JP2017179453A - MANUFACTURING METHOD OF Al-Mg-Si-BASED ALLOY SHEET - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide a manufacturing method of an Al-Mg-Si-based alloy sheet having high conductivity and high strength.SOLUTION: In a manufacturing method of an alloy sheet in which hot rolling and cold rolling are conducted in sequence on an ingot containing 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 at least one of Ti: 0.1 mass% or less or B: 0.1 mass% or less and the balance Al with inevitable impurities, the surface temperature of the Al-Mg-Si-based alloy sheet just after completion of the hot rolling is 230°C or less.SELECTED DRAWING: None

Description

  The present invention relates to a method for producing an Al—Mg—Si based alloy plate, and more particularly to a method for producing an Al—Mg—Si based alloy plate excellent in thermal conductivity, conductivity and strength.

  Heating elements such as flat panel TVs, thin monitors for personal computers, laptop 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 internal covers In a member material to be built in or mounted, excellent thermal conductivity and strength for promptly radiating heat are required.

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

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

  For example, Patent Document 1 contains Si: 0.2 to 1.5% by mass, Mg: 0.2 to 1.5% by mass, Fe: 0.3% by mass or less, and Mn: 0. Containing one or two of 02 to 0.15% by mass and Cr: 0.02 to 0.15%, and the balance of Al and Ti in inevitable impurities is restricted to 0.2% or less, or An aluminum alloy plate having a composition containing one or two of Cu: 0.01 to 1% by mass or rare earth element: 0.01 to 0.2% by mass was produced by continuous casting and rolling, and then cold-worked. Rolling, and then performing a solution treatment at 500 to 570 ° C., followed by further cold rolling at a cold rolling rate of 5 to 40%, and performing an aging treatment for heating to 150 to 190 ° C. after the cold rolling. Aluminum composite with excellent thermal conductivity, strength and bending workability Method for producing a plate is described.

  Patent Document 2 contains 0.1 to 0.34% by mass of Mg, 0.2 to 0.8% by mass of Si, 0.22 to 1.0% by mass of Cu, and the balance is Al and inevitable impurities. An Al—Mg—Si based alloy having a Si / Mg content ratio of 1.3 or more is made into an ingot having a thickness of 250 mm or more by semi-continuous casting, and is heated through preheating at a temperature of 400 to 540 ° C. Disclosed is a method for producing an Al—Mg—Si alloy rolled sheet, characterized by performing cold rolling at a rolling rate of 50 to 85% and annealing at a temperature of 140 to 280 ° C. ing.

  Patent Document 3 contains Si: 0.2 to 0.8 wt%, Mg: 0.3 to 0.9 wt%, Fe: 0.35 wt% or less, Cu: 0.20 mass% or less, and the balance Al. A method for producing an alloy in which an Al-Mg-Si alloy ingot made of inevitable impurities is homogenized, cold-rolled after hot rolling and hot finish rolling, and an optional pass of the hot rolling In the process, the material temperature before pass is set to 350 to 450 ° C., the rising plate thickness is set to 10 mm or less, and the reduction ratio of the cold rolling is set to 30% or more. A method for manufacturing a plate is disclosed.

  In the Al-Mg-Si based alloy, the thermal conductivity and electrical conductivity have a good correlation, and the aluminum alloy plate having excellent thermal conductivity has excellent electrical conductivity, not to mention the heat dissipation member material It can be used as a conductive member material.

JP 2007-9262 A JP 2012-62517 A JP 2000-87198 A

  In Patent Document 1, although an aluminum alloy plate having a relatively high strength is obtained, a solution treatment comprising high-temperature heat treatment at 500 ° C. or higher and subsequent rapid cooling is performed on the aluminum alloy plate in the middle of cold rolling, A complicated process of performing an aging treatment after further cold rolling is required, which increases the manufacturing cost.

In the manufacturing method described in Patent Document 2, no solution treatment is required in the process after hot rolling, but the maximum value of the tensile strength of the invention example remains at 213 N / mm ² (MPa).

In Patent Document 3, as in Patent Document 2, no solution treatment is required in the process after hot rolling, and a higher tensile strength than that in Patent Document 2 is obtained. However, in the example of Patent Document 2, 300 N / mm is used. ^The tensile strength exceeding ² (MPa) can be obtained only in the examples where the cold rolling reduction rate is 98% and the product sheet thickness is 0.1 mm, and there is a limit to the improvement in strength.

  In view of the technical background described above, the present invention provides an Al—Mg—Si based alloy plate that has high conductivity and can further improve strength without applying a solution treatment in a step after hot rolling. It aims at providing the manufacturing method of.

