WO2014168147A1 - Aluminum alloy sheet for press forming, process for manufacturing same, and press-formed product thereof - Google Patents
Aluminum alloy sheet for press forming, process for manufacturing same, and press-formed product thereof Download PDFInfo
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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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- 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
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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
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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
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
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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
- C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
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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
- C22C21/10—Alloys based on aluminium with zinc as the next major constituent
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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
- C22F1/043—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.
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Abstract
Description
ボディ、ドア、フェンダなどの自動車用外装用の板材の素材として、アルミニウム合金(以下、「Al合金」とも記載する。)の中でも、強度、耐食性に優れたAl-Mg-Si系の6000系Al合金が検討されている。 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.
As a material for automotive exterior panel materials such as bodies, doors, and fenders, Al-Mg-Si based 6000 series Al, which is excellent in strength and corrosion resistance, among aluminum alloys (hereinafter also referred to as "Al alloys"). Alloys are being considered.
前記構成によれば、成形性をさらに向上させることが可能となる。 Further, 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.
また、上記のAl合金が、Si:0.6~1.3質量%、Mg:0.3~0.8質量%を含有し、残部がAlおよび不可避的不純物からなることが好ましい。 Alternatively, 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.
また、本発明に係るプレス成形用Al合金板をプレス成形することにより、Al合金プレス成形体を得ることができる。 According to 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.
本発明のAl合金を構成する各元素とその含有量について、以下に説明する。 The 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は、Mgとともに、固溶強化と、塗装焼き付け処理などの低温での人工時効処理時に、強度向上に寄与する時効析出物を形成させることができ、自動車の外装用パネルとして必要な強度(耐力)を付与するために必須な元素である。Siの含有量が0.4質量%未満であると、時効析出物の形成が少なく、塗装焼付け硬化性(強度)が低下する。一方、Siの含有量が1.5質量%を超えると、粗大な晶出物および析出物が形成され、プレス成形性や溶接性が低下する。したがって、Siの含有量は0.4~1.5質量%とする。好ましくは0.6~1.3質量%である。 (Si: 0.4-1.5% by mass)
Si, together with Mg, 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. When the Si content is less than 0.4% by mass, the formation of aging precipitates is small, and the paint bake hardenability (strength) decreases. On the other hand, when 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は、Siとともに、固溶強化と、塗装焼き付け処理などの低温での人工時効処理時に、強度向上に寄与する時効析出物を形成させることができ、自動車の外装用パネルとして必要な強度(耐力)を付与するために必須な元素である。Mgの含有量が0.3質量%未満であると、時効析出物の形成が少なく、塗装焼付け硬化性(強度)が低下する。一方、Mgの含有量が1.0質量%を超えると、粗大な晶出物および析出物が形成され、プレス成形性や溶接性が低下する。したがって、Mgの含有量は0.3~1.0質量%とする。好ましくは0.3~0.8質量%である。 (Mg: 0.3-1.0% by mass)
Mg, together with 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は、比較的低温短時間の人工時効処理の条件で、時効析出物の形成を促進させる効果を有しており、固溶したCuは、成形性を向上させることができる元素である。上記の効果を期待するためには、Cuの含有量は、0.1質量%以上であることが好ましい。一方、Cuの含有量が1.0質量%を超えると、耐応力腐食割れ性、耐糸さび性および溶接性が著しく劣化する。したがって、Cuを含有させる場合は、Cuの含有量は1.0質量%以下とする。好ましくは0.1~0.8質量%である。 (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, and solid solution Cu is an element that can improve the formability. In order to expect the above effect, the Cu content is preferably 0.1% by mass or more. On the other hand, if the Cu content exceeds 1.0% by mass, the stress corrosion cracking resistance, the thread rust resistance and the weldability are significantly deteriorated. Therefore, when Cu is contained, the content of Cu is 1.0% by mass or less. The content is preferably 0.1 to 0.8% by mass.
Feは、鋳造時や均質化熱処理時に、Mnとともに、FeMnAl6、AlMnFeSi相などの晶出物を生成させ、熱間圧延中および最終溶体化処理時に再結晶核として働き、再結晶粒の微細化、集合組織のランダム化に有効な元素である。Feの含有量が0.5質量%を超えると、粗大な晶出物が生成し、プレス成形性が低下する。したがって、Feを含有させる場合は、Feの含有量は0.5質量%以下とする。好ましくは0.1~0.3質量%である。 (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は、鋳造時や均質化熱処理時に、Feとともに、FeMnAl6、AlMnFeSi相などの晶出物を生成させ、熱間圧延中および最終溶体化処理時に再結晶核として働き、再結晶粒の微細化、集合組織のランダム化に有効な元素である。Mnの含有量が0.5質量%を超えると、粗大な晶出物が生成し、プレス成形性が低下する。したがって、Mnを含有させる場合は、Mnの含有量は0.5質量%以下とする。好ましくは0.1~0.4質量%である。 (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. 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は、均質化熱処理時に分散粒子(分散相)を生成し、結晶粒を微細化する作用を有する元素である。Crの含有量が0.3質量%を超えると、粗大な金属間化合物が生成し、プレス成形性および耐食性が低下する。したがって、Crを含有させる場合は、Crの含有量は0.3質量%以下とする。好ましくは0.01~0.2質量%である。 (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. When 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. Preferably, the content is 0.01 to 0.2% by mass.
