CN110872665B - Al-Mg-Si alloy plate - Google Patents
Al-Mg-Si alloy plate Download PDFInfo
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- CN110872665B CN110872665B CN201910787655.0A CN201910787655A CN110872665B CN 110872665 B CN110872665 B CN 110872665B CN 201910787655 A CN201910787655 A CN 201910787655A CN 110872665 B CN110872665 B CN 110872665B
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- 229910021365 Al-Mg-Si alloy Inorganic materials 0.000 title claims abstract description 62
- 239000012535 impurity Substances 0.000 claims abstract description 27
- 239000000835 fiber Substances 0.000 claims abstract description 18
- 239000000203 mixture Substances 0.000 claims abstract description 11
- 239000000126 substance Substances 0.000 claims abstract description 9
- 229910052802 copper Inorganic materials 0.000 claims abstract description 7
- 229910052761 rare earth metal Inorganic materials 0.000 claims description 11
- 238000003754 machining Methods 0.000 claims description 9
- 229910052804 chromium Inorganic materials 0.000 claims description 5
- 229910052748 manganese Inorganic materials 0.000 claims description 5
- 229910052797 bismuth Inorganic materials 0.000 claims description 4
- 229910052759 nickel Inorganic materials 0.000 claims description 4
- 229910052718 tin Inorganic materials 0.000 claims description 4
- 229910052720 vanadium Inorganic materials 0.000 claims description 4
- 229910052725 zinc Inorganic materials 0.000 claims description 4
- 229910052726 zirconium Inorganic materials 0.000 claims description 4
- 230000003287 optical effect Effects 0.000 claims description 3
- 239000000956 alloy Substances 0.000 abstract description 56
- 238000005098 hot rolling Methods 0.000 description 80
- 229910045601 alloy Inorganic materials 0.000 description 28
- 238000001816 cooling Methods 0.000 description 28
- 238000005096 rolling process Methods 0.000 description 17
- 238000010438 heat treatment Methods 0.000 description 16
- 238000005097 cold rolling Methods 0.000 description 14
- 229910000838 Al alloy Inorganic materials 0.000 description 11
- 239000010949 copper Substances 0.000 description 11
- 238000000034 method Methods 0.000 description 9
- 230000000052 comparative effect Effects 0.000 description 8
- 238000000265 homogenisation Methods 0.000 description 8
- 239000000243 solution Substances 0.000 description 8
- 229910052751 metal Inorganic materials 0.000 description 7
- 239000002184 metal Substances 0.000 description 7
- 239000000047 product Substances 0.000 description 7
- 230000000171 quenching effect Effects 0.000 description 7
- 238000005266 casting Methods 0.000 description 6
- 150000002910 rare earth metals Chemical class 0.000 description 6
- 238000005520 cutting process Methods 0.000 description 5
- 239000000463 material Substances 0.000 description 5
- 238000010791 quenching Methods 0.000 description 5
- 230000009467 reduction Effects 0.000 description 5
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 5
- 229910052782 aluminium Inorganic materials 0.000 description 4
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 4
- 230000007423 decrease Effects 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 230000017525 heat dissipation Effects 0.000 description 4
- 238000004519 manufacturing process Methods 0.000 description 4
- 229910018464 Al—Mg—Si Inorganic materials 0.000 description 3
- 230000014509 gene expression Effects 0.000 description 3
- 238000000227 grinding Methods 0.000 description 3
- 230000004075 alteration Effects 0.000 description 2
- 239000003153 chemical reaction reagent Substances 0.000 description 2
- 238000007796 conventional method Methods 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 238000000465 moulding Methods 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- LEMQFBIYMVUIIG-UHFFFAOYSA-N trifluoroborane;hydrofluoride Chemical compound F.FB(F)F LEMQFBIYMVUIIG-UHFFFAOYSA-N 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910000861 Mg alloy Inorganic materials 0.000 description 1
- 229910001122 Mischmetal Inorganic materials 0.000 description 1
- 244000137852 Petrea volubilis Species 0.000 description 1
- 238000003483 aging Methods 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 238000007743 anodising Methods 0.000 description 1
- 239000007864 aqueous solution Substances 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 238000007664 blowing Methods 0.000 description 1
- 230000001413 cellular effect Effects 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 239000002826 coolant Substances 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000001035 drying Methods 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 150000002736 metal compounds Chemical class 0.000 description 1
- 239000003595 mist Substances 0.000 description 1
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- 230000008023 solidification Effects 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
- C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
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- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Conductive Materials (AREA)
Abstract
An Al-Mg-Si alloy sheet having a chemical composition containing 0.2 to 0.8 mass% of Si, 0.3 to 1 mass% of Mg, 0.5 mass% or less of Fe and 0.5 mass% or less of Cu, at least 1 of 0.1 mass% or less of Ti and 0.1 mass% or less of B, and the balance of Al and inevitable impurities, and having a fiber structure, wherein the tensile strength of the Al-Mg-Si alloy material is 170MPa or more, the value obtained by dividing the 0.2% yield strength (MPa) by the tensile strength (MPa) is 0.91 or more and 1.00 or less, the electrical conductivity is 50% < electrical conductivity < 54% (IACS), and the sheet thickness is 3mm or less and the sheet thickness is 9mm or less.
