EP0375572A1 - Aluminium alloy for cupping, containing silicon, magnesium and copper - Google Patents

Aluminium alloy for cupping, containing silicon, magnesium and copper Download PDF

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EP0375572A1
EP0375572A1 EP89420499A EP89420499A EP0375572A1 EP 0375572 A1 EP0375572 A1 EP 0375572A1 EP 89420499 A EP89420499 A EP 89420499A EP 89420499 A EP89420499 A EP 89420499A EP 0375572 A1 EP0375572 A1 EP 0375572A1
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Prior art keywords
alloy
content
contents
transformation
dissolution
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EP0375572B1 (en
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Daniel Ferton
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Constellium Issoire SAS
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Cegedur Pechiney Rhenalu SA
Pechiney Rhenalu SAS
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    • 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
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • C22C21/14—Alloys based on aluminium with copper as the next major constituent with silicon

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  • the invention relates to an Al alloy essentially containing Si, Mg and Cu intended for the manufacture of stampable sheets or strips, in particular sheets used in automobile bodywork.
  • the alloy responding to the problem posed above has the following composition by weight:
  • the Mn content is further limited since this element has the following disadvantages in higher quantities: . It gives rise to the solidification of intermetallic compounds based on Fe, Mn, Si which reduce the deformation capacity of the alloy and can initiate decohesions and ruptures, during shaping operations; . It increases the critical quenching speed and therefore limits the possibilities of heat treatments for thick products; . It gives the alloy a fairly poor corrosion behavior; . It is not suitable for short-term homogenizations, such as those generally obtained in passage ovens.
  • the manufacturing range used generally includes the following operations: . continuous or semi-continuous casting of blanks, possible homogenization, hot transformation, possible cold transformation, dissolution and tempering.
  • homogenization at high temperature between 520 ° C and 560 ° C with a holding time of 6 to 24 hours is desirable. Homogenization is preferably preceded by a slow rise in temperature.
  • the temperature at the end of hot transformation to avoid these recrystallizations, must imperatively be between 270 ° and 320 ° C.
  • the alloy After possible cold transformation, the alloy is put into a complete solution. This takes place in the temperature range between 520 and 560 ° C, and preferably between 530 ° and 550 ° C by targeting the temperature of 550 ° C.
  • the rise in temperature before dissolving must be rapid (V ⁇ 10 ° C / sec) and dissolving preferably performed either in a pass-through oven or in a sheet-to-sheet processing oven.
  • the processing time varies from a few seconds to a few minutes, without being able to exceed one hour.
  • the sheets and strips thus obtained have good isotropy and an average grain size generally not exceeding 60 ⁇ m.
  • the quenching must be rapid and depends on the thickness of the product. For sheets and strips, it is generally carried out in calm or pulsed air.
  • the parts undergo hardening income, under the usual conditions; the hardening is due to the precipitation of the Mg2Si phase and of AlCuMgSi complex phases. Tempering is typically carried out between 8 and 12 hrs around 165 ° C.
  • FIG. 1 giving the field of composition of alloys in the Mg-Si plane and is illustrated by the following example: - A 1100x300x2850 mm3 plate of the following weight composition was poured semi-continuously: Yes 1.05% Mg 0.4% Cu 0.7% Mn 0.25% + Fe 0.24% Ti 0.035% Rest A1
  • This plate was homogenized at 530 ° C-8h and immediately hot rolled; up to 4 mm thick, the final rolling temperature was 300 ° C; the strip thus obtained has been cold rolled until 1.2 mm thick, then dissolved in a passing oven at 550 ° C (about 1 min at temperature) at a speed of 20 m / min and quenched in a mist (air + water).
  • an alloy with the following weight composition If: 1%; Mg: 0.4%; Cu: 0.15%; Mn: 0.1%; rest Al and usual impurities having followed the same range of transformation and heat treatment as above, has the following characteristics in state T4: R 0.2 (MPa) Rm (MPa) AT (%) 100 205 26.5

