WO2019021899A1 - Plaque d'alliage d'aluminium et procédé de production de celle-ci - Google Patents

Plaque d'alliage d'aluminium et procédé de production de celle-ci Download PDF

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Publication number
WO2019021899A1
WO2019021899A1 PCT/JP2018/026827 JP2018026827W WO2019021899A1 WO 2019021899 A1 WO2019021899 A1 WO 2019021899A1 JP 2018026827 W JP2018026827 W JP 2018026827W WO 2019021899 A1 WO2019021899 A1 WO 2019021899A1
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WIPO (PCT)
Prior art keywords
aluminum alloy
temperature
less
range
alloy sheet
Prior art date
Application number
PCT/JP2018/026827
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English (en)
Japanese (ja)
Inventor
喜文 新里
健史 永井
峰生 浅野
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株式会社Uacj
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Publication date
Application filed by 株式会社Uacj filed Critical 株式会社Uacj
Priority to CN201880049900.1A priority Critical patent/CN110945153A/zh
Priority to KR1020207003047A priority patent/KR20200034729A/ko
Publication of WO2019021899A1 publication Critical patent/WO2019021899A1/fr
Priority to US16/752,490 priority patent/US20200157668A1/en

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/047—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with magnesium as the next major constituent
    • 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
    • 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

