Classifications

• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21B—ROLLING OF METAL
  • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
• • 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
• • 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
  • 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

Definitions

• the present invention relates to a method for producing an Al—Mg—Si based alloy plate, and more particularly to a method for producing an Al—Mg—Si based alloy plate excellent in thermal conductivity, conductivity and strength.
• Flat panel TVs thin monitors for personal computers, notebook computers, tablet computers, car navigation systems, portable navigation systems, chassis of products such as mobile terminals such as smartphones and mobile phones, metal base printed boards, and heating elements such as internal covers
• excellent thermal conductivity and strength for promptly radiating heat are required.
• Pure aluminum alloys such as JIS 1100, 1050, and 1070 have excellent thermal conductivity but low strength.
• An Al—Mg alloy (5000-based alloy) such as JIS 5052 used as a high strength material is significantly inferior in thermal conductivity and conductivity to a pure aluminum-based alloy.
• an Al—Mg—Si alloy (6000 alloy) has good thermal conductivity and electrical conductivity, and can be improved in strength by age hardening.
• a method for obtaining an aluminum alloy plate excellent in conductivity and conductivity has been studied.
• Patent Document 1 contains Si: 0.2 to 1.5% by mass, Mg: 0.2 to 1.5% by mass, Fe: 0.3% by mass or less, and Mn: 0. Containing one or two of 02 to 0.15% by mass and Cr: 0.02 to 0.15%, and the balance of Al and Ti in inevitable impurities is regulated to 0.2% or less, or
• An aluminum alloy plate having a composition containing one or two of Cu: 0.01 to 1% by mass or rare earth element: 0.01 to 0.2% by mass was prepared by continuous casting and rolling, and then cold-worked. Rolling, followed by solution treatment at 500 to 570 ° C., followed by further cold rolling at a cold rolling rate of 5 to 40%, followed by aging treatment after heating to 150 to 190 ° C.
• Aluminum with excellent thermal conductivity, strength and bending workability Method for producing a gold plate have been described.
• Patent Document 2 contains 0.1 to 0.34% by mass of Mg, 0.2 to 0.8% by mass of Si, and 0.22 to 1.0% by mass of Cu, with the balance being Al and inevitable impurities.
• An Al—Mg—Si based alloy having a Si / Mg content ratio of 1.3 or more is made into an ingot having a thickness of 250 mm or more by semi-continuous casting, and is heated through preheating at a temperature of 400 to 540 ° C.
• Disclosed is a method for producing an Al—Mg—Si alloy rolled sheet, characterized by performing cold rolling at a rolling reduction of 50 to 85% and annealing at a temperature of 140 to 280 ° C. ing.
• Patent Document 3 contains Si: 0.2 to 0.8 wt%, Mg: 0.3 to 0.9 wt%, Fe: 0.35 wt% or less, Cu: 0.20 mass% or less, and the balance Al And a method of producing an alloy in which an Al—Mg—Si alloy ingot made of inevitable impurities is homogenized, hot-rolled and hot-finished, and then cold-rolled, and any pass of said hot-rolling
• an Al—Mg—Si based alloy is characterized in that the material temperature before the pass is 350 to 450 ° C., the rising plate thickness is 10 mm or less, and the reduction ratio of the cold rolling is 30% or more.
• a method for manufacturing a plate is disclosed.
• the thermal conductivity and the electrical conductivity have a good correlation, and the aluminum alloy plate having an excellent thermal conductivity has an excellent electrical conductivity, not to mention the heat radiating member material. It can be used as a conductive member material.
• Patent Document 1 Although an aluminum alloy plate having a relatively high strength is obtained, a solution treatment comprising high-temperature heat treatment at 500 ° C. or higher and subsequent rapid cooling is performed on the aluminum alloy plate in the middle of cold rolling, A complicated process of performing an aging treatment after further cold rolling is required, which increases the manufacturing cost.
• Patent Document 3 as in Patent Document 2, no solution treatment is required in the process after hot rolling, and a higher tensile strength than that in Patent Document 2 is obtained.
• 300 N / mm is used.