Abstract

The invention relates to an Al alloy for stamping, essentially containing Si, Mg and Cu, and to its process of manufacture. This alloy comprises (in % by weight) contents of Mg and Si which are within a polygon ABCDE having the following coordinates: <IMAGE> the copper content being between 0.5 and 0.8%, the contents of the elements Cr and Zr being less than 0.2% each, the Mn content being </= 0.3%, the Fe content being </= 0.35% and the content of the other elements being individually </= 0.05%, and in total </= 0.15%, the remainder being Al. The range of fabrication methods comprises semi-continuous or continuous ingot casting, optional homogenisation, hot transformation ending in the range 270-320 DEG C, optional cold transformation, complete dissolution, shaping by stamping, folding, roll bending etc., and annealing. This alloy is principally employed in panels for automobile bodywork. <IMAGE>

Description

L'invention concerne un alliage d'Al contenant essentiellement du Si, du Mg et du Cu destiné à la fabrication de tôles ou bandes emboutis­sables, en particulier des tôles utilisées en carrosserie automobile.The invention relates to an Al alloy essentially containing Si, Mg and Cu intended for the manufacture of stampable sheets or strips, in particular sheets used in automobile bodywork.

Dans le brevet français FR-2 601 040 est divulguée une composition d'alliages d'Al chaudronnable et soudable, utilisable à l'état traité (trempé/revenu) après mise en forme entre l'état trempé et l'état revenu. Cependant pour certaines applications telles que celle indiquée ci-dessus, les caractéristiques de résistance de cet alliage à l'état trempé-mûri restent insuffisantes (R 0,2

Figure imgb0001
100 MPa, Rm
Figure imgb0002
200 MPa, R0,2 étant la limite élastique à 0,2% de déformation résiduelle et Rm la charge de rupture).In French patent FR-2 601 040, a composition of boilable and weldable Al alloys is disclosed, usable in the treated state (quenched / tempered) after shaping between the quenched state and the tempered state. However for certain applications such as that indicated above, the resistance characteristics of this alloy in the quenched-cured state remain insufficient (R 0.2
Figure imgb0001
100 MPa, Rm
Figure imgb0002
200 MPa, R0,2 being the elastic limit at 0.2% of residual deformation and Rm the breaking load).

Il a été trouvé que l'augmentation modérée de la teneur en Cu permet de façon surprenante d'améliorer les caractéristiques de résistance, sans perte sur les caractéristiques de ductilité.It has been found that the moderate increase in the Cu content makes it possible, surprisingly, to improve the strength characteristics, without loss of the ductility characteristics.

L'alliage répondant au problème posé ci-dessus à la composition pondé­rales suivante:
Les teneurs en Si et Mg sont comprises dans un polygone dont les sommets sont:
A Si = 0,9% Mg = 0,1%
B Si = 0,9% Mg = 0,45%
C Si = 1% Mg = 0,5%
D Si = 1,15% Mg = 0,5%
E Si = 1,35% Mg = 0,1%
la teneur en Cu étant comprise entre 0,5 et 0,8
la teneur en Mn inférieure ou égale à 0,3%
la teneur en Fe inférieure ou égale à 0,35%
les teneurs en Cr et Zr inférieures à 0,2% chacune autres éléments chacun ≦ 0,05%
total ≦ 0,15%
reste AlThe alloy responding to the problem posed above has the following composition by weight:
The Si and Mg contents are included in a polygon whose vertices are:
A Si = 0.9% Mg = 0.1%
B Si = 0.9% Mg = 0.45%
C Si = 1% Mg = 0.5%
D Si = 1.15% Mg = 0.5%
E Si = 1.35% Mg = 0.1%
the Cu content being between 0.5 and 0.8
the Mn content less than or equal to 0.3%
Fe content less than or equal to 0.35%
contents of Cr and Zr less than 0.2% each other elements each ≦ 0.05%
total ≦ 0.15%
stay Al

Pour les valeurs minimales en éléments principaux les caractéristiques mécaniques minimales indiquées ci-dessus ne sont pas atteintes.
Pour Si supérieur à la limite DE, les risques de précipitation de Si élémentaire submicroscopique existent si la mise en solution est conduite à une température trop basse.For the minimum values in main elements the minimum mechanical characteristics indicated above are not reached.
For Si greater than the DE limit, the risks of precipitation of submicroscopic elementary Si exist if the dissolution is carried out at too low a temperature.

