TW201807210A - Al-mg-Si-based alloy material, Al-Mg-Si-based alloy plate, and method for manufacturing Al-Mg-Si-based alloy plate - Google Patents

Abstract

Provided is an Al-Mg-Si-based alloy material that has high strength while having high conductivity and good processability. The tensile strength of the Al-Mg-Si-based alloy material, which has a fibrous structure, is set to be equal to or greater than 280 MPa, and the conductivity thereof is set to be equal to or greater than 54 % IACS.

Description

Manufacturing method of Al-Mg-Si based alloy material, Al-Mg-Si based alloy plate and Al-Mg-Si based alloy plate

The present invention relates to an Al-Mg-Si-based alloy material, and particularly to an Al-Mg-Si-based alloy material having excellent thermal conductivity, electrical conductivity, strength, and processability, and having excellent thermal conductivity, electrical conductivity, strength, and workability. A method for manufacturing an Al-Mg-Si-based alloy plate having a thickness of less than 0.9 mm, and an Al-Mg-Si-based alloy plate.

Frames, metal-based printed circuit boards, and inner covers for products such as thin TVs, thin displays for personal computers, laptops, tablets, car navigation systems, portable navigation systems, portable terminals such as smartphones and cell phones Among the component materials in which the heat sink is incorporated or mounted, excellent thermal conductivity, strength, and processability for rapid heat dissipation are sought.

Pure aluminum alloys such as JIS1100, 1050, and 1070 have excellent thermal conductivity but low strength. Al-Mg alloys (5000 series alloys) such as JIS5052, which are used as high-strength materials, have significantly lower thermal conductivity and electrical conductivity than pure aluminum series alloys.

In contrast, since Al-Mg-Si-based alloys (6000-based alloys) In order to obtain good thermal conductivity and electrical conductivity and increase the strength by aging hardening, a method of using an Al-Mg-Si-based alloy to obtain an aluminum alloy plate having excellent strength, thermal conductivity, and workability is discussed.

For example, Patent Document 1 discloses a method for manufacturing an Al-Mg-Si-based alloy rolled sheet, which is characterized by containing Mg 0.1 to 0.34% by mass, Si 0.2 to 0.8% by mass, and Cu 0.22 to 1.0% by mass. Al and unavoidable impurities. Al-Mg-Si alloys with Si / Mg content ratio of 1.3 or more are semi-continuously cast into ingots with a thickness of 250 mm or more. They are pre-heated at a temperature of 400 to 540 ° C and hot rolled. After cold rolling is applied at a rolling reduction of 50 to 85%, annealing is performed at a temperature of 140 to 280 ° C.

Patent Document 2 describes a method for manufacturing an aluminum plate having excellent thermal conductivity, strength, and bending workability, which is characterized by containing Si: 0.2 to 1.5% by mass, Mg: 0.2 to 1.5% by mass, and Fe: 0.3% by mass or less. Contains one or two of Mn: 0.02 to 0.15% by mass and Cr: 0.02 to 0.15%, while the remaining part is Al and Ti in the inevitable impurities is less than 0.2%; or Cu: 0.01 ~ 1% by mass or rare earth elements: 0.01 ~ 0.2% by mass of one or two types of aluminum alloy plates are produced by continuous casting and rolling, followed by cold rolling, followed by solution treatment at 500 ~ 570 ° C Continue cold rolling at a cold rolling rate of 5 to 40%. After cold rolling, the aging treatment is heated to 150 to 190 ° C.

Patent Document 3 discloses a method for manufacturing an Al-Mg-Si-based alloy plate, which includes Si: 0.2 to 0.8% by mass, Mg: 0.3 to 1% by mass, Fe: 0.5% by mass or less, and Cu: 0.5% by mass. % Or less, further containing at least one of Ti: 0.1% by mass or less, or B: 0.1% by mass or less, The remaining part is composed of Al and unavoidable impurities, or further as an impurity, the Mn and Cr specifications are Mn: 0.1% by mass or less, and Cr: 0.1% by mass or less of Al-Mg-Si based alloy ingot is hot rolled, and further The method for manufacturing an alloy sheet that is subjected to the cold rolling step is characterized in that heat treatment is performed by holding at 200 to 400 ° C. for more than 1 hour after hot rolling to the end of cold rolling.

In addition, as described in Patent Document 3, among aluminum alloys of JIS 1000 to 7000 series, thermal conductivity and electrical conductivity show a good correlation, and aluminum alloy plates having excellent thermal conductivity have excellent electrical conductivity, and of course they can be used as The heat dissipation member material can also be used as a conductive member material.

[Prior technical literature] [Patent Literature]

[Patent Document 1] Japanese Patent Laid-Open No. 2012-62517

[Patent Document 2] Japanese Patent Laid-Open No. 2007-9262

[Patent Document 3] Japanese Patent Laid-Open No. 2003-321755

Although there are improvements in the Al-Mg-Si-based alloy plate as described above, compared to the requirements for Al-Mg-Si-based alloy plates, the performance, size, and thickness of the products that use aluminum alloy components are accompanied by high performance, miniaturization, and thinness, and high conductivity It has a higher strength than the conventional ones in addition to processability. It is difficult to obtain the necessary strength while maintaining high electrical conductivity and processability in the methods described in Patent Documents 1, 2, and 3, and it is relatively thin. The improvement of the thickness of the Al-Mg-Si-based alloy plate is also insufficient.

An object of the present invention is to provide an Al-Mg-Si-based alloy material having high electrical conductivity and good workability while having higher strength in view of the above-mentioned technical background.

Another object of the present invention is to provide an Al-Mg-Si-based alloy plate having high electrical conductivity and good processability, and at the same time having a higher strength and a thickness of less than 0.9 mm.

Another object of the present invention is to provide a method for manufacturing an Al-Mg-Si-based alloy plate having high electrical conductivity and good processability, and at the same time having higher strength.

The above problems are solved by the following means.

(1) An Al-Mg-Si based alloy material having a fiber structure with a tensile strength of 280 MPa or more and a conductivity of 54% IACS or more.

(2) The chemical composition contains Si: 0.2 to 0.8% by mass, Mg: 0.3 to 1% by mass, Fe: 0.5% by mass or less, and Cu: 0.5% by mass or less. The remainder is composed of Al and unavoidable impurities. The Al-Mg-Si-based alloy material according to the above item 1.

(3) Mn, Cr, Zn, and Ti, as impurities, are Al-Mg-Si based alloy materials described in the above item 2 with 0.1% by mass or less, respectively.

(4) An Al-Mg-Si-based alloy material having a 0.2% endurance of 230 MPa or more as described in any one of the items 1 to 3 above.

(5) An Al-Mg-Si-based alloy material having a tensile strength of 285 MPa or more according to any one of the foregoing items 1 to 3.

(6) An Al-Mg-Si-based alloy material having a tensile strength of 285 MPa or more as described in the foregoing paragraph 4.

(7) An Al-Mg-Si-based alloy plate having a tensile strength of 280 MPa or more and a conductivity of 54% IACS or more and a thickness of less than 0.9 mm.

(8) The chemical composition system contains Si: 0.2 to 0.8% by mass, Mg: 0.3 to 1% by mass, Fe: 0.5% by mass or less, and Cu: 0.5% by mass or less. The remainder is composed of Al and unavoidable impurities. The Al-Mg-Si based alloy plate described in 7.

(9) Mn, Cr, Zn, and Ti, as impurities, are Al-Mg-Si-based alloy plates as described in the preceding item 8, each having a specification of 0.1% by mass or less.

(10) The difference (TS-YS) between the tensile strength TS (MPa) and the 0.2% resistance YS (MPa) is 0 MPa or more and 30 MPa or less. The Al-Mg-Si system described in any one of the foregoing items 7 to 9 Alloy plate.

(11) The chemical composition system contains Si: 0.2 to 0.8% by mass, Mg: 0.3 to 1% by mass, Fe: 0.5% by mass or less, and Cu: 0.5% by mass or less, and further contains Ti: 0.1% by mass or less, or B: 0.1% by mass. Al-Mg-Si-based alloy material with a fibrous structure with a tensile strength of 280 MPa or more and an electrical conductivity of 54% IACS or more.

(12) The Mn, Cr, and Zn as impurities are the Al-Mg-Si-based alloy materials described in Item 11 above 0.1% by mass, respectively.

(13) Ni, V, Ga, Pb, Sn, Bi, and Zr as impurities are the Al-Mg-Si-based alloy materials described in Item 12 above 0.05% by mass, respectively.

(14) The Al-Mg-Si-based alloy material described in the preceding item 13 having an Ag specification of 0.05 mass% or less.

(15) The Al-Mg-Si-based alloy material as described in the preceding item 13 whose total content of rare earth elements as impurities is 0.1% by mass or less.

(16) The Al-Mg-Si-based alloy material described in the foregoing Item 14 with a total content of rare earth elements as impurities of 0.1% by mass or less.

(17) An Al-Mg-Si-based alloy material having a tensile strength of 285 MPa or more as described in item 11 above.

(18) An Al-Mg-Si-based alloy material having a tensile strength of 285 MPa or more as described in item 12 above.

(19) An Al-Mg-Si-based alloy material having a tensile strength of 285 MPa or more as described in item 13 above.

(20) An Al-Mg-Si-based alloy material having a tensile strength of 285 MPa or more as described in item 14 above.

(21) An Al-Mg-Si-based alloy material having a tensile strength of 285 MPa or more as described in item 15 above.

(22) An Al-Mg-Si-based alloy material having a tensile strength of 285 MPa or more as described in item 16 above.

(23) An Al-Mg-Si-based alloy material having a 0.2% endurance of 230 MPa or more as described in any one of the items 11 to 22 above.

(24) Chemical composition system contains Si: 0.2 to 0.8% by mass, Mg: 0.3 to 1% by mass, Fe: 0.5% by mass or less and Cu: 0.5% by mass or less, and further contains Ti: 0.1% by mass or less, or B: 0.1% by mass At least 1% or less, the remainder is composed of Al and unavoidable impurities, and the tensile strength is Al-Mg-Si-based alloy plate with a thickness of 280 MPa or more and a conductivity of 54% IACS or more and a thickness of less than 0.9 mm.

(25) The Mn, Cr, and Zn as impurities are each specified to be an Al-Mg-Si-based alloy sheet as described in Item 24 above 0.1 mass%.

(26) Ni, V, Ga, Pb, Sn, Bi, and Zr as impurities are Al-Mg-Si-based alloy plates as described in Item 25 above 0.05 mass%, respectively.

(27) The Al-Mg-Si-based alloy sheet described in the aforementioned Item 26 in which the specification of Ag as an impurity is 0.05% by mass or less.

(28) An Al-Mg-Si-based alloy sheet as described in the above item 26, whose total content of rare earth elements as impurities is 0.1% by mass or less.

(29) The Al-Mg-Si-based alloy sheet as described in the item 27 above, whose total content of rare earth elements as impurities is 0.1% by mass or less.

(30) The difference (TS-YS) between the tensile strength TS (MPa) and the 0.2% resistance YS (MPa) is 0 MPa or more and 30 MPa or less. The Al-Mg-Si system described in any one of the preceding items 24 to 29 Alloy plate.

(31) A method of manufacturing an Al-Mg-Si-based alloy plate by sequentially hot-rolling and cold-rolling an Al-Mg-Si-based alloy ingot, and the surface of the Al-Mg-Si-based alloy plate immediately after hot rolling A method for producing an Al-Mg-Si-based alloy sheet having a temperature of 170 ° C or lower and heat treatment at a temperature of 120 ° C or higher and less than 200 ° C before the end of cold rolling after the end of hot rolling.

(32) The chemical composition of the Al-Mg-Si alloy ingot contains Si: 0.2 to 0.8% by mass, Mg: 0.3 to 1% by mass, Fe: 0.5% by mass or less, and Cu: 0.5% by mass or less. Al and unavoidable impurities The method for producing an Al-Mg-Si-based alloy plate according to the aforementioned item 31.

(33) The manufacturing method of the Al-Mg-Si-based alloy sheet described in the foregoing Item 32, in which Mn, Cr, Zn, and Ti as impurities are each 0.1% by mass or less.

(34) A method for producing an Al-Mg-Si-based alloy sheet according to item 31 before performing heat treatment before the start of cold rolling after completion of hot rolling.

(35) A method for producing an Al-Mg-Si-based alloy sheet according to Item 32 before performing heat treatment before the start of cold rolling after completion of hot rolling.

(36) A method for producing an Al-Mg-Si-based alloy sheet according to Item 33 before performing heat treatment before the start of cold rolling after completion of hot rolling.

(37) A method for producing an Al-Mg-Si-based alloy sheet as described in the preceding item 31, in which the surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 150 ° C or lower.

(38) A method for producing an Al-Mg-Si-based alloy sheet as described in the above item 32, in which the surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 150 ° C or lower.

(39) A method for producing an Al-Mg-Si-based alloy sheet as described in the item 33 above, after the surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 150 ° C or lower.

(40) A method for producing an Al-Mg-Si-based alloy sheet as described in the foregoing item 34, in which the surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 150 ° C or lower.

(41) Manufacture of the Al-Mg-Si-based alloy sheet described in the previous item 35 after the surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 150 ° C or lower method.

(42) A method for producing an Al-Mg-Si-based alloy sheet as described in Item 36 above, in which the surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 150 ° C or lower.

