excellent also in BH property (bake hard property) which an intensity
  • BH property bake hard property
  • the Al alloy plate for press forming according to the present invention contains Si: 0.4 to 1.5 mass%, Mg: 0.3 to 1.0 mass%, and the balance is made of Al and inevitable impurities.
  • the ratio P (%) to L0 is 2.0% or less.
  • the Al alloy preferably contains Si: 0.6 to 1.3% by mass, Mg: 0.3 to 0.8% by mass, and the balance is made of Al and inevitable impurities.
  • the aluminum alloy constituting the aluminum alloy plate for press forming according to the present invention further contains Cu: 1.0% by mass or less, Fe: 0.5% by mass or less, and Mn: 0.5% by mass. Including at least one of Cr: 0.3% by mass or less, Zr: 0.3% by mass or less, and Ti: containing 0.3% by mass or less, Zn: It is possible to regulate to 0.5% by mass or less. According to the said structure, it becomes possible to further improve a moldability.
  • the method for producing an Al alloy sheet for press forming according to the present invention comprises a homogenization heat treatment step for subjecting an ingot of Al alloy having the above composition to a homogenization heat treatment, and a condition that the end temperature of hot rolling is 300 ° C. or less.
  • the method for producing an Al alloy plate for press forming according to the present invention includes a homogenization heat treatment step for subjecting an ingot of the Al alloy having the above composition to a homogenization heat treatment step, and a hot rolling step for subjecting the hot rolling step, A first cold rolling step in which cold rolling is performed at a cold rolling end temperature of 100 ° C. or lower, an intermediate annealing step in which intermediate annealing is performed at a temperature of 300 to 500 ° C., and a cold rolling at a cold rolling end temperature of 100 ° C. or lower.
  • the second cold rolling process is performed in this order, the solution treatment process is performed at a temperature of 500 ° C. or higher, and the heating process is performed in this order.
  • the Al alloy preferably contains Si: 0.6 to 1.3% by mass, Mg: 0.3 to 0.8% by mass, and the balance is made of Al and inevitable impurities.
  • the Al alloy further contains Cu: 1.0% by mass or less, Fe: 0.5% by mass or less, and Mn: 0.00%. At least one of 5% by mass or less, Cr: 0.3% by mass or less, Zr: 0.3% by mass or less, and Ti: 0.3% by mass or less In addition, it is possible to regulate the Zn content to 0.5% by mass or less.
  • the manufacturing method of the said structure it becomes possible to manufacture the Al alloy plate for press molding excellent in the isotropy in a forming process from Al alloy which has the said composition. Moreover, an Al alloy press-formed body can be obtained by press-forming the Al alloy plate for press forming according to the present invention.
  • the Al alloy plate for press molding of the present invention can cope with deep press molding, has a small ear rate, and is excellent in ridging mark properties.
  • the method for producing an Al alloy plate for press forming according to the present invention can produce an Al alloy plate having excellent isotropy in forming.
  • composition of the Al alloy constituting the Al alloy plate for press forming of the present invention contains Si: 0.4 to 1.5 mass%, Mg: 0.3 to 1.0 mass%, with the balance being Al and inevitable. Consists of impurities. Each element constituting the Al alloy of the present invention and its content will be described below.
  • Si 0.4-1.5% by mass
  • Si can form aging precipitates that contribute to strength improvement during solid solution strengthening and artificial aging treatment at low temperatures such as paint baking treatment, and the strength (proof strength) required for automotive exterior panels ) Is an essential element.
  • the Si content is less than 0.4% by mass, the formation of aging precipitates is small, and the paint bake hardenability (strength) decreases.
  • the content of Si exceeds 1.5% by mass, coarse crystallized products and precipitates are formed, and press formability and weldability deteriorate. Therefore, the Si content is 0.4 to 1.5 mass%. Preferably, it is 0.6 to 1.3% by mass.
  • Mg 0.3-1.0% by mass
  • Si can form aging precipitates that contribute to strength improvement during low-temperature artificial aging treatment such as solid solution strengthening and paint baking treatment, and the strength (proof strength) required for automotive exterior panels ) Is an essential element. If the Mg content is less than 0.3% by mass, the formation of aging precipitates is small, and the paint bake hardenability (strength) decreases. On the other hand, if the Mg content exceeds 1.0% by mass, coarse crystallized substances and precipitates are formed, and the press formability and weldability deteriorate. Therefore, the Mg content is set to 0.3 to 1.0% by mass. Preferably, the content is 0.3 to 0.8% by mass.