Description
Technical Field
The present invention relates to an Al-Mg-Si alloy sheet, and more particularly to an Al-Mg-Si alloy sheet having excellent thermal conductivity, electrical conductivity, and strength.
Background
Excellent thermal conductivity, strength, and workability for rapid heat dissipation are required for component materials in which a heat generating body is built in or mounted, such as chassis (chassis) of products such as thin televisions, thin monitors for personal computers, notebook computers, tablet computers, car navigation systems, portable terminals such as smart phones and cellular phones, metal-based printed boards, and internal bushings.
Pure aluminum alloys such as JIS 1100, 1050, 1070 have excellent thermal conductivity but low strength. An Al — Mg alloy (5000 series alloy) such as JIS 5052 used as a high-strength material has significantly deteriorated thermal conductivity and electrical conductivity as compared with a pure aluminum alloy.
On the other hand, since the Al — Mg — Si alloy (6000 series alloy) is excellent in thermal conductivity and electrical conductivity and can improve strength by age hardening, a method of obtaining an aluminum alloy sheet excellent in strength, thermal conductivity and workability by using the Al — Mg — Si alloy has been studied.
For example, patent document 1 discloses a method for producing a rolled sheet, characterized by comprising preparing an alloy into an ingot having a thickness of 250mm or more by semicontinuous casting, preheating the ingot at a temperature of 400 to 540 ℃, hot rolling the ingot, cold rolling the ingot at a reduction ratio of 50 to 85%, and annealing the ingot at a temperature of 140 to 280 ℃, wherein the alloy contains 0.1 to 0.34 mass% of Mg, 0.2 to 0.8 mass% of Si, 0.22 to 1.0 mass% of Cu, the balance being Al and unavoidable impurities, and the Si/Mg content ratio being 1.3 or more.
Patent document 2 discloses a method for producing an aluminum alloy sheet having excellent thermal conductivity, strength, and bending workability, which comprises producing an aluminum alloy sheet by continuous casting and rolling, cold rolling, solution treatment at 500 to 570 ℃, further cold rolling at a cold rolling reduction ratio of 5 to 40%, and aging treatment by heating at 150 ℃ or higher and lower than 190 ℃, wherein the aluminum alloy sheet has the following composition: the alloy contains 0.2-1.5 mass% of Si, 0.2-1.5 mass% of Mg, 0.3 mass% or less of Fe, 1 or 2 of 0.02-0.15 mass% of Mn and 0.02-0.15 mass% of Cr, and the balance of Al and inevitable impurities, wherein Ti in the inevitable impurities is limited to 0.2 mass% or less, or 1 or 2 of 0.01-1 mass% of Cu and 0.01-0.2 mass% of rare earth elements are contained in the inevitable impurities.
Patent document 3 discloses an aluminum heat dissipation member produced by homogenizing an Al — Mg — Si alloy ingot, rough hot rolling and finish hot rolling, cold rolling to obtain an alloy sheet, and processing the obtained alloy sheet into a desired shape, wherein the aluminum heat dissipation member contains 0.2 to 0.8 wt% of Si, 0.3 to 0.9 wt% of Mg, 0.35 wt% or less of Fe, and 0.20 wt% or less of Cu, with the balance being Al and unavoidable impurities.
Further, in the Al — Mg — Si based alloy, an aluminum alloy plate having excellent thermal conductivity and excellent correlation between thermal conductivity and electrical conductivity has excellent electrical conductivity, and the heat dissipation member material can be used as a conductive member material.
Patent document 1: japanese patent laid-open publication No. 2012 and 62517
Patent document 2: japanese patent laid-open publication No. 2007-9262
Patent document 3: japanese patent laid-open No. 2000-226628
Disclosure of Invention
Processability is affected by the relationship of tensile strength to yield strength. When the yield strength is lower than the tensile strength, work hardening occurs, and in the case of multi-stage molding, the workability is lowered. The workability also varies depending on the metal structure of the Al — Mg — Si alloy sheet.
However, in patent document 1, the study of process conditions is insufficient, and the yield strength is not studied. In patent document 1, the tensile strength is improved by the presence of Si or Cu, and an alloy containing Si and Mg at substantially the same ratio is not included in the claims of patent document 1, except that the element more abundant than Al is Si or Cu and the Mg content is small. The claims of patent document 1 do not describe the properties and thickness of the plate material.
In patent document 2, although a high strength is obtained, the conductivity described in the examples is low.