(43) A method for producing an Al-Mg-Si-based alloy sheet according to the item 31 described above, in which the heat treatment temperature is 130 ° C or higher and 180 ° C or lower.

(44) A method for producing an Al-Mg-Si-based alloy sheet according to the item 32 described above in which the heat treatment temperature is 130 ° C or higher and 180 ° C or lower.

(45) A method for producing an Al-Mg-Si-based alloy sheet according to the item 33 described above, in which the heat treatment temperature is 130 ° C or higher and 180 ° C or lower.

(46) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 34, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower.

(47) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 35, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower.

(48) A method for producing an Al-Mg-Si-based alloy sheet according to the above item 36, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower.

(49) A method for producing an Al-Mg-Si based alloy sheet according to the item 37 above, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower.

(50) A method for producing an Al-Mg-Si-based alloy sheet according to the above item 38, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower.

(51) A method for producing an Al-Mg-Si based alloy plate according to the item 39 above, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower.

(52) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 40, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower.

(53) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 41, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower.

(54) A method for producing an Al-Mg-Si based alloy sheet according to the item 42 above, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower.

(55) A method for producing an Al-Mg-Si-based alloy sheet as described in Item 43 above in which the rolling reduction ratio of the cold rolling after the heat treatment is 20% or more.

(56) A method for producing an Al-Mg-Si-based alloy sheet according to the item 44 described above in which the rolling reduction ratio of the cold rolling after the heat treatment is 20% or more.

(57) A method for producing an Al-Mg-Si-based alloy sheet according to the item 45 described above, in which the rolling reduction ratio of the cold rolling after the heat treatment is 20% or more.

(58) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 46, in which the rolling reduction ratio of the cold rolling after the heat treatment is 20% or more.

(59) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 47, in which the rolling reduction ratio of the cold rolling after the heat treatment is 20% or more.

(60) A method for producing an Al-Mg-Si-based alloy sheet as described in the foregoing Item 48, in which the rolling reduction ratio of the cold rolling after the heat treatment is 20% or more.

(61) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 49, wherein the rolling reduction ratio of the cold rolling after the heat treatment is 20% or more.

(62) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 50, wherein the rolling reduction ratio of the cold rolling after the heat treatment is 20% or more.

(63) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 51, in which the rolling reduction ratio of the cold rolling after the heat treatment is 20% or more.

(64) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 52, in which the rolling reduction ratio of the cold rolling after the heat treatment is 20% or more.

(65) A method for producing an Al-Mg-Si-based alloy sheet according to the item 53 described above in a cold rolling reduction ratio of 20% or more after heat treatment.

(66) A method for producing an Al-Mg-Si-based alloy sheet as described in the foregoing Item 54 in which the reduction ratio of cold rolling after heat treatment is 20% or more.

(67) After cold rolling, the method for producing an Al-Mg-Si based alloy sheet according to item 55 before final annealing is performed.

(68) A method for producing an Al-Mg-Si-based alloy sheet according to Item 56 before final annealing after cold rolling.

(69) After cold rolling, the method for producing an Al-Mg-Si-based alloy sheet according to item 57 before final annealing is performed.

(70) The method for producing an Al-Mg-Si-based alloy sheet according to Item 58 before final annealing is performed after cold rolling.

(71) A method for producing an Al-Mg-Si-based alloy sheet according to item 59 before final annealing is performed after cold rolling.

(72) A method for producing an Al-Mg-Si-based alloy sheet according to item 60 before final annealing after cold rolling.

(73) After cold rolling, the method for producing an Al-Mg-Si based alloy sheet according to item 61 before final annealing is performed.

(74) After cold rolling, the method for producing an Al-Mg-Si-based alloy sheet according to Item 62 before final annealing is performed.

(75) The method for producing an Al-Mg-Si-based alloy sheet according to item 63 before final annealing is performed after cold rolling.

(76) A method for producing an Al-Mg-Si-based alloy sheet according to Item 64 before final annealing after cold rolling.

(77) A method for producing an Al-Mg-Si-based alloy sheet according to Item 65 before final annealing after cold rolling.

(78) A method for producing an Al-Mg-Si-based alloy sheet according to item 66 before final annealing after cold rolling.

(79) A method for producing an Al-Mg-Si-based alloy sheet according to the item 67 above, in which the final annealing temperature is 180 ° C or lower.

(80) A method for producing an Al-Mg-Si-based alloy sheet according to the item 68 described above in a final annealing temperature of 180 ° C or lower.

(81) A method for producing an Al-Mg-Si-based alloy sheet according to the item 69 above, in which the final annealing temperature is 180 ° C or lower.

(82) A method for producing an Al-Mg-Si-based alloy sheet according to the item 70 above, in which the final annealing temperature is 180 ° C or lower.

(83) A method for producing an Al-Mg-Si-based alloy sheet according to the item 71 described above, in which the final annealing temperature is 180 ° C or lower.

(84) A method for producing an Al-Mg-Si-based alloy sheet according to the item 72 above, in which the final annealing temperature is 180 ° C or lower.

(85) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 73, wherein the final annealing temperature is 180 ° C or lower.

(86) A method for producing an Al-Mg-Si-based alloy sheet according to the item 74 above, in which the final annealing temperature is 180 ° C or lower.

(87) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 75, in which the final annealing temperature is 180 ° C or lower.

(88) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 76, in which the final annealing temperature is 180 ° C or lower.

(89) A method for producing an Al-Mg-Si based alloy sheet according to the item 77 above, in which the final annealing temperature is 180 ° C or lower.

(90) A method for producing an Al-Mg-Si-based alloy sheet according to the item 78 above, in which the final annealing temperature is 180 ° C or lower.

(91) Among the plurality of passes of hot rolling, the surface temperature of the Al-Mg-Si-based alloy plate before performing the pass at least once is 470 to 350 ° C, and the Al-Mg-Si system caused by the passes The Al-Mg-Si system according to any one of the preceding paragraphs 31 to 90, in which the average cooling rate due to the cooling of the alloy plate or the pass and forced cooling after the passes is 50 ° C / min or more Manufacturing method of alloy plate.

(92) Contains Si: 0.2 to 0.8% by mass, Mg: 0.3 to 1% by mass, Fe: 0.5% by mass or less and Cu: 0.5% by mass or less, and further contains Ti: 0.1% by mass or less or B: 0.1% by mass or less Al-Mg-Si based alloy ingots composed of Al and unavoidable impurities in the remaining at least one type, a method of manufacturing a hot-rolled and cold-rolled alloy sheet in sequence, and the Al- A method for manufacturing an Al-Mg-Si-based alloy sheet having a surface temperature of 170 ° C or lower and heat-treated at a temperature of 120 ° C or higher and less than 200 ° C before the end of cold rolling after hot rolling.

(93) A method for producing Mn, Cr, and Zn as impurities, the Al-Mg-Si-based alloy sheet described in Item 92 above 0.1% by mass, respectively.

(94) A method for producing an Al-Mg-Si-based alloy sheet as described in the foregoing item 93, in which Ni, V, Ga, Pb, Sn, Bi, and Zr are specified as impurities at 0.05 mass% or less, respectively.

(95) A method for producing an Al-Mg-Si-based alloy sheet as described in the aforementioned item 94, in which the specification of Ag as an impurity is 0.05% by mass or less.

(96) A method for producing an Al-Mg-Si-based alloy sheet according to the aforementioned item 94, whose total content of rare earth elements as impurities is 0.1% by mass or less.

(97) A method for producing an Al-Mg-Si-based alloy sheet according to the aforementioned item 95, whose total content of rare earth elements as impurities is 0.1% by mass or less.

(98) A method for producing an Al-Mg-Si-based alloy sheet according to Item 92 before performing heat treatment before the start of cold rolling after the completion of hot rolling.

(99) A method for producing an Al-Mg-Si-based alloy sheet according to item 93, in which the heat treatment is performed before the start of cold rolling after the completion of hot rolling.

(100) A method for producing an Al-Mg-Si-based alloy sheet according to item 94, in which the heat treatment is performed before the start of cold rolling after the completion of hot rolling.

(101) A method for producing an Al-Mg-Si-based alloy sheet according to item 95 before performing heat treatment before the start of cold rolling after completion of hot rolling.

(102) A method for producing an Al-Mg-Si-based alloy sheet according to item 96, before subjecting the heat treatment to the start of cold rolling after the completion of hot rolling.

(103) A method for producing an Al-Mg-Si-based alloy sheet according to item 97 before performing heat treatment before the start of cold rolling after completion of hot rolling.

(104) A method for producing an Al-Mg-Si-based alloy sheet as described in Item 92 above, in which the surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 150 ° C or lower.

(105) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 93, in which the surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 150 ° C or lower.

(106) Manufacture of the Al-Mg-Si based alloy sheet described in the foregoing item 94, the surface temperature of the Al-Mg-Si based alloy sheet immediately after the hot rolling is 150 ° C or lower method.

(107) A method for producing an Al-Mg-Si-based alloy sheet as described in the foregoing item 95, in which the surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 150 ° C or lower.

(108) A method for producing an Al-Mg-Si-based alloy sheet according to the aforementioned item 96, in which the surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 150 ° C or lower.

(109) A method for producing an Al-Mg-Si-based alloy sheet according to the aforementioned item 97, in which the surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 150 ° C or lower.

(110) A method for producing an Al-Mg-Si-based alloy sheet as described in the foregoing item 98, in which the surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 150 ° C or lower.

(111) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 99, in which the surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 150 ° C or lower.

(112) A method for producing an Al-Mg-Si-based alloy sheet according to the preceding paragraph 100, in which the surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 150 ° C or lower.

(113) A method for producing an Al-Mg-Si-based alloy sheet according to the above-mentioned item 101, in which the surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 150 ° C or lower.

(114) Manufacture of the Al-Mg-Si-based alloy sheet immediately after the hot rolling has a surface temperature of 150 ° C. or lower method.

(115) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 103, in which the surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 150 ° C or lower.

(116) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 104, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower.

(117) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 105, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower.

(118) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 106, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower.

(119) A method for producing an Al-Mg-Si based alloy sheet according to the item 107 described above, in which the heat treatment temperature is 130 ° C or higher and 180 ° C or lower.

(120) A method for producing an Al-Mg-Si-based alloy sheet according to the item 108 described above, in which the heat treatment temperature is 130 ° C or higher and 180 ° C or lower.

(121) A method for producing an Al-Mg-Si-based alloy sheet according to the item 109, in which the heat treatment temperature is 130 ° C or higher and 180 ° C or lower.

(122) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 110, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower.

(123) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 111, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower.

(124) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 112, in which the heat treatment temperature is 130 ° C or higher and 180 ° C or lower.

(125) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing paragraph 113, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower.

(126) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 114, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower.

(127) A method for producing an Al-Mg-Si-based alloy sheet according to the above item 115, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower.

(128) A method for producing an Al-Mg-Si-based alloy sheet according to the aforementioned item 116, in which the reduction ratio of cold rolling after heat treatment is 20% or more.

(129) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 117, in which the rolling reduction ratio of the cold rolling after the heat treatment is 20% or more.

(130) A method for producing an Al-Mg-Si-based alloy sheet as described in the foregoing item 118 in a cold rolling reduction ratio of 20% or more after heat treatment.

(131) A method for producing an Al-Mg-Si-based alloy sheet according to the aforementioned item 119, in which the rolling reduction ratio of the cold rolling after the heat treatment is 20% or more.

(132) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 120, in which the rolling reduction ratio of the cold rolling after the heat treatment is 20% or more.

(133) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 121, in which the rolling reduction ratio of the cold rolling after the heat treatment is 20% or more.

(134) A method for producing an Al-Mg-Si-based alloy sheet according to the item 122 described above in which the rolling reduction ratio of the cold rolling after the heat treatment is 20% or more.

(135) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 123, in which the rolling reduction ratio of the cold rolling after the heat treatment is 20% or more.

(136) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 124, in which the rolling reduction ratio of the cold rolling after the heat treatment is 20% or more.

(137) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 125, wherein the rolling reduction ratio of the cold rolling after the heat treatment is 20% or more.

(138) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 126, wherein the rolling reduction ratio of the cold rolling after the heat treatment is 20% or more.

(139) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 127, in which the rolling reduction ratio of the cold rolling after the heat treatment is 20% or more.

(140) A method for producing an Al-Mg-Si-based alloy sheet according to Item 128 before final annealing after cold rolling.

(141) A method for producing an Al-Mg-Si-based alloy sheet according to item 129 before final annealing after cold rolling.

(142) A method for producing an Al-Mg-Si-based alloy sheet according to item 130 before final annealing after cold rolling.

(143) After cold rolling, the method for producing an Al-Mg-Si-based alloy sheet according to item 131 before final annealing is performed.

(144) A method for manufacturing an Al-Mg-Si-based alloy sheet according to item 132 before final annealing after cold rolling.

(145) After cold rolling, the method for producing an Al-Mg-Si based alloy sheet according to item 133 before final annealing is performed.

(146) After cold rolling, the method for producing an Al-Mg-Si-based alloy sheet according to item 134 before the final annealing is performed.

(147) After cold rolling, the method for producing an Al-Mg-Si based alloy sheet according to item 135 before final annealing is performed.

