EP0690142A1 - Aluminiumlegierungsblech für Autokarosserie, Verfahren zu ihrer Herstellung sowie Verfahren zu ihrer Verformung - Google Patents

Aluminiumlegierungsblech für Autokarosserie, Verfahren zu ihrer Herstellung sowie Verfahren zu ihrer Verformung Download PDF

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Publication number
EP0690142A1
EP0690142A1 EP95401319A EP95401319A EP0690142A1 EP 0690142 A1 EP0690142 A1 EP 0690142A1 EP 95401319 A EP95401319 A EP 95401319A EP 95401319 A EP95401319 A EP 95401319A EP 0690142 A1 EP0690142 A1 EP 0690142A1
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EP
European Patent Office
Prior art keywords
sheet
less
rolling
aluminum alloy
hot
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Withdrawn
Application number
EP95401319A
Other languages
English (en)
French (fr)
Inventor
Tetsushi Habu
Yoichiro Bekki
Kunihiro C/O K.K. Honda Yasunaga
Noboru C/O K.K. Honda Hayashi
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Honda Motor Co Ltd
Furukawa Electric Co Ltd
Original Assignee
Honda Motor Co Ltd
Furukawa Electric Co Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Honda Motor Co Ltd, Furukawa Electric Co Ltd filed Critical Honda Motor Co Ltd
Publication of EP0690142A1 publication Critical patent/EP0690142A1/de
Withdrawn legal-status Critical Current

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Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • B21B1/227—Surface roughening or texturing
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B21B2003/001—Aluminium or its alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B45/00—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
    • B21B45/004—Heating the product
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B45/00—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
    • B21B45/02—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills for lubricating, cooling, or cleaning
    • B21B45/0239—Lubricating
    • B21B45/0245—Lubricating devices
    • B21B45/0248—Lubricating devices using liquid lubricants, e.g. for sections, for tubes

