WO2017168890A1

WO2017168890A1 - Al-mg-si-based alloy material, al-mg-si-based alloy plate, and method for manufacturing al-mg-si-based alloy plate

Info

Publication number: WO2017168890A1
Application number: PCT/JP2016/088715
Authority: WO
Inventors: 眞二籠重; 和章谷口; 西森　秀樹; 智明山ノ井
Original assignee: 昭和電工株式会社
Priority date: 2016-03-30
Filing date: 2016-12-26
Publication date: 2017-10-05
Also published as: TW201807210A; CN108699641B; CN108699641A

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

Al-Mg-Si alloy material, Al-Mg-Si alloy plate, and method for producing Al-Mg-Si alloy plate

This invention is an Al—Mg—Si based alloy material, particularly an Al—Mg—Si based alloy material excellent in thermal conductivity, conductivity, strength and workability, and excellent in thermal conductivity, conductivity, strength and workability. Further, the present invention relates to an Al—Mg—Si based alloy plate having a thickness of less than 0.9 mm and a method for producing an Al—Mg—Si based alloy plate.

Flat panel TVs, thin monitors for personal computers, notebook computers, tablet computers, car navigation systems, portable navigation systems, chassis of products such as mobile terminals such as smartphones and mobile phones, metal base printed boards, and heating elements such as internal covers In a member material to be built in or mounted, excellent thermal conductivity, strength, and workability for quickly radiating heat are required.

Pure aluminum alloys such as JIS 1100, 1050, and 1070 have excellent thermal conductivity but low strength. An Al—Mg alloy (5000-based alloy) such as JIS 5052 used as a high strength material is significantly inferior in thermal conductivity and conductivity to a pure aluminum-based alloy.

In contrast, an Al—Mg—Si alloy (6000 alloy) has good thermal conductivity and electrical conductivity, and can be improved in strength by age hardening. A method for obtaining an aluminum alloy plate excellent in conductivity and workability has been studied.

For example, Patent Document 1 contains 0.1 to 0.34% by mass of Mg, 0.2 to 0.8% by mass of Si, and 0.22 to 1.0% by mass of Cu, with the balance being Al and An Al—Mg—Si alloy composed of inevitable impurities and having a Si / Mg content ratio of 1.3 or more is made into an ingot of thickness 250 mm or more by semi-continuous casting and preheated at a temperature of 400 to 540 ° C. A method for producing an Al—Mg—Si alloy rolled sheet, characterized in that after hot rolling and cold rolling at a reduction rate of 50 to 85%, annealing is performed at a temperature of 140 to 280 ° C. It is disclosed.

Patent Document 2 contains Si: 0.2 to 1.5 mass%, Mg: 0.2 to 1.5 mass%, Fe: 0.3 mass% or less, and Mn: 0.02 to 0.15% by mass, Cr: 0.02 to 0.15% of one or two types, and the balance is Al and Ti in unavoidable impurities is regulated to 0.2% or less, or An aluminum alloy plate having a composition containing one or two of Cu: 0.01 to 1% by mass or rare earth element: 0.01 to 0.2% by mass is produced by continuous casting and rolling and then cold-rolling. Next, a solution treatment at 500 to 570 ° C. is performed, followed by further cold rolling at a cold rolling rate of 5 to 40%, and an aging treatment for heating to 150 to 190 ° C. after the cold rolling. Of aluminum plate with excellent thermal conductivity, strength and bending workability The law has been described.

Patent Document 3 contains Si: 0.2 to 0.8 mass%, Mg: 0.3 to 1 mass%, Fe: 0.5 mass% or less, Cu: 0.5 mass% or less, and It contains at least one of Ti: 0.1% by mass or less or B: 0.1% by mass or less, and consists of the balance Al and inevitable impurities, or Mn and Cr as impurities are further Mn: 0.1% by mass %, Cr: 0.1% by mass or less of an Al—Mg—Si alloy ingot that is hot-rolled and further cold-rolled. There is shown a method for producing an Al—Mg—Si alloy plate, characterized in that heat treatment is performed by holding at 200 to 400 ° C. for 1 hour or longer after cold rolling until the end of cold rolling.

In addition, as described in Patent Document 3, in JIS 1000 series to 7000 series aluminum alloys, thermal conductivity and electrical conductivity have a good correlation, and an aluminum alloy plate having excellent thermal conductivity has excellent electrical conductivity. It can be used as a conductive member material as well as a heat radiating member material.

JP 2012-62517 A JP 2007-9262 A JP 2003-321755 A

As described above, Al-Mg-Si alloy plates have been improved, but with the improvement in performance, size, and thickness of products using aluminum alloy member materials, in addition to high conductivity and workability, it has become more difficult than before. While the Al—Mg—Si based alloy sheet is required to have higher strength, the methods described in Patent Document 1, Patent Document 2 and Patent Document 3 maintain high conductivity and workability. It was difficult to obtain the required strength, and improvement studies on relatively thin Al—Mg—Si alloy plates were insufficient.

In view of the above technical background, an object of the present invention is to provide an Al—Mg—Si based alloy material having high conductivity and good workability while having higher strength.

Another object of the present invention is to provide an Al—Mg—Si based alloy sheet having a thickness of less than 0.9 mm and having a higher strength while having high conductivity and good workability.

Still another object of the present invention is to provide a method for producing an Al—Mg—Si based alloy plate having higher electrical conductivity and better workability while having higher strength.