(148) A method for producing an Al-Mg-Si-based alloy sheet according to item 136 before final annealing after cold rolling.

(149) A method for producing an Al-Mg-Si-based alloy sheet according to item 137 before final annealing after cold rolling.

(150) A method for producing an Al-Mg-Si-based alloy sheet according to item 138 before final annealing after cold rolling.

(151) A method for producing an Al-Mg-Si-based alloy sheet according to item 139 before final annealing after cold rolling.

(152) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 140, in which the final annealing temperature is 180 ° C or lower.

(153) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 141, in which the final annealing temperature is 180 ° C or lower.

(154) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 142, in which the final annealing temperature is 180 ° C or lower.

(155) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 143, in which the final annealing temperature is 180 ° C or lower.

(156) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 144, in which the final annealing temperature is 180 ° C or lower.

(157) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 145, in which the final annealing temperature is 180 ° C or lower.

(158) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 146, in which the final annealing temperature is 180 ° C or lower.

(159) A method for producing an Al-Mg-Si-based alloy sheet described in the foregoing item 147 in a final annealing temperature of 180 ° C or lower.

(160) A method for producing an Al-Mg-Si-based alloy sheet described in the foregoing item 148 in a final annealing temperature of 180 ° C or lower.

(161) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 149, in which the final annealing temperature is 180 ° C or lower.

(162) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing item 150, in which the final annealing temperature is 180 ° C or lower.

(163) A method for producing an Al-Mg-Si-based alloy sheet according to the foregoing Item 151, in which the final annealing temperature is 180 ° C or lower.

(164) Among the multiple passes of hot rolling, the surface temperature of the Al-Mg-Si-based alloy sheet before the at least one pass is 470 to 350 ° C, and the Al-Mg-Si-based alloys caused by the passes The Al-Mg-Si system according to any one of the preceding paragraphs 92 to 163, in which the average cooling rate due to the cooling of the alloy plate or the pass and forced cooling after the passes is 50 ° C / min or more Manufacturing method of alloy plate.

According to the invention described in the above item (1), an Al-Mg-Si-based alloy material having a fibrous structure and having excellent strength, thermal conductivity, and processability can be obtained.

According to the invention described in the above item (2), since Si: 0.2 to 0.8% by mass, Mg: 0.3 to 1% by mass, Fe: 0.5% by mass or less and Cu: 0.5% by mass or less, the remainder is made of Al and unavoidable Containing impurities, it can be an Al-Mg-Si based alloy material with a fibrous structure that is excellent in strength, thermal conductivity, and processability.

According to the invention described in the above item (3), since the Mn, Cr, Zn, and Ti as impurities are regulated to 0.1% by mass or less, they can be Al-Mg with a fibrous structure having excellent strength, thermal conductivity, and processability -Si-based alloy material.

According to the invention described in the above item (4), the Al-Mg-Si-based alloy material having a fibrous structure with high endurance can be obtained.

According to the inventions described in the above paragraphs (5) and (6), an Al-Mg-Si-based alloy material having a fibrous structure with stronger tensile strength can be obtained.

According to the invention described in the above item (7), an Al-Mg-Si-based alloy plate having a thickness of less than 0.9 mm, which is excellent in strength, thermal conductivity, and workability, can be obtained.

According to the invention described in the above item (8), since the chemical composition system is composed of Si: 0.2 to 0.8% by mass, Mg: 0.3 to 1% by mass, Fe: 0.5% by mass or less, and Cu: 0.5% by mass or less, the remainder Since it is composed of Al and unavoidable impurities, it can be an Al-Mg-Si-based alloy plate having excellent strength, thermal conductivity, and workability.

According to the invention described in the above item (9), since the Mn, Cr, Zn, and Ti as impurities are regulated to 0.1 mass% or less, and the remaining portion is composed of Al and unavoidable impurities, it can become strength and thermal conductivity. Al-Mg-Si alloy plate with excellent workability.

According to the invention described in the above item (10), an Al-Mg-Si-based alloy plate having both strong tensile strength and high endurance can be obtained.

According to the invention described in the above item (11), the chemical composition contains Si: 0.2 to 0.8% by mass, Mg: 0.3 to 1% by mass, Fe: 0.5% by mass or less, and Cu: 0.5% by mass or less, and further contains Ti: 0.1% by mass. % Or B: At least one of 0.1% by mass or less, and the remaining portion is composed of Al and unavoidable impurities, and can be an Al-Mg-Si-based alloy material having a fibrous structure with excellent strength, thermal conductivity, and processability.

According to the invention described in the above item (12), since the Mn, Cr, and Zn as impurities are regulated to 0.1% by mass or less, they can be used as strength and heat. An Al-Mg-Si alloy material with a fibrous structure that is excellent in conductivity and workability.

According to the invention described in the above item (13), as the impurities Ni, V, Ga, Pb, Sn, Bi, and Zr are respectively regulated to 0.05 mass% or less, they can have a fibrous structure with excellent strength, thermal conductivity, and processability Al-Mg-Si based alloy.

According to the invention described in the above item (14), since the specification of Ag as an impurity is 0.05% by mass or less, it can be an Al-Mg-Si-based alloy material having a fibrous structure with excellent strength, thermal conductivity, and processability.

According to the inventions described in the above paragraphs (15) and (16), since the total content of rare earth elements as impurities is specified to be 0.1% by mass or less, it can be an Al-Mg with a fibrous structure having excellent strength, thermal conductivity, and processability. -Si-based alloy material.

According to the inventions described in the above paragraphs (17) to (22), it can be an Al-Mg-Si-based alloy material having a fibrous structure with high endurance.

According to the invention described in the above item (23), it can be an Al-Mg-Si-based alloy material having a fibrous structure with high endurance.

According to the invention described in the above item (24), the chemical composition contains Si: 0.2 to 0.8% by mass, Mg: 0.3 to 1% by mass, Fe: 0.5% by mass or less, and Cu: 0.5% by mass or less, and further contains Ti: 0.1% by mass. % Or less: B: at least one of 0.1% by mass or less, and the remaining portion is composed of Al and unavoidable impurities, and can be an Al-Mg-Si based alloy with a thickness of less than 0.9 mm, excellent in strength, thermal conductivity, and workability board.

According to the invention described in (25) above, since Mn, Cr and Zn are each specified to be 0.1 mass% or less, so they can be Al-Mg-Si based alloy plates having a thickness of less than 0.9 mm, which is excellent in strength, thermal conductivity, and workability.

According to the invention described in the above paragraph (26), as the impurities Ni, V, Ga, Pb, Sn, Bi, and Zr are respectively regulated to 0.05 mass% or less, they can be Al-Mg with excellent strength, thermal conductivity, and processability. -Si series alloy plate.

According to the invention described in the foregoing paragraph (27), the specification of Ag as an impurity is 0.05% by mass or less, and it can be an Al-Mg-Si-based alloy plate having excellent strength, thermal conductivity, and workability.

According to the inventions described in the above paragraphs (28) and (29), the total content of rare earth elements as impurities is less than 0.1% by mass, so it can be an Al-Mg-Si alloy plate with strength, thermal conductivity, and processability. .

According to the invention described in the above paragraph (30), an Al-Mg-Si-based alloy plate having both strong tensile strength and high endurance can be obtained.

According to the invention described in the above item (31), since Al-Mg-Si-based alloy ingots are sequentially subjected to a hot-rolled and cold-rolled Al-Mg-Si-based alloy sheet manufacturing method, the Al- The surface temperature of the Mg-Si alloy sheet is 170 ° C or lower, and the heat treatment is performed at a temperature of 120 ° C or higher and less than 200 ° C before the end of cold rolling after hot rolling. Therefore, an effective quenching effect due to hot rolling can be obtained. With the improvement of age hardening and electrical conductivity during heat treatment and improvement of work hardening and workability caused by cold rolling, it is possible to produce Al-Mg-Si series alloy plates with good workability showing high tensile strength and electrical conductivity. .

According to the invention described in (32) above, since the chemical composition contains Si: 0.2 to 0.8% by mass, Mg: 0.3 to 1% by mass, Fe: 0.5% by mass or less and Cu: 0.5% by mass or less. The remaining portion is composed of Al and unavoidable impurities. Al-Mg-Si-based alloy sheet is manufactured by hot rolling and cold rolling, and the surface temperature of Al-Mg-Si-based alloy sheet immediately after the hot rolling is 170 ° C or less. Before the end of cold rolling, heat treatment is performed at a temperature of 120 ° C or higher and less than 200 ° C, so the quenching effect caused by hot rolling can be obtained. The aging hardening and electrical conductivity increase during heat treatment, and the work hardening caused by cold rolling. The workability is improved, and an Al-Mg-Si-based alloy sheet having good workability showing high tensile strength and high electrical conductivity can be produced.

According to the invention described in the above item (33), since the Mn, Cr, Zn, and Ti as impurities are regulated to 0.1% by mass or less, it is possible to produce Al-Mg with good processability showing high tensile strength and electrical conductivity. -Si series alloy plate.

According to the inventions described in the above paragraphs (34) to (36), since the heat treatment is performed before the cold rolling is started after the hot rolling is completed, the aging hardening and electrical conductivity increase during the heat treatment, and the work hardening and processing caused by cold rolling The Al-Mg-Si-based alloy plate with improved processability and high workability exhibiting high tensile strength and electrical conductivity can be produced.

According to the inventions described in the foregoing paragraphs (37) to (42), since the surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 150 ° C or lower, the quenching effect due to hot rolling can be improved.

According to the inventions described in the above paragraphs (43) to (54), since the heat treatment temperature is 130 ° C or higher and 180 ° C or lower, the aging hardening and conduction can be reliably obtained. The effect of power increase.

According to the inventions described in the foregoing paragraphs (55) to (66), since the rolling reduction rate of cold rolling after heat treatment is 20% or more, good strength can be obtained while improving the strength of Al-Mg-Si based alloy plates by cold rolling. Processability.

According to the inventions described in the above paragraphs (67) to (78), since the final annealing is performed after cold rolling, it becomes the Al-Mg-Si-based alloy sheet having good workability.

According to the inventions described in the above paragraphs (79) to (90), since the final annealing temperature is 180 ° C. or lower, an Al-Mg-Si-based alloy plate having good workability showing high tensile strength and electrical conductivity can be produced.

According to the invention described in the above item (91), the surface temperature of the Al-Mg-Si based alloy sheet before the at least one pass among the plurality of passes of hot rolling is 470 to 350 ° C, and The cooling rate of the Al-Mg-Si based alloy plate, or the average cooling rate caused by the pass and forced cooling after the pass is 50 ° C / min or more, so the quenching effect by hot rolling can be improved.

According to the invention described in the above item (92), since it contains Si: 0.2 to 0.8% by mass, Mg: 0.3 to 1% by mass, Fe: 0.5% by mass or less, and Cu: 0.5% by mass or less, and further contains Ti: 0.1% by mass. The following or B: at least one of 0.1% by mass or less, an Al-Mg-Si based alloy ingot composed of Al and unavoidable impurities, and a method of manufacturing a hot-rolled and cold-rolled alloy plate in order, The surface temperature of the Al-Mg-Si-based alloy sheet immediately after the rolling is 170 ° C or lower, and the heat treatment is performed at a temperature of 120 ° C or higher and less than 200 ° C before the cold rolling ends after the hot rolling ends. The effective quenching effect can be produced by aging hardening and electrical conductivity increase during heat treatment, and work hardening and workability improvement by cold rolling. An Al-Mg-Si based alloy plate with good workability showing high tensile strength and electrical conductivity.

According to the invention described in the above item (93), since the Mn, Cr, and Zn as impurities are regulated to 0.1% by mass or less, it is possible to produce an Al-Mg-Si system with good processability that exhibits high tensile strength and electrical conductivity. Alloy plate.

According to the invention described in the above item (94), since Ni, V, Ga, Pb, Sn, Bi, and Zr as impurities are regulated to 0.05 mass% or less, the tensile strength and electrical conductivity exhibit high processability. Al-Mg-Si based alloy plate.

According to the invention described in the above item (95), since the specification of Ag as an impurity is 0.05% by mass or less, it is possible to produce an Al-Mg-Si-based alloy plate with good workability that exhibits high tensile strength and high electrical conductivity.

According to the inventions described in the above paragraphs (96) and (97), since the total content of rare earth elements as impurities is specified to be 0.1% by mass or less, it is possible to produce Al-Mg with good processability that exhibits high tensile strength and electrical conductivity. -Si series alloy plate.

In the inventions described in the above paragraphs (98) to (103), since the heat treatment is performed before the cold rolling is started after the hot rolling is completed, the aging hardening and electrical conductivity increase during the heat treatment, and the work hardening and workability caused by the cold rolling It is improved, and an Al-Mg-Si-based alloy plate having good workability exhibiting high values of tensile strength and electrical conductivity can be produced.

In the inventions described in the above paragraphs (104) to (115), since the surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 150 ° C or lower, the quenching effect by hot rolling can be improved.

In the inventions described in the above paragraphs (116) to (127), since the heat treatment temperature is 130 ° C. or higher and 180 ° C. or lower, the effects of definite age hardening and electrical conductivity improvement can be obtained.

In the inventions described in the above paragraphs (128) to (139), since the rolling reduction ratio of cold rolling after heat treatment is 20% or more, good processing can be achieved while improving the strength of Al-Mg-Si based alloy plates by cold rolling Sex.