In patent document 3, the invention product 1 described in the examples has a small difference between the tensile strength and the yield strength, but has a low thermal conductivity, and the invention product 2 has a higher thermal conductivity than the invention product 1, but has a larger difference between the tensile strength and the yield strength than the invention product 1.
Further, patent documents 2 and 3 do not describe the metal structure of the obtained Al — Mg — Si alloy sheet.
As described above, it is very difficult to obtain an Al — Mg — Si alloy sheet having a tensile strength close to the yield strength and a high electric conductivity in patent documents 1 to 3.
The invention aims to: in view of the above-mentioned background, an Al-Mg-Si alloy sheet having a high value of 0.2% yield strength (MPa) divided by tensile strength (MPa), high electrical conductivity and high strength is provided.
The above problems are solved by the following means.
(1) An Al-Mg-Si alloy sheet having a chemical composition containing 0.2 to 0.8 mass% of Si, 0.3 to 1 mass% of Mg, 0.5 mass% or less of Fe and 0.5 mass% or less of Cu, and at least 1 of 0.1 mass% or less of Ti and 0.1 mass% or less of B, with the balance being Al and unavoidable impurities, wherein the tensile strength of the Al-Mg-Si alloy sheet is 170MPa or more, the value obtained by dividing the tensile strength (MPa) by the 0.2% yield strength (MPa) is 0.91 or more and 1.00 or less, the electrical conductivity is 50% < electrical conductivity < 54% (IACS), and the sheet thickness is 3mm or less and 9mm or less and has a fiber structure.
(2) The Al-Mg-Si alloy sheet according to item 1 above, wherein Mn, Cr, and Zn as impurities are limited to 0.1 mass% or less, respectively.
(3) The Al-Mg-Si based alloy material according to item 1 or item 2 above, wherein Ni, V, Ga, Pb, Sn, Bi and Zr as impurities are each limited to 0.05 mass% or less.
(4) The Al-Mg-Si alloy sheet according to any one of the preceding items 1 to 3, wherein Ag as an impurity is limited to 0.05 mass% or less.
(5) The Al-Mg-Si alloy sheet according to any one of the preceding items 1 to 4, wherein the total content of rare earth elements as impurities is limited to 0.1 mass% or less.
According to the invention described in the aforementioned item (1), an Al-Mg-Si alloy sheet having a high tensile strength, a large value obtained by dividing 0.2% yield strength (MPa) by the tensile strength (MPa), a high electrical conductivity, and a fiber structure having a sheet thickness of 3mm or less and 9mm or less can be formed, and the Al-Mg-Si alloy sheet has a chemical composition containing 0.2 to 0.8 mass% of Si, 0.3 to 1 mass% of Mg, 0.5 mass% or less of Fe and 0.5 mass% or less of Cu, and further containing at least 1 of 0.1 mass% or less of Ti and 0.1 mass% or less of B, with the balance being Al and unavoidable impurities.
According to the invention described in the aforementioned item (2), since Mn, Cr, and Zn as impurities are each limited to 0.1 mass% or less, an Al — Mg — Si alloy sheet having a high tensile strength, a large value obtained by dividing 0.2% yield strength (MPa) by tensile strength (MPa), high electrical conductivity, and a fiber structure can be formed.
According to the invention described in the aforementioned item (3), since Ni, V, Ga, Pb, Sn, Bi, and Zr as impurities are limited to 0.05 mass% or less, the Al — Mg — Si alloy sheet having a strong tensile strength, a large value obtained by dividing 0.2% yield strength (MPa) by tensile strength (MPa), high electrical conductivity, and a fiber structure can be formed.
According to the invention described in the aforementioned item (4), since Ag as an impurity is limited to 0.05 mass% or less, an Al-Mg-Si alloy sheet having a high tensile strength, a large value obtained by dividing 0.2% yield strength (MPa) by tensile strength (MPa), high electrical conductivity, and a fiber structure can be formed.
According to the invention described in the aforementioned item (5), since the total content of the rare earth elements as impurities is limited to 0.1 mass% or less, an Al — Mg — Si alloy sheet having a high tensile strength, a large value obtained by dividing the 0.2% yield strength (MPa) by the tensile strength (MPa), a high electric conductivity, and a fiber structure can be formed.
Drawings
FIG. 1 is a schematic representation of the fiber structure of the Al-Mg-Si alloy sheet according to the present invention.
Detailed Description
The present inventors have found that, in a method for producing an Al-Mg-Si alloy sheet by sequentially performing hot rolling and cold rolling, an Al-Mg-Si alloy sheet having a large value of 0.2% yield strength (MPa) divided by tensile strength (MPa) and having high electrical conductivity and high strength is obtained by setting the surface temperature of the alloy sheet after hot rolling to a predetermined temperature or lower, and have completed the present invention.
The Al-Mg-Si alloy sheet according to the present invention will be described in detail below.
The reason why the purpose of adding and the content of each element in the composition of the Al — Mg — Si alloy sheet of the present application are limited is as follows.