  • Cu 1.0% by mass or less
  • Cu has the effect of promoting the formation of aging precipitates under conditions of artificial aging treatment at a relatively low temperature for a short time
  • solid solution Cu is an element that can improve the formability.
  • the Cu content is preferably 0.1% by mass or more.
  • the content of Cu is 1.0% by mass or less.
  • the content is preferably 0.1 to 0.8% by mass.
  • Fe 0.5% by mass or less
  • Fe forms crystallized materials such as FeMnAl 6 and AlMnFeSi phases together with Mn during casting and homogenization heat treatment, and acts as a recrystallization nucleus during hot rolling and final solution treatment. It is an effective element for randomizing textures. If the Fe content exceeds 0.5% by mass, a coarse crystallized product is generated, and the press formability deteriorates. Therefore, when Fe is contained, the content of Fe is 0.5% by mass or less. Preferably, the content is 0.1 to 0.3% by mass.
  • Mn (Mn: 0.5% by mass or less) Mn generates crystallized materials such as FeMnAl 6 and AlMnFeSi phases together with Fe during casting and homogenization heat treatment, and acts as a recrystallization nucleus during hot rolling and final solution treatment, and refines the recrystallized grains It is an effective element for randomizing textures.
  • Mn When the content of Mn exceeds 0.5% by mass, a coarse crystallized product is generated and press formability is lowered. Therefore, when Mn is contained, the Mn content is 0.5% by mass or less.
  • the content is preferably 0.1 to 0.4% by mass.
  • Cr 0.3% by mass or less
  • Cr is an element that has the action of generating dispersed particles (dispersed phase) during the homogenization heat treatment to refine crystal grains.
  • the content of Cr exceeds 0.3% by mass, a coarse intermetallic compound is generated, and press formability and corrosion resistance are lowered. Therefore, when Cr is contained, the Cr content is 0.3 mass% or less.
  • the content is 0.01 to 0.2% by mass.
  • Zr 0.3% by mass or less
  • Zr is an element that has the effect of generating dispersed particles (dispersed phase) during the homogenization heat treatment to refine crystal grains.
  • the content of Zr exceeds 0.3% by mass, a coarse intermetallic compound is generated, and press formability and corrosion resistance are lowered. Therefore, when Zr is contained, the content of Zr is set to 0.3% by mass or less.
  • the content is 0.05 to 0.2% by mass.
  • Ti 0.3% by mass or less
  • Ti is an element that refines the crystal grains of the ingot and improves the press formability.
  • the content of Ti is set to 0.3% by mass or less.
  • the content is 0.01 to 0.2% by mass.
  • Zn 0.5% by mass or less
  • inevitable impurities As inevitable impurities other than the above Cu, Fe, Mn, Cr, Zr, Ti, and Zn, elements such as Sn, Sc, Ni, C, In, Na, Ca, V, Bi, and Sr can be assumed. Any of these may be contained at a level that does not inhibit the features of the present invention. Specifically, the total content of elements of Cu, Fe, Mn, Cr, Zr, Ti, Zn and inevitable impurities is preferably 1.0% by mass or less.
  • Vickers hardness is a measurement method for measuring the hardness of a metal material described in JIS Z2244. This is a test in which the hardness of the sample is measured from the size of the resulting indentation (dent) by pressing a square pyramidal diamond indenter into the test surface of the sample with a constant test load. When the indentation is viewed in plan, it becomes almost square, and there are two diagonal lines.
  • the difference in the length of the diagonal line due to the difference in the angle with respect to the rolling direction is used as an isotropic index in the formability of the Al alloy sheet.
  • the diagonal length of the indentation by the Vickers hardness meter of the Al alloy plate for press forming is 45 ° or ⁇ 45 ° (135 °) with respect to the rolling direction.
  • / L0 100 ⁇ ⁇ L / L0 (1)
  • the diagonal length (L0) of the impression that is 0 ° or 90 ° with respect to the rolling direction is simplified as follows. It may be described as “0 ° diagonal length L0”.
  • the diagonal length (L45) of the indentation that is 45 ° or ⁇ 45 ° (135 °) with respect to the rolling direction is simplified below. It may be described as “diagonal length L45 of 45 ° with respect to the rolling direction”.