• the tensile strength exceeding 2 (MPa) can be obtained only in the examples where the cold rolling reduction rate is 98% and the product sheet thickness is 0.1 mm, and there is a limit to the improvement in strength.
• an object of the present invention is an Al—Mg—Si system that has high conductivity and can further improve strength without applying a solution treatment in a process after hot rolling. It is providing the manufacturing method of an alloy plate.
• a method of manufacturing an alloy plate in which hot rolling and cold rolling are sequentially performed on an Al—Mg—Si alloy ingot, and the surface temperature of the Al—Mg—Si alloy plate immediately after the end of hot rolling A method for producing an Al—Mg—Si based alloy sheet having a temperature of 230 ° C. or lower.
• the chemical composition of the Al—Mg—Si alloy ingot is Si: 0.2 to 0.8 mass%, Mg: 0.3 to 1 mass%, Fe: 0.5 mass% or less, and Cu: 2.
• a method for producing an alloy plate wherein the surface temperature of the Al—Mg—Si alloy plate immediately after the end of hot rolling is 230 ° C. or less.
• the surface temperature of the Al—Mg—Si based alloy sheet immediately after the end of hot rolling is 230 ° C. or less, an effective quenching effect by hot rolling can be obtained, An Al—Mg—Si alloy plate having a high tensile strength can be produced.
• the chemical composition of the Al—Mg—Si alloy ingot is Si: 0.2 to 0.8 mass%, Mg: 0.3 to 1 mass%, Fe: Since it contains 0.5% by mass or less and Cu: 0.5% by mass or less, and consists of the balance Al and unavoidable impurities, an Al—Mg—Si based alloy sheet having high tensile strength can be manufactured.
• the strength of the Al—Mg—Si based alloy sheet can be improved by cold rolling.
• the strength of the Al—Mg—Si based alloy sheet can be further increased by age hardening, and at the same time, the conductivity is improved. I can do it.
• the surface temperature of the Al—Mg—Si based alloy plate immediately before the pass among the plurality of passes of hot rolling is 470 to 350 ° C., and the Al—Mg—Si due to the pass is used. Since the pass in which the average cooling rate by cooling of the alloy plate or the forced cooling after the pass is 50 ° C./min or more is performed at least once, the quenching effect by hot rolling can be enhanced.
• Si 0.2 to 0.8 mass%, Mg: 0.3 to 1 mass%, Fe: 0.5 mass% or less, and Cu: 0.5 mass%
• at least one of Ti: 0.1% by mass or less or B: 0.1% by mass or less is contained in the Al—Mg—Si alloy ingot consisting of the remainder Al and inevitable impurities.
• the surface temperature of the Al—Mg—Si alloy sheet immediately after the end of hot rolling is 230 ° C. or less, so that effective quenching effect by hot rolling And an Al—Mg—Si based alloy sheet having a high tensile strength can be produced.
• Ni, V, Ga, Pb, Sn, Bi and Zr as impurities are respectively regulated to 0.05% by mass or less, they have high tensile strength.
• An Al—Mg—Si based alloy plate can be manufactured.
• the strength of the Al—Mg—Si based alloy sheet can be improved by cold rolling.
• the strength of the Al—Mg—Si based alloy plate can be further increased by age hardening, and at the same time the conductivity is improved. I can do it.
• the final annealing temperature is 200 ° C. or less, an Al—Mg—Si based alloy sheet exhibiting high values of tensile strength and electrical conductivity can be produced.
• the surface temperature of the Al—Mg—Si based alloy plate immediately before the pass among the plurality of passes of hot rolling is 470 to 350 ° C., and the Al—Mg—Si due to the pass is used. Since the pass in which the average cooling rate by cooling of the alloy plate or the forced cooling after the pass is 50 ° C./min or more is performed at least once, the quenching effect by hot rolling can be enhanced.
• the inventor of the present application provides a method for producing an Al—Mg—Si based alloy sheet, which is sequentially subjected to hot rolling and cold rolling, while keeping the surface temperature of the alloy sheet after hot rolling below a predetermined temperature, It has been found that an Al—Mg—Si alloy sheet having high strength while having high conductivity and good workability can be obtained by performing heat treatment after the end of rolling and before the end of cold rolling. Invented.