Since the inventions described in the above paragraphs (140) to (151) are subjected to final annealing after cold rolling, they become those having good processability of Al-Mg-Si based alloy plates.

According to the inventions described in the above paragraphs (152) to (163), since the final annealing temperature is 180 ° C or lower, it is possible to produce an Al-Mg-Si-based alloy plate with good workability that exhibits high tensile strength and electrical conductivity.

The invention described in the above paragraph (164) is caused by the surface temperature of the Al-Mg-Si based alloy sheet of 470 to 350 ° C in the plurality of passes of hot rolling at least once before the pass. The cooling rate of the Al-Mg-Si series alloy plate, or the average cooling rate caused by the pass and forced cooling after the pass is 50 ° C / min or more, so the quenching effect by hot rolling can be improved.

[Fig. 1] A schematic view of a fiber structure of an Al-Mg-Si based alloy material in this case.

The inventor of the present case found that a method for producing a hot-rolled and cold-rolled Al-Mg-Si-based alloy material (including an Al-Mg-Si-based alloy plate, which is the same below) is sequentially applied. In the meantime, while the surface temperature of the hot-rolled alloy material is lower than a specific temperature, by applying heat treatment as an aging treatment before the end of cold rolling after the end of hot rolling, high conductivity and good workability can be obtained at the same time. Al-Mg-Si alloy material with higher strength finally completed the invention of this case.

Hereinafter, the Al-Mg-Si-based alloy material and the manufacturing method therefor will be described in detail.

The composition of the Al-Mg-Si alloy in this case shows the purpose of addition of each element and the preferred content.

Mg and Si are elements necessary for strength performance, and their respective contents are preferably Si: 0.2% by mass to 0.8% by mass, and Mg: 0.3% by mass to 1% by mass. When the Si content is less than 0.2% by mass or the Mg content is less than 0.3% by mass, the strength becomes low. On the other hand, if the Si content exceeds 0.8% by mass and the Mg content exceeds 1 mass, the rolling load during hot rolling becomes high and productivity decreases, and the formed aluminum alloy sheet also has poor formability. The Si content is more preferably 0.2% by mass to 0.6% by mass, and even more preferably 0.32% by mass to 0.60% by mass. The Mg content is more preferably from 0.45 mass% to 0.9 mass%, particularly from 0.45 mass% to 0.55 mass%.

Although Fe and Cu are components necessary for forming processing, if they are contained in a large amount, the corrosion resistance decreases. In this case, it is better to regulate the Fe content and Cu content to 0.5% by mass or less, respectively. The Fe content specification is more preferably 0.35 mass% or less, and particularly preferably 0.1 mass% or more and 0.25 mass% or less. The Cu content is more preferably 0.1% by mass or less.

Ti and B prevent fine crystal grains during alloy casting The effect of melting and solidifying cracking. The aforementioned effect can be obtained by adding at least one of Ti or B, or adding both of them. However, when it is contained in a large amount, a large number of crystals are formed in the crystals, which reduces the workability, thermal conductivity, and electrical conductivity of the product. 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 or less.

Although the alloy elements contain various unavoidable impurity elements, Mn and Cr decrease the conductivity and conductivity, and when the Zn content is increased, the corrosion resistance of the alloy material is reduced in a small amount. The content of each of Mn, Cr, and Zn as impurities is preferably 0.1% by mass or less, and further preferably 0.05% by mass or less.

Examples of other impurity elements other than the above include Ni, V, Ga, Pb, Sn, Bi, Zr, Ag, rare earths, and the like, but are not limited to these. Each of these other impurity elements other than rare earths The content of the element is preferably 0.05% by mass or less. The rare earths among the other impurity elements may include one or more kinds of elements, and may also be derived from a raw material for foundry contained in a cerium alloy state, but the total content of the rare earths is 0.1% by mass or less. The content is preferably not more than 0.05% by mass.

Next, the processing steps for obtaining the Al-Mg-Si-based alloy plate specified in this case will be described.

The dissolved component was adjusted by a conventional method to obtain an Al-Mg-Si-based alloy ingot. It is preferable that the obtained alloy ingot be subjected to a homogenization treatment by heating before hot rolling as a previous step.

The homogenization treatment is preferably performed at 500 ° C or higher.

The aforementioned pre-hot rolling heating is performed in order to solid-dissolve crystals, Mg, and Si into a uniform structure in an Al-Mg-Si-based alloy ingot, but if the temperature is too high, partial melting occurs in the ingot. Possibly, it is preferably performed at 450 ° C or higher and 580 ° C or lower, and particularly preferably performed at 500 ° C or higher and 580 ° C or lower.

The Al-Mg-Si alloy ingot is homogenized and then cooled. It can be heated before hot rolling, or it can be continuously homogenized and heated before hot rolling. The comparison between the aforementioned homogenization and heating before hot rolling It is also possible to heat within the optimum temperature range at the same temperature that takes into account the homogenization treatment and the heating before hot rolling.

In order to remove the impurity layer near the surface of the ingot before the hot rolling before the heating after the casting, it is better to subject the ingot to a surface shaving. The surface cutting can be performed before the homogenization treatment after casting, or before the hot rolling after the homogenization treatment.

Hot rolling is performed on the Al-Mg-Si based alloy ingot after heating before hot rolling.

The hot rolling system is composed of rough hot rolling and finish hot rolling. After rough hot rolling with a plurality of passes is performed using a rough hot rolling mill, finish hot rolling is performed using a finish hot rolling mill different from the rough hot rolling mill. In addition, in this case, when the final pass of the rough hot rolling mill is used as the final pass of the hot rolling, the final hot rolling may be omitted.

In this case, the final hot rolling is carried out by using a calender provided with successively one or more sets of work rolls or two or more sets of work rolls. The Al-Mg-Si alloy material is introduced from one direction.

When cold rolling is performed with a steel coil, a coiling device can be used to coil the Al-Mg-Si alloy material after the final hot rolling to make a hot-rolled steel coil. Omit final hot rolling, rough hot rolling When the final pass is used as the final pass of hot rolling, after rough hot rolling, an Al-Mg-Si alloy material can also be wound by a coiling device to make a hot-rolled steel coil.

In rough hot rolling, after the solution treatment of Mg and Si is maintained in a solid solution state, cooling of the Al-Mg-Si series alloy material caused by the course of rough hot rolling, or the course of rough hot rolling Quenching effect can be obtained by lowering the temperature caused by forced cooling after and after the pass.

In this case, among the multiple passes of rough hot rolling, the surface temperature of the Al-Mg-Si series alloy material before the pass is 350 ° C to 470 ° C, and the Al-Mg-Si series alloy material caused by the pass The cooling, or the pass and the forced cooling after the pass with an average cooling rate of 50 ° C / min or more are called control passes. The temperature of the surface of the Al-Mg-Si alloy plate before the control pass is 350 ° C to 470 ° C, because the quenching effect due to rapid cooling during rough hot rolling is less than 350 ° C, which is higher than 470 ° C. The rapid cooling of the Al-Mg-Si-based alloy sheet after the pass at a temperature of 50 ° C is a cause of difficulty.

The above average cooling rate is determined as the Al-Mg from the start of the control pass to the end of the forced cooling when the forced cooling is not performed during the control pass, and when the forced cooling is performed after the control pass. The value of the reduction temperature (° C) of the -Si-based alloy plate divided by the required time (minutes).

The forced cooling after controlling the passes may be performed sequentially on the rolled portion while rolling the Al-Mg-Si-based alloy plate, or may be performed after rolling the entire Al-Mg-Si-based alloy plate. The method of forced cooling is not limited, but it can be water-cooled, air-cooled, or a coolant.

It is better to implement the aforementioned control passes at least once, and it is also possible to implement plural times. When multiple control passes are implemented, after each control pass can be selected Whether to perform forced cooling. As long as the surface temperature of the Al-Mg-Si-based alloy material before the pass is 470 to 350 ° C and the cooling rate is 50 ° C / min or more, the pass can be performed a plurality of times, but it can be performed once The number of passes is controlled to reduce the temperature of the Al-Mg-Si-based alloy material to less than 350 ° C, and the quenching is performed efficiently and effectively.

In this case, when forced cooling is not performed after the final pass of rough hot rolling, the surface temperature of the Al-Mg-Si alloy material immediately after the final pass of hot rolling is set as the finish temperature of rough hot rolling. When forced cooling is performed after the final pass, the surface temperature of the Al-Mg-Si-based alloy material immediately after the completion of the forced cooling is set as the rough hot rolling finish temperature.

In the present case, the final hot rolling is completed when the final hot rolling is implemented, and when the final hot rolling is not performed, the end of the last pass of the rough hot rolling is regarded as the end of the hot rolling. The surface temperature is preferably 170 ° C or lower. The effective quenching effect can be obtained by setting the temperature of the alloy plate immediately after the hot rolling to 170 ° C or lower, and then the aging hardens and the conductivity is improved during the subsequent heat treatment.

If the surface temperature of the Al-Mg-Si-based alloy material immediately after the hot rolling is too high, the quenching effect is insufficient, and even if the heat treatment strength is increased before the cold rolling is completed after the hot rolling is completed, the strength is insufficient. The surface temperature of the Al-Mg-Si-based alloy material immediately after hot rolling is more preferably 150 ° C or less, and particularly preferably 130 ° C or less.

In addition, when performing final hot rolling after rough hot rolling, in order to obtain the quenching effect due to the final hot rolling pass, it is preferable that the surface temperature of the Al-Mg-Si based alloy material before final hot rolling is 280 ° C or lower.

Also, when the final pass of rough hot rolling is not performed and the control passes are not the same, the surface temperature of the Al-Mg-Si based alloy material before the final pass of rough hot rolling is preferably 280 ° C or lower.

On the other hand, when the final hot rolling is not performed and the final pass of the rough hot rolling is the control pass, since the control pass becomes the final pass of the hot rolling, the Al-Mg-Si before the final pass of the hot rolling The surface temperature of the base alloy material is 470 ~ 350 ℃, and the surface temperature of the Al-Mg-Si based alloy material is 170 at a cooling rate of 50 ° C / min or more by rolling or forced cooling after rolling and rolling. It is better to carry out control passes in a manner below ℃.

After the end of hot rolling, the Al-Mg-Si based alloy material before the end of cold rolling is heat-treated to age harden and increase the conductivity.

In this case, the heat treatment of the Al-Mg-Si based alloy material after the end of hot rolling and before the end of cold rolling is preferably performed at a temperature of 120 ° C or higher and less than 200 ° C in order to obtain the effects of age hardening and conductivity improvement. The temperature of the heat treatment is more preferably 130 ° C or more and 190 ° C or less, and particularly preferably 140 ° C or more and 180 ° C or less.

Although the time for heat treatment of the Al-Mg-Si based alloy material performed at a temperature of 120 ° C. or higher and less than 200 ° C. before the end of the cold rolling after the completion of the aforementioned hot rolling is not particularly limited, it is possible to obtain aging hardening and increase in electrical conductivity. For the effect method, the temperature adjustment time may be specified. For example, the heat treatment may be performed in the adjustment time range of 1 to 12 hours.

After the heat treatment, the strength is further improved by performing work hardening by cold rolling.

Improved aging hardened Al-Mg-Si alloy due to the aforementioned heat treatment The effect of strength improvement caused by the cold rolling of the material, so it is better to implement before the cold rolling starts after the hot rolling.

An Al-Mg-Si-based alloy material having a predetermined thickness is formed by cold rolling after the heat treatment. The cold rolling after the heat treatment is preferably performed at a reduction ratio of 20% or more in order to improve the strength and improve the workability. The rolling rate of the Al-Mg-Si-based alloy sheet caused by the cold rolling after the heat treatment is further more than 30%, further 50% or more, further 60% or more, and more preferably 70% or more. For aluminum materials up to 0.9mm, it is more than 60%, more preferably 70% or more, especially 80% or more.

The cold-rolled Al-Mg-Si-based alloy material may be cleaned if necessary.

When the workability of the Al-Mg-Si based alloy material is more important, the final annealing may be performed after cold rolling. In order to prevent the strength of the Al-Mg-Si alloy material from being too low, the final annealing is preferably performed at 180 ° C or lower, and further preferably at 160 ° C or lower, particularly at 140 ° C or lower.

The final annealing time of the aforementioned Al-Mg-Si based alloy material carried out at a temperature below 180 ° C may be adjusted so that the required workability and strength can be obtained, for example, in the range of 1 to 10 hours depending on the final annealing temperature. Select the temperature.

In addition, the production of the Al-Mg-Si-based alloy material in this case may be performed by a steel coil or by a single plate. In addition, the alloy sheet can be cut at any step after cold rolling and then cut with a single sheet, or it can be cut into strips according to the application.

According to the above-mentioned manufacturing method, high electrical conductivity can be obtained and strength can be improved. Al-Mg-Si based alloy material which is excellent in workability despite high strength can be obtained, and excellent in workability despite high strength. Thickness 0.9mm Al-Mg-Si based alloy plate.

