EP0786535B2 - Procede de production d'une plaque d'alliage d'aluminium destinee au formage - Google Patents

Procede de production d'une plaque d'alliage d'aluminium destinee au formage Download PDF

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Publication number
EP0786535B2
EP0786535B2 EP95908373A EP95908373A EP0786535B2 EP 0786535 B2 EP0786535 B2 EP 0786535B2 EP 95908373 A EP95908373 A EP 95908373A EP 95908373 A EP95908373 A EP 95908373A EP 0786535 B2 EP0786535 B2 EP 0786535B2
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European Patent Office
Prior art keywords
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aluminum alloy
temperature
forming
rolling
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.)
Expired - Lifetime
Application number
EP95908373A
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German (de)
English (en)
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EP0786535A1 (fr
EP0786535B1 (fr
EP0786535A4 (fr
Inventor
Hidetoshi Sumitomo Light Metal Ind. Ltd. UCHIDA
Hideo Sumitomo Light Metal Ind. Ltd. YOSHIDA
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Sumitomo Light Metal Industries Ltd
Reynolds Metals Co
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Sumitomo Light Metal Industries Ltd
Reynolds Metals Co
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Publication of EP0786535A1 publication Critical patent/EP0786535A1/fr
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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
    • C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • 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
    • C22F1/043—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 silicon as the next major constituent
    • 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
    • C22F1/05—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 of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions

Definitions

  • the present invention relates to a method for manufacturing aluminum alloy plate for forming, specifically to a method for manufacturing aluminum alloy plate for forming with favorable press-forming properties, giving excellent appearance after forming, and being suitable for vehicle materials such as automobile external body panels.
  • the 6000-Series AI-Mg-Si alloys such as 6009, 6111, and 6016 alloys were produced.
  • the 8000-Series aluminum alloys are somewhat inferior to the 5000-Series aluminum alloys in their forming properties, they have sufficient forming characteristics to permit them to be used as automobile external body panels, and they feature high strength due to the application of heat treatment during the coating and baking stage. Accordingly, the 6000-Series aluminum alloys are expected to further reduce plate thickness and applied weight over the 5000-Series.
  • the 6000-Series aluminum alloys have, however, the disadvantage of poor appearance after forming compared with the 5000, Series aluminum alloys.
  • JP,A,5-43974 describes a method for manufacturing a sheet of a 6000-Series aluminium alloy.
  • an ingot is subjected to a homogenizing treatment at 520°C, cooled to room temperature, hot rolled starting at 460°C and enoling at 280°C cold rolled with a draft of 75% solution heat treated at 550°C, for 60 sec with a heating rate of 10°C/sec and a cooling rate of 20°C/sec.
  • SS marks stretcher strain marks
  • coarse peel range peel
  • ridging marks are surface irregularities which appear even when the crystal grains are sufficiently fine not to induce a rough surface, but only under conditions where crystal grains with nearly equal crystalline plane orientation to each other are grouped, inducing a significant difference in deformation behavior at the boundary of the group.
  • the present invention was completed by focusing on the 6000-Series aluminum alloys which are expected to further reduce plate thickness and weight as the materials of vehicles such as external automobile body panels compared with the 5000-Series alloys, and by performing detailed study on the relations among the chemical ingredients, the manufacturing conditions, and the post-forming surface defects (particularly ridging marks) to solve the above-described problems experienced in the 5000-Series alloys.
  • the object of the present invention is to provide a method for manufacturing aluminum alloy plate for forming with high strength and favorable forming properties, and futher providing excellent appearance after forming.
  • the method for manufacturing aluminum alloy plate for forming to achieve the above-described object embodies the first aspect of the present invention which comprises: applying solid solution treatment to an aluminum alloy ingot consisting of between 0,4% and 1.7% of Si, between 0.2 % and 1.2% of Mg, by weight, the remaining Al and inevitable impurities and heating from a temperature range of 500°C to below the melting point of the aluminum alloy; cooling the aluminum alloy ingot from a temperature of 500°C or above to a cooling temperature range between 350 and 400°C; starting hot-rolling the aluminum alloy at the cooling temperature and ending the hot-rolling at a temperature range between 200 and 250°C; applying cold-rolling to the hot-rolled aluminum alloy to 50% or more of draft immediately before applying solid-solution treatment; heating the cold-rolled aluminum alloy to a temperature range between 500 and 580°C at a rate of 2°C/s or more, followed by holding the heated aluminum alloy for 10 minutes or less to conduct solid-solution treatment; then cooling the aluminum alloy to a temperature of 100°C or below at a rate of
  • the second aspect of the present invention comprises: aluminum alloy consisting of between 0.4% and 1.7% of Si, between 0.2% and 1.2% of Mg, and at least one element selected from the group of 1.0% or less of Cu, 1.0% or less of Zn, 0.5% or less of Mn, 0.2% or less of Cr, 0.2% or less of Zr, and 0.2% or less of V, by weight, and the remaining Al and inevitable impurities.
  • the third and fourth aspects of the present invention comprise: soaking an aluminum alloy ingot consisting of 0.8 to 1.3% of Si, 0.3 to 0.8% of Mg, by weight, and the remaining Al and inevitable impurities, or consisting of 0.8 to 1.3% of Si, and 0.3 to 0.8% of Mg, and at least one element selected from the group of 1.0% or less of Cu, 1.0% or less of Zn, 0.5% or less of Mn, 0.2% or less of Cr, 0.2% or less of Zr, and 0.2% or less of V, by weight, and the balance of Al and inevitable impurities, at a temperature range of 500°C to below the melting point of the aluminum alloy; cooling the soaked aluminum alloy ingot from a temperature of 500°C or above to a cooling temperature range of between 350 and 400°C; starting hot-rolling the aluminum alloy at the cooling temperature and ending the hot-rolling at a temperature range between 200 and 250°C; applying cold-rolling to the hot-rolled aluminum alloy to 80% or more of draft immediately before applying solid-solution treatment; heating the
  • the present invention was derived on the basis of findings that the suppression of ridging mark generation in the 6000-Series aluminum alloys without degrading the forming property needs to specify the alloy composition and requires strict control of soaking conditions, hot-rolling conditions, cold-rolling conditions, and final solid solution treatment conditions.