Definitions

  • This invention relates to an aluminum alloy sheet suitable for a material to form an auto body sheet or the like, a method for manufacturing the same and a method for forming the same, and more particularly, to an aluminum alloy sheet, which can be formed under low-viscosity lubrication condition only by subjecting a sheet surface to mill finish with an ordinary reduction roll without any special shot dull finish, a method for manufacturing such an aluminum alloy sheet and a method for forming such an aluminum alloy sheet.
  • the surface of a reduction roll is roughened by hitting sand, steel balls or the like against the roll surface or patterning the roll surface with fine irregularities by use of a laser or the like (such a roughened surface is called a shot surface), and the roll surface pattern is transferred to the sheet by rolling to provide a material having a roughened surface.
  • This material is termed a shot dull finish material.
  • the roll surface pattern should be transferred to the sheet surface by subjecting the sheet to skin pass rolling with a roll having a shot surface in a final cold rolling pass. Therefore, the manufacture of the conventional shot dull finish material requires one extra pass, and the shot working on the roll is highly expensive. In addition, it is necessary to hold the roll at all times, and a frequent roll exchange is required during rolling. Accordingly, there is caused a problem in an increase of cost.
  • An object of the present invention is to overcome the above problems, and more specifically, to provide an aluminum alloy sheet, which permits improvement in formability by forming micro pools on the sheet surface at a forming process under lubrication condition using a low-viscosity lubricant of 20 or less cSt in case of mill finish with an ordinary reduction roll, a method for manufacturing such an aluminum alloy sheet and a method for forming such an aluminum alloy sheet.
  • the first invention relates to an aluminum alloy sheet used for an auto body sheet and containing 2.0 to 8.0 wt.% of Mg, one or two or more elements selected from a group consisting of 1.5 wt.% or less of Fe, 1.0 wt.% or less of Mn, 0.3 wt.% or less of Cr and 0.3 wt.% or less of Zr, and the remainder consisting of inevitable impurities and aluminum, wherein the surface layer in a former step is 70 to 300 ⁇ m in recrystallized grain size, the finally-annealed surface layer in a final finish sheet is 10 to 50 ⁇ m in recrystallized grain size and 0.5 ⁇ m or less in surface roughness Ra (Ra ⁇ 0.5 ⁇ m), and the surface roughness Ra in case of applying 10% of stretch is set to be 0.8 ⁇ m or above (Ra ⁇ 0.8 ⁇ m).
  • the second invention relates to a method for manufacturing the above aluminum alloy sheet used for an auto body sheet, comprising the steps of hot-rolling an aluminum alloy slab having the above composition, subsequently cold-rolling the hot-rolled sheet at a rolling reduction of 20 % or less, then subjecting the cold-rolled sheet to intermediate annealing at 320 to 550°C, then cold-rolling the annealed sheet as final-cold rolling with a roll having a roll roughness Ra of 0.5 ⁇ m or less (Ra ⁇ 0.5 ⁇ m), and subjecting the resultant sheet to final annealing at a heating rate of 3.0°C/sec or above so as to hold at 450 to 550°C for 120 sec or less, wherein the intermediate-annealed surface layer is 70 to 300 ⁇ m in recrystallized grain size, the finally-annealed surface layer in a final finish sheet is 10 to 50 ⁇ m in recrystallized grain size and 0.5 ⁇ m or less in surface roughness Ra (Ra ⁇ 0.5 ⁇
  • the third invention relates to another method for manufacturing the above aluminum alloy sheet for an auto body sheet, comprising the steps of hot-rolling an aluminum alloy slab having the above composition on condition that the hot-rolling end temperature reaches 250 to 300°C, subsequently annealing the hot-rolled sheet at 320 to 550°C, then cold-rolling the annealed sheet as final-cold rolling with a roll having a roll roughness Ra of 0.5 ⁇ m or less (Ra ⁇ 0.5 ⁇ m), and subjecting the resultant sheet to final annealing at a heating rate of 3.0°C/sec or above so as to hold at 450 to 550°C for 120 sec or less, wherein the intermediate-annealed surface layer is 70 to 300 ⁇ m in recrystallized grain size, the finally-annealed surface layer in a final finish sheet is 10 to 50 ⁇ m in recrystallized grain size and 0.5 ⁇ m or less in surface roughness Ra (Ra ⁇ 0.5 ⁇ m), and the surface roughness Ra in case of