Pour Mg supérieur à la ligne BC (soit Si/Mg ≳ 2,6) des précipitations grossières de Mg₂Si sont possibles lors de la solidification et nuisent de ce fait aux propriétés de ductilité et d'aptitude à l'emboutissage.For Mg greater than the line BC (ie Si / Mg ≳ 2.6) coarse precipitation of Mg₂Si is possible during solidification and thereby adversely affect the properties of ductility and ability to stamp.

Pour Cu ≧ 0,8%, le gain de résistance en caractéristiques mécaniques devient négligeable; de plus la résistance à la corrosion et l'emboutis­sabilité diminuent.
Il est possible d'ajouter à la composition des éléments anti-recristal­lisants tels que le Mn, le Cr et/ou le Zr cependant en quantité limitée.For Cu ≧ 0.8%, the gain in strength in mechanical characteristics becomes negligible; moreover, the corrosion resistance and the drawability decrease.
It is possible to add anti-recrystallizing elements such as Mn, Cr and / or Zr to the composition, however in limited quantities.

La teneur en Mn est limitée supérieurement car cet élément présente en quantité plus élevée les inconvénients suivants:
. Il donne naissance à la solidification des composés intermétalliques à base de Fe, Mn, Si qui réduisent la capacité de déformation de l'allia­ge et peuvent initier des décohésions et ruptures, lors des opérations de mise en forme;
. Il augmente la vitesse critique de trempe et limite donc les possibi­lités de traitements thermiques pour les produits épais;
. Il confère à l'alliage un comportement à la corrosion assez médiocre;
. Il n'est pas adapté aux homogénéisations de courte durée, telles que celles généralement obtenues dans des fours à passage.The Mn content is further limited since this element has the following disadvantages in higher quantities:
. It gives rise to the solidification of intermetallic compounds based on Fe, Mn, Si which reduce the deformation capacity of the alloy and can initiate decohesions and ruptures, during shaping operations;
. It increases the critical quenching speed and therefore limits the possibilities of heat treatments for thick products;
. It gives the alloy a fairly poor corrosion behavior;
. It is not suitable for short-term homogenizations, such as those generally obtained in passage ovens.

Le Cr et le Zr ont des effets similaires à ceux du Mn, et sont donc aussi limités supérieurement.
Une composition préférentielle de l'alliage selon l'invention est la suivante:
rectangle de sommets dans le plan Si-Mg :
A′ Si = 1,0% Mg = 0,25%
C Si = 1% Mg = 0,5%
D Si = 1,15% Mg = 0,5%
E′ Si = 1,15% Mg = 0,25% avec
0,5 ≦ Cu ≦ 0,8% Mn ≦ 0,2% Zr et Cr ≦ 0,05% chacun, reste Al.Cr and Zr have similar effects to those of Mn, and are therefore also superiorly limited.
A preferred composition of the alloy according to the invention is as follows:
rectangle of vertices in the Si-Mg plane:
A ′ Si = 1.0% Mg = 0.25%
C Si = 1% Mg = 0.5%
D Si = 1.15% Mg = 0.5%
E ′ Si = 1.15% Mg = 0.25% with
0.5 ≦ Cu ≦ 0.8% Mn ≦ 0.2% Zr and Cr ≦ 0.05% each, remains Al.

