JP2017179451A - 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 strength while having high conductivity and good processability.SOLUTION: In a manufacturing method of an alloy sheet in which hot rolling and cold rolling is 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 is set at 170°C or less just after completion of the hot rolling and heat treatment at a temperature of 120°C or more and less than 200°C is conducted after completion of the hot rolling and before completion of the cold rolling.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, strength and workability.

  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, 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, 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 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, 0.22 to 1.0% by mass of Cu, and the balance is 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 having a thickness of 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 is 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 1 type or 2 types, and the balance of Al and Ti in unavoidable 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 is produced by continuous casting and then cold rolled. Then, 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 There 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: A method for producing an alloy plate including a step of hot rolling an Al—Mg—Si alloy ingot regulated to 0.1% by mass or less and further cold rolling, There is shown a method for producing an Al—Mg—Si based 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 along with higher performance, smaller size, and thinner products using aluminum alloy member materials, in addition to high conductivity and workability, While the Al-Mg-Si alloy plate 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.

  An object of this invention is to provide the manufacturing method of the Al-Mg-Si type alloy board which has still higher intensity | strength, having high electrical conductivity and favorable workability in view of the technical background mentioned above.

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 based alloy plate immediately after the end of hot rolling is 170 ° C. or less, 120 ° C. or more after the end of hot rolling and before the end of cold rolling The manufacturing method of the Al-Mg-Si type alloy board which heat-processes at the temperature below 200 degreeC.
(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 based alloy sheet according to any one of the preceding items 1 to 5, wherein the heat treatment is performed after completion of hot rolling and before the start of cold rolling.
(7) The method for producing an Al—Mg—Si alloy plate according to any one of the preceding items 1 to 6, wherein the surface temperature of the Al—Mg—Si alloy plate immediately after the end of hot rolling is 150 ° C. or less. .
(8) The method for producing an Al—Mg—Si alloy plate according to any one of items 1 to 7, wherein the heat treatment temperature is 130 ° C. or higher and 180 ° C. or lower.
(9) The method for producing an Al—Mg—Si based alloy sheet according to any one of the preceding items 1 to 8, wherein the rolling rate of the cold rolling after the heat treatment is 20% or more.
(10) The method for producing an Al—Mg—Si based alloy sheet according to any one of the preceding items 1 to 9, wherein the final annealing is performed after cold rolling.
(11) The method for producing an Al—Mg—Si-based alloy sheet according to item 10 above, wherein the final annealing temperature is 180 ° C. or less.
(12) 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 12. The method for producing an Al—Mg—Si-based alloy plate according to any one of the preceding items 1 to 11, 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. A method for producing an alloy plate that sequentially performs rolling and cold rolling, wherein the surface temperature of the Al—Mg—Si based alloy plate 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. And improved workability show high tensile strength and high electrical conductivity. 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, the tensile strength and the conductivity are high and the workability is high. Can be produced.

  According to the invention described in the preceding item (3), 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 item (4) above, since Ag as an impurity is regulated to 0.05% by mass or less, Al—Mg— showing high values of tensile strength and electrical conductivity and good workability. Si-based alloy plates can be manufactured.

  According to the invention described in the preceding item (5), 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 workability is good. An Al—Mg—Si based alloy plate can be manufactured.

  According to the invention described in the preceding item (6), since the heat treatment is performed after the end of hot rolling and before the start of cold rolling, age hardening and conductivity improvement during heat treatment, and work hardening by cold rolling are performed. By improving the workability, an Al—Mg—Si alloy plate having high tensile strength and high conductivity and good workability can be produced.

  According to the invention described in item (7) above, since the surface temperature of the Al—Mg—Si based alloy plate 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 item (8) above, 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 reliably obtained.

  According to the invention described in item (9) 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 is improved by cold rolling and good processing is performed. Sex can be obtained.

  According to the invention described in item (10), since the final annealing is performed after cold rolling, the workability of the Al—Mg—Si based alloy sheet is good.

  According to the invention described in item (11) above, 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 (12), the surface temperature of the Al—Mg—Si 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, By performing a heat treatment as an aging treatment after the end of rolling and before the end of cold rolling, an Al—Mg—Si based alloy sheet having a higher strength while having high conductivity and good workability can be obtained. As a result, the inventors have reached the present invention.

  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 0.45 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 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 0.1% 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 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 plate immediately after the end of 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 the end of hot rolling and before the end of cold rolling. Is insufficient. The surface temperature of the Al—Mg—Si based alloy sheet immediately after the hot rolling is preferably 150 ° C. or lower, more preferably 130 ° C. or lower.

  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 280 degrees C or less.

  Similarly, when the final hot rolling is not performed and the final pass of the rough hot rolling is not the control pass, the surface temperature of the Al—Mg—Si alloy plate immediately before the final hot hot rolling pass is 280 ° 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 pass so that the surface temperature of the alloy plate is 470 to 350 ° C., and the surface temperature of the alloy plate is 170 ° C. or less at a cooling rate of 50 ° C./min or more by rolling or forced cooling after rolling and rolling. To implement.

  A heat treatment is applied to the Al—Mg—Si based alloy plate after the hot rolling and before the cold rolling to age-harden and improve the conductivity.

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

  The heat treatment time of the Al—Mg—Si based alloy sheet performed at a temperature of 120 ° C. or more and less than 200 ° C. after the hot rolling is finished but before 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, it is work-hardened by cold rolling to 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 by cold rolling of the age-hardened Al—Mg—Si based alloy sheet.

  An Al—Mg—Si based alloy plate having a predetermined thickness is formed by cold rolling after the heat treatment. The cold rolling after the heat treatment is preferably performed at a rolling rate of 20% or more in order to improve strength and improve workability. 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.

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

  When the workability of the Al—Mg—Si based alloy plate is further emphasized, final annealing may be performed after cold rolling. The final annealing is preferably performed at 180 ° C. or lower, and more preferably 160 ° C. or lower, particularly 140 ° C. or lower, in order to prevent the strength of the Al—Mg—Si based alloy sheet from becoming too low.

  The final annealing time of the Al—Mg—Si based alloy sheet 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 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 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 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 2-47, Comparative Examples 1-7]
After chamfering the aluminum alloy slab described in Table 1, treatment was performed under the conditions described in Tables 2 to 7 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 17, the final pass of rough hot rolling was used as the final pass of hot rolling, and the finish hot rolling was not performed.

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

  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.

  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 The bending test by the 6.3 V block method of the JIS Z 2248 metal material bending test method was carried out with the radius set to 0, and the case where no crack was generated was evaluated as ◯, and the case where the crack was generated was evaluated as ×.

  Tables 2 to 7 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.

Claims (12)

  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 surface temperature of the Al-Mg-Si type alloy sheet immediately after completion | finish of hot rolling is 170 degrees C or less, It is after completion | finish of hot rolling, and before completion | finish of cold rolling 120 degreeC or more and less than 200 degreeC The manufacturing method of the Al-Mg-Si type alloy plate which heat-processes at the temperature of.   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 sheet according to any one of claims 1 to 5, 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 1 to 6, wherein the surface temperature of the Al-Mg-Si alloy plate immediately after the end of hot rolling is 150 ° C or lower.   The method for producing an Al-Mg-Si alloy plate according to any one of claims 1 to 7, wherein a 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 1 to 8, 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 1 to 9, wherein final annealing is performed after cold rolling.   The method for producing an Al-Mg-Si alloy plate according to claim 10, wherein the temperature of the final annealing is 180 ° 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 based alloy plate according to any one of claims 1 to 11, wherein a pass having an average cooling rate by forced cooling of 50 ° C / min or more is performed at least once.