Mg and Si are elements required for embodying strength, and the respective contents are Si: 0.2 to 0.8 mass% of Mg: 0.3 to 1 mass%. When the Si content is less than 0.2 mass% or the Mg content is less than 0.3 mass%, sufficient strength cannot be obtained. On the other hand, if the Si content exceeds 0.8 mass% and the Mg content exceeds 1 mass%, the rolling load during hot rolling increases, and the productivity decreases, and the formability of the obtained aluminum sheet also deteriorates. The Si content is preferably 0.2 mass% or more and 0.6 mass% or less, and more preferably 0.32 mass% or more and 0.60 mass% or less. The Mg content is preferably 0.45 mass% or more and 0.9 mass% or less, and more preferably 0.45 mass% or more and 0.55 mass% or less.
Fe and Cu are components necessary for molding, but if contained in large amounts, the corrosion resistance is lowered. In the present application, the Fe content and the Cu content are each limited to 0.5 mass% or less. The Fe content is preferably limited to 0.35 mass% or less, and more preferably 0.1 mass% or more and 0.25 mass% or less. The Cu content is preferably 0.1 mass% or less.
Ti and B have the following effects: the alloy is refined when being cast into a slab, and solidification cracking is prevented. The above-mentioned effects are obtained by adding at least 1 of Ti and B, and both of them may be added. However, when the amount of the metal compound is large, large-sized precipitates are generated in a large amount, and thus the workability, thermal conductivity and electric conductivity of the product are lowered. The Ti content is preferably 0.1 mass% or less, and more preferably 0.005 mass% or more and 0.05 mass% or less. The B content is preferably 0.1 mass% or less, and particularly preferably 0.06 mass% or less.
Further, it is preferable that the alloy element contains various impurity elements inevitably, Mn and Cr to lower conductivity and electrical conductivity, and if the Zn content is increased, the corrosion resistance of the alloy material is lowered. The respective contents of Mn, Cr, and Zn as impurities are preferably 0.1 mass% or less, and more preferably 0.05 mass% or less.
Examples of the impurity elements other than those described above include Ni, V, Ga, Pb, Sn, Bi, Zr, Ag, rare earth, and the like, but are not limited to these elements, and the content of each element other than rare earth among these other impurity elements is preferably 0.05 mass% or less. The rare earth among the other impurity elements may contain 1 or more elements, or may be a rare earth derived from a casting raw material contained in a state of being mixed with a rare earth, and the total content of the rare earth elements is preferably 0.1 mass% or less, and more preferably 0.05 mass% or less.
Next, a processing step for obtaining the Al — Mg — Si alloy sheet defined in the present application will be described.
The Al-Mg-Si alloy ingot is obtained by adjusting the dissolved components by a conventional method. The homogenization treatment is preferably performed on the obtained alloy ingot as a step before heating before hot rolling.
The homogenization treatment is preferably carried out at 500 ℃ or higher.
In order to form a uniform structure by dissolving the precipitates, Mg and Si in the Al — Mg — Si alloy ingot, the heating before the hot rolling is performed, and if the temperature is too high, eutectic melting occurs, and therefore the heating is preferably performed at 450 ℃ to 580 ℃, and particularly preferably at 500 ℃ to 580 ℃.
The Al-Mg-Si alloy ingot may be homogenized, cooled, and then heated before hot rolling, or the homogenization treatment and the heating before hot rolling may be continuously performed, or the homogenization treatment and the heating before hot rolling may be performed at the same time and at the same temperature within the preferable temperature range of the homogenization treatment and the heating before hot rolling.
The ingot is preferably subjected to surface cutting in order to remove the impurity layer in the vicinity of the surface of the ingot after casting and before heating before hot rolling. The surface cutting may be performed after casting and before the homogenization treatment, or may be performed after the homogenization treatment and before heating before hot rolling.
The Al-Mg-Si alloy ingot heated before and after hot rolling is hot-rolled.
The hot rolling includes rough hot rolling and finish hot rolling, and after the rough hot rolling including a plurality of passes is performed by using a rough hot rolling mill, finish hot rolling is performed by using a finish hot rolling mill different from the rough hot rolling mill. In the present application, when the final pass in the rough hot rolling mill is set as the final pass of hot rolling, the finish hot rolling can be omitted.
In the present application, an Al — Mg — Si based alloy material is introduced from 1 direction using a rolling mill in which a set of upper and lower work rolls or two or more sets of work rolls are continuously provided, and finish hot rolling is performed in 1 pass.
When cold rolling is performed on a coil, the Al — Mg — Si alloy material after finish hot rolling may be coiled by a coiling apparatus to form a hot rolled coil. When the final pass of the rough hot rolling is set to the final pass of the hot rolling without the finish hot rolling, the Al — Mg — Si based alloy material may be coiled by a coiler after the rough hot rolling to produce a hot-rolled coil.