Definitions

  • the present invention relates to members and parts used in various vehicles represented by car body sheets and body panels, members and parts used in ships, aircraft, etc., or construction materials, structural materials, and various other machine tools, Aluminum alloy sheets used after forming and painting baking as materials for home appliances and parts thereof, particularly Al which has excellent press formability and stress corrosion cracking resistance while having high tensile strength.
  • the present invention relates to a Mg-based aluminum alloy sheet and a method of manufacturing the same.
  • an Al-Mg based alloy for example, a 5000 series Al alloy containing 3.5 mass% or more of Mg such as 5056, 5082, 5182, 5083, 5086 is used.
  • Mg metal-organic compound
  • These Al-Mg based alloys are used as welded structural members because they have high strength, good formability, and excellent weldability.
  • Patent Document 1 cooling after solution treatment is performed subsequent to hot rolling and cold rolling is performed in two stages under different cooling rate conditions in the high temperature region and the low temperature region, and the low temperature region is A method of manufacturing an Al-Mg-Cu-based aluminum alloy sheet for forming processing which can prevent continuous precipitation of ⁇ phase at grain boundaries during cooling by increasing the cooling rate in the above is described.
  • Patent Document 2 contains Mg: 3.5 to 5.5%, the strength after final annealing is 250 N / mm 2 or more, and the conductivity after the annealing is 26.5 to 29.
  • the structural aluminum alloy plate is described as having 6 IACS%, and according to the description, the conductivity is 296 IACS% or less, and the strength is obtained by causing precipitation of all precipitates including the ⁇ phase and solid solution state. It is said that it is possible to improve stress corrosion cracking resistance without deteriorating the properties.
  • the aluminum alloy sheet described in Patent Document 1 has a large content of Cu of 0.5 to 1.8 mass%, so that the hot workability is lowered and a coarse compound is formed, and the formability is inferior.
  • the hot workability is lowered and a coarse compound is formed, and the formability is inferior.
  • the structural aluminum alloy sheet described in Patent Document 2 has only Mg as an essential component and limits the strength and conductivity after final annealing treatment, but contains a specific component other than Mg.
  • the cooling rate during casting It is necessary to make the cooling rate faster in the intermediate annealing in cold rolling and in the cooling after heating in the final annealing after cold rolling, which means an increase in the number of manufacturing steps and manufacturing conditions.
  • the strict control of the above causes a decrease in productivity.
  • the present invention was made in view of such circumstances, and its object is to provide an aluminum alloy sheet having high tensile strength and excellent in press formability and stress corrosion cracking resistance, in particular An Al-Mg-based aluminum alloy sheet and a method of manufacturing the same.
  • the present inventors conducted various experiments and studies on composition components and manufacturing processes of Al-Mg-based alloys in order to solve the above problems, and limit the composition components and manufacturing processes to appropriate conditions. Found that it is possible to control the size and number density of the intermetallic compounds present in the aluminum alloy sheet, thereby providing excellent press formability and stress corrosion resistance while maintaining high tensile strength. We succeeded in the development of the aluminum alloy sheet which also has the properties and came to complete the present invention.
  • each embodiment of an aluminum alloy plate and its manufacturing method is as follows.
  • (1) By mass%, Si: 0.03 to 0.35%, Fe: 0.03 to 0.35%, Mg: 3.0 to 5.0%, Cu: 0.09% or more and 0.50
  • An aluminum alloy sheet characterized by containing less than 10% and Mn: more than 0.05% and not more than 0.35%, and having a composition comprising the balance of Al and unavoidable impurities.
  • (2) The number density of the intermetallic compound having a circle equivalent diameter of 0.1 to 0.5 ⁇ m and containing no Cu is 1 ⁇ 10 6 / mm 2 or less.
  • Aluminum alloy sheet as described.
  • the equivalent circle diameter is 0.3 to 4 ⁇ m, and the number density of the Cu-containing intermetallic compound is 1 ⁇ 10 4 pieces / mm 2 or more.
  • Aluminum alloy sheet (4) The aluminum alloy sheet according to the above (1), characterized in that Cu: 0.13 to 0.35 mass%. (5) The aluminum alloy according to (1), wherein the composition further contains one or two of Ti: 0.05% by mass or less and B: 0.05% by mass or less Board.
  • a method for producing an aluminum alloy sheet comprising: winding at a third temperature within the range of (1), and then performing cold rolling and final annealing treatment sequentially.
  • the first temperature is in the range of 500 to 570 ° C.
  • Said second temperature is in the range of 440-490 ° C .
  • Si 0.03 to 0.35%
  • Fe 0.03 to 0.35%
  • Mg 3.0 to 5.0%
  • Cu 0.09%
  • Si 0.03 to 0.35%
  • Fe 0.03 to 0.35%
  • Mg 3.0 to 5.0%
  • Cu 0.09%
  • Si 0.03 to 0.35%
  • Fe 0.03 to 0.35%
  • Mg 3.0 to 5.0%
  • Cu 0.09%
  • the aluminum alloy sheet according to one embodiment is, by mass%, Si: 0.03 to 0.35%, Fe: 0.03 to 0.35%, Mg: 3.0 to 5.0%, Cu: 0.09 %, Less than 0.50% and Mn: more than 0.05% and 0.35% or less, and the balance has a composition consisting of Al and unavoidable impurities.
  • Si Chemical composition ⁇ Si: 0.03 to 0.35%> Si (silicon) has an effect of improving stress corrosion cracking resistance, and is one of the important components in one embodiment. If the Si content is less than 0.03%, it is not possible to prevent preferential precipitation of ⁇ phase (Al 3 Mg 2 ) to the grain boundaries, stress corrosion cracking resistance deteriorates, and crystal grains after final annealing become This is because roughening tends to occur and rough skin is likely to occur. On the other hand, if the Si content exceeds 0.35%, an intermetallic compound is formed to deteriorate press formability, in particular, stretchability and deep drawability. Therefore, the Si content is in the range of 0.03 to 0.35%, preferably in the range of 0.09 to 0.25%.