La gamme de fabrication utilisée comporte généralement les opérations suivantes:
. la coulée continue ou semi-continue d'ébauches, une homogénéisation éventuelle, une transformation à chaud, une transformation à froid éventuelle, une mise en solution et un revenu.The manufacturing range used generally includes the following operations:
. continuous or semi-continuous casting of blanks, possible homogenization, hot transformation, possible cold transformation, dissolution and tempering.

Cependant, pour obtenir de bonnes propriétés de l'alliage, ces opérations doivent être conduites dans des conditions assez étroites.However, to obtain good properties of the alloy, these operations must be carried out under fairly narrow conditions.

Ainsi, pour limiter le temps de mise en solution ultérieure, il est préférable de bien homogénéiser l'alliage en évitant de le brûler par fusion des phases eutectiques. Une homogénéisation à haute tempéra­ture entre 520°C et 560°C avec un temps de maintien de 6 à 24 h est souhaitable. L'homogénéisation est, de préférence précédée d'une montée lente en température.Thus, to limit the time for subsequent dissolution, it is preferable to homogenize the alloy well, avoiding burning it by fusion of the eutectic phases. Homogenization at high temperature between 520 ° C and 560 ° C with a holding time of 6 to 24 hours is desirable. Homogenization is preferably preceded by a slow rise in temperature.

Dans le cas des tôles et bandes, les recristallisations à chaud grossiè­res (taille de grain supérieure à 80 µm) sont la source de lignes de déformations macroscopiques, visibles après emboutissage, donc rédhibitoires pour cette application.In the case of sheets and strips, coarse hot recrystallizations (grain size greater than 80 μm) are the source of macroscopic deformation lines, visible after stamping, therefore unacceptable for this application.

De ce fait, la température de fin de transformation à chaud, pour éviter ces recristallisations, doit être impérativement entre 270° et 320°C.Therefore, the temperature at the end of hot transformation, to avoid these recrystallizations, must imperatively be between 270 ° and 320 ° C.

Après transformation à froid éventuelle l'alliage est mis en solution complète. Celle-ci a lieu dans le domaine de température compris entre 520 et 560°C, et de préférence entre 530° et 550°C en visant la tempéra­ture de 550°C.After possible cold transformation, the alloy is put into a complete solution. This takes place in the temperature range between 520 and 560 ° C, and preferably between 530 ° and 550 ° C by targeting the temperature of 550 ° C.

En l'absence volontaire d'éléments inhibiteurs de recristallisation (Mn, Cr, Zr ≦ 0,05% chacun), la montée en température avant mise en solution doit être rapide (V ≧ 10°C/sec) et la mise en solution de préférence exécutée soit dans un four à passage, soit dans un four de traitement tôle à tôle.In the voluntary absence of recrystallization inhibiting elements (Mn, Cr, Zr ≦ 0.05% each), the rise in temperature before dissolving must be rapid (V ≧ 10 ° C / sec) and dissolving preferably performed either in a pass-through oven or in a sheet-to-sheet processing oven.

Le temps de traitement varie de quelques secondes à quelques minutes, sans pouvoir dépasser une heure. Les tôles et bandes ainsi obtenues présentent une bonne isotropie et une grosseur de grain moyenne ne dépassant pas en général 60 µm.The processing time varies from a few seconds to a few minutes, without being able to exceed one hour. The sheets and strips thus obtained have good isotropy and an average grain size generally not exceeding 60 μm.

La trempe doit être rapide et dépend de l'épaisseur du produit. Pour les tôles et bandes, elle est généralement effectuée à l'air calme ou pulsé.The quenching must be rapid and depends on the thickness of the product. For sheets and strips, it is generally carried out in calm or pulsed air.

Après les opérations de mise en forme à froid telles que emboutissage, pliage, cintrage etc...et/ou d'assemblage telle que le soudage par points, les pièces subissent un revenu de durcissement, dans les condi­tions habituelles; le durcissement est dû à la précipitation de la phase Mg₂Si et de phases complexes AlCuMgSi. Le revenu est typiquement effectué entre 8 et 12 h vers 165°C.After the cold forming operations such as stamping, bending, bending, etc. and / or assembly such as spot welding, the parts undergo hardening income, under the usual conditions; the hardening is due to the precipitation of the Mg₂Si phase and of AlCuMgSi complex phases. Tempering is typically carried out between 8 and 12 hrs around 165 ° C.