  • the ratio P needs to be 2.0% or less. That is, in the diagonal length of the indentation by the Vickers hardness tester, the difference L0 between the diagonal length L0 of 0 ° with respect to the rolling direction and the diagonal length L45 of 45 ° with respect to the rolling direction is L0. It is necessary that the ratio P (%) to 2.0% or less.
  • the alloy is an Al alloy having the above-mentioned specific composition, and the following specific manufacturing conditions are adopted, and the anisotropy of the crystal structure inside the Al alloy plate It is necessary to eliminate
  • the method of measuring the diagonal length of the indentation is as follows.
  • the indentation by the Vickers hardness tester is created along the rolling direction (RD direction) near the center of the width of the sample. At least three indentations are made on each of the diagonals so that the diagonal line is 0 ° (90 °) or 45 ° ( ⁇ 45 °) with respect to the rolling direction.
  • the surface to be indented may be attached to the surface of the Al alloy plate or may be attached to the cross section of the Al alloy plate.
  • the indentation diagonal length is determined by taking a photograph of a plurality of indentations from above using a microscope, measuring the two diagonal lengths of each indentation from the obtained planar image, and averaging the measured values. Calculate as a value.
  • the load of the Vickers hardness meter can be appropriately set according to the hardness of the sample.
  • the manufacturing method according to the present invention is characterized in that the anisotropy of the crystal structure in the plate material is eliminated by finely recrystallizing in an annealing process provided after the hot rolling process in a state where strain is accumulated. It is what has.
  • FIG. 1 is a flowchart showing manufacturing steps of a first embodiment of a method for manufacturing a press-formed Al alloy plate according to the present invention.
  • FIG. 2 is a flowchart showing manufacturing steps of the second embodiment of the method for manufacturing a press-formed Al alloy plate according to the present invention.
  • the first embodiment of the method for producing an Al alloy sheet for press forming according to the present invention contains Si: 0.4 to 1.5 mass%, Mg: 0.3 to 1.0 mass%, with the balance being Al and A casting process for casting an Al alloy composed of inevitable impurities, a homogenization heat treatment process for subjecting the ingot of the Al alloy to a homogenization heat treatment, and hot rolling under conditions where the end temperature of the hot rolling is 300 ° C. or less.
  • a solution treatment step and a heating step of heating to a temperature of 70 ° C. or higher are performed in this order.
  • the casting step S1 is a step for producing an Al alloy ingot by melting and casting an Al alloy for press forming.
  • an ingot having a predetermined shape is produced from a molten metal in which an Al alloy having the above composition is melted.
  • the method for melting and casting the Al alloy is not particularly limited, and a conventionally known method may be used. For example, it can melt
  • the homogenization heat treatment step S2 is performed in order to make the entire structure uniform because the structure is not uniform depending on the location simply by casting.
  • the starting temperature for the homogenization heat treatment is preferably 500 to 580 ° C. If it is less than 500 ° C., it takes time until it becomes uniform, so that the productivity is lowered. If it exceeds 580 ° C., local melting may occur due to the melting point of the segregation part being lowered.
  • the homogenization heat treatment time is preferably 1 to 10 hours. If the homogenization heat treatment time is less than 1 hour, segregation may not be lost. On the other hand, when it exceeds 10 hours, productivity will fall.
  • the hot rolling step S3 is a step of performing hot rolling to obtain a predetermined thickness after the homogenization heat treatment step S2. In the temperature decreasing process, the process is repeated until a predetermined thickness is reached.
  • the starting temperature of hot rolling is preferably 400 to 550 ° C. Rolling is performed at a high temperature in order to obtain a predetermined plate thickness with as few rolling reductions as possible. If the starting temperature of hot rolling is low, rolling becomes difficult because of high deformation resistance. On the other hand, if the starting temperature of hot rolling is too high, it will cause coarse recrystallization of the surface and cause rough skin of the final product.
  • Hot rolling can be performed in a range of about 30 to 50% of hot working rate (rolling rate) in one pass, as in the case of hot rolling of a general aluminum material.
  • the rolling reduction in hot rolling is preferably 30 to 40%. This is because by performing within this range, the amount of heat generated during hot rolling is reduced, and the amount of strain accumulation is increased.