The conductivity of the Al-Mg-Si based alloy material in this case is specified to be 54% IA ° C or higher, and the tensile strength is specified to be 280 MPa or higher. The tensile strength is preferably 285 MPa or more, and more preferably 290 MPa or more. The 0.2% resistance of the Al-Mg-Si alloy material in this case is preferably 230 MPa or more, further preferably 240 MPa or more, and particularly preferably 250 MPa or more. In addition, the difference (TS-YS) between the tensile strength TS (MPa) and the 0.2% endurance YS (MPa) of the Al-Mg-Si-based alloy sheet in this case is preferably 0 MPa or more and 30 MPa or less, and TS-YS is further 0 MPa or more. It is preferably below 20 MPa.

The Al-Mg-Si-based alloy material in this case preferably has a fibrous structure. The fibrous structure is a metal structure drawn by plastic working.

FIG. 1 is a schematic view showing a fiber structure of an Al-Mg-Si based alloy material of the present case.

As shown in Figure 1, in this case, the normal of the observation surface is to expose the metal structure perpendicular to both the processing direction vector of the Al-Mg-Si based alloy material and the normal direction vector of the processing surface. The grain boundary in the normal direction of the metal structure of the observation surface of the microscope observation surface is 3/100 μm or more, and the metal structure having grain boundaries with a length in the processing direction of 300 μm or more is defined as a fibrous structure. In addition, the plastic processing is a rolling delay, the processing direction is a rolling direction, the processing surface is a rolling surface, and the observation surface is a cross section in a thickness direction cut parallel to the rolling direction.

As a method for exposing the metal structure, the surface of an Al-Mg-Si-based alloy material whose grinding normal is perpendicular to the processing direction vector of the Al-Mg-Si-based alloy material and the normal direction vector of the processed surface can be exemplified. Polishing the polished surface Method of extreme oxidation treatment. As the anodizing treatment solution, Barker's solution (3% aqueous solution of fluoboric acid) can be suitably used.

[Example]

Examples and comparative examples of the present invention are shown below.

(First Embodiment)

This embodiment is an embodiment related to the inventions of claims 1 to 6.

Aluminum alloy steel blanks having different chemical compositions shown in Table 1 were obtained by the DC casting method.

[Example 1]

The aluminum alloy steel blank of chemical composition number 1 in Table 1 was subjected to face cutting. Next, the alloy steel blank after the face-cutting was subjected to a homogenization treatment at 560 ° C. for 5 hours in a heating furnace, and then the temperature was changed in the same furnace to perform heating at 540 ° C. for 4 hours before hot rolling. Take out the steel billet heated at 540 ℃ before hot rolling from the heating furnace and start rough hot rolling. After the thickness of the alloy sheet during rough hot rolling becomes 25 mm, the temperature of the alloy sheet before the pass is from 450 ° C at an average cooling rate of 80 ° C / min. The final pass of the rough hot rolling is performed to obtain a rough hot rolling finish temperature of 221 ℃ 12mm thick alloy plate. In addition, in the final pass of the rough hot rolling, the alloy plate is moved while being rolled, and forced cooling by spraying water onto the alloy plate from above and below is performed on the rolled alloy plate in order.

After the rough hot rolling, the alloy sheet was subjected to finish hot rolling from a temperature of 219 ° C before the finish hot rolling to obtain an alloy sheet having a thickness of 7.0 mm. Immediately after finishing hot rolling The temperature of the alloy plate was 110 ° C. After the alloy sheet after the final hot rolling was subjected to a heat treatment at 170 ° C. for 5 hours, cold rolling was performed at a rolling rate of 98% to obtain an aluminum alloy sheet having a product thickness of 0.15 mm.

[Examples 2 to 40, Comparative Examples 1 to 6]

After the aluminum alloy steel blanks described in Table 1 are subjected to face shaving, the conditions described in Tables 2 to 6 are treated to obtain aluminum alloy plates. In addition, as in Example 1, the homogenizing treatment and heating before hot rolling were continuously performed in the same furnace in all the examples and comparative examples, and forced cooling after the final pass of rough hot rolling was performed. The alloy plate was selected to be rolled while rolling. Moving the part of the rolled alloy sheet sequentially sprays water to the alloy sheet from above and below, either water cooling or air cooling after the final pass of rough hot rolling is performed by air cooling. In some examples, final annealing is performed after cold rolling.

In Example 15, the final pass of the rough hot rolling was used as the final pass of the hot rolling, and the final hot rolling was not performed.

In Comparative Example 1 and Comparative Example 2, during the cold rolling, a heat treatment was performed at 550 ° C for 1 minute, and then a solution treatment was performed at a rate of 5 ° C / second or more. In Comparative Example 1 and Comparative Example 2, the cold rolling rate is the total reduction ratio of the cold rolling after the solution treatment, and the cold rolling after the solution treatment is the cold rolling rate of the alloy material thickness after the solution treatment. 30% way to implement.

The obtained alloy sheet was evaluated for tensile strength, 0.2% endurance, electrical conductivity, and workability by the following methods.

Tensile strength and 0.2% endurance were measured by a normal method on a JIS No. 5 test piece at normal temperature.

The conductivity is calculated by taking the conductivity of annealed standard soft copper (1.7241 × 10 ^-2 μΩm) adopted internationally as the relative value (% IACS) at 100% IACS.

For workability, the bending angle is set to 90 °. When the thickness of the alloy plate is 0.4 mm or more, the thickness of the respective alloy plate is set to the inside radius of the bend. In the 6.3V block method of the JIS Z 2248 bending test method for metallic materials, the bending test was evaluated as ○ for those who did not break, and × when the crack occurred.

In Examples and Comparative Examples, when the metal structure of the cross section of the Al-Mg-Si-based alloy plate in the thickness direction cut parallel to the rolling direction is exposed, the grains in the normal direction of the rolling surface of the metal structure observed with an optical microscope are exposed. A metal structure having three boundaries / 100 μm or more and a grain boundary having a length in the rolling direction of 300 μm or more is defined as a fibrous structure.

As a method for exposing the metal structure, an Al-Mg-Si-based alloy plate is cross-sectioned in parallel to the rolling direction by grinding with emery paper, rough-grinding and fine-grinding are performed, and then water washing and drying are performed. A method of applying an anodizing treatment to a Barker's solution (3% aqueous solution of fluoboric acid) under conditions of a bath temperature: 28 ° C., an applied voltage: 30 V, and an applied time: 90 seconds.

Evaluation results of tensile strength, 0.2% endurance, electrical conductivity, and processability, Tables 7 and 8 show whether the Al-Mg-Si-based alloy plate has a fibrous structure.

The Al-Mg-Si based alloy material described in the examples that satisfy the chemical composition, tensile strength, and electrical conductivity specified in this case and have a fibrous structure also has good processability. On the other hand, in Comparative Examples 1 and 2 in which solution treatment was performed during cold rolling, the conductivity was worse than that of the examples in this case, and the tensile strength or At least one of the electrical conductivity was inferior to that of the examples, and there were also those having poor processability.

(Second embodiment)

This embodiment is an embodiment related to the inventions of claims 7 to 10.

Aluminum alloy steel billets having different chemical compositions shown in Table 9 were obtained by the DC casting method.

[Example 101]

The aluminum alloy steel billet with the chemical composition number 101 in Table 9 was subjected to face cutting. Next, the alloy steel blank after the face-cutting was subjected to a homogenization treatment at 560 ° C. for 5 hours in a heating furnace, and then the temperature was changed in the same furnace to perform heating at 540 ° C. for 4 hours before hot rolling. Take out the steel billet heated at 540 ℃ before hot rolling from the heating furnace and start rough hot rolling. After the thickness of the alloy sheet during rough hot rolling becomes 25 mm, the average pass rate of the rough hot rolling is 80 ° C / min from the temperature of the alloy sheet before the pass of 450 ° C, and the final pass of the rough hot rolling is 221. ℃ 12mm thick alloy plate. In addition, in the final pass of the rough hot rolling, the alloy plate is moved while being rolled, and forced cooling by spraying water onto the alloy plate from above and below is performed on the rolled alloy plate in order.

After rough hot rolling, the alloy sheet is solidified from a temperature of 219 ° C before the final hot rolling. After final hot rolling, an alloy plate having a thickness of 7.0 mm was obtained. The temperature of the alloy sheet immediately after the finish hot rolling was 110 ° C. After the alloy sheet after the final hot rolling was subjected to a heat treatment at 170 ° C. for 5 hours, cold rolling was performed at a rolling rate of 98% to obtain an aluminum alloy sheet having a product thickness of 0.15 mm.

[Examples 102 to 140, Comparative Examples 101 to 106]

After subjecting the aluminum alloy steel blanks described in Table 9 to surface shaving, the conditions described in Tables 10 to 14 were treated to obtain aluminum alloy plates. In addition, as in Example 101, the homogenization treatment and the heating before hot rolling were continuously performed in the same furnace in all Examples and Comparative Examples, and forced cooling after the final pass of rough hot rolling was selected. The alloy plate was selected while rolling. Moving the part of the rolled alloy sheet sequentially sprays water to the alloy sheet from above and below, either water cooling or air cooling after the final pass of rough hot rolling is performed by air cooling. In some examples, final annealing is performed after cold rolling.

In Example 115, the final pass of the rough hot rolling was used as the final pass of the hot rolling, and the final hot rolling was not performed.

In Comparative Example 101 and Comparative Example 102, a solution treatment was performed at a rate of 5 ° C / second or more after a heat treatment of 550 ° C for 1 minute was performed during cold rolling. In Comparative Example 101 and Comparative Example 102, the cold rolling rate is the total reduction ratio of the cold rolling after the solution treatment, and the cold rolling after the solution treatment is the cold rolling rate of the alloy material thickness after the solution treatment. 30% way to implement.

The obtained alloy sheet was evaluated for tensile strength, 0.2% endurance, electrical conductivity, and workability by the following methods.

Tensile strength and 0.2% endurance were measured by a normal method on a JIS No. 5 test piece at normal temperature.

The conductivity is calculated by taking the conductivity of annealed standard soft copper (1.7241 × 10 ^-2 μΩm) adopted internationally as the relative value (% IACS) at 100% IACS.

For workability, the bending angle is set to 90 °. When the thickness of the alloy plate is 0.4 mm or more, the thickness of the respective alloy plate is set to the inner radius of the bend. When the thickness of the alloy plate is less than 0.4 mm, the inner radius of the bend is set to 0. In the 6.3V block method of the JIS Z 2248 bending test method for metallic materials, the bending test was evaluated as ○ for those who did not break, and × when the crack occurred.

The evaluation results of tensile strength, 0.2% endurance, electrical conductivity, and processability are shown in Tables 15 and 16.

The Al-Mg-Si-based alloy material described in the examples that satisfy the chemical composition, tensile strength, and electrical conductivity specified in this case is also good in workability. On the other hand, in Comparative Examples 101 and 102, which were subjected to a solution treatment during cold rolling, the conductivity was worse than that of the examples in this case, and the comparative examples 103 to 106 of which the chemical composition did not satisfy the range specified in this case had tensile strength or Up to One less is worse than the examples, and there are also those with poor processability.

(Third embodiment)

This embodiment is an embodiment related to the inventions of claims 11 to 23.

Aluminum alloy steel blanks having different chemical compositions shown in Table 17 were obtained by the DC casting method.

[Example 201]

The aluminum alloy steel blank of chemical composition number 201 in Table 17 was subjected to face cutting. Next, the surface-cut alloy steel billet was subjected to a homogenization treatment at 570 ° C for 3 hours in a heating furnace, and then the temperature was changed in the same furnace to perform heating before hot rolling at 540 ° C for 4 hours. Take out the steel billet heated at 540 ℃ before hot rolling from the heating furnace and start rough hot rolling. After the thickness of the alloy sheet during rough hot rolling becomes 25 mm, the average pass rate of the rough hot rolling is 80 ° C / min from the temperature of the alloy sheet before the pass of 451 ° C, and the final pass of the rough hot rolling is 222. ℃ 12mm thick alloy plate. In addition, in the final pass of the rough hot rolling, the alloy plate is moved while being rolled, and forced cooling by spraying water onto the alloy plate from above and below is performed on the rolled alloy plate in order.

After the rough hot rolling, the alloy sheet was subjected to finish hot rolling from a temperature of 220 ° C. before the finish hot rolling to obtain an alloy sheet having a thickness of 7.0 mm. The temperature of the alloy sheet immediately after the finish hot rolling was 111 ° C. After the alloy sheet after the final hot rolling was subjected to a heat treatment at 170 ° C. for 5 hours, cold rolling was performed at a rolling rate of 98% to obtain an aluminum alloy sheet having a product thickness of 0.15 mm.

[Examples 202 to 242, Comparative Examples 201 to 206]

After the aluminum alloy steel blanks described in Table 17 are subjected to surface shaving, the conditions described in Tables 18 to 22 are treated to obtain aluminum alloy plates. In addition, as in Example 201, the homogenization treatment and the heating before hot rolling were continuously performed in the same furnace in all Examples and Comparative Examples. The rough cooling was forcedly cooled after the final pass, and the alloy plate was selected to be rolled while rolling. Moving the part of the rolled alloy sheet sequentially sprays water to the alloy sheet from above and below, either water cooling or air cooling after the final pass of rough hot rolling is performed by air cooling. In some examples, final annealing is performed after cold rolling.

In Example 215, the final pass of the rough hot rolling was used as the final pass of the hot rolling, and the final hot rolling was not performed.