Zrは、均質化熱処理時に分散粒子(分散相)を生成し、結晶粒を微細化する作用を有する元素である。Zrの含有量が0.3質量%を超えると、粗大な金属間化合物が生成し、プレス成形性および耐食性が低下する。したがって、Zrを含有させる場合は、Zrの含有量は0.3質量%以下とする。好ましくは0.05~0.2質量%である。 (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. When 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. Preferably, the content is 0.05 to 0.2% by mass.
Tiは、鋳塊の結晶粒を微細化させ、プレス成形性を向上させる元素である。Tiの含有量が0.3質量%を超えると、粗大な晶出物が形成され、プレス成形性が低下する。したがって、Tiを含有させる場合は、Tiの含有量は0.3質量%以下とする。好ましくは0.01~0.2質量%である。 (Ti: 0.3% by mass or less)
Ti is an element that refines the crystal grains of the ingot and improves the press formability. When the Ti content exceeds 0.3% by mass, a coarse crystallized product is formed, and the press formability deteriorates. Therefore, when Ti is contained, the content of Ti is set to 0.3% by mass or less. Preferably, the content is 0.01 to 0.2% by mass.
Znの含有量が0.5質量%を超えると、粗大な金属間化合物が生成されてアルミニウム合金板の成形性が低下し、また耐食性が著しく低下する。したがって、Znの含有量は0.5質量%以下に規制する。 (Zn: 0.5% by mass or less)
If the Zn content exceeds 0.5% by mass, a coarse intermetallic compound is generated, the formability of the aluminum alloy plate is lowered, and the corrosion resistance is significantly lowered. Therefore, the Zn content is regulated to 0.5% by mass or less.
上記のCu、Fe、Mn、Cr、Zr、TiおよびZn以外の不可避的不純物としては、Sn、Sc、Ni、C、In、Na、Ca、V、Bi、Sr等の元素が想定し得るが、いずれも本発明の特徴を阻害しないレベルで含有することは許容される。具体的には、Cu、Fe、Mn、Cr、Zr、Ti、Znおよび不可避的不純物の元素の合計含有量が1.0質量%以下であることが好ましい。 (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.
ビッカース硬さは、JIS Z2244に記載されている金属材料の硬度を測定するための測定方法である。正四角錘形のダイヤモンドの圧子を一定の試験荷重で試料の試験面に押込み、生じた圧痕(くぼみ)の大きさから、試料の硬さを測定する試験である。圧痕を平面視するとほぼ正方形となり、2本の対角線が存在することとなる。 (Ratio of indentation diagonal length)
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.
数式で表わすと、以下のようになる。
P(%)=100×|L45-L0|/L0=100×△L/L0 ・・・(1)
ここで、|L45-L0|は、L45とL0との差(絶対値)を示す。 Specifically, 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. L45) and the length of the diagonal line (L0) of the indentation at an angle of 0 ° or 90 ° with respect to the rolling direction (L0) of the indentation at an angle of 0 ° or 90 ° with respect to the rolling direction. The ratio P (%) to the diagonal length (L0) is obtained.
This is expressed as follows:
P (%) = 100 × | L45−L0 | / L0 = 100 × ΔL / L0 (1)
Here, | L45−L0 | indicates the difference (absolute value) between L45 and L0.
同様に、ビッカース硬度計による圧痕の対角線の長さにおいて、圧延方向に対して45°または-45°(135°)の角度である圧痕の対角線の長さ(L45)を、以下簡略化して、「圧延方向に対して45°の対角線の長さL45」と記載することがある。 In addition, in the diagonal length of the impression by the Vickers hardness tester, 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”.
Similarly, in the diagonal length of the indentation by the Vickers hardness tester, 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”.
つまり、ビッカース硬度計による圧痕の対角線の長さにおいて、圧延方向に対して0°の対角線の長さL0と圧延方向に対して45°の対角線の長さL45との差△Lの、前記L0に対する比率P(%)が2.0%以下であることが必要である。 In the present invention, 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.
比率Pを2.0%以下にするためには、上記の特定の組成を有するAl合金であって、下記の特定の製造条件を採用して、Al合金板の内部の結晶構造の異方性を解消させることが必要である。 When the ratio P exceeds 2.0%, the anisotropy in the moldability is large, and it is difficult to increase the overhang height in the overhang molding.
In order to reduce 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
ビッカース硬度計による圧痕は、試料の幅の中央付近に、圧延方向(RD方向)に沿って作成する。圧延方向に対して対角線が、0°(90°)または45°(-45°)の角度となるように、それぞれについて、少なくとも3箇所ずつ、圧痕を付ける。圧痕を付ける面は、Al合金板の表面に付けてもよいし、Al合金板の断面に付けてもよい。
圧痕の対角線の長さは、複数の圧痕を上方から顕微鏡を用いて写真撮影し、得られた平面画像から、個々の圧痕の2本の対角線の長さを測定し、それらの測定値の平均値として求める。ビッカース硬度計の荷重は、試料の硬度に応じて、適宜設定することができる。 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.