The above problem is solved by the following means.
(1) 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% by mass or less or B: 0.1% by mass or less of Al—Mg—Si based alloy ingot containing the balance Al and inevitable impurities is subjected to hot rolling and cold rolling in order. A method for producing an alloy plate, wherein the surface temperature of the Al—Mg—Si alloy plate immediately after the end of hot rolling is 230 ° C. or less.
(2) The method for producing an Al—Mg—Si based alloy plate according to item 1 above, wherein Mn, Cr, and Zn as impurities are each regulated to 0.1 mass% or less.
(3) Ni—V—Ga—Pb—Sn—Bi and Zr as impurities are each of the Al—Mg—Si-based alloy plate according to the preceding item 1 or 2, wherein the mass is regulated to 0.05% by mass or less. Production method.
(4) The method for producing an Al—Mg—Si alloy plate according to any one of the preceding items 1 to 3, wherein Ag as an impurity is regulated to 0.05% by mass or less.
(5) The method for producing an Al—Mg—Si alloy plate according to any one of the preceding items 1 to 4, wherein the total content of rare earth elements as impurities is regulated to 0.1% by mass or less.
(6) The method for producing an Al—Mg—Si alloy plate according to any one of the preceding items 1 to 5, wherein the surface temperature of the Al—Mg—Si alloy plate immediately after the end of hot rolling is 200 ° C. or less. .
(7) The method for producing an Al—Mg—Si based alloy sheet according to any one of the preceding items 1 to 6, wherein the rolling rate of cold rolling is 20% or more.
(8) The method for producing an Al—Mg—Si alloy plate according to any one of items 1 to 7, wherein the final annealing is performed after cold rolling.
(9) The method for producing an Al—Mg—Si based alloy plate according to item 8 above, wherein the final annealing temperature is 200 ° C. or less.
(10) 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 10. The method for producing an Al—Mg—Si based alloy sheet according to any one of the preceding items 1 to 9, wherein a pass in which an 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), 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, it contains at least one of Ti: 0.1% by mass or less or B: 0.1% by mass or less, and is hot in an Al—Mg—Si alloy ingot consisting of the balance Al and inevitable impurities. In the method for producing an alloy sheet that sequentially performs rolling and cold rolling, the surface temperature of the Al—Mg—Si alloy sheet immediately after the end of hot rolling is 230 ° C. or less, so that an effective quenching effect by hot rolling. And an Al—Mg—Si alloy plate having high tensile strength can be produced.

  According to the invention described in the preceding item (2), since Mn, Cr, and Zn as impurities are respectively regulated to 0.1% by mass or less, an Al—Mg—Si-based alloy having high tensile strength A board can be manufactured.

  According to the invention described in the preceding item (3), Ni, V, Ga, Pb, Sn, Bi, and Zr as impurities are each regulated to be 0.05% by mass or less, and thus have high tensile strength. An Al—Mg—Si based alloy plate can be manufactured.

  According to the invention described in item (4) above, since Ag as an impurity is regulated to 0.05% by mass or less, an Al—Mg—Si based alloy plate having high tensile strength can be manufactured. .

  According to the invention described in item (5) above, since the total content of rare earth elements as impurities is regulated to 0.1% by mass or less, an Al—Mg—Si based alloy sheet having high tensile strength is obtained. Can be manufactured.

  According to the invention described in item (6) above, since the surface temperature of the Al—Mg—Si alloy plate immediately after the end of hot rolling is 200 ° C. or less, the quenching effect by hot rolling can be enhanced.

  According to the invention described in item (7) above, 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 can be improved by cold rolling.

  According to the invention described in item (8), since the final annealing is performed after the cold rolling, the strength of the Al—Mg—Si based alloy plate can be further increased by age hardening, and at the same time the conductivity is improved. I can do it.

  According to the invention described in item (9) above, since the final annealing temperature is 200 ° C. or less, an Al—Mg—Si based alloy sheet showing high values of tensile strength and electrical conductivity can be produced.

  According to the invention described in item (10) above, the surface temperature of the Al—Mg—Si based alloy plate immediately before the pass among the plurality of passes of hot rolling is 470 to 350 ° C., and the Al—Mg—Si due to the pass is used. Since the pass in which the average cooling rate by cooling of the alloy plate or the forced cooling after the pass is 50 ° C./min or more is performed at least once, the quenching effect by hot rolling can be enhanced.

  The inventor of the present application, in a method for producing an Al-Mg-Si alloy plate that is sequentially subjected to hot rolling and cold rolling, sets the surface temperature of the alloy plate after hot rolling to a predetermined temperature or less, It is found that an Al-Mg-Si alloy sheet having high strength while having high conductivity and good workability can be obtained by performing heat treatment after the end of rolling and before the end of cold rolling. Invented.

  Below, the manufacturing method of the Al-Mg-Si type alloy plate of this application is demonstrated in detail.