  • the finishing temperature of the hot rolling finishing process needs to be 300 ° C. or lower. More preferably, it is 170 to 290 ° C.
  • the end temperature of hot rolling exceeds 300 ° C, the accumulated amount of strain is insufficient, so that recrystallization does not occur finely in the annealing process, and only a specific crystal orientation develops, resulting in a bias in the direction of deformation.
  • the Al plate cannot have a highly isotropic structure.
  • the annealing step S4 is a step for performing annealing.
  • the finishing step of the hot rolling step S3 since the end temperature of the hot rolling is set to 300 ° C. or less, strain is accumulated in the crystal structure inside the Al plate.
  • the annealing step S4 by releasing the strain without applying a restraining force, the crystal structure in the Al plate can be made to have a highly isotropic structure with little strain in any direction.
  • the annealing temperature must be 300 to 500 ° C. When the temperature is lower than 300 ° C., recrystallization may not occur. When the temperature exceeds 500 ° C., crystal grain coarsening may occur.
  • the annealing time is preferably more than 0 seconds in the case of a continuous furnace and 30 seconds or less, and in the case of a batch furnace, 5 hours or less. If the length is too long, crystal grain coarsening occurs and anisotropy increases. In addition, since the rate of temperature rise is fast, it is preferable to use a continuous furnace that is easy to recrystallize finely and set the rate of temperature rise to 1 ° C./second or more.
  • Cold rolling process S5 is a process which performs cold rolling. After the annealing step S4, cold rolling is performed once or a plurality of times to obtain a desired final thickness.
  • the cold working rate is preferably 40% or more. When the cold working rate is less than 40%, the effect of crystal grain refinement during solution formation may not be sufficiently obtained.
  • the end temperature of cold rolling needs to be 100 ° C. or lower, and preferably 80 ° C. or lower. When the cold rolling finish temperature is high, the accumulated amount of strain is insufficient, the solution treatment process does not recrystallize finely, and only a specific crystal orientation develops, causing a bias in a direction that tends to deform, etc. New organization cannot be obtained.
  • the cold rolling end temperature refers to the temperature at which the final cold rolling is completed when the cold rolling is performed a plurality of times. Further, after the cold rolling is completed, cold rolling at a low processing rate such as skin pass rolling for correcting the flatness of the plate and rolling using an EDT (electric discharge textured) roll for controlling the surface roughness may be performed. good.
  • Solution treatment process S6 is a process required in order to solidify Mg and Si and to ensure the yield strength after baking.
  • the solution temperature must be 500 ° C. or higher, and preferably 500 to 570 ° C. If the solution temperature is less than 500 ° C., the amount of solid solution may be insufficient, and if it exceeds 570 ° C., eutectic melting or recrystallization grain coarsening may occur.
  • the solution time is preferably more than 0 seconds and 60 seconds or less. If the solution time is too long, the effect is saturated and the economy is impaired. In cooling after reaching the heating temperature, if the cooling rate is slow, coarse Mg 2 Si, Si, etc. are likely to be precipitated at the grain boundary, and the formability is lowered. Therefore, cooling can be performed by water cooling (water quenching) or the like. preferable.
  • the heating step S7 is a step of reducing the amount of change due to room temperature aging and ensuring the yield strength after baking.
  • the heating temperature needs to be 70 ° C. or higher, and preferably 70 to 150 ° C. When kept below 70 ° C., the increase in strength after baking is reduced. If it exceeds 150 ° C., the initial strength becomes too high and the moldability deteriorates.
  • the second embodiment of the method for producing an Al alloy sheet for press forming according to the present invention contains Si: 0.4 to 1.5 mass%, Mg: 0.3 to 1.0 mass%, with the balance being Al and A casting process for casting an Al alloy composed of inevitable impurities, a homogenization heat treatment process for subjecting the ingot of the Al alloy to a homogenization heat treatment, a hot rolling process for hot rolling, and a cold rolling end temperature of 100
  • a rolling process, a solution treatment process that is performed at a temperature of 500 ° C. or higher, and a heating process that is heated to a temperature of 70 ° C. or higher are performed in this order.
  • the casting step S1, the homogenization heat treatment step S2, the solution treatment step S6, and the heating step S7 have the same conditions as those in the first embodiment of the manufacturing method. Description of is omitted.
  • the hot working rate (rolling rate) and the starting temperature during hot rolling are the same as those in the first embodiment.