In the rough hot rolling, after Mg and Si are held in a solid solution state, the effect of quenching can be obtained by a temperature decrease due to cooling of the Al — Mg — Si-based alloy material in the pass of the rough hot rolling or forced cooling in the pass and after the pass of the rough hot rolling.
In the present application, among the plurality of passes of the rough hot rolling, the pass in which the surface temperature of the Al-Mg-Si based alloy material immediately before the pass is 350 ℃ or more and 470 ℃ or less and the average cooling rate obtained by cooling the Al-Mg-Si based alloy material by the pass or by forced cooling after the pass and the pass is 50 ℃/min or more is referred to as a control pass. The reason why the surface temperature of the Al — Mg — Si alloy material immediately before passing through the control pass is set to 350 ℃ or more and 470 ℃ or less is that: when the temperature is less than 350 ℃, the quenching effect by the quenching by the rough hot rolling is small, and when the temperature is higher than 470 ℃, it is difficult to quench the Al — Mg — Si-based alloy material after the pass is completed.
The average cooling rate is a value obtained by dividing the temperature decrease (c) of the Al — Mg — Si-based alloy material from the start to the end of the control pass by the required time (minutes) when the forced cooling is not performed in the control pass, and is a value obtained by dividing the temperature decrease (c) of the Al — Mg — Si-based alloy material from the start to the end of the forced cooling by the required time (minutes) when the forced cooling is performed after the control pass.
The forced cooling after the control pass may be performed sequentially on the rolled portions while rolling the Al — Mg — Si based alloy material, or may be performed after rolling the entire Al — Mg — Si based alloy material. The method of forced cooling is not limited, and water cooling, air cooling, or a coolant may be used.
The above-described control pass is preferably performed at least 1 time, and may be performed a plurality of times. When the control pass is performed a plurality of times, whether or not to perform forced cooling after the pass can be selected for each control pass. If the surface temperature of the Al-Mg-Si alloy material immediately before the pass is 470 to 350 ℃ and the cooling rate is 50 ℃/min or more, the pass can be controlled a plurality of times, and the temperature of the Al-Mg-Si alloy material can be reduced to less than 350 ℃ in 1 pass, whereby the quenching can be efficiently and effectively performed.
In the present application, when forced cooling is not performed after the final pass of rough hot rolling, the surface temperature of the Al — Mg — Si based alloy material immediately after the final pass of hot rolling is set to the rough hot rolling completion temperature, and when forced cooling is performed after the final pass of rough hot rolling, the surface temperature of the Al — Mg — Si based alloy material immediately after the completion of forced cooling is set to the rough hot rolling completion temperature.
In the present application, when the finish hot rolling is performed, the end of the finish hot rolling is regarded as the end of the hot rolling, and when the finish hot rolling is not performed, the end of the final pass of the rough hot rolling is regarded as the end of the hot rolling, and the surface temperature of the Al — Mg — Si-based alloy material immediately after the end of the hot rolling is preferably 170 ℃.
The alloy material immediately after hot rolling is cooled to 170 ℃ or lower, whereby an effective quenching effect is obtained.
If the surface temperature of the Al — Mg — Si based alloy material immediately after the hot rolling is too high, the effect of quenching is insufficient, and even if the heat treatment is performed after the hot rolling and before the cold rolling is completed, the improvement of the strength is insufficient. The surface temperature of the aluminum sheet immediately after the completion of hot rolling is more preferably 150 ℃ or less, and particularly preferably 130 ℃ or less.
Further, when the finish hot rolling is performed after the rough hot rolling, the surface temperature of the Al — Mg — Si alloy sheet immediately before the finish hot rolling is preferably 280 ℃ or less in order to obtain the quenching effect in the pass of the finish hot rolling.
In addition, when the final pass of the rough hot rolling is not the controlled pass without the finish hot rolling, the surface temperature of the Al — Mg — Si alloy sheet immediately before the final pass of the rough hot rolling is also preferably 280 ℃.
On the other hand, when the final pass of the rough hot rolling is the controlled pass without the finish hot rolling, since the controlled pass is the final pass of the hot rolling, it is preferable to perform the controlled pass so that the surface temperature of the Al — Mg — Si alloy sheet immediately before the final pass by the hot rolling is 470 to 350 ℃, and the surface temperature of the alloy sheet is set to 170 ℃ or less at a cooling rate of 50 ℃/min or more by the forced cooling after the rolling or the rolling and the rolling.
The Al-Mg-Si alloy material of the present invention may be produced by a coil or a single plate.
According to the above production method, an Al-Mg-Si alloy sheet having improved strength while maintaining high conductivity can be obtained.
The Al-Mg-Si alloy material has a fibrous structure. The fibrous structure is a metal structure stretched by plastic working.
Fig. 1 is a schematic view showing a fiber structure of the Al — Mg — Si alloy sheet according to the present invention.