The above problem is solved by the following means.
(1) An Al—Mg—Si alloy material having a tensile strength of 280 MPa or more, an electrical conductivity of 54% IACS or more, and a fiber structure.
(2) The chemical composition contains Si: 0.2 to 0.8 mass%, Mg: 0.3 to 1 mass%, Fe: 0.5 mass% or less and Cu: 0.5 mass% or less, 2. The Al—Mg—Si based alloy material according to item 1, comprising the balance Al and inevitable impurities.
(3) The Al—Mg—Si alloy material according to item 2, wherein Mn, Cr, Zn, and Ti as impurities are each controlled to be 0.1 mass% or less.
(4) The Al—Mg—Si alloy material according to any one of items 1 to 3, wherein the 0.2% proof stress is 230 MPa or more.
(5) The Al—Mg—Si alloy material according to any one of items 1 to 4, wherein the tensile strength is 285 MPa or more.
(6) An Al—Mg—Si alloy plate having a tensile strength of 280 MPa or more, an electrical conductivity of 54% IACS or more, and a thickness of less than 0.9 mm.
(7) The chemical composition contains Si: 0.2 to 0.8 mass%, Mg: 0.3 to 1 mass%, Fe: 0.5 mass% or less, and Cu: 0.5 mass% or less, 7. The Al—Mg—Si based alloy sheet according to item 6 above, comprising the balance Al and inevitable impurities.
(8) The Al—Mg—Si based alloy plate according to item 7 above, wherein Mn, Cr, Zn, and Ti as impurities are each regulated to 0.1 mass% or less.
(9) The Al—Mg as described in any one of the preceding items 6 to 8, wherein the difference (TS−YS) between the tensile strength TS (MPa) and the 0.2% proof stress YS (MPa) is 0 MPa or more and 30 MPa or less. -Si alloy plate.
(10) The chemical composition contains Si: 0.2 to 0.8 mass%, Mg: 0.3 to 1 mass%, Fe: 0.5 mass% or less, and Cu: 0.5 mass% or less, Further, it contains at least one of Ti: 0.1% by mass or less or B: 0.1% by mass or less, the balance is Al and inevitable impurities, the tensile strength is 280 MPa or more, and the conductivity is 54% IACS or more. An Al—Mg—Si alloy material having a fiber structure.
(11) The Al—Mg—Si based alloy material according to item 10 above, wherein Mn, Cr, and Zn as impurities are each regulated to 0.1 mass% or less.
(12) The Al—Mg—Si based alloy material according to item 10 or 11, wherein Ni, V, Ga, Pb, Sn, Bi, and Zr as impurities are each regulated to 0.05 mass% or less.
(13) The Al—Mg—Si alloy material according to any one of items 10 to 12, wherein Ag as an impurity is regulated to 0.05% by mass or less.
(14) The Al—Mg—Si alloy material according to any one of items 10 to 13, wherein the total content of rare earth elements as impurities is regulated to 0.1 mass% or less.
(15) The Al—Mg—Si alloy material according to any one of items 10 to 14, wherein the tensile strength is 285 MPa or more.
(16) The Al—Mg—Si alloy material according to any one of items 10 to 15, wherein the 0.2% proof stress is 230 MPa or more.
(17) The chemical composition contains Si: 0.2 to 0.8 mass%, Mg: 0.3 to 1 mass%, Fe: 0.5 mass% or less, and Cu: 0.5 mass% or less, Further, it contains at least one of Ti: 0.1% by mass or less or B: 0.1% by mass or less, the balance is Al and inevitable impurities, the tensile strength is 280 MPa or more, and the conductivity is 54% IACS or more. Al—Mg—Si alloy plate with a thickness of less than 0.9 mm.
(18) The Al—Mg—Si based alloy plate according to item 17 above, wherein Mn, Cr, and Zn as impurities are each regulated to 0.1 mass% or less.
(19) The Al—Mg—Si based alloy plate according to the above item 17 or 18, wherein Ni, V, Ga, Pb, Sn, Bi, and Zr as impurities are each regulated to 0.05 mass% or less.
(20) The Al—Mg—Si alloy plate according to any one of items 17 to 19, wherein Ag as an impurity is regulated to 0.05% by mass or less.
(21) The Al—Mg—Si based alloy sheet according to any one of items 17 to 20, wherein the total content of rare earth elements as impurities is regulated to 0.1 mass% or less.
(22) The Al—Mg as described in any one of 17 to 19 above, wherein the difference (TS−YS) between the tensile strength TS (MPa) and the 0.2% proof stress YS (MPa) is 0 MPa or more and 30 MPa or less. -Si alloy plate.
(23) A method for producing an Al—Mg—Si alloy plate in which hot rolling and cold rolling are sequentially performed on an Al—Mg—Si alloy ingot, wherein Al—Mg—Si immediately after the end of hot rolling For producing an Al—Mg—Si based alloy sheet, wherein the surface temperature of the alloy plate is 170 ° C. or less, and heat treatment is performed at a temperature of 120 ° C. or more and less than 200 ° C. after the hot rolling is finished and before the cold rolling is finished .
(24) The chemical composition of the Al—Mg—Si alloy ingot is Si: 0.2 to 0.8 mass%, Mg: 0.3 to 1 mass%, Fe: 0.5 mass% or less, and Cu: 24. The method for producing an Al—Mg—Si-based alloy plate according to item 23, which contains 0.5% by mass or less and the balance is Al and inevitable impurities.
(25) The method for producing an Al—Mg—Si based alloy plate as described in 24 above, wherein Mn, Cr, Zn, and Ti as impurities are each controlled to be 0.1 mass% or less.
(26) The method for producing an Al—Mg—Si based alloy sheet according to any one of items 23 to 25, wherein the heat treatment is performed after the hot rolling is finished and before the cold rolling is started.
(27) The method for producing an Al—Mg—Si alloy plate according to any one of items 23 to 26, wherein the surface temperature of the Al—Mg—Si alloy plate immediately after completion of hot rolling is 150 ° C. or less. .
(28) The method for producing an Al—Mg—Si alloy sheet according to any one of items 23 to 27, wherein the heat treatment temperature is 130 ° C. or higher and 180 ° C. or lower.
(29) The method for producing an Al—Mg—Si alloy sheet according to any one of items 23 to 28, wherein a rolling rate of cold rolling after heat treatment is 20% or more.
(30) The method for producing an Al—Mg—Si based alloy sheet according to any one of items 23 to 29, wherein the final annealing is performed after cold rolling.
(31) The method for producing an Al—Mg—Si alloy plate as described in 30 above, wherein the final annealing temperature is 180 ° C. or lower.
(32) Among a plurality of hot rolling passes, the surface temperature of the Al—Mg—Si alloy plate immediately before the pass is 470 to 350 ° C., and the Al—Mg—Si alloy plate is cooled by the pass, or 32. The method for producing an Al—Mg—Si based alloy sheet according to any one of items 23 to 31, wherein the pass at which the average cooling rate by forced cooling after the pass is 50 ° C./min or more is performed at least once.
(33) 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 Ti: 0 .Hot rolling and cold rolling are sequentially performed on an Al—Mg—Si alloy ingot containing at least one type of 1% by mass or less or B: 0.1% by mass or less, the balance being Al and inevitable impurities. A method for producing an alloy plate, wherein the surface temperature of an Al—Mg—Si alloy plate immediately after the end of hot rolling is 170 ° C. or less, and 120 ° C. or more after the end of hot rolling and before the end of cold rolling A method for producing an Al—Mg—Si alloy plate, which is heat-treated at a temperature of less than 200 ° C.
(34) The method for producing an Al—Mg—Si based alloy plate according to the above 33, wherein Mn, Cr, and Zn as impurities are each regulated to 0.1 mass% or less.
(35) The Al—Mg—Si based alloy sheet according to the preceding item 33 or 34, wherein Ni, V, Ga, Pb, Sn, Bi and Zr as impurities are regulated to 0.05 mass% or less, respectively. Production method.
(36) The method for producing an Al—Mg—Si based alloy sheet according to any one of the preceding items 33 to 35, wherein Ag as an impurity is regulated to 0.05 mass% or less.
(37) The method for producing an Al—Mg—Si-based alloy plate according to any one of the preceding items 33 to 36, wherein the total content of rare earth elements as impurities is regulated to 0.1 mass% or less.
(38) The method for producing an Al—Mg—Si alloy sheet according to any one of items 33 to 37, wherein the heat treatment is performed after the hot rolling is completed and before the cold rolling is started.
(39) The method for producing an Al—Mg—Si alloy plate according to any one of the preceding items 33 to 38, wherein the surface temperature of the Al—Mg—Si alloy plate immediately after the end of hot rolling is 150 ° C. or less. .
(40) The method for producing an Al—Mg—Si based alloy sheet according to any one of items 33 to 39, wherein the heat treatment temperature is 130 ° C. or higher and 180 ° C. or lower.
(41) The method for producing an Al—Mg—Si alloy sheet according to any one of items 33 to 40, wherein the rolling rate of cold rolling after heat treatment is 20% or more.
(42) The method for producing an Al—Mg—Si alloy sheet according to any one of items 33 to 41, wherein the final annealing is performed after cold rolling.
(43) The method for producing an Al—Mg—Si based alloy plate as described in 42 above, wherein the final annealing temperature is 180 ° C. or lower.
(44) Among a plurality of hot rolling passes, the surface temperature of the Al—Mg—Si alloy plate immediately before the pass is 470 to 350 ° C., and the Al—Mg—Si alloy plate is cooled by the pass, or 44. The method for producing an Al—Mg—Si based alloy sheet according to any one of the preceding items 33 to 43, wherein the pass in which the average cooling rate by forced cooling after the pass is 50 ° C./min or more is performed at least once.

According to the invention described in item (1), an Al—Mg—Si alloy material having a fiber structure excellent in strength, thermal conductivity, and workability can be obtained.

According to the invention described in item (2), Si: 0.2 to 0.8 mass%, Mg: 0.3 to 1 mass%, Fe: 0.5 mass% or less, and Cu: 0.5 mass% Since it contains the following and the balance Al and inevitable impurities, it can be an Al—Mg—Si alloy material having a fiber structure excellent in strength, thermal conductivity, and workability.

According to the invention described in the preceding item (3), Mn, Cr, Zn, and Ti as impurities are each regulated to 0.1% by mass or less, and thus excellent in strength, thermal conductivity, and workability. An Al—Mg—Si alloy material having a fiber structure can be obtained.

According to the invention described in item (4) above, an Al—Mg—Si based alloy material having a strong fiber structure can be obtained.

According to the invention described in item (5), an Al—Mg—Si based alloy material having a fiber structure having a higher tensile strength can be obtained.

According to the invention described in item (6) above, an Al—Mg—Si alloy plate having a thickness of less than 0.9 mm and excellent in strength, thermal conductivity and workability can be obtained.

According to the invention described in item (7), the chemical composition is Si: 0.2 to 0.8 mass%, Mg: 0.3 to 1 mass%, Fe: 0.5 mass% or less. And Cu: 0.5% by mass or less, and the balance being Al and unavoidable impurities, it can be an Al—Mg—Si based alloy plate excellent in strength, thermal conductivity, and workability.

According to the invention described in the preceding item (8), since Mn, Cr, Zn, and Ti as impurities are respectively regulated to 0.1% by mass or less, the balance is composed of the remaining Al and inevitable impurities. An Al—Mg—Si alloy plate excellent in thermal conductivity and workability can be obtained.

According to the invention described in item (9) above, an Al—Mg—Si alloy plate having both high tensile strength and proof stress can be obtained.

According to the invention described in item (10), the chemical composition is Si: 0.2 to 0.8 mass%, Mg: 0.3 to 1 mass%, Fe: 0.5 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 balance being Al and inevitable impurities, strength, thermal conductivity, processing Al-Mg-Si alloy material having a fiber structure with excellent properties can be obtained.