本発明に係る製造方法は、歪みを蓄積させた状態で、熱間圧延工程後に設けた焼鈍工程で微細に再結晶させることで、板材内の結晶構造の異方性を解消させるところに大きな特徴を有するものである。 Next, a method for producing an Al alloy plate for press forming according to the present invention will be described.
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.
本発明のプレス成形用Al合金板の製造方法の第1実施形態は、Si:0.4~1.5質量%、Mg:0.3~1.0質量%を含有し、残部がAlおよび不可避的不純物からなるAl合金を鋳造する鋳造工程と、前記Al合金の鋳塊に、均質化熱処理を施す均質化熱処理工程と、熱間圧延の終了温度が300℃以下となる条件で熱間圧延を施す熱間圧延工程と、300~500℃の温度で焼鈍を施す焼鈍工程と、冷間圧延終了温度100℃以下で冷間圧延を施す冷間圧延工程と、500℃以上の温度で処理する溶体化処理工程と、70℃以上の温度に加熱する加熱工程とをこの順に行うことを特徴としている。 <First Embodiment of Manufacturing Method>
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 hot rolling process for performing annealing, an annealing process for performing annealing at a temperature of 300 to 500 ° C., a cold rolling process for performing cold rolling at a cold rolling end temperature of 100 ° C. or lower, and a temperature of 500 ° C. or higher. A solution treatment step and a heating step of heating to a temperature of 70 ° C. or higher are performed in this order.
鋳造工程S1は、プレス成形用Al合金を溶解、鋳造してAl合金鋳塊を作製する工程である。鋳造工程では、前記した組成を有するAl合金を溶解した溶湯から、所定形状の鋳塊を作製する。Al合金を溶解、鋳造する方法は、特に限定されるものではなく、従来公知の方法を用いればよい。例えば、誘導溶解炉または反射溶解炉等を用いて溶解し、連続鋳造法や、半連続鋳造法を用いて鋳造することができる。 (Casting process S1)
The casting step S1 is a step for producing an Al alloy ingot by melting and casting an Al alloy for press forming. In the casting process, 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 | dissolve using an induction melting furnace or a reflective melting furnace, and can be cast using a continuous casting method or a semi-continuous casting method.
均質化熱処理工程S2は、鋳造しただけでは組織が場所によって不均一であるため、全体を均一な組織にするために行う。均質化熱処理開始温度は、好ましくは、500~580℃である。500℃未満では、均一になるまでに時間がかかるために生産性が低下し、580℃を超えると、偏析部分の融点が下がっていることによる局部融解が発生することがある。
均質化熱処理時間は、1~10時間であることが好ましい。均質化熱処理時間が、1時間未満であると偏析が無くなっていない可能性がある。一方、10時間を超えると生産性が低下する。 (Homogenization heat treatment step S2)
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.
熱間圧延工程S3は、前記均質化熱処理工程S2後に、所定の厚みとするために熱間圧延を施す工程である。温度の降下過程において、所定の厚みとなるまで繰り返し行われる。熱間圧延の開始温度は、400~550℃であることが好ましい。出来るだけ少ない圧下回数で所定の板厚にするためには、圧延は高い温度で行われる。熱間圧延の開始温度が低いと、変形抵抗が大きいため圧延が困難となる。一方、熱間圧延の開始温度が高過ぎると、表面の粗大再結晶の原因になり、最終製品の肌荒れの原因となる。
熱間圧延は、一般的なアルミニウム材の熱間圧延と同様に1パスの熱間加工率(圧下率)30~50%程度の範囲で行うことができる。熱間圧延の圧下率は、30~40%であることが好ましい。この範囲の中で行うことにより、熱間圧延時の加工発熱量が少なくなり、歪み蓄積量が大きくなるからである。 (Hot rolling process S3)
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.
焼鈍工程S4は、焼鈍を行う工程である。熱間圧延工程S3の仕上げ工程において、熱間圧延の終了温度を300℃以下としているため、Al板内部の結晶構造組織内には歪みが蓄積している。焼鈍工程S4において、拘束力のかからない状態で、この歪みを解放させることによって、Al板内部の結晶構造組織をいかなる方向においても歪みが少なく、等方性の高い構造のものとすることができる。 (Annealing process S4)
The annealing step S4 is a step for performing annealing. In 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. In 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.
冷間圧延工程S5は、冷間圧延を施す工程である。焼鈍工程S4終了後に、冷間圧延を1回あるいは複数回行なって、所望の最終板厚とする。冷間加工率は、40%以上が好ましい。冷間加工率が40%未満の場合、溶体化時の結晶粒微細化効果が十分に得られないことがある。冷間圧延終了温度は、100℃以下であることが必要であり、好ましくは80℃以下である。冷間圧延終了温度が高い場合、歪みの蓄積量が不足し、溶体化処理工程において微細に再結晶せず、特定の結晶方位のみが発達することで変形しやすい方向に偏りが生じて、等方な組織が得られない。なお、冷間圧延終了温度は、冷間圧延を複数回行う場合、最終の冷間圧延を終了した温度のことを指す。
また、上記冷間圧延終了後に板平坦度の矯正のためのスキンパス圧延や表面粗さ制御のためのEDT(electric discharge textured)ロールを用いた圧延などの低加工率の冷間圧延を行っても良い。 (Cold rolling process S5)
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. Note that 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.