  • the fourth present invention relates to a further method for manufacturing the above aluminum alloy sheet for an auto body sheet, comprising the steps of hot-rolling an aluminum alloy slab having the above composition on conditions of hot-rolling end pass that a rolling reduction is set to be 20 % or less, and a hot-rolling end temperature reaches 400°C or above, subsequently cold-rolling the hot-rolled sheet as final-cold rolling with a roll having a roll roughness Ra of 0.5 ⁇ m or less (Ra ⁇ 0.5 ⁇ m), and then subjecting the resultant sheet to final annealing at a heating rate of 3.0°C/sec or above so as to hold at 450 to 550°C for 120 sec or less, wherein the hot-rolled surface layer is 70 to 300 ⁇ m in recrystallized grain size, the finally-annealed surface layer in a final finish sheet is 10 to 50 ⁇ m in recrystallized grain size and 0.5 ⁇ m or less in surface roughness Ra (Ra ⁇ 0.5 ⁇ m), and the surface rough
  • the fifth present invention relates to a method for forming the aluminum alloy sheet for an auto body sheet according to claim 1, comprising the step of forming the aluminum alloy sheet with a low-viscosity lubricant having viscosity of 20 cSt or less on condition that a maximum equivalent strain value of a sliding part reaches 0.06 or above.
  • the aluminum alloy sheet (the above first invention) of the present invention can be manufactured through some special steps (the above second to fourth inventions) such as to adjust the recrystallized grain size of the surface layer in the former step (after intermediate annealing or hot rolling) and that of the surface layer in the final finish sheet.
  • steps such as to adjust the recrystallized grain size of the surface layer in the former step (after intermediate annealing or hot rolling) and that of the surface layer in the final finish sheet.
  • intergranular steps are caused for grains to roughen the sheet surface.
  • the surface of a mill finish material can be roughened similarly to that of a shot dull finish material, and the intergranular steps serve as micro pools to permit improvement in formability under low-viscosity lubrication condition.
  • composition of the aluminum alloy employed in the present invention is limited as described above.
  • Mg permits an increase of strength through solid solution and also permits an increase of work hardenability to increase ductility, thus resulting in contribution to the improvement in formability.
  • the amount of Mg to be added is limited to 2.0 to 8.0 wt. % for the following reasons. If the amount of Mg to be added is less than 2.0 wt. %, it is of little effect. On the other hand, when the amount exceeds 8.0 wt. %, hot workability is degraded to result in an increase in cost for manufacture.
  • Elements of Fe, Mn, Cr, Zr or the like are effective in increasing the strength. However, if the amounts of Fe, Mn, Cr and Zr to be added respectively exceed 1.5 wt. %, 1.0 wt. %, 0.3 wt. % and 0.3 wt. %, the ductility is lowered.
  • Cu, Si and Ti or the like are contained as impurities. As long as the contents of Cu, Si and Ti are respectively 0.5 wt. % or less, 0.2 wt. % or less and 0.2 wt. % or less, these elements do not hinder the effects of the present invention.
  • the surface layer in the former step is 70 to 300 ⁇ m in recrystallized grain size
  • the finally-annealed surface layer in the final finish sheet is 10 to 50 ⁇ m in recrystallized grain size and 0.5 ⁇ m or less in surface roughness Ra (Ra ⁇ 0.5 ⁇ m)
  • the surface roughness Ra in case of applying 10 % of stretch is set to be 0.8 ⁇ m or above (Ra ⁇ 0.8 ⁇ m).
  • the recrystallized texture in the former step i.e., the intermediate-stage step among the whole rolling steps, specifically the intermediate annealing or hot rolling step still affects the final finish sheet.
  • the intergranular steps are caused depending on a difference in orientation of recrystallized grains in the former step, in addition to a difference in orientation of final recrystallized grains, thus resulting in an increase of roughness. Therefore, since a micro pool is formed on a roughened recess to hold a low-viscosity lubricant, the formability can be improved.
  • Fig. 1(a) shows coarse recrystallized grains (I.G) in the former step
  • Fig. 1(b) shows the coarse recrystallized grains elongated in the rolling direction by cold rolling
  • Fig. 1(c) shows the state, in which the cold-rolled texture of Fig. 1(b) is subjected to final annealing to produce finely final-recrystallized grains (F.G) in the recrystallized grains (I.G) in the former step.