According to the invention described in the above item (11), since Mn, Cr, and Zn as impurities are respectively regulated to 0.1% by mass or less, a fiber structure excellent in strength, thermal conductivity, and workability Al—Mg—Si based alloy material having

According to the invention described in the preceding item (12), since Ni, V, Ga, Pb, Sn, Bi and Zr as impurities are respectively regulated to 0.05% by mass or less, strength, thermal conductivity, An Al—Mg—Si alloy material having a fiber structure excellent in workability can be obtained.

According to the invention described in item (13), since Ag as an impurity is regulated to 0.05% by mass or less, Al—Mg—Si having a fiber structure excellent in strength, thermal conductivity, and workability. It can be made of an alloy material.

According to the invention described in item (14) above, since the total content of rare earth elements as impurities is regulated to 0.1% by mass or less, it has a fiber structure excellent in strength, thermal conductivity, and workability. An Al—Mg—Si alloy material can be formed.

According to the invention described in item (15), an Al—Mg—Si based alloy material having a fiber structure having a higher tensile strength can be obtained.

According to the invention described in item (16), an Al—Mg—Si alloy material having a strong proof fiber structure can be obtained.

According to the invention described in item (17), the chemical composition is Si: 0.2 to 0.8 mass%, Mg: 0.3 to 1 mass%, Fe: 0.5 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 balance being Al and inevitable impurities, strength, thermal conductivity, processing An Al—Mg—Si based alloy plate having a thickness of less than 0.9 mm can be obtained.

According to the invention described in the above item (18), Mn, Cr, and Zn as impurities are regulated to 0.1% by mass or less, respectively, so that the thickness is excellent in strength, thermal conductivity, and workability. An Al—Mg—Si based alloy plate of less than 0.9 mm can be formed.

According to the invention described in the preceding item (19), since Ni, V, Ga, Pb, Sn, Bi, and Zr as impurities are respectively regulated to 0.05% by mass or less, strength, thermal conductivity, An Al—Mg—Si based alloy plate with excellent workability can be obtained.

According to the invention described in item (20) above, since Ag as an impurity is regulated to 0.05% by mass or less, an Al—Mg—Si based alloy plate excellent in strength, thermal conductivity, and workability can be obtained. It can be done.

According to the invention described in the preceding item (21), since the total content of rare earth elements as impurities is regulated to 0.1% by mass or less, Al—Mg—Si system is used for strength, thermal conductivity, and workability. An alloy plate can be used.

According to the invention described in the preceding item (22), an Al—Mg—Si based alloy sheet having both high tensile strength and yield strength can be obtained.

According to the invention described in the preceding item (23), there is provided a method for producing an Al—Mg—Si alloy plate, in which hot rolling and cold rolling are sequentially performed on an Al—Mg—Si alloy ingot, Since the surface temperature of the Al—Mg—Si based alloy sheet immediately after the end of rolling is 170 ° C. or less, and heat treatment is performed at a temperature of 120 ° C. or more and less than 200 ° C. after the end of hot rolling and before the end of cold rolling, Effective quenching effect by hot rolling is obtained, and aging hardening and electrical conductivity improvement during heat treatment, and work hardening and workability improvement by cold rolling, high tensile strength and electrical conductivity and high workability A good Al—Mg—Si alloy plate can be produced.

According to the invention described in item (24), the chemical composition is Si: 0.2 to 0.8 mass%, Mg: 0.3 to 1 mass%, Fe: 0.5 mass% or less, and Cu: 0 This is a method for producing an Al—Mg—Si alloy plate, in which hot rolling and cold rolling are sequentially performed on an Al—Mg—Si alloy ingot containing less than 5% by mass and comprising the balance Al and inevitable impurities. Then, the surface temperature of the Al—Mg—Si alloy sheet immediately after the end of hot rolling is 170 ° C. or less, and heat treatment is performed at a temperature of 120 ° C. or more and less than 200 ° C. after the end of hot rolling and before the end of cold rolling. As a result, the effect of quenching by hot rolling is obtained, and the tensile strength and conductivity are high due to aging hardening and conductivity improvement during heat treatment, and work hardening and workability improvement by cold rolling. Al-Mg-Si alloy plate with good properties can be manufactured .

According to the invention described in the preceding item (25), since Mn, Cr, Zn, and Ti as impurities are regulated to 0.1% by mass or less, the tensile strength and the conductivity are high. An Al—Mg—Si based alloy plate with good workability can be produced.

According to the invention described in the preceding item (26), since the heat treatment is performed after the hot rolling is finished and before the cold rolling is started, the age hardening and the electrical conductivity are improved during the heat treatment, and the work hardening by the cold rolling. By improving the workability, it is possible to produce an Al—Mg—Si based alloy plate that exhibits high tensile strength and electrical conductivity and good workability.

According to the invention described in the preceding item (27), since the surface temperature of the Al—Mg—Si based alloy sheet immediately after the end of hot rolling is 150 ° C. or less, the quenching effect by hot rolling can be enhanced. *

According to the invention described in the preceding item (28), since the heat treatment temperature is 130 ° C. or higher and 180 ° C. or lower, the effects of age hardening and conductivity improvement can be surely obtained.

According to the invention described in the preceding item (29), since the rolling rate of the cold rolling after the heat treatment is 20% or more, the strength of the Al—Mg—Si based alloy sheet is improved by the cold rolling and the good processing Sex can be obtained.

According to the invention described in the preceding item (30), the final annealing is performed after the cold rolling, so that the workability of the Al—Mg—Si based alloy sheet is good.

According to the invention described in the preceding item (31), since the final annealing temperature is 180 ° C. or lower, an Al—Mg—Si alloy plate having high tensile strength and high conductivity and good workability is manufactured. can do.

According to the invention described in the preceding item (32), the surface temperature of the Al—Mg—Si based alloy plate immediately before the pass among the plurality of passes of hot rolling is 470 to 350 ° C., and the Al—Mg—Si due to the pass is used. Since the pass in which the average cooling rate by cooling of the alloy plate or the forced cooling after the pass is 50 ° C./min or more is performed at least once, the quenching effect by hot rolling can be enhanced.

According to the invention described in the preceding item (33), Si: 0.2 to 0.8 mass%, Mg: 0.3 to 1 mass%, Fe: 0.5 mass% or less, and Cu: 0.5 mass% In addition, at least one of Ti: 0.1% by mass or less or B: 0.1% by mass or less is contained in the Al—Mg—Si alloy ingot consisting of the remainder Al and inevitable impurities. A method for producing an alloy sheet in which rolling and cold rolling are sequentially performed, wherein the surface temperature of the Al—Mg—Si alloy sheet immediately after the end of hot rolling is 170 ° C. or less, and after the end of hot rolling, Since the heat treatment is performed at a temperature of 120 ° C. or more and less than 200 ° C. before the end of the cold rolling, an effective quenching effect by the hot rolling can be obtained, age hardening at the time of the heat treatment and improvement of conductivity, and work hardening by the cold rolling. As a result of improved workability, the tensile strength and conductivity are high. Workability can be manufactured good Al-Mg-Si alloy plates.

According to the invention described in the preceding item (34), Mn, Cr, and Zn as impurities are respectively regulated to 0.1% by mass or less, so that the tensile strength and the electrical conductivity are high and the workability is high. Can be produced.

According to the invention described in the preceding item (35), since Ni, V, Ga, Pb, Sn, Bi, and Zr as impurities are respectively regulated to 0.05% by mass or less, the tensile strength and the conductivity are An Al—Mg—Si based alloy plate having a high value and good workability can be produced.

According to the invention described in the preceding item (36), since Ag as an impurity is regulated to 0.05% by mass or less, Al—Mg— showing high values of tensile strength and conductivity and good workability. Si-based alloy plates can be manufactured.

According to the invention described in the preceding item (37), since the total content of rare earth elements as impurities is regulated to 0.1% by mass or less, the tensile strength and conductivity are high, and the workability is good. An Al—Mg—Si based alloy plate can be manufactured.

According to the invention described in the preceding item (38), since the heat treatment is performed after the hot rolling is finished and before the cold rolling is started, the age hardening and the electrical conductivity are improved during the heat treatment, and the work hardening by the cold rolling is performed. By improving the workability, it is possible to produce an Al—Mg—Si based alloy plate that exhibits high tensile strength and electrical conductivity and good workability.

According to the invention described in the preceding item (39), since the surface temperature of the Al—Mg—Si based alloy sheet immediately after the end of hot rolling is 150 ° C. or less, the quenching effect by hot rolling can be enhanced. *

According to the invention described in the preceding item (40), since the heat treatment temperature is 130 ° C. or higher and 180 ° C. or lower, the effects of age hardening and conductivity improvement are surely obtained.

According to the invention described in the preceding item (41), since the rolling rate of the cold rolling after the heat treatment is 20% or more, the strength of the Al—Mg—Si based alloy sheet is improved by the cold rolling and the good processing Sex can be obtained.