As shown in fig. 1, in the present application, the microstructure is exposed such that the normal line of the observation surface is perpendicular to both the machining direction vector of the Al — Mg — Si alloy sheet and the normal direction vector of the machining surface, and the microstructure in which 3 grain boundaries per 100 μm or more are present in the normal direction of the machining surface and grain boundaries having a length in the machining direction of 300 μm or more are present in the microstructure observed with an optical microscope is defined as a fiber structure. When the plastic working is rolling, the working direction is the rolling direction, the working surface is the rolling surface, and the observation surface is a cross section in the thickness direction cut parallel to the rolling direction.
Examples of the method of exposing the metal structure include the following methods: a surface of an Al-Mg-Si alloy material, the normal of which is perpendicular to both a vector in the machine direction of the Al-Mg-Si alloy material and a vector in the normal direction of the machine surface, is polished, and then the polished surface is anodized. The anodizing solution can suitably use a Barker reagent (3% aqueous hydrofluoroboric acid solution).
The Al-Mg-Si alloy sheet of the present invention has an electrical conductivity of 50% < electrical conductivity < 54% (IACS), a sheet thickness of 3mm or less and a sheet thickness of 9mm or less, and a tensile strength of 170MPa or more. The value obtained by dividing 0.2% yield strength (MPa) by tensile strength (MPa) of the Al-Mg-Si alloy material of the present application is defined to be 0.91 to 1.00. An Al-Mg-Si alloy sheet having a fiber structure and a tensile strength satisfying a value obtained by dividing 0.2% yield strength (MPa) by tensile strength (MPa) specified in the present application. The value obtained by dividing the 0.2% yield strength (MPa) by the tensile strength (MPa) is more preferably 0.92 or more and 1.00 or less, and particularly preferably 0.93 or more and 1.00 or less.
Examples
Examples of the present invention and comparative examples are shown below.
Aluminum alloy slabs having different chemical compositions shown in table 1 were obtained by the DC casting method. Further, the rare earth-containing ingot of chemical composition No. 20 used a raw material containing misch metal for casting.
[ example 1]
The aluminum alloy slab of chemical composition No. 1 of table 1 was subjected to surface cutting. Subsequently, the alloy slab after the face cutting was homogenized in a heating furnace at 570 ℃ for 3 hours, and thereafter heated in the same furnace at 540 ℃ for 4 hours before hot rolling while changing the temperature. The slab at 540 ℃ was taken out of the heating furnace after heating before hot rolling, and rough hot rolling was started. After the thickness of the alloy sheet in the rough hot rolling was 25mm, the final pass of the rough hot rolling was performed at an average cooling rate of 80 ℃/min from the temperature of the alloy sheet immediately before the pass, and an alloy sheet having a thickness of 12mm was produced at a rough hot rolling completion temperature of 222 ℃. In the final pass of rough hot rolling, the alloy sheet is moved while being rolled, and the alloy sheet is subjected to forced cooling by water cooling in which water mist is sprayed sequentially from above and below the alloy sheet.
After the rough hot rolling, the alloy sheet was subjected to finish hot rolling from a temperature of 220 ℃ immediately 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 ℃.
Examples 2 to 32 and comparative examples 1 to 6
The aluminum alloy slabs described in table 1 were subjected to surface cutting and then to treatment under the conditions described in tables 2 to 5, thereby obtaining aluminum alloy sheets. In all of the examples and comparative examples, as in example 1, homogenization treatment and heating before hot rolling were continuously performed in the same furnace, and forced cooling after the final pass of rough hot rolling was selected from water cooling in which the alloy sheet was moved while being rolled, and further air cooling in which air cooling was performed by blowing air from above and below to the alloy sheet at the portion of the alloy sheet after rolling in this order.
In example 18, the final pass of the rough hot rolling was set to the final pass of the hot rolling, and the finish hot rolling was not performed.
In comparative examples 1 and 2, heat treatment was performed at 550 ℃ for 1 minute during cold rolling, and then solution treatment was performed by cooling at a rate of 5 ℃/sec or more. In comparative examples 1 and 2, the cold rolling reduction is the total cold rolling reduction before and after the solution treatment, and the cold rolling after the solution treatment is performed so that the cold rolling reduction from the thickness of the alloy material after the solution treatment is 30%.
The tensile strength, 0.2% yield strength, electric conductivity, and presence or absence of a fiber structure of the obtained alloy sheet were evaluated by the following methods.
The tensile strength and 0.2% yield strength of the test piece of JIS5 were measured at room temperature by a conventional method.
Conductivity to annealed standard soft copper (volume resistivity 1.7241 x 10) to be adopted internationally-2μ Ω m) was determined as a relative value (% IACS) when the conductivity was 100% IACS。
In the examples and comparative examples, when the microstructure of the cross section of the Al — Mg — Si alloy sheet in the thickness direction cut parallel to the rolling direction was exposed, the microstructure where the grain boundaries in the normal direction of the rolling surface of the microstructure were 3 grains/100 μm or more and the grain boundaries having a length in the rolling direction of 300 μm or more were present as the fiber structure, as observed with an optical microscope.