溶体化処理工程S6は、Mg、Siを固溶させて、ベーク後の耐力を確保するために必要な工程である。溶体化温度は、500℃以上の温度で行うことが必要であり、500~570℃が好ましい。溶体化温度が、500℃未満であると、固溶量が不足する可能性があり、570℃を超えると、共晶融解や再結晶粒の粗大化の可能性がある。溶体化時間は、0秒を超えて60秒以下であることが好ましい。溶体化時間が長すぎる場合、効果が飽和して経済性を損なう。加熱温度に到達した後の冷却においては、冷却速度が遅いと粒界に粗大なMg2Si、Si等が析出し易く、成形性が低下するため、水冷(水焼入れ)等により冷却することが好ましい。 (Solution treatment step S6)
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.
加熱工程S7は、室温時効による変化量を低減させ、ベーク後の耐力を確保させる工程である。加熱温度は、70℃以上であることが必要であり、70~150℃が好ましい。70℃未満に保持した場合、焼付け処理後の強度上昇が小さくなる。150℃を超えると、初期強度が高くなりすぎて成形性が悪化する。 (Heating step S7)
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.
本発明のプレス成形用Al合金板の製造方法の第2実施形態は、Si:0.4~1.5質量%、Mg:0.3~1.0質量%を含有し、残部がAlおよび不可避的不純物からなるAl合金を鋳造する鋳造工程と、前記Al合金の鋳塊に、均質化熱処理を施す均質化熱処理工程と、熱間圧延を施す熱間圧延工程と、冷間圧延終了温度100℃以下で冷間圧延を施す第1冷間圧延工程と、300~500℃の温度で中間焼鈍を施す中間焼鈍工程と、冷間圧延終了温度100℃以下で冷間圧延を施す第2冷間圧延工程と、500℃以上の温度で処理する溶体化処理工程と、70℃以上の温度に加熱する加熱工程とをこの順に行うことを特徴としている。 <Second Embodiment of Manufacturing Method>
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 first cold rolling process in which cold rolling is performed at a temperature not higher than ° C., an intermediate annealing process in which intermediate annealing is performed at a temperature of 300 to 500 ° C., and a second cold rolling in which cold rolling is performed at a cold rolling end temperature of 100 ° C. or lower. 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.
製造方法の第2実施形態では、熱間圧延時の熱間加工率(圧下率)、開始温度は第1実施形態と同じである。熱間圧延の仕上げ工程の終了温度について特に上限はないが、生産効率の観点から400℃以下が好ましい。 (Hot rolling process S3)
In the second embodiment of the manufacturing method, the hot working rate (rolling rate) and the starting temperature during hot rolling are the same as those in the first embodiment. Although there is no upper limit in particular about the completion | finish temperature of the finishing process of hot rolling, 400 degrees C or less is preferable from a viewpoint of production efficiency.
冷間加工工程S5aは、前記熱間圧延工程S3後に、冷間圧延を施す工程である。熱間圧延工程S3終了後、冷間圧延を1回あるいは複数回行なって、所望の最終板厚とする。冷間加工率は、40%以上が好ましく、50%以上がより好ましい。冷間圧延終了温度は、100℃以下であることが必要であり、好ましくは80℃以下である。これらの範囲を逸脱した場合、中間焼鈍工程で微細な再結晶組織が得られない。 (First cold rolling step S5a)
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.
中間焼鈍工程S4aは、第1冷間圧延工程S5a後に、中間焼鈍を行う工程である。第1冷間圧延工程S5aにおいて、Al板内部の結晶構造組織内には歪みが蓄積している。中間焼鈍工程S4aにおいて、拘束力のかからない状態で、この歪みを解放させることによって、Al板内部の結晶構造組織をいかなる方向においても歪みが少なく、等方性の高い構造のものとすることができる。 (Intermediate annealing step S4a)
The intermediate annealing step S4a is a step of performing intermediate annealing after the first cold rolling step S5a. In the first cold rolling step S5a, strain is accumulated in the crystal structure inside the Al plate. In 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. .