Il est à remarquer que dans certains cas, la cuisson de revêtements de surface tels que des vernis ou peintures, bien que plus courte, et généralement à plus haute température, réalise ipso facto ce traite­ment.It should be noted that in certain cases, the baking of surface coatings such as varnishes or paints, although shorter, and generally at higher temperature, ipso facto performs this treatment.

L'invention sera mieux comprise à l'aide de la figure 1 donnant le domaine de composition des alliages dans le plan Mg-Si et est illustrée par l'exemple suivant:
- on a coulé en semi-continu une plaque 1100x300x2850 mm3 de la composi­tion pondérale suivante: Si 1,05% Mg 0,4% Cu 0,7% Mn 0,25% + Fe 0,24% Ti 0,035% Reste A1 The invention will be better understood with the aid of FIG. 1 giving the field of composition of alloys in the Mg-Si plane and is illustrated by the following example:
- A 1100x300x2850 mm3 plate of the following weight composition was poured semi-continuously: Yes 1.05% Mg 0.4% Cu 0.7% Mn 0.25% + Fe 0.24% Ti 0.035% Rest A1

Cette plaque a été homogénéisée à 530°C-8h et immédiatement laminée à chaud; jusqu'à 4 mm d'épaisseur,la température finale du laminage était de 300°C; la bande ainsi obtenue a été relaminée à froid jusqu'a 1,2 mm d'épaisseur, puis mise en solution en four à passage à 550°C (de l'ordre de 1 min à température) à la vitesse de 20 m/min et trempée au brouillard (air+eau).This plate was homogenized at 530 ° C-8h and immediately hot rolled; up to 4 mm thick, the final rolling temperature was 300 ° C; the strip thus obtained has been cold rolled until 1.2 mm thick, then dissolved in a passing oven at 550 ° C (about 1 min at temperature) at a speed of 20 m / min and quenched in a mist (air + water).

Les résultats obtenus sur tôle de 1,2 mm d'épaisseur aux états T4 et T6, dans le sens travers long, sont les suivants: Etat R 0,2 (MPa) Rm (MPa) A (%) T4 (1 mois) 155 295 28 T6 (180°C;1,5 h) 255 345 15 The results obtained on sheet 1.2 mm thick in states T4 and T6, in the long transverse direction, are as follows: State R 0.2 (MPa) Rm (MPa) AT (%) T4 (1 month) 155 295 28 T6 (180 ° C; 1.5 h) 255 345 15

A titre de comparaison, un alliage de composition pondérale suivante :
Si: 1%; Mg: 0,4%; Cu: 0,15%; Mn: 0,1%; reste Al et impuretés habituelles ayant suivi la même gamme de transformation et de traitement thermique que ci-dessus, présente à l'état T4 les caractéristiques suivantes : R 0,2 (MPa) Rm (MPa) A (%) 100 205 26,5 By way of comparison, an alloy with the following weight composition:
If: 1%; Mg: 0.4%; Cu: 0.15%; Mn: 0.1%; rest Al and usual impurities having followed the same range of transformation and heat treatment as above, has the following characteristics in state T4: R 0.2 (MPa) Rm (MPa) AT (%) 100 205 26.5

Claims (7)