  • the alloy composition contains essential elements of Si in a range of between 0.4% and 1.7% and of Mg in a range between 0.2% and 1.2%. Silicon and Mg coexist to form Mg 2 Si, increasing the strength of the alloy. If the Si content is below 0.4%, sufficient strength cannot be obtained. If the Si content is 1.7% or more, the proof stress during the press-forming of the alloy becomes too high and degrades the forming properties, and the corrosion resistance also degrades.
  • the Mg content is less than 0.2%, satisfactory strength cannot be attained. If the Mg content is 1.2% or more, the proof stress rises, and the forming properties and the characteristic of precisely producing the press-mold shape during press-forming, or what is called the shape-freezing property, is degraded. To confer further improved anti-denting properties and shape-freezing property after forming to the aluminum alloy plate of the present invention, it is preferable to limit the content of the essential elements to between 0.8 and 1.3% for Si and between 0.3 and 0.8% for Mg.
  • addition of Cu as a selective component to a content of 1.0% or less further increases the strength of the alloy. If the Cu content exceeds 1.0%, corrosion resistance degrades and anti-filiform corrosion properties also degrade. Addition of Zn also improves the strength of alloy. If the Zn content exceeds 1.0%, however, corrosion resistance degrades, and the aging properties at room temperature increase. Therefore, the addition of Zn is limited to 1.0% or less.
  • the addition of 0.5% or less of Mn, 0.2% or less of Cr, 0.2% or less of Zr, and 0.2% or less of V further increases the strength of the alloy and decreases the crystal grain size, inducing favorable effects by preventing rough surface occurrence during the forming process. If these additives are added at above their respective upper limits, generation of coarse intermetallic compounds increases, degrading the forming properties.
  • 0.05% or less of Ti, or 0.05% or less of Ti and 100 ppm or less of B may be added other than the above-specified elements. If the added amount of Ti and B exceeds the respective upper limit, generation of coarse intermetallic compounds increases, degrading the forming properties. The inclusion of Fe as an inevitable impurity is allowed up to 0.3%. If the Fe content exceeds 0.3%, the forming properties, particularly bend-forming property, tend to degrade.
  • an ingot of aluminum alloy having the composition described above is prepared using a semi-continuous casting process, and the ingot is soaked in a temperature range between 500°C and the melting point of the alloy.
  • the soaking temperature is below 500°C, the removal of ingot segregation and the homogenizing of alloy structure cannot be fully achieved, and the formation of solid solution of Mg 2 Si which contributes to the strength of alloy becomes insufficient, which may result in poor forming properties.
  • the alloy is not cooled to room temperature but is instead subjected to hot-rolling at a starting temperature range between 350 and 400°C.
  • the ingot If the soaked ingot is cooled to room temperature followed by heating to the temperature of hot-rolling, coarse Mg 2 Si deposits appear during the heating process, making the formation of solid solution difficult during the solid solution treatment process, which results in degraded forming properties. If the ingot is cooled to room temperature after being soaked, the ingot needs to be heated to 500°C or above again, then to be cooled to a temperature range between 350 and 400°C, before beginning hot-rolling.
  • Hot-rolling begins at a temperature ranging between 350 and 400°C, and ends at a temperature ranging between 200 and 250°C.
  • the starting temperature of hot-rolling is below 350°C
  • the deformation resistance of the material rises.
  • the starting temperature exceeds 450°C
  • the structure grows excessively during the hot-rolling process with a high probability of forming groups of grains having similar crystalline plane orientation in the alloy plate after cold-rolling and after solid solution treatment, and ridging marks are likely appear on the plate surface after press-forming.
  • the hot-rolling is concluded at a temperature of 300°C or above, secondary recrystallization tends to occur after the rolling, and the structure becomes coarse, resulting in the generation of ridging marks.
  • the ending temperature of hot-rolling is below 200°C, water-soluble rolling oil stains are likely to remain on the surface of the alloy plate, degrading the surface quality.
  • the plate After the completion of hot-rolling, intermediate annealing and cold-rolling are carried out, when necessary, to prepare a plate having a specified thickness.
  • the plate Immediately before the solid solution treatment, the plate is cold-rolled to 50% or more of draft, preferably to 80% or more of draft, then the plate is subjected to solid solution treatment. If the draft of the cold-rolling immediately before the solid solution treatment is less than 50%, the crystal grains tend to become coarse after the solid solution treatment, and may result in a rough surface. Furthermore, the decomposition of the hot-rolled structure cannot be fully achieved, easily generating ridging marks, and the forming property degrades.