According to the invention described in the preceding item (42), since the final annealing is performed after cold rolling, the workability of the Al—Mg—Si based alloy plate is improved.

According to the invention described in the preceding item (43), since the final annealing temperature is 180 ° C. or less, an Al—Mg—Si based alloy sheet having high tensile strength and high electrical conductivity and good workability is manufactured. can do.

According to the invention described in the preceding item (44), the surface temperature of the Al—Mg—Si based alloy plate immediately before the pass among the plurality of passes of hot rolling is 470 to 350 ° C., and the Al—Mg—Si due to the pass is used. Since the pass in which the average cooling rate by cooling of the alloy plate or the forced cooling after the pass is 50 ° C./min or more is performed at least once, the quenching effect by hot rolling can be enhanced.

It is a model figure of the fiber structure of the Al-Mg-Si alloy material of the present application.

The inventor of the present application uses a hot-rolled alloy in a manufacturing method of an Al—Mg—Si based alloy material (including Al—Mg—Si based alloy plate, the same applies hereinafter) that is sequentially subjected to hot rolling and cold rolling. While maintaining the surface temperature of the material at a predetermined temperature or less and performing heat treatment as an aging treatment after the end of hot rolling and before the end of cold rolling, while having high conductivity and good workability, The inventors have found that an Al—Mg—Si based alloy material having high strength can be obtained, leading to the present invention.

Hereinafter, the Al—Mg—Si alloy material of the present application and the manufacturing method thereof will be described in detail. *

In the Al—Mg—Si based alloy composition of the present application, the purpose of addition of each element and the preferred content are shown.

Mg and Si are elements necessary for the development of strength, and the respective contents thereof are Si: 0.2% by mass or more and 0.8% by mass or less, and Mg: 0.3% by mass or more and 1% by mass or less. preferable. If the Si content is less than 0.2% by mass or the Mg content is less than 0.3% by mass, the strength is lowered. On the other hand, if the Si content exceeds 0.8% by mass and the Mg content exceeds 1% by mass, the rolling load in hot rolling increases and the productivity decreases, and the formability of the resulting aluminum alloy sheet also increases. Deteriorate. The Si content is more preferably 0.2% by mass or more and 0.6% by mass or less, and particularly preferably 0.32% by mass or more and 0.60% by mass or less. The Mg content is more preferably 0.45% by mass or more and 0.9% by mass or less, and particularly preferably 0.45% by mass or more and 0.55% by mass or less.

Fe and Cu are components necessary for molding, but if they are contained in a large amount, the corrosion resistance decreases. In the present application, the Fe content and the Cu content are preferably regulated to 0.5% by mass or less, respectively. The Fe content is more preferably regulated to 0.35% by mass or less, and particularly preferably from 0.1% by mass to 0.25% by mass. The Cu content is more preferably 0.1% by mass or less.

Ti and B have the effect of refining crystal grains and preventing solidification cracking when casting the alloy into a slab. The effect is obtained by adding at least one of Ti or B, and both may be added. However, if it is contained in a large amount, a large amount of crystallized crystals are generated, and the workability, thermal conductivity, and conductivity of the product are lowered. The Ti content is preferably 0.1% by mass or less, and more preferably 0.005% by mass or more and 0.05% by mass or less.

The B content is preferably 0.1% by mass or less, and particularly preferably 0.06% by mass or less.

In addition, various impurity elements are unavoidably contained in the alloy element, but Mn and Cr decrease conductivity and conductivity, and Zn increases in content and decreases in corrosion resistance of the alloy material. preferable. The content of each of Mn, Cr, and Zn as impurities is preferably 0.1% by mass or less, and more preferably 0.05% by mass or less.

Other impurity elements other than the above include Ni, V, Ga, Pb, Sn, Bi, Zr, Ag, rare earth, etc., but are not limited to these, and among these other impurity elements, rare earth Other than the above, the content of each element is preferably 0.05% by mass or less. Among the other impurity elements, the rare earth may contain one or more kinds of elements, and may be derived from a casting raw material contained in the state of misch metal, but the total content of rare earth elements The amount is preferably 0.1% by mass or less, and more preferably 0.05% by mass or less.

Next, the processing steps for obtaining the Al—Mg—Si alloy material specified in the present application will be described.

The dissolved components are adjusted by a conventional method to obtain an Al—Mg—Si alloy ingot. The obtained alloy ingot is preferably subjected to a homogenization treatment as a step prior to heating before hot rolling.

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

The heating before hot rolling is carried out in order to solidify the crystallized substance and Mg, Si in the Al—Mg—Si alloy ingot to form a uniform structure. Therefore, it is preferable to carry out at 450 ° C. or higher and 580 ° C. or lower, particularly preferably at 500 ° C. or higher and 580 ° C. or lower.

The Al-Mg-Si alloy ingot is cooled after being homogenized, and may be heated before hot rolling, or the homogenization and heating before hot rolling may be performed continuously, In the preferable temperature range of the homogenization treatment and heating before hot rolling, the homogenization treatment and the heating before hot rolling may be combined and heated at the same temperature.

It is preferable to chamfer the ingot in order to remove an impurity layer near the surface of the ingot before heating after casting and before hot rolling. The chamfering may be performed after casting and before homogenization treatment, or after homogenization treatment and before heating before hot rolling.

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

Hot rolling consists of rough hot rolling and finishing hot rolling, and after performing rough hot rolling consisting of multiple passes using a rough hot rolling mill, a finishing hot rolling mill different from the rough hot rolling mill is used. Finish hot rolling using. In the present application, when the final pass in the rough hot rolling mill is the final pass of hot rolling, the finish hot rolling can be omitted.

In the present application, finish hot rolling is performed once by introducing an Al—Mg—Si alloy material from one direction using a rolling mill in which a pair of upper and lower work rolls or two or more work rolls are continuously installed. It is carried out in the pass.

When the cold rolling is performed with a coil, the Al—Mg—Si alloy material after finish hot rolling may be wound with a winding device to form a hot rolled coil. When finishing hot rolling is omitted and the final pass of rough hot rolling is used as the final pass of hot rolling, the Al-Mg-Si alloy material is taken up with a winder after the rough hot rolling. It may be a hot rolled coil.

In rough hot rolling, Mg and Si are kept in a solid solution state in accordance with the solution treatment, followed by cooling of the Al—Mg—Si alloy material by a rough hot rolling pass, or rough hot rolling. The quenching effect can be obtained by the temperature drop due to forced cooling after the pass and after the pass.

In the present application, among a plurality of passes of rough hot rolling, the surface temperature of the Al—Mg—Si alloy material immediately before the pass is 350 ° C. or higher and 470 ° C. or lower, and the Al—Mg—Si alloy material is cooled by the pass, or A pass having an average cooling rate of 50 ° C./min or more by the pass and forced cooling after the pass is called a control pass. The reason why the surface temperature of the Al—Mg—Si alloy plate immediately before the control pass is set to 350 ° C. or more and 470 ° C. or less is that if it is less than 350 ° C., the effect of quenching in the rapid hot rolling is small and the temperature is higher than 470 ° C. This is because it is difficult to rapidly cool the Al-Mg-Si based alloy plate having a rising path.

The average cooling rate is an Al—Mg—Si alloy from the start to the end of the control pass when forced cooling is not performed in the control pass, and from the start of the control pass to the end of forced cooling when forced cooling is performed after the control pass. A value obtained by dividing the temperature drop (° C) of the plate by the time (minutes) required.

Forced cooling after the control pass may be performed sequentially on the rolled part while rolling the Al—Mg—Si alloy plate, or after rolling the entire Al—Mg—Si alloy plate. Also good. The method of forced cooling is not limited, but water cooling, air cooling, or coolant may be used.

The control pass is preferably performed at least once, and may be performed a plurality of times. When performing the control pass a plurality of times, it is possible to select whether to perform forced cooling after each pass for each control pass. If the surface temperature of the Al—Mg—Si alloy material just before the pass is 470 to 350 ° C. and the cooling rate is 50 ° C./min or more, the control pass can be performed multiple times. By lowering the temperature of the Al—Mg—Si alloy material below 350 ° C., quenching can be performed efficiently and effectively.

In the present application, in the case where forced cooling is not performed after the final pass of the rough hot rolling, the surface temperature of the Al—Mg—Si alloy material immediately after the final pass of the hot rolling is defined as the temperature after the rough hot rolling, When forced cooling is performed after the final pass of rolling, the surface temperature of the Al—Mg—Si alloy material immediately after the end of forced cooling is set as the temperature after rough hot rolling.