1. Alliage d'aluminium pour la fabrication de tôles emboutissables caractérisé en ce que sa composition est la suivante (en poids %): les teneurs en Mg et Si sont comprises dans un polygone ABCDE dont les coordonnées sont les suivantes: Si Mg A 0,9 0,1 B 0,9 0,45 C 1,0 0,5 D 1,15 0,5 E 1,35 0,1
le cuivre est compris entre 0,5 et 0,8%
les éléments Cr et Zr inférieurs à 0,2% chacun
le Mn ≦ 0,3%
le Fe ≦ 0,35%
autres éléments : chacun ≦0,05%, total ≦ 0,15%
reste Al1. Aluminum alloy for the manufacture of stampable sheets, characterized in that its composition is as follows (by weight%): the contents of Mg and Si are included in a polygon ABCDE whose coordinates are the following: Yes Mg AT 0.9 0.1 B 0.9 0.45 VS 1.0 0.5 D 1.15 0.5 E 1.35 0.1
copper is between 0.5 and 0.8%
elements Cr and Zr less than 0.2% each
Mn ≦ 0.3%
Fe ≦ 0.35%
other items: each ≦ 0.05%, total ≦ 0.15%
stay Al 2. Alliage selon la revendication 1 caractérisé en ce que les teneurs en Mg et Si sont comprises dans un rectangle A′CDE′ de coordonnées Si Mg A′ 1,0 0,25 C 1,0 0,5 D 1,15 0,5 E′ 1,15 0,25
Mn ≦ 0,2%, Cr et Zr ≦ 0,05% chacun.2. Alloy according to claim 1 characterized in that the contents of Mg and Si are included in a rectangle A′CDE ′ of coordinates Yes Mg AT' 1.0 0.25 VS 1.0 0.5 D 1.15 0.5 E ′ 1.15 0.25
Mn ≦ 0.2%, Cr and Zr ≦ 0.05% each. 3. Alliage suivant l'une des revendications 1 ou 2 caractérisé en ce que la grosseur de grain moyenne est inférieure à 80 µm et de préférence inférieure à 60 µm.3. Alloy according to one of claims 1 or 2 characterized in that the average grain size is less than 80 µm and preferably less than 60 µm. 4. Procédé d'obtention des produits selon l'une des revendications 1 à 3, comprenant la coulée continue ou semi-continue d'ébauches, une homogénéisation éventuelle, une transformation à chaud, une transformation à froid éventuelle, une mise en solution, une trempe, une mise en forme par emboutissage, pliage, cintrage, etc... et enfin un revenu caractérisé en ce que la transformation à chaud finale a lieu entre 270 et 320°C.4. Method for obtaining the products according to one of claims 1 to 3, comprising continuous or semi-continuous casting of blanks, possible homogenization, hot transformation, possible cold transformation, dissolution, quenching, shaping by stamping, bending, bending, etc ... and finally an income characterized in that the final hot transformation takes place between 270 and 320 ° C. 5. Procédé selon la revendication 4, caractérisé en ce que l'homogénéisa­tion ou la mise en solution complète sont conduites entre 520 et 560°C.5. Method according to claim 4, characterized in that the homogenization or the placing in complete solution are carried out between 520 and 560 ° C. 6. Procédé selon la revendication 5, caractérisé en ce que l'homogénéisa­tion ou la mise en solution ont lieu entre 530 et 550°C.6. Method according to claim 5, characterized in that the homogenization or the dissolution takes place between 530 and 550 ° C. 7. Procédé selon l'une des revendications 5 ou 6, caractérisé en ce que la mise en solution est précedée d'une montée en température à une vitesse supérieure à 10°C/sec.7. Method according to one of claims 5 or 6, characterized in that the dissolution is preceded by a rise in temperature at a speed greater than 10 ° C / sec.
EP89420499A 1988-12-21 1989-12-19 Aluminium alloy for cupping, containing silicon, magnesium and copper Expired - Lifetime EP0375572B1 (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
AT89420499T ATE90978T1 (en) 1988-12-21 1989-12-19 DRAWING ALUMINUM ALLOY CONTAINING SILICON, MAGNESIUM AND COPPER.