In Comparative Example 201 and Comparative Example 202, during the cold rolling, a heat treatment was performed at 550 ° C for 1 minute, and then a solution treatment was performed at a rate of 5 ° C / second or more. In Comparative Example 201 and Comparative Example 202, the cold rolling rate is the total reduction ratio of the cold rolling after the solution treatment, and the cold rolling after the solution treatment is the cold rolling rate of the alloy material thickness after the solution treatment. 30% way to implement.

The obtained alloy sheet was evaluated for tensile strength, 0.2% endurance, electrical conductivity, and workability by the following methods.

Tensile strength and 0.2% endurance were measured by a normal method on a JIS No. 5 test piece at normal temperature.

The conductivity is calculated by taking the conductivity of annealed standard soft copper (1.7241 × 10 ^-2 μΩm) adopted internationally as the relative value (% IACS) at 100% IACS.

For workability, the bending angle is set to 90 °. When the thickness of the alloy plate is 0.4 mm or more, the thickness of the respective alloy plate is set to the inside radius of the bend. In the 6.3V block method of the JIS Z 2248 bending test method for metallic materials, the bending test was evaluated as ○ for those who did not break, and × when the crack occurred.

In Examples and Comparative Examples, when the metal structure of the cross section of the Al-Mg-Si-based alloy plate in the thickness direction cut parallel to the rolling direction is exposed, the grains in the normal direction of the rolling surface of the metal structure observed with an optical microscope are exposed A metal structure having three boundaries / 100 μm or more and a grain boundary having a length in the rolling direction of 300 μm or more is defined as a fibrous structure.

As a method for exposing the metal structure, an Al-Mg-Si-based alloy plate is cross-sectioned in parallel to the rolling direction by grinding with emery paper, rough-grinding and fine-grinding are performed, and then water washing and drying are performed. A method of applying an anodizing treatment to a Barker's solution (3% aqueous solution of fluoboric acid) under conditions of a bath temperature: 28 ° C., an applied voltage: 30 V, and an applied time: 90 seconds.

The evaluation results of tensile strength, 0.2% endurance, electrical conductivity, and workability, and whether the Al-Mg-Si-based alloy sheet has a fibrous structure are shown in Table 23 and Table 24.

The Al-Mg-Si based alloy material described in the examples that satisfy the chemical composition, tensile strength, and electrical conductivity specified in this case and have a fibrous structure also has good processability. On the other hand, in Comparative Examples 201 and 202, which were subjected to a solution treatment during cold rolling, the conductivity was worse than that of the examples in this case, and Comparative Examples 203 to 206, whose chemical composition did not satisfy the range specified in this case, had tensile strength or At least one of the electrical conductivity was inferior to that of the examples, and there were also those having poor processability.

(Fourth embodiment)

This embodiment is an embodiment regarding the inventions of claims 24 to 30.

By the DC casting method, aluminum alloy steel billets having different chemical compositions shown in Table 25 were obtained.

[Example 301]

The aluminum alloy steel blank of chemical composition number 301 in Table 25 was subjected to face cutting. Next, the surface-cut alloy steel billet was subjected to a homogenization treatment at 570 ° C for 3 hours in a heating furnace, and then the temperature was changed in the same furnace to perform heating before hot rolling at 540 ° C for 4 hours. Take out the steel billet heated at 540 ℃ before hot rolling from the heating furnace and start rough hot rolling. After the thickness of the alloy sheet during rough hot rolling becomes 25 mm, the average pass rate of the rough hot rolling is 80 ° C / min from the temperature of the alloy sheet before the pass of 451 ° C, and the final pass of the rough hot rolling is 222. ℃ 12mm thick alloy plate. In addition, in the final pass of the rough hot rolling, the alloy plate is moved while being rolled, and forced cooling by spraying water onto the alloy plate from above and below is performed on the rolled alloy plate in order.

After the rough hot rolling, the alloy sheet was subjected to finish hot rolling from a temperature of 220 ° C. before the finish hot rolling to obtain an alloy sheet having a thickness of 7.0 mm. The temperature of the alloy sheet immediately after the finish hot rolling was 111 ° C. After the alloy sheet after the final hot rolling was subjected to a heat treatment at 170 ° C. for 5 hours, cold rolling was performed at a rolling rate of 98% to obtain an aluminum alloy sheet having a product thickness of 0.15 mm.

[Examples 302 to 342, Comparative Examples 301 to 306]

After the aluminum alloy steel blanks described in Table 25 are subjected to surface shaving, the conditions described in Tables 26 to 30 are treated to obtain aluminum alloy plates. In addition, as in Example 301, the homogenization treatment and heating before hot rolling were continuously performed in the same furnace in all Examples and Comparative Examples, and forced cooling after the final pass of rough hot rolling was performed. The alloy plate was selected while rolling. Moving the part of the rolled alloy sheet sequentially sprays water to the alloy sheet from above and below, either water cooling or air cooling after the final pass of rough hot rolling is performed by air cooling. In some examples, final annealing is performed after cold rolling.

In Example 315, the final pass of the rough hot rolling was used as the final pass of the hot rolling, and the final hot rolling was not performed.

In Comparative Example 301 and Comparative Example 302, during the cold rolling, a heat treatment was performed at 550 ° C for 1 minute, and then a solution treatment was performed at a rate of 5 ° C / second or more. In Comparative Example 301 and Comparative Example 302, the cold rolling rate is the total reduction ratio of the cold rolling after the solution treatment, and the cold rolling after the solution treatment is the cold rolling rate of the alloy material thickness after the solution treatment 30% way to implement.

The obtained alloy sheet was evaluated for tensile strength, 0.2% endurance, electrical conductivity, and workability by the following methods.

Tensile strength and 0.2% endurance were measured by a normal method on a JIS No. 5 test piece at normal temperature.

The conductivity is calculated by taking the conductivity of annealed standard soft copper (1.7241 × 10 ^-2 μΩm) adopted internationally as the relative value (% IACS) at 100% IACS.

For workability, the bending angle is set to 90 °. When the thickness of the alloy plate is 0.4 mm or more, the thickness of the respective alloy plate is set to the inside radius of the bend. In the 6.3V block method of the JIS Z 2248 bending test method for metallic materials, the bending test was evaluated as ○ for those who did not break, and × when the crack occurred.

The evaluation results of tensile strength, 0.2% resistance, electrical conductivity, and processability are shown in Tables 31 and 32.

The Al-Mg-Si-based alloy material described in the examples that satisfy the chemical composition, tensile strength, and electrical conductivity specified in this case is also good in workability. On the other hand, in Comparative Examples 301 and 302, which were subjected to a solution treatment during cold rolling, the conductivity was worse than that of the examples in this case, and the comparative examples 303 to 306, whose chemical composition did not satisfy the range specified in this case, had tensile strength or Up to One less is worse than the examples, and there are also those with poor processability.

(Fifth Embodiment)

This embodiment is an embodiment related to the inventions of claims 31 to 91.

Aluminum alloy steel blanks having different chemical compositions shown in Table 33 were obtained by the DC casting method.

[Example 401]

The aluminum alloy steel blank of chemical composition number 401 in Table 33 was subjected to face cutting. Next, the alloy steel blank after the face-cutting was subjected to a homogenization treatment at 560 ° C. for 5 hours in a heating furnace, and then the temperature was changed in the same furnace to perform heating at 540 ° C. for 4 hours before hot rolling. Take out the steel billet heated at 540 ℃ before hot rolling from the heating furnace and start rough hot rolling. After the thickness of the alloy sheet during the rough hot rolling becomes 25 mm, the average temperature of the alloy sheet before the pass is 450 ° C, and the average cooling rate is 80 ° C / min. ℃, 12mm thick alloy plate. In addition, in the final pass of the rough hot rolling, the alloy plate is moved while being rolled, and forced cooling by spraying water onto the alloy plate from above and below is performed on the rolled alloy plate in order.

After the rough hot rolling, the alloy sheet was subjected to finish hot rolling from a temperature of 220 ° C. before the finish hot rolling to obtain an alloy sheet having a thickness of 7.0 mm. The temperature of the alloy sheet immediately after the finish hot rolling was 110 ° C. After the final hot-rolled alloy plate was subjected to a heat treatment at 170 ° C. for 5 hours, cold rolling was performed at a processing degree of 98% to obtain an aluminum alloy plate with a product thickness of 0.15 mm.

[Examples 402 to 445, Comparative Examples 401 to 407]

After the aluminum alloy steel blanks described in Table 33 are subjected to surface shaving, the conditions described in Tables 34 to 39 are treated to obtain aluminum alloy plates. In addition, as in Example 401, the homogenization treatment and heating before hot rolling were continuously performed in the same furnace in all Examples and Comparative Examples, and forced cooling after the final pass of rough hot rolling was performed by rolling the alloy while rolling. The plate is moved from the top to the bottom of the rolled alloy plate by spraying water on the alloy plate from top to bottom, water cooling by air cooling after the final pass of rough hot rolling, and air cooling without forced cooling. In some examples, final annealing is performed after cold rolling.

In Example 417, the final pass of the rough hot rolling was used as the final pass of the hot rolling, and the final hot rolling was not performed.

The tensile strength, electrical conductivity, and workability of the obtained alloy plate were evaluated by the following methods.

The tensile strength was measured by a normal method with respect to a JIS No. 5 test piece at room temperature.

The conductivity is calculated by taking the conductivity of annealed standard soft copper (1.7241 × 10 ^-2 μΩm) adopted internationally as the relative value (% IACS) at 100% IACS.

For workability, the bending angle is set to 90 °. When the thickness of the alloy plate is 0.4 mm or more, the thickness of each alloy plate is set to the inner radius of the bend. In the 6.3V block method of the JIS Z 2248 bending test method for metallic materials, the bending test was evaluated as ○ for those who did not break, and × when the crack occurred.

The evaluation results of tensile strength, electrical conductivity, and processability are shown in Tables 34 to 39.

In the example, the surface temperature of the Al-Mg-Si alloy sheet immediately after the hot rolling was 170 ° C or lower, and the heat treatment temperature before the cold rolling was completed after the hot rolling was in the range of 120 to 195 ° C. Comparative example 401, in which at least one of the surface temperature of the alloy sheet immediately after the end of hot rolling or the heat treatment temperature before the end of cold rolling after the end of hot rolling did not satisfy the range specified in the case, showed high values of strength and conductivity. In Comparative Example 402 and Comparative Example 403, one of the tensile strength and the electrical conductivity was inferior to the examples. In addition, Comparative Example 404 with less Si content than in Example, Comparative Example 405 with more Si content than Example, Comparative Example 406 with less Mg content than Example, and Comparative Example 407 with more Mg content than Example, also tensile strength Or at least one of the electrical conductivity Poor, Comparative Example 405 and Comparative Example 407 also had poor processability.

(Embodiment 6)

This embodiment is an embodiment related to the invention of claims 92 to 164.

Aluminum alloy steel blanks having different chemical compositions shown in Table 40 were obtained by the DC casting method. In addition, an ingot having a chemical composition number 20 containing a rare earth is used as a raw material for a cerium alloy for casting.

[Example 501]

The aluminum alloy steel blank of chemical composition number 501 in Table 40 was subjected to face cutting. Next, after the surface-cut alloy steel billet was subjected to a homogenization treatment at 570 ° C for 4 hours in a heating furnace, the temperature was changed to 540 ° C for 3 hours before hot rolling in the same furnace. Take out the steel billet heated at 540 ℃ before hot rolling from the heating furnace and start rough hot rolling. After the thickness of the alloy sheet during the rough hot rolling becomes 25 mm, the average temperature of the alloy sheet before the pass is 450 ° C, and the average cooling rate is 80 ° C / min. ℃ 12mm thick alloy plate. In addition, in the final pass of the rough hot rolling, the alloy plate is moved while being rolled, and forced cooling by spraying water onto the alloy plate from above and below is performed on the rolled alloy plate in order.

After the rough hot rolling, the alloy sheet was subjected to finish hot rolling from a temperature of 218 ° C before the finish hot rolling to obtain an alloy sheet having a thickness of 7.0 mm. The temperature of the alloy sheet immediately after the finish hot rolling was 110 ° C. After the alloy sheet after the final hot rolling was subjected to a heat treatment at 170 ° C. for 5 hours, cold rolling was performed at a rolling rate of 98% to obtain an aluminum alloy sheet having a product thickness of 0.15 mm.

[Examples 502 to 547, Comparative Examples 501 to 507]

After the aluminum alloy steel slabs described in Table 40 are subjected to surface shaving, the conditions described in Tables 41 to 46 are treated to obtain aluminum alloy plates. In addition, as in Example 501, the homogenization treatment and the heating before hot rolling were continuously performed in the same furnace in all Examples and Comparative Examples. The forced cooling after the final pass of the rough hot rolling was performed by rolling the alloy while rolling. The plate is moved from the top to the bottom of the rolled alloy plate by spraying water on the alloy plate from top to bottom, water cooling by air cooling after the final pass of rough hot rolling, and air cooling without forced cooling. In some examples, final annealing is performed after cold rolling.

In Example 517, the final pass of the rough hot rolling was used as the final pass of the hot rolling, and the final hot rolling was not performed.

The tensile strength, electrical conductivity, and workability of the obtained alloy plate were evaluated by the following methods.

The tensile strength was measured by a normal method with respect to a JIS No. 5 test piece at room temperature.

The conductivity is calculated by taking the conductivity of annealed standard soft copper (1.7241 × 10 ^-2 μΩm) adopted internationally as the relative value (% IACS) at 100% IACS.