In the present application, when finishing hot rolling is performed, finishing hot rolling ends. When finishing hot rolling is not performed, hot rolling ends with the end of the final pass of rough hot rolling, and immediately after the hot rolling ends. The surface temperature of the Al—Mg—Si based alloy plate is preferably 170 ° C. or less. An effective quenching effect is obtained by setting the temperature of the alloy plate immediately after the end of hot rolling to 170 ° C. or less, and the electrical conductivity is improved while age hardening by the subsequent heat treatment.

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

In addition, when performing finish hot rolling after rough hot rolling, the surface temperature of the Al—Mg—Si alloy material immediately before finish hot rolling is: 280 ° C. or lower is preferable.

Similarly, when the final hot rolling is not performed and the final pass of rough hot rolling is not a control pass, the surface temperature of the Al—Mg—Si alloy material immediately before the final hot hot rolling pass is 280 ° C. or less. preferable.

On the other hand, if the final pass of rough hot rolling is a control pass without finishing hot rolling, the control pass is the final pass of hot rolling, so the Al—Mg—Si system immediately before the final pass of hot rolling. The surface temperature of the alloy material is 470 to 350 ° C., and the surface temperature of the Al—Mg—Si alloy material is 170 ° C. or less at a cooling rate of 50 ° C./min or more by rolling or forced cooling after rolling and rolling. It is preferable to implement the control pass so that

The Al—Mg—Si alloy material after the hot rolling and before the cold rolling is heat treated to age harden and improve the conductivity. *

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

The heat treatment time of the Al—Mg—Si based alloy material performed at a temperature of 120 ° C. or more and less than 200 ° C. after the end of the hot rolling and before the end of the cold rolling is not particularly limited. What is necessary is just to adjust time at predetermined temperature so that it may be obtained, for example, heat processing may be implemented by adjusting time in the range of 1 to 12 hours.

After the heat treatment, cold rolling is performed to harden and further improve the strength.

The heat treatment is preferably performed after the end of hot rolling and before the start of cold rolling in order to enhance the effect of improving the strength of the age-hardened Al—Mg—Si based alloy material by cold rolling.

The Al—Mg—Si alloy material having a predetermined thickness is obtained by cold rolling after the heat treatment. The cold rolling after the heat treatment is preferably performed at a rolling rate of 20% or more in order to improve strength and improve workability. The rolling rate of the Al—Mg—Si alloy sheet by cold rolling after heat treatment is further 30% or more, more preferably 50% or more, more preferably 60% or more, and more preferably 70% or more, and the thickness is less than 0.9 mm In order to make this aluminum material, it is preferably 60% or more, more preferably 70% or more, and particularly preferably 80% or more.

The Al—Mg—Si based alloy material after cold rolling may be cleaned as necessary.

If the workability of the Al—Mg—Si alloy material is more important, final annealing may be performed after cold rolling. The final annealing is preferably performed at 180 ° C. or less, more preferably 160 ° C. or less, particularly 140 ° C. or less, so that the strength of the Al—Mg—Si based alloy material does not become too low.

The final annealing time of the Al—Mg—Si based alloy material carried out at the temperature of 180 ° C. or lower may be adjusted so as to obtain necessary workability and strength. For example, the final annealing is performed in the range of 1 to 10 hours. What is necessary is just to select by temperature.

The production of the Al—Mg—Si alloy material of the present application may be performed by a coil or a single plate. Further, the alloy plate may be cut in an arbitrary step after the cold rolling, and the step after the cutting may be performed with a single plate, or may be slit and formed depending on the application.

According to the manufacturing method described above, an Al—Mg—Si alloy material that can improve strength while obtaining high electrical conductivity and has excellent workability despite its high strength can be obtained. An Al—Mg—Si based alloy sheet having a thickness of 0.9 mm and excellent workability despite its strength can be obtained.

The electrical conductivity of the Al—Mg—Si based alloy material of the present application is defined as 54% IACS or more, and the tensile strength is defined as 280 MPa or more. The tensile strength is preferably 285 MPa or more, and more preferably 290 MPa or more. The 0.2% yield strength of the Al—Mg—Si alloy material of the present application is preferably 230 MPa or more, more preferably 240 MPa or more, and particularly preferably 250 MPa or more. Further, the difference (TS−YS) between the tensile strength TS (MPa) and the 0.2% proof stress YS (MPa) of the Al—Mg—Si based alloy sheet of the present application is preferably 0 MPa or more and 30 MPa or less. YS is preferably 0 MPa or more and 20 MPa or less.

The Al—Mg—Si alloy material of the present application preferably has a fiber structure. The fiber structure is a metal structure stretched by plastic working.

FIG. 1 shows a model diagram of the fiber structure of the Al—Mg—Si alloy material of the present application.

As shown in FIG. 1, in the present application, the metal structure is exposed so that the normal of the observation surface is perpendicular to both the processing direction vector of the Al—Mg—Si based alloy material and the normal direction vector of the processing surface, A metal structure in which the grain boundary in the normal direction of the processed surface of the metal structure of the observation surface observed with an optical microscope is 3 lines / 100 μm or more and the grain boundary having a length in the processing direction of 300 μm or more is defined as a fiber structure. . When the plastic processing is rolling, the processing direction is the rolling direction, the processing surface is the rolling surface, and the observation surface is a cross section in the thickness direction cut in parallel to the rolling direction.

As a method of exposing the metal structure, the surface of the Al-Mg-Si alloy material whose normal is perpendicular to both the processing direction vector of the Al-Mg-Si alloy material and the normal direction vector of the processing surface is polished. Then, a method of anodizing the polished surface can be exemplified. Barker's solution (3% borohydrofluoric acid aqueous solution) can be preferably used as the anodizing solution.

Examples of the present invention and comparative examples are shown below.
(First embodiment)
This embodiment is an embodiment of the invention according to claims 1 to 5.

Aluminum alloy slabs having different chemical compositions shown in Table 1 were obtained by the DC casting method.
[Example 1]
The aluminum alloy slab having the chemical composition number 1 in Table 1 was chamfered. Next, the homogenized treatment at 560 ° C. for 5 hours was performed on the alloy slab after chamfering in a heating furnace, and then the pre-hot rolling at 540 ° C. for 4 hours was performed by changing the temperature in the same furnace. After heating before hot rolling, a 540 ° C. slab was taken out from the heating furnace, and rough hot rolling was started. After the thickness of the alloy plate during the rough hot rolling reaches 25 mm, the final pass of the rough hot rolling is performed at an average cooling rate of 80 ° C./minute from the alloy plate temperature of 450 ° C. immediately before the pass, An alloy plate having a hot rolling temperature of 221 ° C. and a thickness of 12 mm was obtained. In the final pass of the rough hot rolling, the alloy plate was moved while rolling, and forced cooling was performed by water cooling in which water was sprayed on the alloy plate sequentially from above and below the portion of the rolled alloy plate.

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

[Examples 2 to 40, Comparative Examples 1 to 6]
After chamfering the aluminum alloy slab described in Table 1, treatment was performed under the conditions described in Table 2 to Table 6 to obtain an aluminum alloy plate. As in Example 1, in all Examples and Comparative Examples, homogenization treatment and heating before hot rolling are continuously performed in the same furnace, and forced cooling after the final pass of rough hot rolling is performed while rolling. Either water cooling in which the alloy plate is moved and water is sprayed on the alloy plate in order from the top and bottom of the rolled alloy plate portion or air cooling in which the air is cooled after completion of the final hot-rolling pass is selected. In some examples, final annealing was performed after cold rolling.

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

In Comparative Example 1 and Comparative Example 2, a solution treatment was performed in which a heat treatment was performed at 550 ° C. for 1 minute during the cold rolling, followed by cooling at a rate of 5 ° C./second or more. In Comparative Example 1 and Comparative Example 2, the cold rolling rate is the total rolling rate of the cold rolling after the solution treatment, and the cold rolling after the solution treatment is based on the thickness of the alloy material after the solution treatment. The cold rolling rate was 30%.

The tensile strength, 0.2% proof stress, electrical conductivity, and workability of the obtained alloy plate were evaluated by the following methods.

Tensile strength and 0.2% proof stress were measured for JIS No. 5 test pieces at ordinary temperature by a conventional method.

The electrical conductivity was obtained as a relative value (% IACS) when the electrical conductivity of annealed standard annealed copper (volume low efficiency 1.7241 × 10 ⁻² μΩm) adopted internationally was 100% IACS.

As for workability, when the bending angle is 90 °, the thickness of the alloy plate is 0.4 mm or more, the thickness of each alloy plate is bent inside radius, and when the thickness of the alloy plate is less than 0.4 mm, the bending inside A radius test was performed with a radius of 0, and a bending test by the 6.3 V block method of JIS Z 2248 metal material bending test method was performed.