  • Fig. 2 is an enlarged-scale sectional view of a surface layer portion showing the state of intergranular steps caused when an aluminum alloy sheet having the texture shown in Fig. 1(c) is formed.
  • a portion A shows the intergranular steps caused by the coarse recrystallized grains I.G
  • a portion B shows the intergranular steps caused by the coarse recrystallized grains F.G.
  • the intergranular steps at the portion A serve as micro pools.
  • the recrystallized grain size in the former step is limited to 70 to 300 ⁇ m for the following reasons. If the size is less than 70 ⁇ m, the above effects can not be sufficiently obtained. On the other hand, if the size exceeds 300 ⁇ m, orange peel is caused to pose a problem in external appearance of the finish sheet, even though the sufficient effects can be obtained.
  • the preferable range of the size is 70 to 150 ⁇ m.
  • the recrystallized grain size of the finally-annealed sheet is limited to 10 to 50 ⁇ m for the following reasons. If the size is less than 10 ⁇ m, Luders band is remarkably caused during forming. On the other hand, if the size exceeds 50 ⁇ m, the orange peel is caused depending on a use to pose a problem in surface quality.
  • the preferable range of the size is 20 to 50 ⁇ m.
  • the recrystallized grain size of the surface layer is adjusted in the former step and in the final finish sheet.
  • the surface roughness Ra as the center average roughness is set to be 0.5 ⁇ m or less (Ra ⁇ 0.5 ⁇ m) so as to discriminate between the surface state of the sheet as a mill finish material according to the present invention and that of a shot dull finish material.
  • the surface roughness of the sheet prior to the forming is approximately equal to that of a normal rolled material.
  • the extent of the intergranular steps caused with deformation is regulated on condition that the surface roughness Ra in case of applying 10 % of stretch is set to be 0.8 ⁇ m or above (Ra ⁇ 0.8 ⁇ m). If Ra is less than 0.8 ⁇ m in the state of a roughened surface when applying 10 % of stretch, the size of resultant micro pool is too small to obtain sufficient effects on improvement in formability.
  • the aluminum alloy sheet of the present invention is manufactured on normal casting and solid-solution conditions and using a normal roll for cold rolling.
  • the method for manufacture in the second invention comprises the steps of hot-rolling the aluminum alloy slab at 350 to 450°C according to a normal process, subsequently cold-rolling the hot-rolled sheet at a rolling reduction of 20 % or less, and then subjecting the cold-rolled sheet to intermediate annealing at 320 to 550°C, wherein the recrystallized grain size of the intermediate-annealed surface layer is adjusted to 70 to 300 ⁇ m.
  • These recrystallized grains are contained in the surface layer of the sheet as a final product together with the grains having the final grain size of 10 to 50 ⁇ m, and the individual grains cause the intergranular steps on the sheet surface at the time of deformation.
  • the intermediate annealing temperature is set to be 320 to 550°C for the following reasons. If this temperature is less than 320°C, no recrystallization is caused. On the other hand, if this temperature exceeds 550°C, it is liable to occur melting.
  • the hot rolling end temperature is in the range of 250 to 300°C
  • no recrystallization is caused during hot rolling.
  • accumulated dislocation caused by hot rolling remains, and the recrystallization is caused by applying the intermediate annealing at 320 to 550°C.
  • a hot rolling end pass is performed on conditions that the rolling reduction is set to be 20 % or less and the hot-rolling end temperature reaches 400°C or above. Under these conditions, the recrystallization is caused by the self annealing effect during hot rolling, and therefore, no intermediate annealing is required.
  • the conditions of the hot rolling end pass are regulated such that the rolling reduction is set to be 20% or less and the hot-rolling end temperature reaches 400°C or above for the following reasons. If the rolling reduction exceeds 20 %, the surface is not sufficiently roughened due to excessive recrystallizing force. On the other hand, if the hot-rolling end temperature is less than 400°C, it is less liable to cause the recrystallization by self annealing.
  • the recrystallized texture obtained by the method of manufacture according to the second to fourth inventions as described above is subjected to cold rolling.