  • Fe iron
  • Fe (iron) also has an effect of improving stress corrosion cracking resistance, similarly to Si, and is one of the important components in one embodiment. If the Fe content is less than 0.03%, it is not possible to prevent the preferential precipitation of ⁇ phase (Al 3 Mg 2 ) to the grain boundaries, stress corrosion cracking resistance deteriorates, and the crystal grains after final annealing become It becomes coarse and it becomes easy to generate rough skin. On the other hand, if the Fe content exceeds 0.35%, an intermetallic compound is formed to deteriorate press formability, in particular, stretchability and deep drawability. Therefore, the Fe content is in the range of 0.03 to 0.35%, preferably in the range of 0.09 to 0.25%.
  • Mg manganesium
  • Mg content is in the range of 3.0 to 5.0%, preferably in the range of 3.2 to 4.7%.
  • Cu more than 0.09% and less than 0.50%>
  • Cu (copper) is a component having the effect of enhancing work hardenability as well as Mg and improving stretchability and deep drawability. Further, Cu also has an action of suppressing the intergranular precipitation of the ⁇ phase to improve stress corrosion cracking resistance by forming an Al-Mg-Cu based compound. In order to exert such an effect, it is necessary to contain the Cu content in excess of 0.09%. In addition, when the Cu content is 0.50% or more, while the hot workability is lowered, a coarse compound is formed, and the press formability is lowered. Therefore, the Cu content is in the range of more than 0.09% and less than 0.50%, preferably in the range of more than 0.09% and 0.35%.
  • Mn manganese
  • the Mn content exceeds 0.35%, the size of the recrystallized grains becomes too small, and the stretcher / strain mark (strain pattern (wrinkling on the surface of the alloy sheet) appears on the surface of the press-formed alloy sheet. ) Is likely to occur, and the formability also decreases.
  • the aluminum alloy sheet according to one embodiment contains Si, Fe, Mg, Cu and Mn as essential components, but if necessary, Ti: 0.05% or less and B: 0.05% or less.
  • Si Si, Fe, Mg, Cu and Mn as essential components, but if necessary, Ti: 0.05% or less and B: 0.05% or less.
  • Ti and B are components having the function of refining the crystal grains of the ingot.
  • the content of each of Ti and B is in the range of 0.05% or less because the content of each of Ti and B does not adversely affect the press formability and the stress corrosion cracking resistance unless the content is more than 0.05%.
  • the circle equivalent diameter is 0.1 to 0.5 ⁇ m, and the number density of Cu-free intermetallic compounds is 1 ⁇ 10 6 / mm 2 or less
  • the aluminum alloy plate of one embodiment preferably has a circle equivalent diameter of 0.1 to 0.5 ⁇ m, and the number density of the Cu-free intermetallic compound is preferably 1 ⁇ 10 6 / mm 2 or less.
  • Intermetallic compounds that do not contain Cu have poor press formability and resistance to stress corrosion cracking when the equivalent circle diameter exceeds 0.5 ⁇ m or the number density exceeds 1 ⁇ 10 6 / mm 2.
  • the equivalent circle diameter of the intermetallic compound not containing Cu is less than 0.1 ⁇ m, although the formability is good, the stress corrosion cracking resistance tends to decrease. Therefore, it is preferable that the equivalent circle diameter is 0.1 to 0.5 ⁇ m and the number density of the Cu-free intermetallic compound is 1 ⁇ 10 6 / mm 2 or less.
  • the lower limit of the number density of the Cu-free intermetallic compound is not particularly limited, but is preferably 0.5 ⁇ 10 4 / mm 2 from the viewpoint of press formability.
  • the term "equivalent circle diameter” as used herein means the diameter (equivalent circle diameter) when the area of the observed particles is converted to circle equivalent.
  • the circle equivalent diameter is 0.3 to 4 ⁇ m, and the number density of the Cu-containing intermetallic compound is 1 ⁇ 10 4 pieces / mm 2 or more.
  • the aluminum alloy plate has a circle equivalent.
  • the number density of the intermetallic compound having a diameter of 0.3 to 4 ⁇ m and containing Cu is preferably 1 ⁇ 10 4 pieces / mm 2 or more.
  • the equivalent circle diameter of the Cu-containing intermetallic compound is more than 4 ⁇ m, the press formability tends to be deteriorated. Therefore, the equivalent circle diameter is preferably 0.3 to 4 ⁇ m, and the number density of the Cu-containing intermetallic compound is preferably 1 ⁇ 10 4 / mm 2 or more.
  • the upper limit of the number density of the Cu-containing intermetallic compound is not particularly limited, but is preferably 7 ⁇ 10 5 pieces / mm 2 from the viewpoint of press formability.
  • the equivalent circle diameter and the number density of the intermetallic compounds present in the aluminum alloy plate are measured by analyzing the observation photograph obtained by observing the thin film sample prepared from the aluminum alloy plate with a transmission electron microscope. be able to.
  • the precipitates to be observed are Cu-containing intermetallic compounds or copper-free intermetallic compounds.
  • an elemental analyzer equipped in a transmission electron microscope It can be identified by conducting elemental analysis of the precipitate.
  • the circle equivalent diameter and the number density of the Cu-containing intermetallic compound and the copper-free intermetallic compound are different from the manufacturing conditions (treatment or treatment conditions under which the solid solution state or precipitation state of the intermetallic compound changes, such as heat treatment during manufacture). Since it changes largely with process, it can control by manufacturing an aluminum alloy plate by the manufacturing method mentioned later.