In Examples and Comparative Examples, when the metal structure of the cross section of the Al—Mg—Si alloy plate in the thickness direction cut parallel to the rolling direction is exposed, the rolling surface normal of the metal structure observed with an optical microscope The metal structure in which the grain boundary in the direction is 3 lines / 100 μm or more and the grain boundary having a length in the rolling direction of 300 μm or more is defined as the fiber structure.

As a method for exposing the metal structure, the cross section of the Al—Mg—Si alloy plate cut in parallel to the rolling direction is polished with emery paper, subjected to rough buffing and final polishing, and then washed with water and dried. Furthermore, a method of applying anodizing treatment in a Barker solution (3% aqueous borofluoric acid solution) under conditions of bath temperature: 28 ° C., applied voltage: 30 V, applied time: 90 seconds was applied.

Tables 7 and 8 show the evaluation results of tensile strength, 0.2% proof stress, electrical conductivity, and workability, and whether the Al—Mg—Si based alloy sheet has a fiber structure.

The Al—Mg—Si alloy materials described in the examples satisfying the chemical composition, tensile strength, and electrical conductivity specified in the present application and having a fiber structure have good workability. On the other hand, Comparative Example 1 and Comparative Example 2 in which solution treatment was performed during the cold rolling had inferior electrical conductivity to that of the present application, and Comparative Examples 3 to 6 in which the chemical composition did not satisfy the specified range of the present application were tensile strengths. Alternatively, at least one of the conductivity is inferior to that of the example, and some of the conductivity is inferior.
(Second embodiment)
This embodiment is an embodiment of the invention according to claims 6-9.

Aluminum alloy slabs having different chemical compositions shown in Table 9 were obtained by the DC casting method.
[Example 101]
The aluminum alloy slab having the chemical composition number 101 in Table 9 was chamfered. Next, the homogenized treatment at 560 ° C. for 5 hours was performed on the alloy slab after chamfering in a heating furnace, and then the pre-hot rolling at 540 ° C. for 4 hours was performed by changing the temperature in the same furnace. After heating before hot rolling, a 540 ° C. slab was taken out from the heating furnace, and rough hot rolling was started. After the thickness of the alloy plate during the rough hot rolling reaches 25 mm, the final pass of the rough hot rolling is performed at an average cooling rate of 80 ° C./minute from the alloy plate temperature of 450 ° C. immediately before the pass, An alloy plate having a hot rolling temperature of 221 ° C. and a thickness of 12 mm was obtained. In the final pass of the rough hot rolling, the alloy plate was moved while rolling, and forced cooling was performed by water cooling in which water was sprayed on the alloy plate sequentially from above and below the portion of the rolled alloy plate.

[Examples 102 to 140, Comparative Examples 101 to 106]
After chamfering the aluminum alloy slab shown in Table 9, it was treated under the conditions shown in Tables 10 to 14 to obtain an aluminum alloy sheet. As in Example 101, in all Examples and Comparative Examples, homogenization and heating before hot rolling were continuously performed in the same furnace, and forced cooling after the final hot hot rolling pass was performed while rolling. Either water cooling in which the alloy plate is moved and water is sprayed on the alloy plate in order from the top and bottom of the rolled alloy plate portion or air cooling in which the air is cooled after completion of the final hot-rolling pass is selected. In some examples, final annealing was performed after cold rolling.

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

In Comparative Example 101 and Comparative Example 102, a solution treatment was performed in which a heat treatment was performed at 550 ° C. for 1 minute during the cold rolling, followed by cooling at a rate of 5 ° C./second or more. In Comparative Example 101 and Comparative Example 102, the cold rolling rate is the total rolling rate of the cold rolling after the solution treatment, and the cold rolling after the solution treatment is based on the thickness of the alloy material after the solution treatment. The cold rolling rate was 30%.

Tables 15 and 16 show the evaluation results of tensile strength, 0.2% proof stress, electrical conductivity, and workability.

The Al—Mg—Si alloy material described in the examples that satisfies the chemical composition, tensile strength, and conductivity specified in this application has good workability. On the other hand, Comparative Example 101 and Comparative Example 102 in which solution treatment was performed in the middle of cold rolling had inferior electrical conductivity to that of the present application, and Comparative Examples 103 to 106 whose chemical compositions did not satisfy the specified range were tensile strengths. Alternatively, at least one of the conductivity is inferior to that of the example, and some of the conductivity is inferior.

(Third embodiment)
This embodiment is an embodiment of the invention according to claims 10 to 16.

Aluminum alloy slabs having different chemical compositions shown in Table 17 were obtained by the DC casting method.
[Example 201]
The aluminum alloy slab having the chemical composition number 201 in Table 17 was chamfered. Next, the homogenized treatment at 570 ° C. for 3 hours was performed on the alloy slab after chamfering 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. After heating before hot rolling, a 540 ° C. slab was taken out from the heating furnace, and rough hot rolling was started. After the thickness of the alloy plate during the rough hot rolling reaches 25 mm, the final pass of the rough hot rolling is performed at an average cooling rate of 80 ° C./min from the alloy plate temperature of 451 ° C. immediately before the pass. An alloy plate having a hot rolling temperature of 222 ° C. and a thickness of 12 mm was obtained. In the final pass of the rough hot rolling, the alloy plate was moved while rolling, and forced cooling was performed by water cooling in which water was sprayed on the alloy plate sequentially from above and below the portion of the rolled alloy plate.

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

[Examples 202 to 242 and Comparative Examples 201 to 206]
After chamfering the aluminum alloy slab described in Table 17, treatment was performed under the conditions described in Table 18 to Table 22 to obtain an aluminum alloy plate. In addition, as in Example 201, homogenization and heating before hot rolling were continuously performed in the same furnace in all Examples and Comparative Examples, and forced cooling after the final rough hot rolling pass was performed while rolling. Either water cooling in which the alloy plate is moved and water is sprayed on the alloy plate in order from the top and bottom of the rolled alloy plate portion or air cooling in which the air is cooled after completion of the final hot-rolling pass is selected. In some examples, final annealing was performed after cold rolling.

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

In Comparative Example 201 and Comparative Example 202, a solution treatment was performed in which heat treatment was performed at 550 ° C. for 1 minute during the cold rolling, followed by cooling at a rate of 5 ° C./second or more. In Comparative Example 201 and Comparative Example 202, the cold rolling rate is the total rolling rate of the cold rolling after the solution treatment, and the cold rolling after the solution treatment is based on the thickness of the alloy material after the solution treatment. The cold rolling rate was 30%.

Tables 23 and 24 show the evaluation results of tensile strength, 0.2% proof stress, electrical conductivity, and workability, and whether the Al—Mg—Si based alloy sheet has a fiber structure.

The Al—Mg—Si alloy materials described in the examples satisfying the chemical composition, tensile strength, and electrical conductivity specified in the present application and having a fiber structure have good workability. On the other hand, Comparative Example 201 and Comparative Example 202 in which solution treatment was performed in the middle of cold rolling had inferior electrical conductivity compared to the present application, and Comparative Examples 203 to 206 whose chemical compositions did not satisfy the specified range were tensile strengths. Alternatively, at least one of the conductivity is inferior to that of the example, and some of the conductivity is inferior.
(Fourth embodiment)
This embodiment is an embodiment of the invention according to claims 17-22.

Aluminum alloy slabs having different chemical compositions shown in Table 25 were obtained by the DC casting method.
[Example 301]
The aluminum alloy slab having the chemical composition number 301 in Table 25 was chamfered. Next, the homogenized treatment at 570 ° C. for 3 hours was performed on the alloy slab after chamfering 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. After heating before hot rolling, a 540 ° C. slab was taken out from the heating furnace, and rough hot rolling was started. After the thickness of the alloy plate during the rough hot rolling reaches 25 mm, the final pass of the rough hot rolling is performed at an average cooling rate of 80 ° C./min from the alloy plate temperature of 451 ° C. immediately before the pass. An alloy plate having a hot rolling temperature of 222 ° C. and a thickness of 12 mm was obtained. In the final pass of the rough hot rolling, the alloy plate was moved while rolling, and forced cooling was performed by water cooling in which water was sprayed on the alloy plate sequentially from above and below the portion of the rolled alloy plate.

[Examples 302 to 342, Comparative Examples 301 to 306]
After chamfering the aluminum alloy slab described in Table 25, it was treated under the conditions described in Table 26 to Table 30 to obtain an aluminum alloy plate. As in Example 301, 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 while rolling. Either water cooling in which the alloy plate is moved and water is sprayed on the alloy plate in order from the top and bottom of the rolled alloy plate portion or air cooling in which the air is cooled after completion of the final hot-rolling pass is selected. In some examples, final annealing was performed after cold rolling.