  • the cold rolling is performed as the final cold rolling using a normal roll having a roughness Ra of 0.5 ⁇ m or less (Ra ⁇ 0.5 ⁇ m).
  • the final annealing is performed at a heating rate of 3.0/sec or above so as to hold at 450 to 550°C for 120 sec or less.
  • the cooling rate is preferably 3.0°C/sec or above from the viewpoint of the prevention of occurrence of Luders band.
  • the fifth invention relates to a method for forming the aluminum alloy sheet manufactured as described above.
  • the use of the low-viscosity lubricant having the viscosity of 20cSt or less is regulated in forming for the following reasons. If the viscosity of lubricant exceeds 20cSt, the removal of lubricant after the forming of the sheet is made difficult in the subsequent degreasing and cleaning steps.
  • the forming conditions are determined such that the maximum equivalent strain value of the sliding part reaches 0.06 or above for the following reasons.
  • the sliding part of a mold product is only deformed to be less than 0.06 in equivalent strain, the unsatisfactory intergranular steps are caused to fulfill no effect on improvement in formability.
  • the deformation of a flange up to breakage is as small as approximately 0.04 in equivalent strain.
  • an increase of roughness is small.
  • equivalent strain 2 3 ( ⁇ 1 2 + ⁇ 2 2 + ⁇ 3 2 ) ⁇ 1 : true strain in length direction ⁇ 2 : true strain in width direction ⁇ 3 : true strain in thickness direction
  • Table 1 shows an aluminum alloy composition used in the embodiments, comparative examples and conventional examples.
  • An aluminum alloy having the composition shown in Table 1 was homogenized according to a normal process, and subsequently subjected to hot rolling, cold rolling (with a roll having Ra of 0.4 ⁇ m in final cold rolling), intermediate annealing and final annealing according to manufacturing conditions shown in Tables 2 and 3 to provide a sheet material having a thickness of 1 mm.
  • Nos. 1 to 9 in Table 2 show aluminum alloy sheets (Claim 1) as embodiments of the present invention manufactured according to a method (Claims 2 to 4).
  • Nos. 10 to 18 in Table 3 show aluminum alloy sheets as comparative examples manufactured according to the conditions without the range of the method of the present invention, and Nos. 19 and 20 show shot dull finish sheets as conventional examples.
  • a deep drawing test was made as a forming test to measure the drawable height.
  • cylindrical deep drawing at a draw ratio of 1.94 with a punch having a diameter of 33mm was done on conditions that force against wrinkling is set to be 1000 Kgf and a low-viscosity anti-rust lubricant having the viscosity of 5 cSt is used.
  • the equivalent strain in an R portion of die serving as a sliding part was 0.07.
  • the conditions in the former step for recrystallization are outside the range of the present invention.
  • the conditions in the former step are within the range of the present invention.
  • the final annealing conditions are outside the range of the present invention, Ra after applying 10% of stretch is small, and the external appearance of the formed sheet is unsatisfactory.
  • the conditions in the former step and the final annealing conditions are both outside the range of the present invention, and therefore, the large final grain size is obtained to cause the orange peel for the sheet after forming.
  • the conditions in the former step are outside the range of the present invention.
  • the final annealing is performed, one of the deep drawing height and the external appearance of the formed sheet is inferior.
  • the aluminum alloy sheet of the present invention is equal in formability to and more excellent in external appearance of the formed sheet than those of the shot dull finish sheets shown in Nos. 19 and 20 as the conventional examples.
  • the aluminum alloy sheet of the present invention has the formability as high as that of the conventional shot dull finish sheet, and is more excellent in external appearance of the formed sheet than that of the conventional shot dull finish sheet. In addition, it is possible to supply a low-cost material, and the remarkable effects on industry can be expected.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Metal Rolling (AREA)
EP95401319A 1994-06-09 1995-06-07 Aluminiumlegierungsblech für Autokarosserie, Verfahren zu ihrer Herstellung sowie Verfahren zu ihrer Verformung Withdrawn EP0690142A1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP12781294 1994-06-09
JP127812/94 1994-06-09