第2冷間圧延工程S5bは、中間焼鈍工程S4a後に、冷間圧延を施す工程である。焼鈍工程S4終了後に、冷間圧延を1回あるいは複数回行なって、所望の最終板厚とする。冷間加工率は40%以上が好ましい。冷間加工率が40%未満の場合、溶体化時の結晶粒微細化効果が十分に得られないことがある。冷間圧延終了温度は、100℃以下であることが必要であり、好ましくは80℃以下である。冷間圧延終了温度が高い場合、歪みの蓄積量が不足し、溶体化処理工程において微細に再結晶せず、特定の結晶方位のみが発達することで変形しやすい方向に偏りが生じて、等方な組織が得られない。なお、冷間圧延終了温度は、冷間圧延を複数回行う場合、最終の冷間圧延を終了した温度のことを指す。
また、上記冷間圧延終了後に板平坦度の矯正のためのスキンパス圧延や表面粗さ制御のためのEDT(electric discharge textured)ロールを用いた圧延などの低圧延率の冷間圧延を行っても良い。 (Second cold rolling step S5b)
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. 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. Note that 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.
試料番号1~27は、いずれも製造方法の第1実施形態によって製造されたアルミニウム合金板である。
後記する表1に示す組成のAl合金(合金記号A~Z)を、DC鋳造法等の公知の鋳造法により、溶解、鋳造して厚さ600mmの鋳塊とした。この鋳塊に、550℃、5時間の均質化熱処理を施した。この熱処理を施した鋳塊に、試料番号1~25と試料番号27については、熱間圧延開始温度500℃で30~40%の圧延率で熱間圧延を繰り返し施して、板厚を減少させていき、熱間圧延終了温度270℃で、板厚3mmの熱間圧延板とした。試料番号26については、熱間圧延終了温度を285℃に変更して、板厚3mmの熱間圧延板とした。 (Sample Nos. 1-27)
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. Thus, a hot rolled plate having a hot rolling finish temperature of 270 ° C. and a thickness of 3 mm was obtained. For sample No. 26, the hot rolling end temperature was changed to 285 ° C. to obtain a hot rolled plate having a plate thickness of 3 mm.
試料番号28~32は、いずれも製造方法の第2実施形態によって製造されたアルミニウム合金板である。
後記する表1に示す組成のAl合金のうち、合金記号でA、E、Mの組成の合金を用いて、試料番号1、5、13と同様に、DC鋳造法等の公知の鋳造法により、溶解、鋳造して厚さ600mmの鋳塊とした。この鋳塊に、550℃、5時間の均質化熱処理を施した。この熱処理を施した鋳塊に、試料番号28~30と試料番号32については、熱間圧延開始温度500℃で30~40%の圧延率で熱間圧延を繰り返し施して、板厚を減少させていき、熱間圧延終了温度250℃で、板厚7mmの熱間圧延板とした。試料番号31については、熱間圧延終了温度を330℃に変更して、板厚7mmの熱間圧延板とした。 (Sample numbers 28-32)
Sample numbers 28 to 32 are all aluminum alloy plates manufactured by the second embodiment of the manufacturing method.
Of the Al 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. Thus, a hot rolled sheet having a hot rolling end temperature of 250 ° C. and a thickness of 7 mm was obtained. For sample number 31, the hot rolling end temperature was changed to 330 ° C. to obtain a hot rolled plate having a thickness of 7 mm.
試料番号33は、試料番号30において、第1および第2の冷間圧延終了温度を120℃にした以外は試料番号30と同等の条件で加工を行った。
試料番号34は、試料番号30において、第1の冷間圧延終了温度を120℃とした以外は試料番号30と同等の条件で加工を行った。
試料番号35は、試料番号30において、第2の冷間圧延終了温度を120℃とした以外は試料番号30と同等の条件で加工を行った。
試料番号36は、試料番号13において、熱間圧延工程の終了温度を330℃にした以外は、試料番号13と同等の条件で加工を行った。
試料番号37は、試料番号13において、冷間圧延終了温度を110℃とした以外は、試料番号13と同等の条件で加工を行った。
試料番号38は、試料番号30において、中間焼鈍工程を行わなかった以外は、試料番号30と同等の条件で加工を行った。
試料番号39は、試料番号1において、熱間圧延工程の終了温度を250℃にして、バッチ式炉を用いて、280℃、4hの焼鈍を施した以外は、試料番号1と同等の条件で加工を行った。
試料番号40は、試料番号5において、熱間圧延工程の終了温度を250℃にして、焼鈍温度を600℃にした以外は、試料番号5と同等の条件で加工を行った。 (Sample numbers 33 to 40)
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.
圧痕の対角線の長さの比の測定方法について、以下に図を用いて説明する。図3~5は、ビッカース硬度計による圧痕の対角線において、圧延方向に対して0°または90°の対角線の長さL0と圧延方向に対して45°または-45°(135°)の対角線の長さL45を測定する方法を説明するための模式図である。 [Ratio of diagonal length of indentation]
A method for measuring the ratio of diagonal lengths of indentations will be described below with reference to the drawings. 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.