  In the Al—Mg—Si based alloy composition of the present application, the purpose of adding each element and the reason for limiting the content are as follows.

  Mg and Si are elements necessary for strength development, and the respective contents thereof are Si: 0.2 mass% to 0.8 mass%, and Mg: 0.3 mass% to 1 mass%. If the Si content is less than 0.2% by mass or the Mg content is less than 0.3% by mass, sufficient strength cannot be obtained. 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 preferably 0.2% by mass or more and 0.6% by mass or less, and more preferably 0.32% by mass or more and 0.60% by mass or less. The Mg content is preferably 0.4% by mass or more and 1.0% by mass or less, more preferably 0.45% by mass or more and 0.9% by mass or less, and particularly preferably 0.45% by mass or more and 0.55% by mass or less. preferable.

  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 each regulated to 0.5% by mass or less. The Fe content is preferably regulated to 0.35% by mass or less, and more preferably from 0.1% by mass to 0.25% by mass. The Cu content is preferably 0.2% by mass or less, and more preferably 0.1% by mass or less.

  Ti and B have the effect of reducing 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.

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

  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, processing steps for obtaining the Al—Mg—Si based alloy sheet defined 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 make the crystallized substance and Mg, Si dissolve 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-based 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 to remove the impurity layer in the vicinity of the surface of the ingot before casting and before heating before hot rolling. The chamfering may be performed after casting and before homogenization treatment, or after homogenization treatment and before heating before hot rolling.

  The Al—Mg—Si alloy ingot after heating before hot rolling is hot rolled.

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

  When cold rolling is performed with a coil, the Al—Mg—Si alloy plate 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 plate is wound up by a winding device after the rough hot rolling. It may be a hot rolled coil.

  In rough hot rolling, after maintaining the state in which Mg and Si are dissolved in accordance with the solution treatment, cooling of the Al-Mg-Si alloy plate by the 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.

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

  The average cooling rate is the Al-Mg-Si alloy from the start of the control pass to the end 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.

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

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

  In this application, when forced cooling is not performed after the final pass of the rough hot rolling, the surface temperature of the Al-Mg-Si based alloy sheet immediately after the final pass of the hot rolling is set as the temperature after the rough hot rolling, When forced cooling is performed after the final pass of rolling, the surface temperature of the Al—Mg—Si based alloy sheet 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 230 ° C. or less. An effective quenching effect can be obtained by setting the temperature of the alloy sheet immediately after the hot rolling to 230 ° C. or less.

  If the surface temperature of the Al—Mg—Si based alloy sheet immediately after the hot rolling is too high, the effect of quenching is insufficient and the strength is not improved sufficiently. The surface temperature of the Al—Mg—Si alloy plate immediately after the hot rolling is preferably 200 ° C. or less, 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 based alloy plate immediately before finish hot rolling is: It is preferable that it is 270 degrees C or less.

  Similarly, when the final hot rolling is not performed and the final pass of the rough hot rolling is not a control pass, the surface temperature of the Al—Mg—Si alloy plate immediately before the final hot hot rolling is 270 ° C. or less. preferable.

  On the other hand, when final hot rolling is not performed and the final pass of rough hot rolling is a control pass, the control pass becomes the final pass of hot rolling, so the Al—Mg—Si system immediately before the final pass of hot rolling Control path so that the surface temperature of the alloy plate is 470 to 350 ° C. and the surface temperature of the alloy plate is 230 ° C. or less at a cooling rate of 50 ° C./min or more by rolling or forced cooling after rolling and rolling. To implement.

  After the hot rolling is finished, the Al—Mg—Si alloy plate is cold-rolled to obtain an Al—Mg—Si alloy plate having a predetermined thickness. The cold rolling after the heat treatment is preferably performed at a rolling rate of 20% or more in order to improve the strength. The rolling rate of the Al—Mg—Si based alloy sheet by cold rolling after the heat treatment is preferably 30% or more, particularly preferably 60% or more.

  By applying the above production conditions to an Al—Mg—Si based alloy, an Al—Mg—Si based alloy plate having high conductivity and high strength can be obtained.

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

  In order to further improve the strength and / or conductivity of the Al—Mg—Si based alloy plate, it is preferable to perform final annealing after cold rolling. When the final annealing is performed, the strength can be further increased by age hardening of the Al—Mg—Si alloy plate, and the electrical conductivity can be improved.

  The conditions for final annealing can be selected depending on whether to improve both strength and conductivity, or to place importance on either strength or conductivity. However, the annealing temperature becomes too high, and the strength of the Al-Mg-Si based alloy sheet is reduced. In order not to decrease, it is preferably carried out at 200 ° C. or lower, more preferably 110 ° C. or higher and 180 ° C. or lower, particularly preferably 120 ° C. or higher and 170 ° C. or lower.