As a method for exposing the metal structure, the following method is applied: grinding the section of the Al-Mg-Si alloy plate cut in parallel with the rolling direction by using sand paper, performing rough polishing and grinding, performing fine grinding, performing water washing and drying, and then performing heat treatment in a Barker reagent (3% aqueous solution of hydrofluoroboric acid) at a bath temperature of: 28 ℃ applied Voltage: 30V, application time: the anodic oxidation treatment was carried out for 90 seconds.
The values obtained by dividing the tensile strength, 0.2% yield strength, and 0.2% yield strength (MPa) by the tensile strength (MPa), the results of evaluating the electrical conductivity and the workability, and whether or not the Al — Mg — Si alloy sheet has a fiber structure are shown in tables 6 and 7.
In each example, the Al — Mg — Si alloy sheet having a fiber structure satisfying the chemical composition, tensile strength, and a value obtained by dividing 0.2% yield strength (MPa) by tensile strength (MPa), electric conductivity, and sheet thickness specified in the present application was also excellent in workability. On the other hand, comparative examples 1 and 2, which were subjected to solution treatment during cold rolling, had no fiber structure, and had inferior electrical conductivity to those of examples, and comparative examples 3 to 6, which had chemical compositions not satisfying the ranges specified in the present application, had inferior tensile strength and at least one of electrical conductivity to those of examples, and also had inferior workability.
The present application claims the priority of japanese patent application No. 2018-161472, which was filed on 30/8/2018, the disclosure of which directly forms part of the present application.
The terms and expressions which have been employed in the specification are to be understood as terms and expressions which have been employed for the purpose of illustration and not of limitation, and there is no intention in the use of such terms and expressions of excluding any equivalents of the features disclosed and described herein, but rather there are alterations and modifications are possible within the scope of the invention claimed.
Although the present invention has been described with reference to the illustrated embodiments, the present invention is not limited to the embodiments described herein, and includes all embodiments having equivalent elements, modifications, omissions, combinations (e.g., of features across various embodiments), improvements, and/or alterations that can be obtained by those skilled in the art based on the disclosure.
Industrial applicability
The present invention can be used for chassis, metal-based printed boards, inner liners, and the like of products such as thin televisions, thin monitors for personal computers, notebook computers, tablet computers, car navigation systems, portable navigation systems, mobile terminals such as smart phones and mobile phones.
Claims (5)
1. An Al-Mg-Si alloy sheet having a chemical composition containing 0.2 to 0.8 mass% of Si, 0.3 to 1 mass% of Mg, 0.5 mass% or less of Fe and 0.5 mass% or less of Cu, at least 1 of 0.1 mass% or less of Ti and 0.1 mass% or less of B, and the balance being Al and unavoidable impurities,
the Al-Mg-Si alloy sheet has a tensile strength of 170MPa or more, a value obtained by dividing 0.2% yield strength by the tensile strength of 0.91 to 1.00, an electric conductivity of 50% IACS < electric conductivity < 54% IACS, a sheet thickness of 3mm or more and a sheet thickness of 9mm or less, a fiber structure, a 0.2% yield strength and a tensile strength unit of MPa,
wherein the microstructure is exposed such that the normal line of the observation surface is perpendicular to both the machining direction vector and the normal direction vector of the machining surface of the Al-Mg-Si alloy plate, and the microstructure in which 3 grain boundaries are present in the normal direction of the machining surface of the microstructure of the observation surface, the grain boundaries being present in the machining surface, the grain boundaries being 3 grains/100 [ mu ] m or more and the length in the machining direction being 300 [ mu ] m or more, as observed with an optical microscope, is defined as a fiber structure.
2. The Al-Mg-Si alloy sheet according to claim 1, wherein Mn, Cr and Zn as impurities are limited to 0.1 mass% or less, respectively.
3. The Al-Mg-Si alloy sheet according to claim 1 or 2, wherein Ni, V, Ga, Pb, Sn, Bi and Zr as impurities are limited to 0.05 mass% or less, respectively.
4. The Al-Mg-Si alloy sheet according to claim 1 or 2, wherein Ag as an impurity is limited to 0.05 mass% or less.
5. The Al-Mg-Si alloy sheet according to claim 1 or 2, wherein the total content of rare earth elements as impurities is limited to 0.1 mass% or less.