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR8817621 1988-12-21
FR8817621A FR2642436B1 (en) 1988-12-21 1988-12-21 A1 ALLOY CONTAINING ESSENTIALLY SI, MG AND CU FOR STAMPING

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EP0375572A1 true EP0375572A1 (en) 1990-06-27
EP0375572B1 EP0375572B1 (en) 1993-06-23

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AT (1) ATE90978T1 (en)
DE (1) DE68907332T2 (en)
ES (1) ES2041438T3 (en)
FR (1) FR2642436B1 (en)

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO1995014113A1 (en) * 1993-11-17 1995-05-26 Pechiney Rhenalu Aluminium-silicon-magnesium alloy having improved ductility and deep-drawing properties, and method for producing same
EP0714993A1 (en) * 1994-11-29 1996-06-05 Alusuisse-Lonza Services AG Deep drawable and weldable AlMgSi type aluminium alloy
FR2748035A1 (en) * 1996-04-29 1997-10-31 Pechiney Rhenalu ALUMINUM-SILICON-MAGNESIUM ALLOY FOR AUTOMOTIVE BODYWORK
WO1997047779A1 (en) * 1996-06-14 1997-12-18 Aluminum Company Of America Highly formable aluminum alloy rolled sheet

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US4424084A (en) * 1980-08-22 1984-01-03 Reynolds Metals Company Aluminum alloy
US4614552A (en) * 1983-10-06 1986-09-30 Alcan International Limited Aluminum alloy sheet product
WO1987002712A1 (en) * 1985-11-04 1987-05-07 Aluminum Company Of America Aluminum alloy vehicular member
US4788037A (en) * 1982-11-30 1988-11-29 Kabushiki Kaisha Kobe Seiko Sho High strength, corrosion-resistant aluminum alloys for brazing

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Publication number Priority date Publication date Assignee Title
FR2360684A1 (en) * 1976-08-05 1978-03-03 Aluminum Co Of America IMPROVED ALUMINUM STRUCTURAL ELEMENTS, FOR MOTOR VEHICLES
US4424084A (en) * 1980-08-22 1984-01-03 Reynolds Metals Company Aluminum alloy
US4788037A (en) * 1982-11-30 1988-11-29 Kabushiki Kaisha Kobe Seiko Sho High strength, corrosion-resistant aluminum alloys for brazing
US4614552A (en) * 1983-10-06 1986-09-30 Alcan International Limited Aluminum alloy sheet product
WO1987002712A1 (en) * 1985-11-04 1987-05-07 Aluminum Company Of America Aluminum alloy vehicular member

Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO1995014113A1 (en) * 1993-11-17 1995-05-26 Pechiney Rhenalu Aluminium-silicon-magnesium alloy having improved ductility and deep-drawing properties, and method for producing same
FR2713664A1 (en) * 1993-11-17 1995-06-16 Pechiney Rhenalu Al-Si-Mg type alloy with improved ductility and drawability and method of production.
EP0714993A1 (en) * 1994-11-29 1996-06-05 Alusuisse-Lonza Services AG Deep drawable and weldable AlMgSi type aluminium alloy
CH688379A5 (en) * 1994-11-29 1997-08-29 Alusuisse Lonza Services Ag Thermaformed and weldable aluminum alloy of the AlMgSi type
FR2748035A1 (en) * 1996-04-29 1997-10-31 Pechiney Rhenalu ALUMINUM-SILICON-MAGNESIUM ALLOY FOR AUTOMOTIVE BODYWORK
WO1997041272A1 (en) * 1996-04-29 1997-11-06 Pechiney Rhenalu Aluminium-silicon-magnesium alloy for motor vehicle body
WO1997047779A1 (en) * 1996-06-14 1997-12-18 Aluminum Company Of America Highly formable aluminum alloy rolled sheet

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FR2642436A1 (en) 1990-08-03
DE68907332T2 (en) 1993-11-11
DE68907332D1 (en) 1993-07-29
FR2642436B1 (en) 1991-06-14
ES2041438T3 (en) 1993-11-16
EP0375572B1 (en) 1993-06-23
ATE90978T1 (en) 1993-07-15

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