  • finish temperature of the finishing process of hot rolling 400 degrees C or less is preferable from a viewpoint of production efficiency.
  • the cold working step S5a is a step of performing cold rolling after the hot rolling step S3. After the hot rolling step S3 is completed, cold rolling is performed once or a plurality of times to obtain a desired final thickness.
  • the cold working rate is preferably 40% or more, and more preferably 50% or more.
  • the end temperature of cold rolling needs to be 100 ° C. or lower, and preferably 80 ° C. or lower. When deviating from these ranges, a fine recrystallized structure cannot be obtained in the intermediate annealing step.
  • the intermediate annealing step S4a is a step of performing intermediate annealing after the first cold rolling step S5a.
  • strain is accumulated in the crystal structure inside the Al plate.
  • the intermediate annealing step S4a by releasing this strain without applying a restraining force, the crystal structure in the Al plate can be made to have a highly isotropic structure with little strain in any direction. .
  • the intermediate annealing temperature must be 300 to 500 ° C. When the temperature is lower than 300 ° C., recrystallization may not occur. When the temperature exceeds 500 ° C., crystal grain coarsening may occur.
  • the intermediate annealing time is preferably more than 0 seconds and 30 seconds or less in the case of a continuous furnace, and 5 hours or less in the case of a batch furnace. If the length is too long, crystal grain coarsening occurs and anisotropy increases. In addition, since the rate of temperature rise is fast, it is preferable to use a continuous furnace that is easy to recrystallize finely and set the rate of temperature rise to 1 ° C./second or more.
  • the second cold rolling step S5b is a step of performing cold rolling after the intermediate annealing step S4a. After the annealing step S4, cold rolling is performed once or a plurality of times to obtain a desired final thickness.
  • the cold working rate is preferably 40% or more. When the cold working rate is less than 40%, the effect of crystal grain refinement during solution formation may not be sufficiently obtained.
  • the end temperature of cold rolling needs to be 100 ° C. or lower, and preferably 80 ° C. or lower.
  • the cold rolling end temperature refers to the temperature at which the final cold rolling is completed when the cold rolling is performed a plurality of times. Further, after the cold rolling is completed, cold rolling at a low rolling rate such as skin pass rolling for correcting the flatness of the plate or rolling using an EDT (electric discharge textured) roll for controlling the surface roughness may be performed. good.
  • the Al alloy plate for press molding obtained through the manufacturing process having the above steps can have excellent press formability as an Al alloy plate for press molding.
  • Sample numbers 1 to 27 are all aluminum alloy plates manufactured by the first embodiment of the manufacturing method.
  • An Al alloy (alloy symbols A to Z) having the composition shown in Table 1 to be described later was melted and cast by a known casting method such as a DC casting method to form an ingot having a thickness of 600 mm.
  • the ingot was subjected to a homogenization heat treatment at 550 ° C. for 5 hours.
  • the ingots subjected to the heat treatment were repeatedly subjected to hot rolling at a rolling rate of 30 to 40% at a hot rolling start temperature of 500 ° C. for sample numbers 1 to 25 and sample number 27 to reduce the plate thickness.
  • a hot rolled plate having a hot rolling finish temperature of 270 ° C. and a thickness of 3 mm was obtained.
  • the hot rolling end temperature was changed to 285 ° C. to obtain a hot rolled plate having a plate thickness of 3 mm.
  • sample numbers 1 to 25 were annealed at 500 ° C. for 20 seconds using a continuous furnace.
  • Sample No. 26 was annealed at 350 ° C. for 20 seconds using a continuous furnace.
  • Sample No. 27 was annealed at 400 ° C. for 4 hours using a batch furnace. Thereafter, the sample Nos. 1 to 27 were cold-rolled at a cold working rate (reduction rate) of 66% to obtain cold-rolled plates having a cold rolling end temperature of 90 ° C. and a plate thickness of 1 mm.
  • a continuous furnace it was heated at a heating rate of 300 ° C./min, and when it reached 550 ° C., it was held for 20 seconds to perform solution treatment.
  • Sample numbers 28 to 32 are all aluminum alloy plates manufactured by the second embodiment of the manufacturing method.
  • alloys having the composition shown in Table 1 to be described later alloys having the alloy symbols A, E, and M are used, and in the same manner as Sample Nos. 1, 5, and 13, by a known casting method such as a DC casting method. , Melting and casting to form an ingot having a thickness of 600 mm.