For workability, the bending angle is set to 90 °. When the thickness of the alloy plate is 0.4 mm or more, the thickness of the respective alloy plate is set to the inner radius of the bend. When the thickness of the alloy plate is less than 0.4 mm, the inner radius of the bend is set to 0. In the 6.3V block method of the JIS Z 2248 bending test method for metallic materials, the bending test was evaluated as ○ for those who did not break, and × when the crack occurred.

The evaluation results of tensile strength, electrical conductivity, and workability are shown in Tables 41 to 46.

Relative to the chemical composition specified in this case, the surface temperature of the alloy sheet immediately after the hot rolling is 170 ° C or lower, and the heat treatment temperature before the end of the cold rolling is 120 ° C or higher and less than 200 ° C. In the example, the tensile strength and electrical conductivity show high values and the workability is also good. At least one of the chemical composition specified in this case, the surface temperature of the alloy sheet immediately after the hot rolling, or the heat treatment temperature before the cold rolling after the hot rolling is completed. The comparative examples that did not satisfy the range specified in the present case, at least one of the tensile strength or the electrical conductivity were inferior to the examples, and there were those with poor processability.

This case is accompanied by Japanese Patent Application No. 2016-67345, Japanese Patent Application No. 2016-67346, Japanese Patent Application, which were filed on March 30, 2016. Priority claimants of 2016-67349, 2016-67350, 2016-67353 and 2016-67354, these disclosures directly constitute a part of this case.

It should be recognized that the terms and expressions used herein are for the purpose of illustration, not for the purpose of restrictive interpretation, nor do they exclude any equivalents of the characteristic matters disclosed and described herein, and also Various modifications within the scope claimed by the present invention are allowed.

The present invention can be embodied in many different ways, but the disclosure should be considered as examples that provide the principles of the invention, and it is understood that these embodiments are not intended to limit the invention to those described and / or illustrated herein. In addition to the preferred embodiments, a plurality of illustrated embodiments are described here.

Although several embodiments of the present invention are described here, the present invention is not limited to the various preferred embodiments described herein, and can be identified by the practitioner based on the present disclosure, and also includes elements with equivalents and modifications. , Delete, combine (for example, a combination of features across various embodiments), improve and / or change all embodiments. The limited items of the claim should be widely interpreted based on the terms used in the claim, and should not be limited to the embodiments described in the description or the examination stage of this application. Such embodiments should be interpreted as non-exclusive.

[Industrial availability]

The present invention can be used in the production of Al-Mg-Si based alloy materials and alloy plates.

Claims (164)