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| JP2018161472A JP7262947B2 (en) | 2018-08-30 | 2018-08-30 | Al-Mg-Si alloy plate |
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Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1639373A (en) * | 2002-03-01 | 2005-07-13 | 昭和电工株式会社 | Process for producing Al-Mg-Si alloy plate, Al-Mg-Si alloy plate and Al-Mg-Si alloy material |
| CA2655567A1 (en) * | 2006-08-02 | 2008-02-07 | Nippon Light Metal Company, Ltd. | Aluminum alloy fin material for heat exchanger, process for manufacturing the same, and process for manufacturing heat exchanger through brazing of the fin material |
| CN103060633A (en) * | 2012-12-28 | 2013-04-24 | 福建省闽发铝业股份有限公司 | A manufacturing method for an aluminum alloy with high conductivity |
| CN105247087A (en) * | 2013-08-09 | 2016-01-13 | 株式会社神户制钢所 | Electrically conductive aluminum alloy plate and method for manufacturing same |
| CN105420556A (en) * | 2015-11-19 | 2016-03-23 | 国家电网公司 | Aluminum alloy conductor for extra-high voltage |
| CN106460104A (en) * | 2014-03-06 | 2017-02-22 | 古河电气工业株式会社 | Aluminum alloy wire, aluminum alloy strand wire, coated electric wire, wire harness, process for producing aluminum alloy wire, and method for examining aluminum alloy wire |
| JP6112437B1 (en) * | 2016-10-31 | 2017-04-12 | 住友電気工業株式会社 | Aluminum alloy wire, aluminum alloy stranded wire, covered wire, and wire with terminal |
| CN107043878A (en) * | 2017-05-10 | 2017-08-15 | 广东伟业铝厂集团有限公司 | Aluminum alloy materials and its production technology, the electric conductor of high-strength high-conductivity |
Family Cites Families (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| MX2013002636A (en) * | 2010-09-08 | 2013-05-09 | Alcoa Inc | Improved aluminum-lithium alloys, and methods for producing the same. |
| JP5925667B2 (en) * | 2012-11-19 | 2016-05-25 | 株式会社神戸製鋼所 | Aluminum alloy material for high-pressure hydrogen gas container and manufacturing method thereof |
| WO2014129385A1 (en) * | 2013-02-25 | 2014-08-28 | 株式会社Uacj | Aluminum alloy plate for can body and production method therefor |
| JP6310250B2 (en) * | 2013-12-25 | 2018-04-11 | 三菱アルミニウム株式会社 | Aluminum alloy material for conductive material and method for producing the same |
| JP2017179457A (en) * | 2016-03-30 | 2017-10-05 | 昭和電工株式会社 | Al-Mg-Si-BASED ALLOY MATERIAL |
| JP6718276B2 (en) * | 2016-03-30 | 2020-07-08 | 昭和電工株式会社 | Method for manufacturing Al-Mg-Si alloy plate |
| JP2020033606A (en) * | 2018-08-30 | 2020-03-05 | 昭和電工株式会社 | MANUFACTURING METHOD OF Al-Mg-Si-BASED ALLOY SHEET |
-
2018
- 2018-08-30 JP JP2018161472A patent/JP7262947B2/en active Active
-
2019
- 2019-08-26 CN CN201910787655.0A patent/CN110872665B/en active Active
Patent Citations (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1639373A (en) * | 2002-03-01 | 2005-07-13 | 昭和电工株式会社 | Process for producing Al-Mg-Si alloy plate, Al-Mg-Si alloy plate and Al-Mg-Si alloy material |
| CA2655567A1 (en) * | 2006-08-02 | 2008-02-07 | Nippon Light Metal Company, Ltd. | Aluminum alloy fin material for heat exchanger, process for manufacturing the same, and process for manufacturing heat exchanger through brazing of the fin material |
| CN101501230A (en) * | 2006-08-02 | 2009-08-05 | 日本轻金属株式会社 | Aluminum alloy fin material for heat exchanger and method ofproduction of same and method of production of heat exchanger by brazing fin material |
| CN103060633A (en) * | 2012-12-28 | 2013-04-24 | 福建省闽发铝业股份有限公司 | A manufacturing method for an aluminum alloy with high conductivity |
| CN105247087A (en) * | 2013-08-09 | 2016-01-13 | 株式会社神户制钢所 | Electrically conductive aluminum alloy plate and method for manufacturing same |
| CN106460104A (en) * | 2014-03-06 | 2017-02-22 | 古河电气工业株式会社 | Aluminum alloy wire, aluminum alloy strand wire, coated electric wire, wire harness, process for producing aluminum alloy wire, and method for examining aluminum alloy wire |
| CN105420556A (en) * | 2015-11-19 | 2016-03-23 | 国家电网公司 | Aluminum alloy conductor for extra-high voltage |
| JP6112437B1 (en) * | 2016-10-31 | 2017-04-12 | 住友電気工業株式会社 | Aluminum alloy wire, aluminum alloy stranded wire, covered wire, and wire with terminal |
| CN107043878A (en) * | 2017-05-10 | 2017-08-15 | 广东伟业铝厂集团有限公司 | Aluminum alloy materials and its production technology, the electric conductor of high-strength high-conductivity |
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