• Mg and Si are elements necessary for the development of strength, and the respective contents thereof are Si: 0.2% by mass or more and 0.8% by mass or less, and Mg: 0.3% by mass or more and 1% by mass or less. preferable. If the Si content is less than 0.2% by mass or the Mg content is less than 0.3% by mass, the strength is lowered. On the other hand, if the Si content exceeds 0.8% by mass and the Mg content exceeds 1% by mass, the rolling load in hot rolling increases and the productivity decreases, and the formability of the resulting aluminum alloy sheet also increases. Deteriorate.
• the Si content is more preferably 0.2% by mass or more and 0.6% by mass or less, and particularly preferably 0.32% by mass or more and 0.60% by mass or less.
• the Mg content is more preferably 0.4% by mass or more and 1.0% by mass or less, more preferably 0.45% by mass or more and 0.9% by mass or less, and particularly preferably 0.45% by mass or more and 0.55% by mass or less. Is preferred.
• Fe and Cu are components necessary for molding, but if they are contained in a large amount, the corrosion resistance decreases.
• the Fe content and the Cu content are preferably regulated to 0.5% by mass or less, respectively.
• the Fe content is more preferably regulated to 0.35% by mass or less, and particularly preferably from 0.1% by mass to 0.25% by mass.
• the Cu content is more preferably 0.2% by mass or less, and particularly preferably 0.1% by mass or less.
• various impurity elements are unavoidably contained in the alloy element, but Mn and Cr decrease conductivity and conductivity, and Zn increases in content and decreases in corrosion resistance of the alloy material.
• the content of each of Mn, Cr, and Zn as impurities is preferably 0.1% by mass or less, and more preferably 0.05% by mass or less.
• Ti and B have the effect of refining crystal grains and preventing solidification cracking when casting the alloy into a slab.
• the effect is obtained by adding at least one of Ti or B, and both may be added. However, if it is contained in a large amount, a large amount of crystallized crystals are generated, and the workability, thermal conductivity, and conductivity of the product are lowered.
• the Ti content is preferably 0.1% by mass or less, and more preferably 0.005% by mass or more and 0.05% by mass or less.
• the B content is preferably 0.1% by mass or less, and particularly preferably 0.06% by mass.
• impurity elements other than the above include Ni, V, Ga, Pb, Sn, Bi, Zr, Ag, rare earth, etc., but are not limited to these, and among these other impurity elements, rare earth Other than the above, the content of each element is preferably 0.05% by mass or less.
• the rare earth may contain one or more kinds of elements, and may be derived from a casting raw material contained in the state of misch metal, but the total content of rare earth elements The amount is preferably 0.1% by mass or less, and more preferably 0.05% by mass or less.
• the dissolved components are adjusted by a conventional method to obtain an Al—Mg—Si alloy ingot.
• the obtained alloy ingot is preferably subjected to a homogenization treatment as a step prior to heating before hot rolling.
• the homogenization treatment is preferably performed at 500 ° C. or higher.
• the heating before hot rolling is carried out in order to solidify the crystallized substance and Mg, Si in the Al—Mg—Si alloy ingot to form a uniform structure. Therefore, it is preferable to carry out at 450 ° C. or higher and 580 ° C. or lower, particularly preferably at 500 ° C. or higher and 580 ° C. or lower.
• the Al-Mg-Si alloy ingot is cooled after being homogenized, and may be heated before hot rolling, or the homogenization and heating before hot rolling may be performed continuously, In the preferable temperature range of the homogenization treatment and heating before hot rolling, the homogenization treatment and the heating before hot rolling may be combined and heated at the same temperature.
• the chamfering may be performed after casting and before homogenization treatment, or after homogenization treatment and before heating before hot rolling.
• Hot rolling is performed on the Al-Mg-Si alloy ingot after heating before hot rolling.