  • the solid solution treatment is implemented by heating the material to a temperature ranging between 500 and 580°C at a rate of 2°C/s or more. If the temperature rise speed is less than 2°C/s, the crystal grains become coarse, tending to cause a rough surface during the press-forming process. If the heating temperature is lower than 500°C, the solid solution of deposit becomes insufficient, and the specified strength and forming properties cannot be attained. Even If the specified strength and forming properties are obtained, the heat treatment requires an extremely long period, which is unfavorable from the industrial point of view. If the material is heated to above 580°C, local eutectic fusing is likely to occur, degrading the forming properties. A preferable holding time is 10 minutes or less.
  • the material is cooled to 100°C or below at a rate of 5°C/s or more. When the cooling speed is less than 5°C/s, coarse compounds deposit at the grain boundary and degrade ductility, thus degrading strength and forming properties.
  • a material's composition is selected to provide optimal strength and forming properties, and a combination of ingot soaking, hot-rolling, cold-rolling, and solid solution treatment is applied under specified conditions.
  • a good surface condition after forming is provided by ensuring fine crystal grain size to prevent rough surface generation with random crystal plane orientation while preventing degradation of forming properties.
  • An aluminum alloy ingot comprising 1.2% of Si, 0.6% of Mg, 0.1% of Mn, 0.2% of Fe, by wt., and the remainder of Al was manufactured using a semi-continuous casting process.
  • the obtained ingot was surface machined, then treated under the conditions given in Table 1 to form a plate 1 mm thick.
  • the prepared plate was subjected to a tensile test.
  • a 200 mm square panel was cut from the plate for press-forming. The formed alloy was visually observed to check for the generation of ridging marks, rough surface, and SS marks, and was tested for intergrain corrosion.
  • Example 1 An aluminum alloy ingot having the same composition as that of Example 1 was manufactured using the semi-continuous casting process. The ingot was treated according to the conditions given in Table 3 to form a plate 1 mm thick. The plate was subjected to the test given in Example 1. The result is shown in Table 4. The values with underline are outside of the condition of the present invention. Condition No.
  • Condition No. 1 and No. 2 applied excessively high starting temperature for hot-rolling, and Condition No. 3 applied excessively high hot-rolling ending temperature, so the specimens thus prepared generated ridging marks after forming.
  • Condition No. 4 applied less cold-rolling draft and insufficient decomposition of the specimen's hot-rolled structure so that ridging marks appeared after forming, and a rough surface appeared owing to the formation of coarse crystal grains.
  • Condition No.5 provided
  • Condition No. 6 experienced cooling to room temperature after soaking followed by re-heating to the hot-rolling temperature so that the specimen had insufficient penetration of alloying elements during the solid solution treatment, and the elongation became low and the forming property degraded.
  • Condition No.7 applied excessively low solid solution treatment temperature so that the deposits were unable to undergo sufficient solid solution formation, so the strength and elongation were poor.
  • An aluminum alloy ingot having the composition given in Table 5 was manufactured by a semi-continuous casting process. After machining the surface, the ingot was treated by Condition No. 1 of Table 1 to form a plate 1 mm thick The plate was subjected to the test given in Example 1. The result is shown in Table 6. As seen in Table 6, all the specimens A through G, which were manufactured in accordance with the present invention, had a high strength of 100 MPa or more and high elongation of 28% or more, and showed excellent forming properties and appearance after forming. They also showed superior corrosion resistance in intergrain corrosion tests, giving a maximum of 0.1 mm of corrosion depth. Alloy No.
  • An aluminum alloy ingot having the composition given in Table 7 was manufactured using a semi-continuous casting process. After machining the surface, the ingot was treated according to Condition No. 1 of Table 1 to form a plate 1 mm thick. The plate was subjected to the test given in Example 1. The result is shown in Table 8. As seen in Table 8, the specimen of alloy H contained less Si and Mg so that the strength was low and crystal grains were coarse, generating a rough surface during the forming stage. Alloy I contained less Mg, so that the strength was insufficient, and the content of Cu was excessive so that the corrosion depth increased significantly during the intergrain corrosion test to degrade the corrosion resistance. The alloy J contained an excessive amount of Si so that the strength increased and the elongation decreased, causing unsatisfactory forming properties.
  • the alloy K was A5182 alloy, and it generated SS marks during the forming process, degrading its appearance.
  • Table 7 underlined values are outside of the conditions of the present invention.
  • the present invention provides a method for manufacturing aluminum alloy plate for forming with excellent strength and forming properties, particularly excellent press-forming properties, with a good appearance after forming, and suitable for vehicle materials such as automobile external body panels.