供試板から、圧延方向が長手方向となるようにJIS5号の引張試験片を打ち抜いた。JIS Z2241に準じて、株式会社島津製作所(SHIMADZU CORPORATION) 製床置形万能引張試験機AG-Iにて引張試験を行い、引張強さ(MPa)、引張伸び(%)および0.2%耐力(MPa)を測定した。クロスヘッド速度は5mm/分で、試験片が破断するまで一定の速度で行い、それぞれ5回測定して平均値で算出した。引張強度は、210MPa以上のときに、耐力は120MPa以上のときに、引張伸びは20%以上のときに、それぞれ優れていると判断した。 [Tensile test]
A tensile test piece of JIS No. 5 was punched from the test plate so that the rolling direction was the longitudinal direction. In accordance with JIS Z2241, a tensile test was conducted using a floor-mounted universal tensile tester AG-I manufactured by Shimadzu Corporation, and tensile strength (MPa), tensile elongation (%), and 0.2% proof stress ( MPa). The crosshead speed was 5 mm / min, and the test piece was run at a constant speed until the test piece broke. It was judged that the tensile strength was excellent when the tensile strength was 210 MPa or more, the proof stress was 120 MPa or more, and the tensile elongation was 20% or more.
AB耐力とは、プレス成形後の塗装焼付等の人工時効処理により強度や耐力が向上するBH性(ベークハード性、塗装焼付硬化性)についての指標である。Al合金板のプレス成形後の成形体に対して、塗装焼付などの比較的低温の処理を施すことにより、その時の加熱により時効硬化して強度・耐力が向上する。この向上の程度を指標として表わすものである。
人工時効硬化処理として、プレス成形を模擬した2%の歪み(ストレッチ)を予め付与した状態で、170℃で20分の加熱処理を行った。その後、JIS Z2241に準じて、株式会社島津製作所(SHIMADZU CORPORATION) 製床置形万能引張試験機AG-Iにて引張試験を行って、0.2%耐力(AB耐力)(MPa)を測定した。クロスヘッド速度は5mm/分で、試験片が破断するまで一定の速度で行い、5回測定して平均値で算出した。AB耐力が170MPa以上のときに優れていると判断した。 [AB proof stress]
AB yield strength 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. By applying a relatively low temperature treatment such as paint baking to the molded body after press-molding the Al alloy plate, 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.
As an artificial age hardening treatment, heat treatment was performed at 170 ° C. for 20 minutes in a state where 2% strain (stretch) simulating press molding was applied in advance. Thereafter, according to JIS Z2241, 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.
供試板から、外径66mmの円板状の試験片(ブランク)を打ち抜き、この試験片に対して直径40mmのポンチを用いてカッピングを施して、カップ径40mmの絞りカップを作製した。この絞りカップの耳高さを測定し、下記式(2)に基づき、耳率(0°、90°耳率)(%)を測定した。下記式(2)において、hXは絞りカップの耳高さを表す。そして、hの添数字Xはカップ高さの測定位置を示し、Al合金板の圧延方向に対してX°の角度をなす位置を意味する。
耳率(%)=〔{(h0+h90+h180+h270)-(h45+h135+h225+h315)}/{1/2(h0+h90+h180+h270+h45+h135+h225+h315)}〕×100 ・・・(2)
耳率が、3.5%以下の場合、圧延方向に対して0°、90°方向と45°方向との変形量が大きく異なることはなく、成形性、歩留まりに優れているものと判断した。 [Ear rate]
A disc-shaped test piece (blank) having an outer diameter of 66 mm was punched out from the test plate, and cupping was performed on the test piece using a punch having a diameter of 40 mm to produce a drawn cup having a cup diameter of 40 mm. The ear height of the squeezed cup was measured, and the ear rate (0 °, 90 ° ear rate) (%) was measured based on the following formula (2). In the following formula (2), hX represents the ear height of the squeezing cup. The suffix “X” of h indicates the measurement position of the cup height, and means a position that forms an angle of X ° with respect to the rolling direction of the Al alloy sheet.
Ear rate (%) = [{(h0 + h90 + h180 + h270) − (h45 + h135 + h225 + h315)} / {1/2 (h0 + h90 + h180 + h270 + h45 + h135 + h225 + h315)}] × 100 (2)
When 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. .
図6は、張出成形性試験機の測定方法を説明するための断面図である。
アルミニウム合金板のプレス加工における割れの有無の評価に代えて、球頭張出し成形による限界張出し高さを評価した。供試板13として、圧延方向長110mm×圧延直角方向長200mmに切り出した。この供試板13を、図6に示すように、内径(穴径)102.8mm、肩半径Rd:5.0mm、外径220mmのダイス10に、治具(ブランクホルダ)11を用いて一定のしわ押さえ力で固定した。そして、ダイス-治具間の隙間を試験片と同じ厚さ1mmのシム(図示省略)を挟むことにより一定に保ちながら、球頭直径100mm(半径Rp:50mm)の球頭ポンチ12を供試板表面に対して垂直方向に押し込んで張出し加工を行い、割れや括れが観察されるまでの張出高さHの限界値を求めた。張出高さHの限界値が30mm以上であるものを合格と判断した。 [Extrusion formability]
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
供試材の圧延方向に対して0°方向の寸法が40mm、90°方向の寸法が200mmの試験片を切り出した。15%の塑性歪みを圧延方向に対して90°方向に付与した後に、自動車車体パネルの塗装を模擬して、リン酸亜鉛処理を行い、次にカチオン電着塗装を行い、さらに塗装焼付硬化処理を模擬した焼鈍処理を施した後に、板表面を目視観察して評価を行った。具体的な処理条件は以下のとおりである。前記歪みを予め付与した後の板に対して、リン酸チタンのコロイド分散液処理、フッ素を低濃度(50ppm)含むリン酸亜鉛浴に浸漬するリン酸亜鉛処理を順に行い、リン酸亜鉛皮膜を板表面に形成させ、さらにカチオン電着塗装を行った後に、170℃×20分の加熱処理を実施した。
前記塗装表面に、リジングマークが発生していないものを◎、リジングマークが発生しているものの比較的軽度であるものを○、リジングマークが顕著に発生したものを×と判断した。 [Ridging mark properties]
A test piece having a dimension in the 0 ° direction of 40 mm and a dimension in the 90 ° direction of 200 mm with respect to the rolling direction of the test material was cut out. After applying 15% plastic strain in the 90 ° direction with respect to the rolling direction, the coating of automobile body panels is simulated, zinc phosphate treatment is performed, then cationic electrodeposition coating is performed, and paint baking and curing treatment is further performed. After performing an annealing treatment simulating No. 1, the plate surface was visually observed and evaluated. Specific processing conditions are as follows. 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. After forming on the plate surface and further performing cationic electrodeposition coating, 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.