• Hot rolling consists of rough hot rolling and finishing hot rolling, and after performing rough hot rolling consisting of multiple passes using a rough hot rolling mill, a finishing hot rolling mill different from the rough hot rolling mill is used. Finish hot rolling using.
• the finish hot rolling can be omitted.
• the finish hot rolling is performed once by introducing an Al—Mg—Si based alloy plate from one direction using a rolling mill in which a pair of upper and lower work rolls or two or more work rolls are continuously installed. It is carried out in the pass.
• an Al—Mg—Si alloy plate after finish hot rolling may be wound with a winding device to form a hot rolled coil.
• finishing hot rolling is omitted and the final pass of rough hot rolling is used as the final pass of hot rolling
• the Al-Mg-Si alloy plate is taken up by a winder after the rough hot rolling. It may be a hot rolled coil.
• the surface temperature of the Al—Mg—Si alloy plate immediately before the pass is 350 ° C. or more and 470 ° C. or less, and the Al—Mg—Si alloy plate is cooled by the pass, or A pass having an average cooling rate of 50 ° C./min or more by the pass and forced cooling after the pass is called a control pass.
• the reason why the surface temperature of the Al—Mg—Si alloy plate immediately before the control pass is set to 350 ° C. or more and 470 ° C. or less is that if it is less than 350 ° C., the effect of quenching in the rapid hot rolling is small and the temperature is higher than 470 ° C. This is because it is difficult to rapidly cool the Al-Mg-Si based alloy plate having a rising path.
• the average cooling rate is an Al—Mg—Si alloy from the start to the end of the control pass when forced cooling is not performed in the control pass, and from the start of the control pass to the end of forced cooling when forced cooling is performed after the control pass.
• Forced cooling after the control pass may be performed sequentially on the rolled part while rolling the Al—Mg—Si alloy plate, or after rolling the entire Al—Mg—Si alloy plate. Also good.
• the method of forced cooling is not limited, but water cooling, air cooling, or coolant may be used.
• the control pass is preferably performed at least once, and may be performed a plurality of times. When performing the control pass a plurality of times, it is possible to select whether to perform forced cooling after each pass for each control pass. If the surface temperature of the Al—Mg—Si based alloy plate immediately before the pass is 470 to 350 ° C. and the cooling rate is 50 ° C./min or more, the control pass can be performed multiple times. By reducing the temperature of the Al—Mg—Si based alloy plate to below 350 ° C., quenching can be performed efficiently and effectively.
• the surface temperature of the Al—Mg—Si based alloy sheet immediately after the final pass of the hot rolling is set as the temperature after the rough hot rolling
• the surface temperature of the Al—Mg—Si alloy sheet immediately after the end of forced cooling is set as the temperature after rough hot rolling.
• finishing hot rolling ends when finishing hot rolling is performed, finishing hot rolling ends.
• hot rolling ends When finishing hot rolling is not performed, hot rolling ends with the end of the final pass of rough hot rolling, and immediately after the hot rolling ends.
• the surface temperature of the Al—Mg—Si based alloy plate is 230 ° C. or less. An effective quenching effect can be obtained by setting the temperature of the alloy sheet immediately after the hot rolling to 230 ° C. or less.
• the surface temperature of the Al—Mg—Si based alloy sheet immediately after the hot rolling is preferably 200 ° C. or less, more preferably 150 ° C. or less, and particularly preferably 130 ° C. or less.
• the surface temperature of the Al-Mg-Si alloy plate immediately before finish hot rolling is It is preferable that it is 270 degrees C or less.
• the surface temperature of the Al—Mg—Si alloy plate immediately before the final hot hot rolling is 270 ° C. or less. preferable.
• the control pass is the final pass of hot rolling, so the Al—Mg—Si system immediately before the final pass of hot rolling.
• Control pass so that the surface temperature of the alloy plate is 470 to 350 ° C., and the surface temperature of the alloy plate is 230 ° C. or less at a cooling rate of 50 ° C./min or more by rolling or forced cooling after rolling and rolling.
• the Al—Mg—Si based alloy sheet is cold rolled to obtain an Al—Mg—Si based alloy sheet having a predetermined thickness.