Claims (4)

  1. Procédé pour fabriquer une feuille d'alliage d'aluminium pour le formage, comprenant: le réchauffage à coeur d'un lingot d'alliage d'aluminium comprenant entre 0,4% et 1,7% de Si, entre 0,2% et 1,2% de Mg, en poids, et facultativement au moins un élément sélectionné parmi le group comprenant 1,0% ou moins de Cu, 1,0% ou moins de Zn, 0,5% ou moins de Mn, 0,2% ou moins de Cr, 0,2 % ou moins de Zr, et 0,2% ou moins de V, en poids, et le reste étant de l'Al et des impuretés inévitables, à une plage de température comprise entre 500° C et le point de fusion de l'alliage d'aluminium ; le refroidissement du lingot d'alliage d'aluminium réchauffé à coeur d'une température de réchauffage à coeur de 500° C ou plus à une plage de température de refroidissement comprise entre 350 et 400° C ; le démarrage du laminage à chaud du lingot d'alliage d'aluminium à la température de refroidissement et l'achèvement du laminage à chaud dans une plage de température comprise entre 200 et 250° C ; l'application d'un laminage à froid du lingot d'alliage d'aluminium laminé à chaud avec 50% d'étirage ou plus avant l'application d'un recuit d'homogénéisation au stade solidus; le chauffage du lingot d'alliage d'aluminium laminé à froid à une plage de température comprise entre 500 et 580° C à une vitesse de 2° C/s ou plus, suivi par le maintien du lingot d'alliage d'aluminium chauffé pendant 10 minutes ou moins pour effectuer un recuit d'homogénéisation au stade solidus ; puis le refroidissement du lingot d'alliage d'aluminium à une température de 100° C ou moins à une vitesse de 5° C/s pour effectuer une trempe.
  2. Procédé pour fabriquer une feuille d'alliage d'aluminium pour le formage selon la revendication 1, dans lequel le lingot d'alliage d'aluminium comprend entre 0,4% et 1,7% de Si, entre 0,2% et 1,2% de Mg, et au moins un élément sélectionné parmi le groupe comprenant 1,0% ou moins de Cu, 1,0% ou moins de Zn, 0,5% ou moins de Mn, 0,2% ou moins de Cr, 0,2% ou moins de Zr, et 0,2% ou moins de V, en poids, et le reste étant de l'Al et des impuretés inévitables.
  3. Procédé pour fabriquer une feuille d'alliage d'aluminium pour le formage selon la revendication 1, comprenant : l'application d'un laminage à froid avec 80% d'étirage ou plus; et le maintien du lingot d'alliage d'aluminium chauffé pendant 1 minute ou moins à une plage de température comprise entre 500 et 580°C pour effectuer un recuit d'homogénéisation au stade solidus.
  4. Procédé pour fabriquer une feuille d'alliage d'aluminium pour le formage selon la revendication 3, dans lequel l'alliage d'aluminium comprend entre 0,8 et 1,3% de Si, entre 0,3 et 0,8% de Mg, et au moins un élément sélectionné parmi le groupe comprenant 1,0% ou moins de Cu, 1,0% ou moins de Zn, 0,5% ou moins de Mn, 0,2% ou moins de Cr, 0,2% ou moins de Zr, et 0,2% ou moins de V, en poids, et le reste étant de l'Al et des impuretés inévitables.
EP95908373A 1994-02-16 1995-02-14 Procede de production d'une plaque d'alliage d'aluminium destinee au formage Expired - Lifetime EP0786535B2 (fr)

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
JP6041850A JP2823797B2 (ja) 1994-02-16 1994-02-16 成形加工用アルミニウム合金板の製造方法
JP4185094 1994-02-16
JP41850/94 1994-02-16
PCT/JP1995/000200 WO1995022634A1 (fr) 1994-02-16 1995-02-14 Procede de production d'une plaque d'alliage d'aluminium destinee au moulage

Publications (4)

Publication Number Publication Date
EP0786535A1 EP0786535A1 (fr) 1997-07-30
EP0786535A4 EP0786535A4 (fr) 1997-07-30
EP0786535B1 EP0786535B1 (fr) 2000-04-12
EP0786535B2 true EP0786535B2 (fr) 2002-11-06

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Country Status (4)

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EP (1) EP0786535B2 (fr)
JP (1) JP2823797B2 (fr)
DE (1) DE69516297T3 (fr)
WO (1) WO1995022634A1 (fr)

Cited By (2)

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DE10324452B4 (de) * 2002-07-01 2010-05-06 Aleris Aluminum Duffel Bvba AI-Mg-Si-Legierungsblech
US9903018B2 (en) 2013-03-21 2018-02-27 Kennametal Inc. Coated body wherein the coating scheme includes a coating layer of TiAl2O3 and method of making the same