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

In Comparative Example 301 and Comparative Example 302, a solution treatment was performed in which heat treatment was performed at 550 ° C. for 1 minute during the cold rolling, followed by cooling at a rate of 5 ° C./second or more. In Comparative Example 301 and Comparative Example 302, the cold rolling rate is the total rolling rate of the cold rolling after the solution treatment, and the cold rolling after the solution treatment is based on the thickness of the alloy material after the solution treatment. The cold rolling rate was 30%.

Table 31 and Table 32 show the evaluation results of tensile strength, 0.2% proof stress, electrical conductivity, and workability.

The Al—Mg—Si alloy materials described in the examples satisfying the chemical composition, tensile strength, and electrical conductivity specified in the present application have good workability. On the other hand, Comparative Example 301 and Comparative Example 302 in which solution treatment was performed during the cold rolling had inferior electrical conductivity to that of the present application, and Comparative Examples 303 to 306 whose chemical compositions did not satisfy the prescribed range were tensile strengths. Alternatively, at least one of the conductivity is inferior to that of the example, and some of the conductivity is inferior.
(Fifth embodiment)
This embodiment is an embodiment of the invention according to claims 23-32.

Aluminum alloy slabs having different chemical compositions shown in Table 33 were obtained by the DC casting method.
[Example 401]
The aluminum alloy slab having the chemical composition number 401 in Table 33 was chamfered. Next, the homogenized treatment at 560 ° C. for 5 hours was performed on the alloy slab after chamfering in a heating furnace, and then the pre-hot rolling at 540 ° C. for 4 hours was performed by changing the temperature in the same furnace. After heating before hot rolling, a 540 ° C. slab was taken out from the heating furnace, and rough hot rolling was started. After the thickness of the alloy plate during the rough hot rolling reaches 25 mm, the final pass of the rough hot rolling is performed at an average cooling rate of 80 ° C./minute from the alloy plate temperature of 450 ° C. immediately before the pass, An alloy plate having a hot rolling temperature of 222 ° C. and a thickness of 12 mm was obtained. In the final pass of the rough hot rolling, the alloy plate was moved while rolling, and forced cooling was performed by water cooling in which water was sprayed on the alloy plate sequentially from above and below the portion of the rolled alloy plate.

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

[Examples 402 to 445, Comparative Examples 401 to 407]
The aluminum alloy slab described in Table 33 was chamfered and then treated under the conditions described in Table 34 to Table 39 to obtain an aluminum alloy plate. As in Example 401, in all Examples and Comparative Examples, homogenization treatment and heating before hot rolling were continuously performed in the same furnace, and forced cooling after the rough hot rolling final pass was performed while rolling. It was selected from water cooling in which the alloy plate was moved and water was sprayed on the alloy plate sequentially from the upper and lower sides with respect to the part of the rolled alloy plate, air cooling to be blown and cooled after completion of the final hot hot rolling pass, and no forced cooling. In some examples, final annealing was performed after cold rolling.

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

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

Tensile strength was measured for JIS No. 5 specimens at room temperature by a conventional method.

Tables 34 to 39 show the evaluation results of tensile strength, electrical conductivity, and workability.

In an embodiment in which the surface temperature of the Al—Mg—Si based alloy sheet immediately after the end of hot rolling is 170 ° C. or less, and the heat treatment temperature after the end of hot rolling and before the end of cold rolling is in the range of 120 to 195 ° C. On the other hand, while the tensile strength and electrical conductivity are high and workability is good, at least either the surface temperature of the alloy sheet immediately after the end of hot rolling or the heat treatment temperature after the end of hot rolling and before the end of cold rolling However, Comparative Example 401, Comparative Example 402, and Comparative Example 403, which do not satisfy the specified range of the present application, are inferior to those of Examples in terms of tensile strength or electrical conductivity. In addition, Comparative Example 404 having a lower Si content than the Examples, Comparative Example 405 having a higher Si content than the Examples, Comparative Example 406 having a lower Mg content than the Examples, and Comparative Example 407 having a higher Mg content than the Examples. However, at least one of tensile strength and electrical conductivity is inferior to the examples, and Comparative Example 405 and Comparative Example 407 are also inferior in workability.

(Sixth embodiment)
This embodiment is an embodiment of the invention according to claims 33-44.
Aluminum alloy slabs having different chemical compositions shown in Table 40 were obtained by the DC casting method. In addition, the ingot of the chemical composition number 20 containing rare earth used the raw material containing misch metal for casting.

[Example 501]
The aluminum alloy slab having the chemical composition number 501 in Table 40 was chamfered. Next, the homogenized treatment at 570 ° C. for 4 hours was performed on the alloy slab after chamfering in a heating furnace, and then the temperature was changed in the same furnace to perform heating before hot rolling at 540 ° C. for 3 hours. After heating before hot rolling, a 540 ° C. slab was taken out from the heating furnace, and rough hot rolling was started. After the thickness of the alloy plate during the rough hot rolling reaches 25 mm, the final pass of the rough hot rolling is performed at an average cooling rate of 80 ° C./minute from the alloy plate temperature of 450 ° C. immediately before the pass, An alloy plate having a hot rolling temperature of 220 ° C. and a thickness of 12 mm was obtained. In the final pass of the rough hot rolling, the alloy plate was moved while rolling, and forced cooling was performed by water cooling in which water was sprayed on the alloy plate sequentially from above and below the portion of the rolled alloy plate.

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

[Examples 502 to 547, Comparative Examples 501 to 507]
The aluminum alloy slab described in Table 40 was chamfered and then treated under the conditions described in Table 41 to Table 46 to obtain an aluminum alloy plate. As in Example 501, in all Examples and Comparative Examples, homogenization treatment and heating before hot rolling were continuously performed in the same furnace, and forced cooling after the final rough hot rolling pass was performed while rolling. It was selected from water cooling in which the alloy plate was moved and water was sprayed on the alloy plate sequentially from the upper and lower sides with respect to the part of the rolled alloy plate, air cooling to be blown and cooled after completion of the final hot hot rolling pass, and no forced cooling. In some examples, final annealing was performed after cold rolling.

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

Tables 41 to 46 show the evaluation results of tensile strength, electrical conductivity, and workability.

Within the range where the surface temperature of the alloy sheet immediately after the end of hot rolling is 170 ° C. or less and the heat treatment temperature after the end of hot rolling and before the end of cold rolling is 120 ° C. or more and less than 200 ° C. In some examples, the tensile strength and electrical conductivity are high and the workability is good, whereas the chemical composition specified in the present application, the surface temperature of the alloy sheet immediately after the hot rolling is finished, or the cold after the hot rolling is finished. In the comparative example in which at least one of the heat treatment temperatures before the end of the hot rolling does not satisfy the specified range of the present application, at least one of the tensile strength and the electrical conductivity is inferior to the examples, and the workability is inferior.

The present application is Japanese Patent Application No. 2016-67345, Japanese Patent Application No. 2016-67346, Japanese Patent Application No. 2016-67349, Japanese Patent Application No. 2016-67350, Japanese Patent Application, all of which were filed on March 30, 2016. This is accompanied by the priority claim of Japanese Patent Application No. 2016-67353 and Japanese Patent Application No. 2016-67354, and the disclosure content thereof constitutes a part of the present application as it is.

The terms and expressions used herein are for illustrative purposes and are not to be construed as limiting, but represent any equivalent of the features shown and described herein. It should be recognized that various modifications within the claimed scope of the present invention are permissible.

While this invention may be embodied in many different forms, this disclosure is to be considered as providing examples of the principles of the invention, which examples are hereby incorporated by reference. Many illustrated embodiments are described herein with the understanding that they are not intended to be limited to the preferred embodiments described and / or illustrated.

Although several embodiments of the present invention have been described herein, the present invention is not limited to the various preferred embodiments described herein, and is equivalent to what may be recognized by those skilled in the art based on this disclosure. It encompasses any and all embodiments that have elements, modifications, deletions, combinations (eg, combinations of features across the various embodiments), improvements, and / or changes. Claim limitations should be construed broadly based on the terms used in the claims, and should not be limited to the embodiments described herein or in the process of this application, as such The examples should be construed as non-exclusive.

The present invention can be used for the production of Al—Mg—Si alloy materials and alloy plates.