  • the above component composition (by mass, Si: 0.03 to 0.35%, Fe: 0.03 to 0.35%, Mg: 3.0 to 5.0%, Cu: more than 0.09% Aluminum alloy containing less than 0.50% and Mn: more than 0.05% and 0.35% or less, and the balance being composed of Al and unavoidable impurities) is melted according to a conventional method, continuous casting method, semi-continuous Select a regular casting method such as casting method at appropriate time and cast.
  • the resulting ingot is then subjected to homogenization treatment at a first temperature in the range of 490 to 580 ° C., preferably 500 to 570 ° C.
  • the treatment time of the homogenization treatment is not particularly limited, and can be, for example, in the range of 0.5 hours to 24 hours.
  • the formation of the Cu-containing intermetallic compound has the effect of improving the stress corrosion cracking resistance, while the formation of the Cu-free intermetallic compound has the effect of reducing the stress corrosion cracking resistance.
  • the average cooling rate exceeds 3000 ° C./h, the formation of Cu-containing intermetallic compounds is impeded, and the stress corrosion cracking resistance tends to decrease, and the average cooling rate is 500 ° C./hour. If it is less than h, the formation of Cu-free intermetallic compounds is promoted and the stress corrosion cracking resistance tends to be reduced.
  • the measurement position of the average cooling rate is set to “1 ⁇ 4 thickness position” because the temperature history of the 1 ⁇ 4 thickness position largely affects the performance of the material. Further, the reason for limiting the second temperature to the range of 430 to 500 ° C.
  • the average cooling rate is 500 to 3000 ° C./° to a second temperature within the range of 430 to 500 ° C. and lower than the first temperature. After cooling so as to be within the range of h, hot rolling is started at the second temperature.
  • the hot rolling After the hot rolling, it is wound at a third temperature in the range of 320 to 380 ° C., preferably in the range of 340 to 360 ° C., and then cold rolling and final annealing are sequentially performed.
  • the reason for limiting the coiling temperature to the third temperature in the range of 320 to 380 ° C. is that if the third temperature is less than 320 ° C., no recrystallized structure is obtained after hot rolling, and surface defects after press forming (rolling If the third temperature exceeds 380 ° C., crystal grains become coarse after hot rolling, and surface roughening may occur.
  • An aluminum alloy having the composition shown in Table 1 was melted and formed into a block by DC casting.
  • the obtained ingot (thickness 30 mm, width 175 mm) is heated to 560 ° C. (first temperature) and held at this first temperature for 4 hours, and then the ingot is shown in Table 2 from the first temperature.
  • the temperature range up to the temperature is cooled at the average cooling rate shown in Table 2 and held at the second temperature for 15 minutes, after which hot rolling is started at the second temperature (hot rolling start temperature), and a plate of 4 mm thickness And
  • the coiling temperature (3rd temperature) after hot rolling was 360 degreeC. Next, this plate was cold-rolled to a thickness of 1 mm, then heated at 540 ° C.
  • the aluminum alloy plates of the example and the comparative example were manufactured by the above steps.
  • Test method Method of measuring crystal grain size
  • the crystal grain size was measured for each of the manufactured aluminum alloy plates.
  • a sample is taken from the width center of the aluminum alloy plate, the grain structure is photographed on the rolling surface, and 5 straight lines at equal intervals in the longitudinal direction and in the horizontal direction in the field of 3 mm ⁇ 3 mm
  • the crystal grain size was measured by the section method, and the average value of the measured crystal grain sizes was calculated as an average crystal grain size ( ⁇ m). In this example, those having a crystal grain size of less than 50 ⁇ m were accepted, and those having a grain size of 50 ⁇ m or more were rejected (surface roughening).
  • a disc having a diameter of 110 mm is formed from each of the produced aluminum alloy plates, a low viscosity lubricating oil is applied to form a test material, and a lock bead is not provided on the die using an Erichsen tester.
  • a flat head punch with a diameter of 50 mm is used under the conditions of a wrinkle suppression force of 10 kN and a forming speed of 2.0 mm / s to measure the limit drawing height (mm) at which cracking does not occur. was evaluated.
  • the overhang formability in the overhang formability, the one having an overhang height of 17 mm or more is passed, the one having an overhang height of less than 17 mm is disqualified, and the deep drawability is an aperture height. Although the thing of 15 mm or more passed, the thing of less than 15 mm was disqualified.
  • Stress corrosion cracking resistance is obtained by cold-rolling a test specimen collected from the width center of each of the manufactured aluminum alloy plates at a processing rate of 30% and then subjecting it to a sensitization treatment of heat treatment at 120 ° C. for 7 days A chromic acid solution (pure water 1) heated to 95 ° C. in a stress-loaded state in which the test specimen subjected to the sensitization treatment is bent in a U shape having a bending radius of 2 mm and 3 mm and both ends of the U shape are restrained.
  • the aluminum alloy sheet of one embodiment has high strength, good press formability, and excellent resistance to stress corrosion cracking, and therefore, members used in various automobiles represented by automobile body sheets and body panels in particular. It is suitable for use in materials such as components and parts used in ships, aircraft, etc., as well as materials such as construction materials, structural materials, other various machine tools, household appliances and their parts, in addition to components and parts. The value is great.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Metal Rolling (AREA)
  • Shaping Metal By Deep-Drawing, Or The Like (AREA)