  • the ingot was subjected to a homogenization heat treatment at 550 ° C. for 5 hours.
  • the ingots subjected to the heat treatment were repeatedly subjected to hot rolling at a rolling rate of 30 to 40% at a hot rolling start temperature of 500 ° C. for sample numbers 28 to 30 and sample number 32 to reduce the plate thickness.
  • a hot rolled sheet having a hot rolling end temperature of 250 ° C. and a thickness of 7 mm was obtained.
  • the hot rolling end temperature was changed to 330 ° C. to obtain a hot rolled plate having a thickness of 7 mm.
  • the first cold rolling was performed at a cold working rate (rolling rate) of 57% at a cold rolling end temperature of 90 ° C. or less shown in Table 2 to be described later, and a cold rolled plate having a thickness of 3 mm. It was. Thereafter, Sample Nos. 28 to 31 were subjected to intermediate annealing at 500 ° C. for 20 seconds using a continuous furnace. Sample No. 32 was subjected to intermediate annealing at 400 ° C. for 5 hours using a batch furnace. Thereafter, the sample Nos. 28 to 32 were each subjected to the second cold rolling at a cold rolling reduction rate (rolling rate) of 67% at a cold rolling end temperature of 90 ° C.
  • Sample No. 33 was processed under the same conditions as Sample No. 30 except that the first and second cold rolling end temperatures were changed to 120 ° C. in Sample No. 30.
  • Sample No. 34 was processed under the same conditions as Sample No. 30 except that Sample No. 30 had a first cold rolling end temperature of 120 ° C.
  • Sample No. 35 was processed under the same conditions as Sample No. 30 except that the second cold rolling end temperature was 120 ° C. in Sample No. 30.
  • Sample No. 36 was processed under the same conditions as Sample No. 13 except that the end temperature of the hot rolling step was changed to 330 ° C. in Sample No. 13.
  • Sample No. 37 was processed under the same conditions as Sample No. 13 except that the cold rolling end temperature was 110 ° C. in Sample No. 13.
  • Sample No. 38 was processed under the same conditions as Sample No. 30 except that Sample No. 30 was not subjected to the intermediate annealing step.
  • Sample No. 39 was the same as Sample No. 1 except that the end temperature of the hot rolling process was 250 ° C. in Sample No. 1 and was annealed at 280 ° C. for 4 hours using a batch furnace. Processing was performed.
  • Sample No. 40 was processed under the same conditions as Sample No. 5 except that the end temperature of the hot rolling step was 250 ° C. and the annealing temperature was 600 ° C. in Sample No. 5.
  • the evaluation conditions of the characteristics of the Al alloy plate obtained after being left for 3 months after the heating step are as follows.
  • FIGS. 3 to 5 show the indentation diagonal line of the Vickers hardness tester with a diagonal length L0 of 0 ° or 90 ° with respect to the rolling direction and a diagonal length of 45 ° or ⁇ 45 ° (135 °) with respect to the rolling direction. It is a schematic diagram for demonstrating the method to measure length L45.
  • FIG. 3 shows an example of a location where an indentation is formed.
  • the diagonal of the indentation is at an angle of 0 ° or 90 ° with respect to the rolling direction at the center of the plate cross section along the rolling direction (RD direction) of the sample taken from the center in the width direction of the plate (A1 to A3)
  • RD direction rolling direction
  • the diagonal of the indentation is at an angle of 45 ° or ⁇ 45 ° (135 °) with respect to the rolling direction (B1 to B3)
  • at least three indentations having a substantially square shape are made with a Vickers hardness meter.
  • the load of the Vickers hardness tester was 100 g.
  • the indentation was imprinted on the cross section of a 1 mm thick specimen left for 3 months after the heating process.
  • the photograph is taken using the auto-focus function of the microscope integrated with the device.
  • FIG. 4 and 5 show an example of measuring a diagonal line from a photograph of an indentation. The length of two diagonals is measured from one impression photo.
  • FIG. 4 shows a case where the diagonal line of the indentation is at an angle of 0 ° or 90 ° with respect to the rolling direction.
  • the lengths a1 and a2 are respectively measured and averaged as the diagonal lengths L0 of 0 ° and 90 ° with respect to the rolling direction (RD direction).