Claims

An Al—Mg—Si alloy material having a tensile strength of 280 MPa or more, electrical conductivity of 54% IACS or more, and a fiber structure.
The chemical composition contains Si: 0.2 to 0.8 mass%, Mg: 0.3 to 1 mass%, Fe: 0.5 mass% or less and Cu: 0.5 mass% or less, the balance Al and 2. The Al—Mg—Si based alloy material according to claim 1, comprising inevitable impurities.
3. The Al—Mg—Si based alloy material according to claim 2, wherein Mn, Cr, Zn, and Ti as impurities are regulated to 0.1% by mass or less.
The Al-Mg-Si alloy material according to any one of claims 1 to 3, wherein the 0.2% proof stress is 230 MPa or more.
The Al-Mg-Si alloy material according to any one of claims 1 to 4, wherein the tensile strength is 285 MPa or more.
An Al—Mg—Si alloy plate having a tensile strength of 280 MPa or more, an electrical conductivity of 54% IACS or more, and a thickness of less than 0.9 mm.
The chemical composition contains Si: 0.2 to 0.8 mass%, Mg: 0.3 to 1 mass%, Fe: 0.5 mass% or less and Cu: 0.5 mass% or less, the balance Al and The Al—Mg—Si based alloy plate according to claim 6, comprising inevitable impurities.
8. The Al—Mg—Si based alloy plate according to claim 7, wherein Mn, Cr, Zn, and Ti as impurities are each regulated to 0.1 mass% or less.
9. The Al—Mg— composition according to any one of claims 6 to 8, wherein a difference (TS-YS) between the tensile strength TS (MPa) and the 0.2% proof stress YS (MPa) is 0 MPa or more and 30 MPa or less. Si alloy plate.
The chemical composition contains Si: 0.2 to 0.8 mass%, Mg: 0.3 to 1 mass%, Fe: 0.5 mass% or less and Cu: 0.5 mass% or less, and further Ti: 0.1 mass% or less or B: containing at least one kind of 0.1 mass% or less, the balance consisting of Al and inevitable impurities, tensile strength of 280 MPa or more, conductivity of 54% IACS or more, Al-Mg-Si based alloy material.
11. The Al—Mg—Si based alloy material according to claim 10, wherein Mn, Cr, and Zn as impurities are regulated to 0.1% by mass or less.
12. The Al—Mg—Si based alloy material according to claim 10 or 11, wherein Ni, V, Ga, Pb, Sn, Bi, and Zr as impurities are each regulated to 0.05 mass% or less.
The Al-Mg-Si alloy material according to any one of claims 10 to 12, wherein Ag as an impurity is regulated to 0.05 mass% or less.
14. The Al—Mg—Si based alloy material according to any one of claims 10 to 13, wherein a total content of rare earth elements as impurities is regulated to 0.1% by mass or less.
The Al-Mg-Si alloy material according to any one of claims 10 to 14, wherein the tensile strength is 285 MPa or more.
The Al-Mg-Si alloy material according to any one of claims 10 to 15, wherein a 0.2% proof stress is 230 MPa or more.
The chemical composition contains Si: 0.2 to 0.8 mass%, Mg: 0.3 to 1 mass%, Fe: 0.5 mass% or less and Cu: 0.5 mass% or less, and further Ti: Contains at least one of 0.1% by mass or less or B: 0.1% by mass or less, consists of the balance Al and inevitable impurities, has a tensile strength of 280 MPa or more, a conductivity of 54% IACS or more, and a thickness of 0 .Al-Mg-Si alloy plate of less than 9 mm.
18. The Al—Mg—Si based alloy plate according to claim 17, wherein Mn, Cr, and Zn as impurities are respectively regulated to 0.1% by mass or less.
19. The Al—Mg—Si based alloy plate according to claim 17 or 18, wherein Ni, V, Ga, Pb, Sn, Bi, and Zr as impurities are regulated to 0.05% by mass or less, respectively.
20. The Al—Mg—Si based alloy plate according to any one of claims 17 to 19, wherein Ag as an impurity is regulated to 0.05% by mass or less.
21. The Al—Mg—Si based alloy plate according to any one of claims 17 to 20, wherein a total content of rare earth elements as impurities is regulated to 0.1% by mass or less.
The difference between the tensile strength TS (MPa) and the 0.2% proof stress YS (MPa) (TS-YS) is 0 MPa or more and 30 MPa or less, and the Al-Mg- composition according to any one of claims 17 to 19. Si alloy plate.
An Al—Mg—Si alloy sheet manufacturing method in which hot rolling and cold rolling are sequentially performed on an Al—Mg—Si alloy ingot, the Al—Mg—Si alloy sheet immediately after the end of hot rolling The surface temperature of the Al—Mg—Si alloy plate is heat-treated at a temperature of 120 ° C. or more and less than 200 ° C. after the end of the hot rolling and before the end of the cold rolling.
The chemical composition of the Al—Mg—Si alloy ingot is Si: 0.2 to 0.8 mass%, Mg: 0.3 to 1 mass%, Fe: 0.5 mass% or less, and Cu: 0.5 24. The method for producing an Al—Mg—Si based alloy plate according to claim 23, comprising at most% by mass, and comprising the balance Al and inevitable impurities.
25. The method for producing an Al—Mg—Si based alloy plate according to claim 24, wherein Mn, Cr, Zn, and Ti as impurities are each regulated to 0.1% by mass or less.
The method for producing an Al-Mg-Si alloy sheet according to any one of claims 23 to 25, wherein the heat treatment is performed after the end of hot rolling and before the start of cold rolling.
27. The method for producing an Al—Mg—Si alloy plate according to any one of claims 23 to 26, wherein the surface temperature of the Al—Mg—Si alloy plate immediately after the end of hot rolling is 150 ° C. or less.
The method for producing an Al-Mg-Si alloy plate according to any one of claims 23 to 27, wherein the heat treatment temperature is 130 ° C or higher and 180 ° C or lower.
The method for producing an Al-Mg-Si alloy sheet according to any one of claims 23 to 28, wherein a rolling rate of cold rolling after heat treatment is 20% or more.
30. The method for producing an Al—Mg—Si based alloy sheet according to any one of claims 23 to 29, wherein final annealing is performed after cold rolling.
The method for producing an Al-Mg-Si alloy plate according to claim 30, wherein the final annealing temperature is 180 ° C or lower.
Of the multiple passes of hot rolling, the surface temperature of the Al—Mg—Si alloy plate immediately before the pass is 470 to 350 ° C., and the Al—Mg—Si alloy plate is cooled by the pass, or after the pass and the pass 32. The method for producing an Al—Mg—Si based alloy plate according to claim 23, wherein the pass in which the average cooling rate by forced cooling is 50 ° C./min or more is performed at least once.
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 Ti: 0.1% by mass % Of alloy plate or B: 0.1% by mass or less of an alloy plate in which hot rolling and cold rolling are sequentially performed on an Al—Mg—Si based alloy ingot consisting of Al and inevitable impurities. A manufacturing method in which the surface temperature of an Al—Mg—Si alloy sheet immediately after the end of hot rolling is 170 ° C. or less, and after the end of hot rolling and before the end of cold rolling, is 120 ° C. or more and less than 200 ° C. A method for producing an Al—Mg—Si alloy plate, which is heat-treated at a temperature of 5 ° C.
34. The method for producing an Al—Mg—Si based alloy plate according to claim 33, wherein Mn, Cr, and Zn as impurities are each regulated to 0.1 mass% or less.
35. The production of an Al—Mg—Si based alloy plate according to claim 33 or claim 34, wherein Ni, V, Ga, Pb, Sn, Bi and Zr as impurities are each regulated to 0.05 mass% or less. Method.
36. The method for producing an Al—Mg—Si based alloy plate according to any one of claims 33 to 35, wherein Ag as an impurity is regulated to 0.05 mass% or less.
37. The method for producing an Al—Mg—Si based alloy plate according to any one of claims 33 to 36, wherein a total content of rare earth elements as impurities is regulated to 0.1% by mass or less.
38. The method for producing an Al—Mg—Si based alloy sheet according to any one of claims 33 to 37, wherein the heat treatment is performed after the end of hot rolling and before the start of cold rolling.
The method for producing an Al-Mg-Si alloy plate according to any one of claims 33 to 38, wherein the surface temperature of the Al-Mg-Si alloy plate immediately after the end of hot rolling is 150 ° C or lower.
40. The method for producing an Al—Mg—Si based alloy plate according to any one of claims 33 to 39, wherein the heat treatment temperature is 130 ° C. or higher and 180 ° C. or lower.
The method for producing an Al-Mg-Si alloy sheet according to any one of claims 33 to 40, wherein a rolling rate of cold rolling after heat treatment is 20% or more.
The method for producing an Al-Mg-Si based alloy sheet according to any one of claims 33 to 41, wherein final annealing is performed after cold rolling.
43. The method for producing an Al—Mg—Si based alloy plate according to claim 42, wherein the final annealing temperature is 180 ° C. or lower.
Of the multiple passes of hot rolling, the surface temperature of the Al—Mg—Si alloy plate immediately before the pass is 470 to 350 ° C., and the Al—Mg—Si alloy plate is cooled by the pass, or after the pass and the pass 44. The method for producing an Al—Mg—Si-based alloy plate according to claim 33, wherein the pass in which the average cooling rate by forced cooling is 50 ° C./min or more is performed at least once.