• Cold rolling is preferably performed at a rolling rate of 20% or more in order to improve strength.
• the rolling rate of the Al—Mg—Si based alloy sheet by cold rolling is preferably 30% or more, particularly preferably 60% or more.
• the Al—Mg—Si alloy plate after cold rolling may be cleaned as necessary.
• the strength and / or conductivity of the Al—Mg—Si based alloy sheet it is preferable to perform final annealing after cold rolling.
• the strength can be further increased by age hardening of the Al—Mg—Si based alloy plate, and the electrical conductivity can be improved.
• the conditions for final annealing can be selected depending on whether both strength and conductivity are improved or whether strength or conductivity is emphasized, but the annealing temperature becomes too high, and the strength of the Al-Mg-Si based alloy sheet is reduced. In order not to decrease, it is preferably carried out at 200 ° C. or lower, more preferably 110 ° C. or higher and 180 ° C. or lower, particularly preferably 120 ° C. or higher and 170 ° C. or lower.
• the final annealing time of the Al—Mg—Si based alloy plate may be adjusted so as to obtain necessary strength and electrical conductivity, and may be selected depending on the final annealing temperature in the range of 1 to 10 hours, for example.
• the production of the Al—Mg—Si based alloy plate of the present application may be performed by a coil or a single plate. Further, the alloy plate may be cut in an arbitrary step after the cold rolling, and the step after the cutting may be performed with a single plate, or may be slit and formed depending on the application.
• Aluminum alloy slabs having different chemical compositions shown in Table 1 were obtained by the DC casting method.
• Example 1 The aluminum alloy slab having the chemical composition number 1 in Table 1 was chamfered. Next, the homogenized treatment at 560 ° C. for 6 hours was performed on the alloy slab after chamfering in a heating furnace, and then the pre-hot rolling at 540 ° C. for 4 hours was performed by changing the temperature in the same furnace. After heating before hot rolling, a 540 ° C. slab was taken out from the heating furnace, and rough hot rolling was started. After the thickness of the alloy plate during the rough hot rolling reaches 25 mm, the final pass of the rough hot rolling is performed at an average cooling rate of 80 ° C./min from the alloy plate temperature 461 ° C. immediately before the pass, An alloy plate having a hot rolling temperature of 243 ° C. and a thickness of 12 mm was obtained. In the final pass of the rough hot rolling, the alloy plate was moved while rolling, and forced cooling was performed by water cooling in which water was sprayed on the alloy plate sequentially from above and below the portion of the rolled alloy plate.
• the alloy plate was subjected to finish hot rolling from a temperature immediately before finishing hot rolling of 241 ° C. to obtain an alloy plate having a thickness of 7.0 mm.
• the temperature of the alloy sheet immediately after the finish hot rolling was 131 ° C.
• the alloy sheet after the finish hot rolling was cold-rolled at a rolling rate of 91% and subjected to final annealing at 160 ° C. for 2 hours to obtain an aluminum alloy sheet having a product sheet thickness of 0.6 mm.
• Example 2 to 33 Comparative Examples 1 to 5
• the aluminum alloy slab shown in Table 1 was chamfered and then treated under the conditions shown in Tables 2 to 5 to obtain an aluminum alloy plate.
• homogenization treatment and heating before hot rolling are continuously performed in the same furnace, and forced cooling after the final pass of rough hot rolling is performed while rolling. It was selected from water cooling in which the alloy plate was moved and water was sprayed on the alloy plate sequentially from the upper and lower sides with respect to the part of the rolled alloy plate, air cooling to be blown and cooled after completion of the final hot hot rolling pass, and no forced cooling.
• final annealing was performed after cold rolling.
• Example 9 the final pass of rough hot rolling was used as the final pass of hot rolling, and the finish hot rolling was not performed.
• the evaluation was carried out by the method below the tensile strength and conductivity of the obtained alloy plate.
• Tensile strength was measured for JIS No. 5 specimens at room temperature by a conventional method.
• the electrical conductivity was obtained as a relative value (% IACS) when the electrical conductivity of annealed standard annealed copper (volume low efficiency 1.7241 ⁇ 10 ⁇ 2 ⁇ m) adopted internationally was 100% IACS.