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EP0690142A1 true EP0690142A1 (de) 1996-01-03

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EP95401319A Withdrawn EP0690142A1 (de) 1994-06-09 1995-06-07 Aluminiumlegierungsblech für Autokarosserie, Verfahren zu ihrer Herstellung sowie Verfahren zu ihrer Verformung

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Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO1999061242A1 (de) * 1998-05-26 1999-12-02 Aluminium Ranshofen Walzwerk Gesellschaft Mbh Verfahren zur herstellung glänzender leichtmetall-verbundbleche, insbesondere luftfahrtbleche
WO2005061744A1 (ja) * 2003-12-19 2005-07-07 Nippon Light Metal Company, Ltd. 耐焼付軟化性に優れたアルミニウム合金板
EP2888382B1 (de) 2012-08-22 2016-11-23 Hydro Aluminium Rolled Products GmbH Gegen interkristalline korrosion beständiges aluminiumlegierungsband und verfahren zu seiner herstellung
US10041154B2 (en) 2011-07-25 2018-08-07 Nippon Light Metal Company, Ltd. Aluminum alloy sheet and method for manufacturing same
CN110042283A (zh) * 2019-05-08 2019-07-23 烟台南山学院 一种中强耐蚀铝合金板材制备方法

Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0035718A1 (de) * 1980-03-06 1981-09-16 Austria Metall Aktiengesellschaft Verfahren zur Herstellung eines tiefziehfähigen Bleches, Bandes oder dgl. aus Aluminium oder- legierungen
JPS5776145A (en) * 1980-10-29 1982-05-13 Mitsui Alum Kogyo Kk Superplastic aluminum alloy
JPS6320437A (ja) * 1986-07-15 1988-01-28 Sumitomo Light Metal Ind Ltd プレス加工性に優れたアルミニウム合金板材及びその製造法
EP0289775A2 (de) * 1987-04-25 1988-11-09 VAW Aluminium AG Tiefziehfähiges Blech oder Band aus Aluminium oder Aluminiumlegierungen sowie Verfahren zu seiner Herstellung
JPH0441003A (ja) * 1990-06-07 1992-02-12 Furukawa Alum Co Ltd 外装用アルミニウムまたはアルミニウム合金板とその製造方法
JPH0446607A (ja) * 1990-06-11 1992-02-17 Sumitomo Light Metal Ind Ltd 塗装後鮮映性に優れたアルミニウム合金板およびその製造方法
JPH06134504A (ja) * 1992-10-27 1994-05-17 Kawasaki Steel Corp プレス加工性に優れたアルミニウム合金板

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0035718A1 (de) * 1980-03-06 1981-09-16 Austria Metall Aktiengesellschaft Verfahren zur Herstellung eines tiefziehfähigen Bleches, Bandes oder dgl. aus Aluminium oder- legierungen
JPS5776145A (en) * 1980-10-29 1982-05-13 Mitsui Alum Kogyo Kk Superplastic aluminum alloy
JPS6320437A (ja) * 1986-07-15 1988-01-28 Sumitomo Light Metal Ind Ltd プレス加工性に優れたアルミニウム合金板材及びその製造法
EP0289775A2 (de) * 1987-04-25 1988-11-09 VAW Aluminium AG Tiefziehfähiges Blech oder Band aus Aluminium oder Aluminiumlegierungen sowie Verfahren zu seiner Herstellung
JPH0441003A (ja) * 1990-06-07 1992-02-12 Furukawa Alum Co Ltd 外装用アルミニウムまたはアルミニウム合金板とその製造方法
JPH0446607A (ja) * 1990-06-11 1992-02-17 Sumitomo Light Metal Ind Ltd 塗装後鮮映性に優れたアルミニウム合金板およびその製造方法
JPH06134504A (ja) * 1992-10-27 1994-05-17 Kawasaki Steel Corp プレス加工性に優れたアルミニウム合金板

Non-Patent Citations (5)

* Cited by examiner, † Cited by third party
Title
PATENT ABSTRACTS OF JAPAN vol. 006, no. 158 (C - 120) 19 August 1982 (1982-08-19) *
PATENT ABSTRACTS OF JAPAN vol. 012, no. 223 (C - 507) 24 June 1988 (1988-06-24) *
PATENT ABSTRACTS OF JAPAN vol. 016, no. 217 (M - 1252) 21 May 1992 (1992-05-21) *
PATENT ABSTRACTS OF JAPAN vol. 016, no. 229 (M - 1255) 27 May 1992 (1992-05-27) *
PATENT ABSTRACTS OF JAPAN vol. 018, no. 435 (M - 1655) 15 August 1994 (1994-08-15) *

Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO1999061242A1 (de) * 1998-05-26 1999-12-02 Aluminium Ranshofen Walzwerk Gesellschaft Mbh Verfahren zur herstellung glänzender leichtmetall-verbundbleche, insbesondere luftfahrtbleche
WO2005061744A1 (ja) * 2003-12-19 2005-07-07 Nippon Light Metal Company, Ltd. 耐焼付軟化性に優れたアルミニウム合金板
US8524015B2 (en) 2003-12-19 2013-09-03 Nippon Light Metal Company, Ltd. Aluminum alloy sheet excellent in resistance to softening by baking
US10041154B2 (en) 2011-07-25 2018-08-07 Nippon Light Metal Company, Ltd. Aluminum alloy sheet and method for manufacturing same
EP2888382B1 (de) 2012-08-22 2016-11-23 Hydro Aluminium Rolled Products GmbH Gegen interkristalline korrosion beständiges aluminiumlegierungsband und verfahren zu seiner herstellung
US10550456B2 (en) 2012-08-22 2020-02-04 Hydro Aluminium Rolled Products Gmbh Intercrystalline corrosion-resistant aluminium alloy strip, and method for the production thereof
CN110042283A (zh) * 2019-05-08 2019-07-23 烟台南山学院 一种中强耐蚀铝合金板材制备方法

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