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JP3729605B2 (ja) * 1997-06-19 2005-12-21 株式会社神戸製鋼所 焼付硬化性が優れ常温時効が抑制されたアルミニウム合金板材の製造方法
NL1006511C2 (nl) * 1997-07-09 1998-05-29 Hoogovens Aluminium Nv Werkwijze voor het vervaardigen van een goed felsbare aluminiumplaat.
JP4186240B2 (ja) * 1997-10-03 2008-11-26 株式会社神戸製鋼所 成形加工用Ａｌ−Ｍｇ−Ｓｉ系アルミニウム合金板材
JP4063388B2 (ja) * 1998-02-20 2008-03-19 株式会社神戸製鋼所 表面性状に優れた成形加工用Ａｌ−Ｍｇ−Ｓｉ系アルミニウム合金板及びその製造方法
JP4045326B2 (ja) * 1999-11-09 2008-02-13 株式会社神戸製鋼所 プレス成形性に優れたＡｌ−Ｍｇ−Ｓｉ系Ａｌ合金板
JP4274674B2 (ja) * 2000-04-12 2009-06-10 トヨタ自動車株式会社 圧壊性に優れたアルミニウム合金部材及びその製造方法
JP3563323B2 (ja) * 2000-04-13 2004-09-08 日産自動車株式会社 耐糸錆び性に優れたアルミニウム合金板およびその製造方法
EP1375691A4 (fr) 2001-03-28 2004-07-21 Sumitomo Light Metal Ind Feuille en alliage aluminium a aptitude au formage et durcissabilite excellentes au cours de la cuisson de revetement, et procede de production
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JP4248796B2 (ja) * 2001-09-27 2009-04-02 住友軽金属工業株式会社 曲げ加工性および耐食性に優れたアルミニウム合金板およびその製造方法
JP4633994B2 (ja) * 2002-03-20 2011-02-16 住友軽金属工業株式会社 曲げ加工性および塗装焼付硬化性に優れたアルミニウム合金板および製造方法
JP4633993B2 (ja) * 2002-03-20 2011-02-16 住友軽金属工業株式会社 曲げ加工性および塗装焼付硬化性に優れたアルミニウム合金板および製造方法
ES2238584T3 (es) * 2001-07-09 2005-09-01 Corus Aluminium Walzprodukte Gmbh Aleacion de al-mg-si de alta resistencia.
WO2003010348A2 (fr) * 2001-07-23 2003-02-06 Corus Aluminium Walzprodukte Gmbh Alliage al-mg-si haute resistance soudable
JP4865174B2 (ja) * 2001-09-28 2012-02-01 古河スカイ株式会社 曲げ加工性と絞り成形性に優れたアルミニウム合金板の製造方法
JP3833574B2 (ja) * 2002-06-07 2006-10-11 株式会社神戸製鋼所 曲げ加工性とプレス成形性に優れたアルミニウム合金板
JP4499369B2 (ja) * 2003-03-27 2010-07-07 株式会社神戸製鋼所 リジングマークの発生が抑制されており表面性状に優れたＡｌ−Ｍｇ−Ｓｉ系合金板
JP5113318B2 (ja) * 2004-04-13 2013-01-09 古河スカイ株式会社 成形加工用アルミニウム合金板およびその製造方法
US20060070686A1 (en) * 2004-10-05 2006-04-06 Corus Aluminium Walzprodukte Gmbh High hardness moulding plate and method for producing said plate
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JP4939093B2 (ja) * 2006-03-28 2012-05-23 株式会社神戸製鋼所 ヘム曲げ性およびベークハード性に優れる自動車パネル用６０００系アルミニウム合金板の製造方法
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US8366846B2 (en) 2008-03-31 2013-02-05 Kobe Steel, Ltd. Aluminum alloy sheet with excellent post-fabrication surface qualities and method of manufacturing same
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EP2570509B1 (fr) 2011-09-15 2014-02-19 Hydro Aluminium Rolled Products GmbH Procédé de fabrication pour une bande d'aluminium AlMgSi
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WO2016115120A1 (fr) 2015-01-12 2016-07-21 Novelis Inc. Tôle d'aluminium hautement déformable pour l'industrie automobile à striage réduit ou nul et procédé de préparation
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US20230219125A1 (en) 2020-06-04 2023-07-13 Constellium Neuf-Brisach Method and equipment for cooling on a reversing hot rolling mill
FR3112297B1 (fr) 2020-07-07 2024-02-09 Constellium Neuf Brisach Procédé et équipement de refroidissement sur un Laminoir réversible à chaud
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EP0786535A1 (fr) 1997-07-30
JP2823797B2 (ja) 1998-11-11
EP0786535B1 (fr) 2000-04-12
WO1995022634A1 (fr) 1995-08-24
JPH07228956A (ja) 1995-08-29
EP0786535A4 (fr) 1997-07-30
DE69516297T3 (de) 2003-04-17
DE69516297D1 (de) 2000-05-18
DE69516297T2 (de) 2000-08-10

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