• Tables 2 to 5 show the evaluation results of tensile strength and electrical conductivity.
• the tensile strength and conductivity are high values, whereas the chemical composition, hot
• the comparative example in which one of the surface temperatures of the alloy sheet immediately after the end of rolling does not satisfy the specified range of the present invention is inferior to the example in either tensile strength or electrical conductivity.
• This embodiment is an embodiment of the invention according to claims 9 to 18.
• Aluminum alloy slabs having different chemical compositions shown in Table 6 were obtained by the DC casting method.
• the ingot of the chemical composition number 120 containing rare earth used the raw material containing misch metal for casting.
• Example 101 The aluminum alloy slab having the chemical composition number 101 in Table 6 was chamfered. Next, the homogenized treatment at 570 ° C. for 5 hours was performed on the alloy slab after chamfering in a heating furnace, and then the pre-hot rolling at 540 ° C. for 4 hours was performed by changing the temperature in the same furnace. After heating before hot rolling, a 540 ° C. slab was taken out from the heating furnace, and rough hot rolling was started. After the thickness of the alloy plate during the rough hot rolling reaches 25 mm, the final pass of the rough hot rolling is performed at an average cooling rate of 80 ° C./min from the alloy plate temperature immediately before the pass of 460 ° C. An alloy plate having a hot rolling temperature of 242 ° C. and a thickness of 12 mm was obtained. In the final pass of the rough hot rolling, the alloy plate was moved while rolling, and forced cooling was performed by water cooling in which water was sprayed on the alloy plate sequentially from above and below the portion of the rolled alloy plate.
• the alloy plate was subjected to finish hot rolling from a temperature immediately before finish hot rolling of 240 ° C. to obtain an alloy plate having a thickness of 7.0 mm.
• the temperature of the alloy sheet immediately after the finish hot rolling was 130 ° C.
• the alloy sheet after the finish hot rolling was cold-rolled at a rolling rate of 91% and subjected to final annealing at 160 ° C. for 2 hours to obtain an aluminum alloy sheet having a product sheet thickness of 0.6 mm.
• Example 102 to 135, Comparative Examples 101 to 105 After chamfering the aluminum alloy slab described in Table 6, the aluminum alloy slab was processed under the conditions described in Tables 7 to 10 to obtain an aluminum alloy sheet.
• Example 41 homogenization and heating before hot rolling were continuously performed in the same furnace in all Examples and Comparative Examples, and forced cooling after the final rough hot rolling pass was performed while rolling. It was selected from water cooling in which the alloy plate was moved and water was sprayed on the alloy plate sequentially from the upper and lower sides with respect to the part of the rolled alloy plate, air cooling to be blown and cooled after completion of the final hot hot rolling pass, and no forced cooling.
• final annealing was performed after cold rolling.
• Example 109 the final pass of rough hot rolling was used as the final pass of hot rolling, and the finish hot rolling was not performed.
• the evaluation was carried out by the method below the tensile strength and conductivity of the obtained alloy plate.
• Tensile strength was measured by a conventional method at normal temperature for a JIS No. 5 test piece.
• the electrical conductivity was obtained as a relative value (% IACS) when the electrical conductivity of annealed standard annealed copper (volume low efficiency 1.7241 ⁇ 10 ⁇ 2 ⁇ m) adopted internationally was 100% IACS.
• Tables 7 to 10 show the evaluation results of tensile strength and electrical conductivity.
• the tensile strength and conductivity are high values, whereas the chemical composition, hot
• the comparative example in which one of the surface temperatures of the alloy sheet immediately after the end of rolling does not satisfy the specified range of the present invention is inferior to the example in either tensile strength or electrical conductivity.
• the present invention can be used for manufacturing an Al—Mg—Si alloy plate.

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• 2016
  • 2016-12-26 WO PCT/JP2016/088716 patent/WO2017168891A1/ja active Application Filing
  • 2016-12-26 CN CN201680080645.8A patent/CN108699663A/zh active Pending
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