  • FIG. 5 shows the case where the diagonal line of the indentation is at an angle of + 45 ° or ⁇ 45 ° (135 °) with respect to the rolling direction.
  • the lengths of b1 and b2 are measured and averaged values are used. Measure at least three indentations, respectively, and calculate the average value of the obtained diagonal lengths.
  • the difference ⁇ L between the diagonal length L0 of 0 ° with respect to the rolling direction and the diagonal length L45 of 45 ° with respect to the rolling direction is determined.
  • the ratio P (%) of the difference ⁇ L between the lengths to the diagonal length L0 of 0 ° with respect to the rolling direction is obtained. When this value was 2.0% or less, it was judged that there was little anisotropy and the moldability was excellent.
  • AB proof stress is an index for BH properties (bake hardness, paint bake hardenability) that improve strength and yield strength by artificial aging treatment such as paint baking after press molding.
  • a relatively low temperature treatment such as paint baking
  • it is age-hardened by heating at that time, and the strength and proof stress are improved. This degree of improvement is expressed as an index.
  • heat treatment was performed at 170 ° C. for 20 minutes in a state where 2% strain (stretch) simulating press molding was applied in advance.
  • a tensile test was performed with a floor-mounted universal tensile tester AG-I manufactured by SHIMADZU CORPORATION to measure 0.2% proof stress (AB proof stress) (MPa).
  • the crosshead speed was 5 mm / min, and the test piece was measured at a constant speed until the test piece broke. It was judged that the AB yield strength was excellent when it was 170 MPa or more.
  • Ear rate (%) [ ⁇ (h0 + h90 + h180 + h270) ⁇ (h45 + h135 + h225 + h315) ⁇ / ⁇ 1/2 (h0 + h90 + h180 + h270 + h45 + h135 + h225 + h315) ⁇ ] ⁇ 100 (2)
  • the ear ratio was 3.5% or less, the deformation amount in the 0 °, 90 ° direction, and 45 ° direction with respect to the rolling direction was not significantly different, and it was judged that the moldability and the yield were excellent. .
  • FIG. 6 is a cross-sectional view for explaining the measuring method of the stretch formability tester. Instead of evaluating the presence or absence of cracks in press working of an aluminum alloy plate, the limit overhang height by ball head overhang forming was evaluated.
  • the test plate 13 was cut into a length of 110 mm in the rolling direction and a length of 200 mm in the direction perpendicular to the rolling. As shown in FIG. 6, the test plate 13 is fixed to a die 10 having an inner diameter (hole diameter) of 102.8 mm, a shoulder radius Rd: 5.0 mm, and an outer diameter of 220 mm using a jig (blank holder) 11. Fixed with the wrinkle holding force.
  • a ball head punch 12 having a ball head diameter of 100 mm (radius Rp: 50 mm) was tested while keeping the gap between the die and the jig constant by sandwiching a shim (not shown) having the same thickness as the test piece.
  • An overhanging process was performed by pushing in the direction perpendicular to the plate surface, and the limit value of the overhang height H until cracking or constriction was observed was determined.
  • the overhang height H having a limit value of 30 mm or more was judged to be acceptable.
  • the plate after applying the strain in advance is sequentially subjected to a colloidal dispersion treatment of titanium phosphate and a zinc phosphate treatment in which the plate is immersed in a zinc phosphate bath containing a low concentration (50 ppm) of fluorine.
  • a heat treatment was performed at 170 ° C. for 20 minutes. The coating surface was evaluated as ⁇ when no ridging marks were generated, ⁇ when ridging marks were generated but relatively light, and ⁇ when ridging marks were significantly generated.
  • sample numbers 1 to 25 are shown in Table 1.
  • the evaluation results of sample numbers 1, 5, 13, and 26 to 40 are shown in Table 2.
  • the composition indicated by “ ⁇ ” indicates that it is below the detection limit of the analyzer.
  • the numerical value underlined indicates that the numerical value is outside the numerical range of Claim 1 or Claims 2 to 3.
  • Sample numbers 1, 5, and 13 in Table 2 are the same as sample numbers 1, 5, and 13 in Table 1.
  • Al alloy sheets for press forming (sample numbers 1 to 15) made of an Al alloy satisfying the provisions of the alloy composition of the present invention are tensile strength, proof stress, tensile elongation, AB proof strength, ear rate. In addition, it had excellent performance in any physical properties of the overhang height.