本出願は、2013年4月9日出願の日本特許出願(特願2013-081149)、2014年3月18日出願の日本特許出願(特願2014-055180)に基づくものであり、その内容はここに参照として取り込まれる。 Although the present invention has been described in detail and with reference to specific embodiments, it will be apparent to those skilled in the art that various changes and modifications can be made without departing from the spirit and scope of the invention.
This application is based on a Japanese patent application filed on April 9, 2013 (Japanese Patent Application No. 2013-081149) and a Japanese patent application filed on March 18, 2014 (Japanese Patent Application No. 2014-055180). Incorporated herein by reference.
S2 均一化熱処理工程
S3 熱間圧延工程
S4 焼鈍工程
S4a 中間焼鈍工程
S5 冷間圧延工程
S5a 第1冷間圧延工程
S5b 第2冷間圧延工程
S6 溶体化処理工程
S7 加熱工程 S1 Casting process
S2 Uniform heat treatment process
S3 Hot rolling process
S4 annealing process
S4a Intermediate annealing process
S5 Cold rolling process
S5a First cold rolling process
S5b Second cold rolling process
S6 Solution treatment process
S7 Heating process
Claims (10)
- Si:0.4~1.5質量%、Mg:0.3~1.0質量%を含有し、残部がAlおよび不可避的不純物からなるアルミニウム合金から構成され、
ビッカース硬度計による圧痕の対角線の長さにおいて、圧延方向に対して0°の対角線の長さL0と圧延方向に対して45°の対角線の長さL45との差△Lの、前記L0に対する比率P(%)が2.0%以下であることを特徴とするプレス成形用アルミニウム合金板。 Si: 0.4 to 1.5% by mass, Mg: 0.3 to 1.0% by mass, the balance is composed of an aluminum alloy consisting of Al and inevitable impurities,
The ratio of the difference ΔL 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 to the L0 in the length of the diagonal of the indentation by the Vickers hardness tester An aluminum alloy sheet for press forming, wherein P (%) is 2.0% or less. - 前記アルミニウム合金に、さらに下記(a)~(d)の少なくとも1種を含有させることを特徴とする請求項1に記載のプレス成形用アルミニウム合金板。
(a)Cu:1.0質量%以下
(b)Fe:0.5質量%以下およびMn:0.5質量%以下の少なくともいずれか1つ
(c)Cr:0.3質量%以下、Zr:0.3質量%以下およびTi:0.3質量%以下の少なくともいずれか1つ
(d)Zn:0.5質量%以下 The aluminum alloy sheet for press forming according to claim 1, wherein the aluminum alloy further contains at least one of the following (a) to (d).
(A) Cu: 1.0 mass% or less (b) Fe: 0.5 mass% or less and Mn: 0.5 mass% or less (c) Cr: 0.3 mass% or less, Zr : At least one of 0.3% by mass or less and Ti: 0.3% by mass or less (d) Zn: 0.5% by mass or less - 前記アルミニウム合金が、Si:0.6~1.3質量%、Mg:0.3~0.8質量%を含有し、残部がAlおよび不可避的不純物からなることを特徴とする請求項1または2記載のプレス成形用アルミニウム合金板。 The aluminum alloy 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. 2. An aluminum alloy plate for press forming according to 2.
- 請求項1または2に記載のプレス成形用アルミニウム合金板をプレス成形してなるアルミニウム合金プレス成形体。 An aluminum alloy press-molded body obtained by press-molding the aluminum alloy plate for press molding according to claim 1 or 2.
- 請求項3記載のプレス成形用アルミニウム合金板をプレス成形してなるアルミニウム合金プレス成形体。 An aluminum alloy press-molded body obtained by press-molding the aluminum alloy plate for press molding according to claim 3.