Abstract

Cette plaque d'alliage d'aluminium a une composition qui contient, en % en masse, 0,03-0,35% de Si, 0,03-0,35% de Fe, 3,0-5,0% de Mg, plus de 0,9% mais moins de 0,50% de Cu et plus de 0,05% mais moins de 0,35% ou moins de Mn, le reste étant constitué d'Al et des impuretés inévitables.
PCT/JP2018/026827 2017-07-26 2018-07-18 Plaque d'alliage d'aluminium et procédé de production de celle-ci WO2019021899A1 (fr)

Priority Applications (3)

Application Number Priority Date Filing Date Title
CN201880049900.1A CN110945153A (zh) 2017-07-26 2018-07-18 铝合金板及其制造方法
KR1020207003047A KR20200034729A (ko) 2017-07-26 2018-07-18 알루미늄 합금판 및 그 제조 방법
US16/752,490 US20200157668A1 (en) 2017-07-26 2020-01-24 Aluminum alloy plate and method for producing the same

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2017-144874 2017-07-26
JP2017144874A JP2019026876A (ja) 2017-07-26 2017-07-26 アルミニウム合金板およびその製造方法

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US (1) US20200157668A1 (fr)
JP (1) JP2019026876A (fr)
KR (1) KR20200034729A (fr)
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WO (1) WO2019021899A1 (fr)

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Publication number Priority date Publication date Assignee Title
WO2023031334A1 (fr) * 2021-09-03 2023-03-09 Speira Gmbh Bande d'alliage d'aluminium optimisée pour le formage, et son procédé de fabrication

Citations (7)

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JPS6050141A (ja) * 1983-08-27 1985-03-19 Kobe Steel Ltd キヤンエンド用アルミニウム合金硬質板およびその製造法
JPH04301055A (ja) * 1991-03-28 1992-10-23 Sumitomo Light Metal Ind Ltd 深絞り性に優れた成形加工用アルミニウム合金板材の製造法
JPH10219412A (ja) * 1997-02-04 1998-08-18 Shinko Alcoa Yuso Kizai Kk 成形加工後の外観性が優れたアルミニウム合金圧延板の製造方法
JP2007100182A (ja) * 2005-10-06 2007-04-19 Furukawa Sky Kk キャップ用アルミニウム合金板およびその製造方法
WO2015125791A1 (fr) * 2014-02-18 2015-08-27 株式会社神戸製鋼所 Tôle d'alliage d'aluminium pour couvercles de boîtes
CN104894442A (zh) * 2015-05-05 2015-09-09 山东南山铝业股份有限公司 一种车用铝合金板材及其制备方法
JP2016141886A (ja) * 2015-02-05 2016-08-08 株式会社神戸製鋼所 缶蓋用アルミニウム合金板

Family Cites Families (2)

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Publication number Priority date Publication date Assignee Title
JP2001032031A (ja) 1999-07-22 2001-02-06 Kobe Steel Ltd 耐応力腐食割れ性に優れた構造材用アルミニウム合金板
JP2003231956A (ja) 2002-02-12 2003-08-19 Sky Alum Co Ltd 成形加工用Ａｌ−Ｍｇ−Ｃｕ系アルミニウム合金板の製造方法

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS6050141A (ja) * 1983-08-27 1985-03-19 Kobe Steel Ltd キヤンエンド用アルミニウム合金硬質板およびその製造法
JPH04301055A (ja) * 1991-03-28 1992-10-23 Sumitomo Light Metal Ind Ltd 深絞り性に優れた成形加工用アルミニウム合金板材の製造法
JPH10219412A (ja) * 1997-02-04 1998-08-18 Shinko Alcoa Yuso Kizai Kk 成形加工後の外観性が優れたアルミニウム合金圧延板の製造方法
JP2007100182A (ja) * 2005-10-06 2007-04-19 Furukawa Sky Kk キャップ用アルミニウム合金板およびその製造方法
WO2015125791A1 (fr) * 2014-02-18 2015-08-27 株式会社神戸製鋼所 Tôle d'alliage d'aluminium pour couvercles de boîtes
JP2016141886A (ja) * 2015-02-05 2016-08-08 株式会社神戸製鋼所 缶蓋用アルミニウム合金板
CN104894442A (zh) * 2015-05-05 2015-09-09 山东南山铝业股份有限公司 一种车用铝合金板材及其制备方法

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JP2019026876A (ja) 2019-02-21
CN110945153A (zh) 2020-03-31
KR20200034729A (ko) 2020-03-31

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