  • all of the Al alloy plates for press forming (sample numbers 16 to 25) made of an Al alloy not satisfying the provisions of the present invention were inferior in the overhang height.
  • sample numbers 17, 18, 20, and 21 were inferior in performance of any one or more of tensile strength, yield strength, tensile elongation, AB yield strength, and ear rate.
  • the Al alloy plates for press forming (sample numbers 1, 5, 13, 26 to 32) made of an Al alloy that satisfies the provisions relating to the production method of the present invention have tensile strength, proof stress, tensile strength. It had excellent performance in all physical properties such as elongation, AB yield strength, ear rate, overhang height, and ridging mark property. In particular, performance such as the overhang height has been further improved by applying a process in which the end temperature of cold rolling is set to 100 ° C. or less and the annealing process or the intermediate annealing process is performed as the manufacturing conditions.
  • sample numbers 13 and 27 and sample numbers 30 and 32 are respectively a case where a case where a continuous furnace is used and a case where a batch type furnace is used are compared in the annealing process.
  • An Al alloy sheet for press molding having superior performance was obtained by using a continuous furnace.
  • the Al alloy plates for press forming (sample numbers 33 to 39) made of an Al alloy that satisfies the composition of the present invention as a production condition although the composition of the Al alloy is satisfied, all have a ratio P of 2.0%. It was inferior in the performance of any one or more of ear rate, overhang height and ridging mark property. Since Sample No. 40 had a high annealing temperature, it could not be obtained by dissolving at the time of annealing. For sample numbers 33 to 35, either the first cold rolling end temperature, the second cold rolling end temperature, or both exceeded 100 ° C. in the second embodiment of the manufacturing method, and the accumulation of strain was small. Thus, the ratio P exceeded 2.0%, and the isotropy was insufficient. In sample No.
  • the end temperature of the hot rolling process in the first embodiment of the manufacturing method exceeds 300 ° C., the accumulation of strain is reduced, the crystal is not recrystallized finely, and the ratio P is 2.0%.
  • the isotropy was insufficient.
  • the cold rolling end temperature is over 100 ° C., the accumulation of strain is reduced and the crystal is not recrystallized finely, the ratio P is over 2.0%, etc.
  • the directivity was insufficient.
  • Sample No. 38 was manufactured without performing the annealing step, and it was not recrystallized finely, the ratio P exceeded 2.0%, and the isotropy was insufficient.
  • Sample No. 39 is the first embodiment of the manufacturing method, the annealing temperature is less than 300 ° C., it does not recrystallize finely, the ratio P exceeds 2.0%, and the isotropic property is insufficient. It was.
  • the aluminum alloy plate of the present invention is useful as a material for automotive exterior plate materials such as bodies, doors, and fenders, and has excellent formability that can be applied to deep press forming.

Abstract

La présente invention concerne une feuille d'alliage d'aluminium pour formage à la presse, ladite feuille d'alliage d'aluminium étant fabriquée d'un alliage d'aluminium qui contient 0,4 à 1,5 % en masse de Si et 0,3 à 1,0 % en masse de Mg, le complément étant Al et les impuretés inévitables et présentant un rapport (P(%)) de ΔL à L0 de 2,0 % ou moins [où : L0 est la longueur d'une ligne diagonale s'étendant à un angle de 0° par rapport à la direction de laminage dans une indentation formée dans un appareil pour essais de dureté Vickers ; et ΔL est une différence entre L0 et la longueur (L45) d'une ligne diagonale s'étendant à un angle de 45° par rapport à la direction de laminage dans celle-ci]. En outre, la présente invention concerne un procédé de fabrication de la feuille d'alliage d'aluminium et un produit formé à la presse associé.
PCT/JP2014/060202 2013-04-09 2014-04-08 Feuille d'alliage d'aluminium pour formage à la presse, son procédé de fabrication et produit formé à la presse associé WO2014168147A1 (fr)

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MX2015014132A MX2015014132A (es) 2013-04-09 2014-04-08 Lamina de aleacion de aluminio para formacion por prensado, proceso para manufactura del mismo, y producto formado por prensado del mismo.
US14/783,202 US20160047021A1 (en) 2013-04-09 2014-04-08 Aluminum alloy sheet for press forming, process for manufacturing same, and press-formed product thereof

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