- Si:0.4~1.5質量%、Mg:0.3~1.0質量%を含有し、残部がAlおよび不可避的不純物からなるアルミニウム合金を鋳造する鋳造工程と、
前記アルミニウム合金の鋳塊に、均質化熱処理を施す均質化熱処理工程と、
熱間圧延の終了温度が300℃以下となる条件で熱間圧延を施す熱間圧延工程と、
300~500℃の温度で焼鈍を施す焼鈍工程と、
冷間圧延終了温度100℃以下で冷間圧延を施す冷間圧延工程と、
500℃以上の温度で処理する溶体化処理工程と、
70℃以上の温度に加熱する加熱工程と
をこの順に行うことを特徴とするプレス成形用アルミニウム合金板の製造方法。 A casting step of casting an aluminum alloy containing Si: 0.4 to 1.5% by mass, Mg: 0.3 to 1.0% by mass, the balance being Al and inevitable impurities;
A homogenization heat treatment step for subjecting the aluminum alloy ingot to a homogenization heat treatment;
A hot rolling step in which hot rolling is performed under a condition that the end temperature of hot rolling is 300 ° C. or less;
An annealing process for annealing at a temperature of 300 to 500 ° C .;
A cold rolling step of performing cold rolling at a cold rolling end temperature of 100 ° C. or less;
A solution treatment step of treating at a temperature of 500 ° C. or higher;
A heating step of heating to a temperature of 70 ° C. or higher;
A method for producing an aluminum alloy plate for press forming, wherein the steps are performed in this order. - Si:0.4~1.5質量%、Mg:0.3~1.0質量%を含有し、残部がAlおよび不可避的不純物からなるアルミニウム合金を鋳造する鋳造工程と、
前記アルミニウム合金の鋳塊に、均質化熱処理を施す均質化熱処理工程と、
熱間圧延を施す熱間圧延工程と、
冷間圧延終了温度100℃以下で冷間圧延を施す第1冷間圧延工程と、
300~500℃の温度で中間焼鈍を施す中間焼鈍工程と、
冷間圧延終了温度100℃以下で冷間圧延を施す第2冷間圧延工程と、
500℃以上の温度で処理する溶体化処理工程と、
70℃以上の温度に加熱する加熱工程と
をこの順に行うことを特徴とするプレス成形用アルミニウム合金板の製造方法。 A casting step of casting an aluminum alloy containing Si: 0.4 to 1.5% by mass, Mg: 0.3 to 1.0% by mass, the balance being Al and inevitable impurities;
A homogenization heat treatment step for subjecting the aluminum alloy ingot to a homogenization heat treatment;
A hot rolling process for performing hot rolling;
A first cold rolling step of performing cold rolling at a cold rolling end temperature of 100 ° C. or less;
An intermediate annealing step in which intermediate annealing is performed at a temperature of 300 to 500 ° C .;
A second cold rolling step of performing cold rolling at a cold rolling end temperature of 100 ° C. or lower;
A solution treatment step of treating at a temperature of 500 ° C. or higher;
A heating step of heating to a temperature of 70 ° C. or higher;
A method for producing an aluminum alloy plate for press forming, wherein the steps are performed in this order. - 前記アルミニウム合金に、さらに下記(a)~(d)の少なくとも1種を含有させることを特徴とする請求項6または7に記載のプレス成形用アルミニウム合金板の製造方法。
(a)Cu:1.0質量%以下
(b)Fe:0.5質量%以下およびMn:0.5質量%以下の少なくともいずれか1つ
(c)Cr:0.3質量%以下、Zr:0.3質量%以下およびTi:0.3質量%以下の少なくともいずれか1つ
(d)Zn:0.5質量%以下 The method for producing an aluminum alloy sheet for press forming according to claim 6 or 7, wherein the aluminum alloy further contains at least one of the following (a) to (d).
(A) Cu: 1.0 mass% or less (b) Fe: 0.5 mass% or less and Mn: 0.5 mass% or less (c) Cr: 0.3 mass% or less, Zr : At least one of 0.3% by mass or less and Ti: 0.3% by mass or less (d) Zn: 0.5% by mass or less - 前記アルミニウム合金が、Si:0.6~1.3質量%、Mg:0.3~0.8質量%を含有し、残部がAlおよび不可避的不純物からなることを特徴とする請求項6または7記載のプレス成形用アルミニウム合金板の製造方法。 The aluminum alloy 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. 8. A method for producing an aluminum alloy sheet for press forming according to item 7.
- 前記アルミニウム合金が、Si:0.6~1.3質量%、Mg:0.3~0.8質量%を含有し、残部がAlおよび不可避的不純物からなることを特徴とする請求項8記載のプレス成形用アルミニウム合金板の製造方法。 9. The aluminum alloy 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. Manufacturing method of aluminum alloy sheet for press forming.
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Also Published As
Publication number | Publication date |
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CN105102645A (en) | 2015-11-25 |
JP5882380B2 (en) | 2016-03-09 |
US20160047021A1 (en) | 2016-02-18 |
CN109385560A (en) | 2019-02-26 |
JP2014218734A (en) | 2014-11-20 |
MX2015014132A (en) | 2015-12-15 |
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