An Al-Mg-Si based alloy material characterized by a tensile strength of 280 MPa or more, a conductivity of 54% IACS or more, and a fibrous structure. For example, the chemical composition of the Al-Mg-Si alloy material of claim 1 contains Si: 0.2 to 0.8% by mass, Mg: 0.3 to 1% by mass, Fe: 0.5% by mass or less, and Cu: 0.5% by mass or less. The rest It is composed of Al and unavoidable impurities. For example, the Al-Mg-Si-based alloy material according to claim 2, wherein the Mn, Cr, Zn, and Ti as impurities are each specified to be 0.1% by mass or less. For example, if the Al-Mg-Si alloy material of any one of claim 1 to claim 3, the 0.2% resistance is 230 MPa or more. For the Al-Mg-Si based alloy material according to any one of claim 1 to claim 3, the tensile strength is 285 MPa or more. For example, the Al-Mg-Si alloy material according to claim 4 has a tensile strength of 285 MPa or more. An Al-Mg-Si based alloy plate is characterized by a tensile strength of 280 MPa or more, a conductivity of 54% IACS or more, and a thickness of less than 0.9 mm. For example, the chemical composition of the Al-Mg-Si alloy sheet according to claim 7 contains Si: 0.2 to 0.8% by mass, Mg: 0.3 to 1% by mass, Fe: 0.5% by mass or less, and Cu: 0.5% by mass or less. The rest It is composed of Al and unavoidable impurities. For example, the Al-Mg-Si-based alloy sheet according to claim 8, wherein the Mn, Cr, Zn, and Ti as impurities are each specified to be 0.1% by mass or less. For example, if the Al-Mg-Si based alloy sheet of any one of claim 7 to claim 9, the difference between the tensile strength TS (MPa) and the 0.2% resistance YS (MPa) (TS-YS) is 0 MPa or more and 30 MPa. the following. An Al-Mg-Si based alloy material whose chemical composition contains Si: 0.2 to 0.8% by mass, Mg: 0.3 to 1% by mass, Fe: 0.5% by mass or less, and Cu: 0.5% by mass or less, and further contains Ti: 0.1 Mass% or less: B: At least one mass of 0.1% by mass or less. The remaining portion is composed of Al and unavoidable impurities. Its tensile strength is 280 MPa or more, the conductivity is 54% IACS or more, and it has a fibrous structure. For example, the Al-Mg-Si alloy material according to claim 11, wherein the Mn, Cr, and Zn as impurities are specified to be 0.1% by mass or less. For example, the Al-Mg-Si-based alloy material of claim 12, wherein Ni, V, Ga, Pb, Sn, Bi, and Zr as impurities are regulated to 0.05 mass% or less, respectively. For example, the Al-Mg-Si alloy material according to claim 13, wherein the specification of Ag as an impurity is 0.05% by mass or less. For example, the Al-Mg-Si alloy material according to claim 13, wherein the total content of rare earth elements as impurities is specified to be 0.1% by mass or less. For example, the Al-Mg-Si alloy material according to claim 14, wherein the total content of rare earth elements as impurities is specified to be 0.1% by mass or less. For example, the Al-Mg-Si alloy material according to claim 11 has a tensile strength of 285 MPa or more. For example, the Al-Mg-Si alloy material according to claim 12 has a tensile strength of 285 MPa or more. For example, the Al-Mg-Si alloy material according to claim 13 has a tensile strength of 285 MPa or more. For example, the Al-Mg-Si alloy material according to claim 14 has a tensile strength of 285 MPa or more. For example, the Al-Mg-Si alloy material according to claim 15 has a tensile strength of 285 MPa or more. For example, the Al-Mg-Si alloy material of claim 16 has a tensile strength of 285 MPa or more. For example, if the Al-Mg-Si based alloy material of any one of claim 11 to claim 22 has a 0.2% endurance of 230 MPa or more. An Al-Mg-Si based alloy plate whose chemical composition contains Si: 0.2 to 0.8% by mass, Mg: 0.3 to 1% by mass, Fe: 0.5% by mass or less, and Cu: 0.5% by mass or less, and further contains Ti: 0.1 Mass% or less: B: At least one of 0.1 mass% or less. The remaining portion is composed of Al and unavoidable impurities. Its tensile strength is 280 MPa or more, the conductivity is 54% IACS or more, and the thickness is less than 0.9 mm. For example, the Al-Mg-Si-based alloy sheet according to claim 24, wherein Mn, Cr, and Zn as impurities are regulated to 0.1 mass% or less, respectively. For example, the Al-Mg-Si-based alloy sheet according to claim 25, wherein Ni, V, Ga, Pb, Sn, Bi, and Zr as impurities are regulated to 0.05 mass% or less, respectively. The Al-Mg-Si-based alloy plate as claimed in claim 26, wherein the specification of Ag as an impurity is 0.05% by mass or less. Al-Mg-Si based alloy plate as claimed in item 26, wherein The total content of high-quality rare earth elements is specified to be less than 0.1% by mass. For example, the Al-Mg-Si based alloy sheet of claim 27, wherein the total content of rare earth elements as impurities is specified to be 0.1% by mass or less. For example, if the Al-Mg-Si based alloy sheet of any one of claim 24 to claim 29, the difference between the tensile strength TS (MPa) and the 0.2% resistance YS (MPa) (TS-YS) is 0 MPa to 30 MPa the following. A manufacturing method of Al-Mg-Si series alloy plate, which is a method for manufacturing Al-Mg-Si series alloy plate by sequentially hot-rolling and cold-rolling Al-Mg-Si series alloy ingot. The surface temperature of the Al-Mg-Si alloy sheet immediately after the rolling is 170 ° C or lower, and the heat treatment is performed at a temperature of 120 ° C or higher and less than 200 ° C before the end of the cold rolling after the hot rolling. For example, the method for manufacturing an Al-Mg-Si-based alloy sheet according to claim 31, wherein the chemical composition of the Al-Mg-Si-based alloy ingot contains Si: 0.2 to 0.8% by mass, Mg: 0.3 to 1% by mass, and Fe: 0.5% by mass or less and Cu: 0.5% by mass or less, and the remainder is composed of Al and unavoidable impurities. For example, the method for manufacturing an Al-Mg-Si-based alloy plate according to claim 32, wherein the Mn, Cr, Zn, and Ti as impurities are each specified to be 0.1% by mass or less. The method for manufacturing an Al-Mg-Si based alloy sheet according to claim 31, wherein the heat treatment is performed before the cold rolling is started after the hot rolling is finished. The method for manufacturing an Al-Mg-Si based alloy sheet according to claim 32, wherein the heat treatment is performed before the start of cold rolling after the end of hot rolling. If the method for manufacturing an Al-Mg-Si alloy sheet according to claim 33, Among them, heat treatment is performed before the start of cold rolling after the completion of hot rolling. For example, the method for manufacturing an Al-Mg-Si-based alloy plate according to claim 31, wherein the surface temperature of the Al-Mg-Si-based alloy plate immediately after the hot rolling is 150 ° C or lower. For example, the method for manufacturing an Al-Mg-Si-based alloy plate according to claim 32, wherein the surface temperature of the Al-Mg-Si-based alloy plate immediately after the hot rolling is 150 ° C or lower. For example, the method for manufacturing an Al-Mg-Si-based alloy plate according to claim 33, wherein the surface temperature of the Al-Mg-Si-based alloy plate immediately after the hot rolling is 150 ° C or lower. For example, the method for manufacturing an Al-Mg-Si-based alloy plate according to claim 34, wherein the surface temperature of the Al-Mg-Si-based alloy plate immediately after the hot rolling is 150 ° C or lower. For example, the method for manufacturing an Al-Mg-Si-based alloy sheet according to claim 35, wherein the surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 150 ° C or lower. For example, the method for manufacturing an Al-Mg-Si-based alloy sheet according to claim 36, wherein the surface temperature of the Al-Mg-Si-based alloy sheet immediately after the hot rolling is 150 ° C or lower. The method for manufacturing an Al-Mg-Si-based alloy plate according to claim 31, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower. The method for manufacturing an Al-Mg-Si-based alloy plate as claimed in claim 32, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower. If the method for manufacturing an Al-Mg-Si alloy sheet according to claim 33, The heat treatment temperature is 130 ° C to 180 ° C. The method for manufacturing an Al-Mg-Si-based alloy plate as claimed in claim 34, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si alloy plate according to claim 35, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower. The method for manufacturing an Al-Mg-Si-based alloy plate as claimed in claim 36, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower. The method for manufacturing an Al-Mg-Si-based alloy sheet according to claim 37, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower. The method for manufacturing an Al-Mg-Si-based alloy plate according to claim 38, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower. The method for manufacturing an Al-Mg-Si-based alloy sheet according to claim 39, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si alloy plate according to claim 40, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si alloy plate according to claim 41, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower. The method for manufacturing an Al-Mg-Si-based alloy sheet according to claim 42, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si alloy sheet according to claim 43, wherein the rolling reduction rate of the cold rolling after the heat treatment is 20% or more. For example, the method for manufacturing an Al-Mg-Si-based alloy sheet according to claim 44, wherein the rolling reduction rate of the cold rolling after the heat treatment is 20% or more. If the method for manufacturing an Al-Mg-Si alloy sheet according to item 45, The rolling rate of cold rolling after heat treatment is more than 20%. For example, the method for manufacturing an Al-Mg-Si alloy sheet according to claim 46, wherein the rolling reduction rate of the cold rolling after the heat treatment is 20% or more. For example, the method for manufacturing an Al-Mg-Si-based alloy sheet according to claim 47, wherein the rolling reduction rate of the cold rolling after the heat treatment is 20% or more. For example, the method for manufacturing an Al-Mg-Si-based alloy sheet according to claim 48, wherein the rolling reduction rate of the cold rolling after the heat treatment is 20% or more. For example, the method for manufacturing an Al-Mg-Si-based alloy sheet according to claim 49, wherein the rolling reduction rate of the cold rolling after the heat treatment is 20% or more. For example, the method for manufacturing an Al-Mg-Si alloy sheet according to claim 50, wherein the rolling reduction rate of the cold rolling after the heat treatment is 20% or more. For example, the method for manufacturing an Al-Mg-Si based alloy sheet according to claim 51, wherein the rolling reduction rate of the cold rolling after the heat treatment is 20% or more. For example, the method for manufacturing an Al-Mg-Si based alloy sheet according to claim 52, wherein the rolling reduction rate of the cold rolling after the heat treatment is 20% or more. For example, the method for manufacturing an Al-Mg-Si based alloy sheet according to claim 53, wherein the rolling reduction rate of the cold rolling after the heat treatment is 20% or more. For example, the method for manufacturing an Al-Mg-Si based alloy sheet according to claim 54, wherein the rolling reduction rate of the cold rolling after heat treatment is 20% or more. The method for manufacturing an Al-Mg-Si based alloy sheet according to claim 55, wherein final annealing is performed after cold rolling. The method for manufacturing an Al-Mg-Si based alloy sheet according to claim 56, wherein final annealing is performed after cold rolling. For example, the method for manufacturing an Al-Mg-Si alloy plate according to claim 57, Among them, final annealing is performed after cold rolling. The method for manufacturing an Al-Mg-Si based alloy sheet according to claim 58, wherein final annealing is performed after cold rolling. The method for manufacturing an Al-Mg-Si based alloy sheet according to claim 59, wherein the final annealing is performed after cold rolling. The method for manufacturing an Al-Mg-Si based alloy sheet according to claim 60, wherein the final annealing is performed after cold rolling. The method for manufacturing an Al-Mg-Si based alloy sheet according to claim 61, wherein the final annealing is performed after cold rolling. The method for manufacturing an Al-Mg-Si based alloy sheet according to claim 62, wherein the final annealing is performed after cold rolling. The method for manufacturing an Al-Mg-Si based alloy sheet according to claim 63, wherein the final annealing is performed after cold rolling. The method for manufacturing an Al-Mg-Si based alloy sheet according to claim 64, wherein final annealing is performed after cold rolling. The method for manufacturing an Al-Mg-Si based alloy sheet according to claim 65, wherein final annealing is performed after cold rolling. The method for manufacturing an Al-Mg-Si based alloy sheet according to claim 66, wherein final annealing is performed after cold rolling. The method for manufacturing an Al-Mg-Si based alloy plate as claimed in claim 67, wherein the final annealing temperature is 180 ° C or lower. The method for manufacturing an Al-Mg-Si based alloy plate as claimed in claim 68, wherein the final annealing temperature is 180 ° C or lower. If the method for manufacturing an Al-Mg-Si alloy sheet according to item 69, The final annealing temperature is below 180 ° C. For example, the method for manufacturing an Al-Mg-Si alloy sheet according to claim 70, wherein the final annealing temperature is 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si based alloy sheet according to claim 71, wherein the final annealing temperature is 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si alloy plate according to claim 72, wherein the final annealing temperature is 180 ° C or lower. The method for manufacturing an Al-Mg-Si-based alloy plate as claimed in claim 73, wherein the final annealing temperature is 180 ° C or lower. The method for manufacturing an Al-Mg-Si-based alloy plate as claimed in claim 74, wherein the final annealing temperature is 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si based alloy sheet according to claim 75, wherein the final annealing temperature is 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si alloy plate according to claim 76, wherein the final annealing temperature is 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si alloy plate according to claim 77, wherein the final annealing temperature is 180 ° C or lower. The method for manufacturing an Al-Mg-Si-based alloy sheet according to claim 78, wherein the final annealing temperature is 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si-based alloy sheet according to any one of claim 31 to claim 90, wherein the Al-Mg-Si before the plurality of passes of hot rolling is performed at least once. The surface temperature of the series alloy plate is 470 ~ 350 ℃, and the average cooling rate caused by the cooling of the Al-Mg-Si series alloy plate caused by the pass, or the forced cooling after the pass and the pass is 50 ° C / min. the above Pass. A method for manufacturing an Al-Mg-Si series alloy plate, which contains Ti: 0.2 to 0.8% by mass, Mg: 0.3 to 1% by mass, Fe: 0.5% by mass or less, and Cu: 0.5% by mass or less, and further contains Ti : 0.1% by mass or less or B: At least one species of 0.1% by mass or less, and an Al-Mg-Si-based alloy ingot composed of Al and unavoidable impurities is sequentially subjected to hot rolling and cold rolling The manufacturing method is characterized in that the surface temperature of the Al-Mg-Si alloy sheet immediately after the hot rolling is 170 ° C or lower, and the heat treatment is performed at a temperature of 120 ° C or higher and less than 200 ° C before the cold rolling ends after the hot rolling ends . For example, the method for manufacturing an Al-Mg-Si-based alloy sheet according to claim 92, wherein the Mn, Cr, and Zn as impurities are each specified to be 0.1% by mass or less. For example, the method for manufacturing an Al-Mg-Si-based alloy plate according to claim 93, wherein the impurities Ni, V, Ga, Pb, Sn, Bi, and Zr are each specified to be 0.05 mass% or less. The method for manufacturing an Al-Mg-Si-based alloy plate according to claim 94, wherein the specification of Ag as an impurity is 0.05% by mass or less. For example, the method for manufacturing an Al-Mg-Si alloy plate according to claim 94, wherein the total content of rare earth elements as impurities is specified to be 0.1% by mass or less. For example, the method for manufacturing an Al-Mg-Si-based alloy plate according to claim 95, wherein the total content of rare earth elements as impurities is specified to be 0.1% by mass or less. The method for manufacturing an Al-Mg-Si based alloy sheet according to claim 92, wherein the heat treatment is performed before the start of cold rolling after the completion of hot rolling. The method for manufacturing an Al-Mg-Si based alloy sheet according to claim 93, wherein the heat treatment is performed before the cold rolling is started after the hot rolling is finished. The method for manufacturing an Al-Mg-Si-based alloy sheet according to claim 94, wherein the heat treatment is performed before the start of cold rolling after the end of hot rolling. The method for manufacturing an Al-Mg-Si based alloy sheet according to claim 95, wherein the heat treatment is performed before the start of cold rolling after the end of hot rolling. The method for manufacturing an Al-Mg-Si based alloy sheet according to claim 96, wherein the heat treatment is performed before the start of cold rolling after the end of hot rolling. The method for manufacturing an Al-Mg-Si based alloy sheet according to claim 97, wherein the heat treatment is performed before the start of cold rolling after the end of hot rolling. For example, the method for manufacturing an Al-Mg-Si-based alloy plate according to claim 92, wherein the surface temperature of the Al-Mg-Si-based alloy plate immediately after the hot rolling is 150 ° C or lower. For example, the method for manufacturing an Al-Mg-Si-based alloy plate according to claim 93, wherein the surface temperature of the Al-Mg-Si-based alloy plate immediately after the hot rolling is 150 ° C or lower. For example, the method for manufacturing an Al-Mg-Si-based alloy plate according to claim 94, wherein the surface temperature of the Al-Mg-Si-based alloy plate immediately after the hot rolling is 150 ° C or lower. For example, the method for manufacturing an Al-Mg-Si-based alloy plate according to claim 95, wherein the surface temperature of the Al-Mg-Si-based alloy plate immediately after the hot rolling is 150 ° C or lower. For example, the method for manufacturing an Al-Mg-Si-based alloy plate according to claim 96, wherein the surface temperature of the Al-Mg-Si-based alloy plate immediately after the hot rolling is 150 ° C or lower. For example, the method for manufacturing an Al-Mg-Si based alloy plate according to claim 97, wherein the surface temperature of the Al-Mg-Si based alloy plate immediately after the hot rolling is 150 ° C or lower. For example, the method for manufacturing an Al-Mg-Si-based alloy plate according to claim 98, wherein the surface temperature of the Al-Mg-Si-based alloy plate immediately after the hot rolling is 150 ° C or lower. For example, the method for manufacturing an Al-Mg-Si-based alloy plate according to claim 99, wherein the surface temperature of the Al-Mg-Si-based alloy plate immediately after the hot rolling is 150 ° C or lower. For example, the method for manufacturing an Al-Mg-Si-based alloy plate according to claim 100, wherein the surface temperature of the Al-Mg-Si-based alloy plate immediately after the hot rolling is 150 ° C or lower. For example, the method for manufacturing an Al-Mg-Si-based alloy plate according to claim 101, wherein the surface temperature of the Al-Mg-Si-based alloy plate immediately after the hot rolling is 150 ° C or lower. For example, the method for manufacturing an Al-Mg-Si-based alloy plate according to claim 102, wherein the surface temperature of the Al-Mg-Si-based alloy plate immediately after the hot rolling is 150 ° C or lower. For example, the method for manufacturing an Al-Mg-Si-based alloy plate according to claim 103, wherein the surface temperature of the Al-Mg-Si-based alloy plate immediately after the hot rolling is 150 ° C or lower. For example, the method for manufacturing an Al-Mg-Si based alloy plate according to claim 104, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si alloy plate according to claim 105, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si alloy plate according to claim 106, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si-based alloy sheet according to claim 107, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si alloy plate according to claim 108, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si alloy plate according to claim 109, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si alloy plate according to claim 110, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si alloy plate according to claim 111, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si alloy plate according to claim 112, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si alloy plate according to claim 113, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si-based alloy plate according to claim 114, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si-based alloy plate according to item 115, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si based alloy sheet according to claim 116, wherein the rolling reduction rate of the cold rolling after the heat treatment is 20% or more. For example, the method for manufacturing an Al-Mg-Si-based alloy sheet according to claim 117, wherein the reduction ratio of the cold rolling after the heat treatment is 20% or more. For example, the method for manufacturing an Al-Mg-Si alloy sheet according to claim 118, wherein the rolling reduction rate of the cold rolling after the heat treatment is 20% or more. For example, the method for manufacturing an Al-Mg-Si-based alloy sheet according to claim 119, wherein the rolling reduction rate of the cold rolling after the heat treatment is 20% or more. For example, the method for manufacturing an Al-Mg-Si based alloy sheet according to claim 120, wherein the rolling reduction rate of the cold rolling after the heat treatment is 20% or more. For example, the method for manufacturing an Al-Mg-Si based alloy sheet according to claim 121, wherein the rolling reduction rate of the cold rolling after the heat treatment is 20% or more. For example, the method for manufacturing an Al-Mg-Si alloy sheet according to claim 122, wherein the rolling reduction rate of the cold rolling after the heat treatment is 20% or more. For example, the method for manufacturing an Al-Mg-Si based alloy sheet according to claim 123, wherein the rolling reduction rate of the cold rolling after the heat treatment is 20% or more. For example, the method for manufacturing an Al-Mg-Si-based alloy sheet according to claim 124, wherein the rolling reduction rate of the cold rolling after the heat treatment is 20% or more. For example, the method for manufacturing an Al-Mg-Si based alloy sheet according to claim 125, wherein the rolling reduction rate of the cold rolling after the heat treatment is 20% or more. For example, the method for manufacturing an Al-Mg-Si based alloy sheet according to claim 126, wherein the rolling reduction rate of the cold rolling after the heat treatment is 20% or more. For example, the method for manufacturing an Al-Mg-Si based alloy sheet according to claim 127, wherein the rolling reduction rate of the cold rolling after the heat treatment is 20% or more. For example, the method for manufacturing an Al-Mg-Si based alloy sheet according to claim 128, wherein the final annealing is performed after cold rolling. For example, the method for manufacturing an Al-Mg-Si-based alloy sheet according to claim 129, wherein final annealing is performed after cold rolling. For example, the method for manufacturing an Al-Mg-Si based alloy sheet according to claim 130, wherein final annealing is performed after cold rolling. For example, the method for manufacturing an Al-Mg-Si based alloy sheet according to claim 131, wherein final annealing is performed after cold rolling. For example, the method for manufacturing an Al-Mg-Si alloy sheet according to claim 132, wherein the final annealing is performed after cold rolling. For example, the method for manufacturing an Al-Mg-Si alloy sheet according to claim 133, wherein final annealing is performed after cold rolling. For example, the method for manufacturing an Al-Mg-Si alloy sheet according to claim 134, wherein final annealing is performed after cold rolling. For example, the method for manufacturing an Al-Mg-Si based alloy sheet according to claim 135, wherein final annealing is performed after cold rolling. For example, the method for manufacturing an Al-Mg-Si alloy sheet according to claim 136, wherein final annealing is performed after cold rolling. For example, the method for manufacturing an Al-Mg-Si alloy sheet according to claim 137, wherein the final annealing is performed after cold rolling. For example, the method for manufacturing an Al-Mg-Si alloy sheet according to claim 138, wherein final annealing is performed after cold rolling. For example, the method for manufacturing an Al-Mg-Si alloy sheet according to claim 139, wherein final annealing is performed after cold rolling. For example, the method for manufacturing an Al-Mg-Si based alloy sheet according to claim 140, wherein the final annealing temperature is 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si based alloy sheet according to claim 141, wherein the final annealing temperature is 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si alloy plate according to claim 142, wherein the final annealing temperature is 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si-based alloy plate according to claim 143, wherein the final annealing temperature is 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si alloy plate according to claim 144, wherein the final annealing temperature is 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si-based alloy plate according to claim 145, wherein the final annealing temperature is 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si based alloy sheet according to claim 146, wherein the final annealing temperature is 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si alloy plate according to claim 147, wherein the final annealing temperature is 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si alloy plate according to claim 148, wherein the final annealing temperature is 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si-based alloy plate according to claim 149, wherein the final annealing temperature is 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si based alloy sheet according to claim 150, wherein the final annealing temperature is 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si based alloy sheet according to claim 151, wherein the final annealing temperature is 180 ° C or lower. For example, the method for manufacturing an Al-Mg-Si alloy sheet according to any one of claim 92 to claim 163, in which the Al-Mg-Si is performed at least once before the plurality of passes of hot rolling. The surface temperature of the system alloy plate is 470 ~ 350 ℃, and the average cooling rate caused by the cooling of the Al-Mg-Si alloy plate caused by the pass, or the forced cooling after the pass is 50 ° C / min The above passes.