  The final annealing time of the Al—Mg—Si based alloy plate may be adjusted so as to obtain necessary strength and electrical conductivity, and may be selected according to the final annealing temperature in the range of 1 to 10 hours, for example.

  The production of the Al—Mg—Si based alloy plate of the present application may be performed with 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.

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. In addition, the ingot of the chemical composition number 20 containing rare earth used the raw material containing misch metal for casting.

[Example 1]
The aluminum alloy slab having the chemical composition number 1 in Table 1 was chamfered. Next, the homogenized treatment at 570 ° C. for 5 hours was performed on the alloy slab after chamfering in a heating furnace, and then the pre-hot rolling at 540 ° C. for 4 hours was performed by changing the temperature in the same furnace. After heating before hot rolling, a 540 ° C. slab was taken out from the heating furnace, and rough hot rolling was started. After the thickness of the alloy plate during the rough hot rolling reaches 25 mm, the final pass of the rough hot rolling is performed at an average cooling rate of 80 ° C./min from the alloy plate temperature immediately before the pass of 460 ° C. An alloy plate having a hot rolling temperature of 242 ° C. and a thickness of 12 mm was obtained. In the final pass of the rough hot rolling, the alloy plate was moved while rolling, and forced cooling was performed by water cooling in which water was sprayed on the alloy plate sequentially from above and below the portion of the rolled alloy plate.

  After the rough hot rolling, the alloy plate was subjected to finish hot rolling from a temperature immediately before finish hot rolling of 240 ° C. to obtain an alloy plate having a thickness of 7.0 mm. The temperature of the alloy sheet immediately after the finish hot rolling was 130 ° C. The alloy sheet after the finish hot rolling was cold-rolled at a rolling rate of 91% and subjected to final annealing at 160 ° C. for 2 hours to obtain an aluminum alloy sheet having a product sheet thickness of 0.6 mm.

[Examples 2-35, Comparative Examples 1-5]
After chamfering the aluminum alloy slab described in Table 1, treatment was performed under the conditions described in Tables 2 to 5 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. 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 9, the final pass of the rough hot rolling was used as the final pass of the hot rolling, and the finish hot rolling was not performed.

  The obtained alloy plate was evaluated by a method below the tensile strength and conductivity.

  Tensile strength was measured by a conventional method at normal temperature for a JIS No. 5 test piece.

The electrical conductivity was determined 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.

  Tables 2 to 5 show the evaluation results of tensile strength and electrical conductivity.

  In the example having the chemical composition defined in the present application and the surface temperature of the alloy sheet immediately after the end of hot rolling is 230 ° C. or less, the tensile strength and conductivity are high values, whereas the chemical composition, hot The comparative example in which one of the surface temperatures of the alloy sheet immediately after the end of rolling does not satisfy the specified range of the present invention is inferior to the example in either tensile strength or electrical conductivity.

Claims (10)

  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 Ti: 0.1 mass% % Or B: 0.1% by mass or less of an alloy plate that sequentially performs hot rolling and cold rolling on an Al—Mg—Si alloy ingot consisting of Al and inevitable impurities. It is a manufacturing method, Comprising: The manufacturing method of the Al-Mg-Si type alloy plate whose surface temperature of the Al-Mg-Si type alloy plate immediately after completion | finish of hot rolling is 230 degrees C or less.   The method for producing an Al-Mg-Si based alloy plate according to claim 1, wherein Mn, Cr, and Zn as impurities are each regulated to 0.1 mass% or less.   The production of an Al-Mg-Si alloy plate according to claim 1 or 2, wherein Ni, V, Ga, Pb, Sn, Bi, and Zr as impurities are each regulated to 0.05 mass% or less. Method.   The method for producing an Al-Mg-Si alloy plate according to any one of claims 1 to 3, wherein Ag as an impurity is regulated to 0.05 mass% or less.   The method for producing an Al-Mg-Si alloy plate according to any one of claims 1 to 4, wherein a total content of rare earth elements as impurities is regulated to 0.1 mass% or less.   The method for producing an Al-Mg-Si alloy plate according to any one of claims 1 to 5, wherein the surface temperature of the Al-Mg-Si alloy plate immediately after the end of hot rolling is 200 ° C or less.   The method for producing an Al-Mg-Si alloy sheet according to any one of claims 1 to 6, wherein a rolling rate of cold rolling is 20% or more.   The method for producing an Al-Mg-Si alloy plate according to any one of claims 1 to 7, wherein final annealing is performed after cold rolling.   The method for producing an Al-Mg-Si-based alloy plate according to claim 8, wherein the final annealing temperature is 200 ° C or lower.   Among 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 The method for producing an Al-Mg-Si alloy plate according to any one of claims 1 to 9, wherein a pass having an average cooling rate by forced cooling of 50 ° C / min or more is performed at least once.