EP0679199A1 - Aluminium-silicon-magnesium alloy having improved ductility and deep-drawing properties, and method for producing same - Google Patents

Aluminium-silicon-magnesium alloy having improved ductility and deep-drawing properties, and method for producing same

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Publication number
EP0679199A1
EP0679199A1 EP95901489A EP95901489A EP0679199A1 EP 0679199 A1 EP0679199 A1 EP 0679199A1 EP 95901489 A EP95901489 A EP 95901489A EP 95901489 A EP95901489 A EP 95901489A EP 0679199 A1 EP0679199 A1 EP 0679199A1
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EP
European Patent Office
Prior art keywords
quenching
temperature
alloy
hot rolling
alloy according
Prior art date
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Granted
Application number
EP95901489A
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German (de)
French (fr)
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EP0679199B1 (en
Inventor
Jean-Christophe Ehrstrom
Daniel Ferton
Christophe Sigli
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Constellium Issoire SAS
Original Assignee
Pechiney Rhenalu SAS
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Priority claimed from FR9313966A external-priority patent/FR2712605B1/en
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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
    • 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
    • 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
    • C22F1/047—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
    • 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 invention relates to aluminum alloys of the Al-Si-Mg type with improved ductility and stampability, used in the form of sheets or strips, as well as a process for obtaining these.
  • the sheets or bands are particularly intended for stamping and in particular for the automobile body.
  • the conventional alloys used in this field such as alloys 6009, 6016, 6111, according to the designation of the Aluminum Association still exhibit insufficient mechanical characteristics of use and formability.
  • the alloy according to the invention contains (by weight%): from 0.1 to 0.8 Mn from 0.25 to 0.8 Mg from 0.5 to 1.3 Si up to 0.9 Cu up to at 0.5 Fe up to 0.5 (each) and 0.15 (total) of other elements remains: Al.
  • a preferred composition is as follows: from 0.15 to 0.65 Mn from 0.3 to 0.6 Mg from 0.7 to 1.2 Si from 0.1 to 0.5 Cu up to 0.4 Fe remains Al + unavoidable impurities.
  • the preferred composition is as follows: from 0.25 to 0.45 Mn from 0.3 to 0.5 Mg from 0.85 to 1.10 Si from 0.1 to 0.3 Cu to 0.3 Fe rest: A1 + unavoidable impurities.
  • Mn is favorable to mechanical strength and to deformability; this action is sensitive beyond 0.1%; however, above 0.8% Mn, coarse compounds (Al, Mn, Fe) are formed which impair formability.
  • the Applicant has also found that high contents of Mn lead to homogenization of the microscopic deformation, which is favorable to a good distribution of the deformations.
  • the mechanical characteristics are too low; if Si> 1.3%, coarse primary compounds appear and impair formability.
  • the manufacturing process usually used includes the following operations:
  • the process according to the invention comprising the casting operations reheating, hot rolling and possibly cold rolling, soluti and quenching, maturation and possibly “baking” surface coating thereof, is characterized in that the temperature reheating before hot rolling and the inlet temperature to the hot laminate is between 460 and 520 ° C.
  • the temperature holding time e is between 30 min and 24 h.
  • the temperature at the end of hot rolling is preferably less than 400 ° C. and even 350 ° C.
  • the dissolution is preferably carried out between 520 and 570 ° C and in particular, between 550 and 570 ° C, for 5 min to 1 h.
  • the average quenching speed is preferably greater than 100 ° C / sec.
  • a pass-through oven can be used Typically the alloy matures at room temperature and reaches a stationary hardness in about 15 days, a state in which it is capable of undergoing shaping.
  • the alloy can undergo a hardening by tempering during the baking treatment of the coating (around 180 ° C. for 30 min). It has however been noted that in the case of an alloy homogenized in a conventional manner, the practice of a pre-annealing between 70 and 150 ° C for 0.5 to 5 h after quenching leads to a significant increase in the coefficient d 'hardening n (after maturation) and a significant increase in the mechanical strength characteristics (after curing of the coatings).
  • FIG. 1 represents the changes in the work hardening coefficient n in the ripened state as a function of the elastic limit in the hardened state with and without pre-tempering, under the conditions reported in Example 2.
  • the dissolution in a passing oven was carried out under the conditions given in Table II, mist cooling and then the sheets were aged for 15 days at room temperature before testing.
  • the Mn precipitates have a median size at 0.06 nm with a maximum dimension of 0.18 ⁇ m.
  • the tensile tests were carried out 14 days after quenching and certain samples were checked after an income of 30 min at

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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)
  • Shaping Metal By Deep-Drawing, Or The Like (AREA)
  • Heat Treatment Of Steel (AREA)
  • Application Of Or Painting With Fluid Materials (AREA)
  • Metal Rolling (AREA)

Abstract

Aluminium-silicon-magnesium alloys having improved ductility and deep-drawing properties for use as sheet or strip, and a method for producing same, are disclosed. The sheet or strip is particularly suitable for deep-drawing and motor vehicle bodywork in particular. The claimed alloy has a chemical composition consisting of: 0.1-0.8 wt % Mn, 0.25-0.8 wt % Mg, 0.5-1.3 wt % Si, up to 0.9 wt % Cu, up to 0.5 wt % Fe, and other elements up to 0.5 wt % each and 0.15 in all, with the balance being Al. The sheet and strip are produced by casting, hot rolling under special reheating and rolling conditions, cold rolling, age-hardening, forming and curing of coatings, and optionally pre-tempering performed between quenching and age-hardening.

Description

ALLIAGE DE TYPE AI_UMIOTXIM-SILICC»^MAGNESIUM A DUCTILITE ET EMI_OOTISSABILITE AlV_EîLIOREES ET PROCEDE D' OBTENTION ALLOY OF AI_UMIOTXIM-SILICC TYPE ^ ^ MAGNESIUM WITH DUCTILITY AND EMI_OOTISSABILITY ALV_EîLIOREES AND PROCESS FOR OBTAINING
L'invention concerne des alliages d'aluminium type Al-Si-Mg à ductilité et emboutissabilité améliorées, utilisés sous forme de tôles ou bandes, ainsi qu'un procédé d'obtention de ceux-ci. Les tôles ou bandes sont particulièrement destinées à 1 'emboutissage et en particulier à la carrosserie automobile.The invention relates to aluminum alloys of the Al-Si-Mg type with improved ductility and stampability, used in the form of sheets or strips, as well as a process for obtaining these. The sheets or bands are particularly intended for stamping and in particular for the automobile body.
Pour une,résistance mécanique donnée, la ductilité et 1 'emboutissabilité sont les caractéristiques essentielles des tôles ou bandes destinées à être mises en forme à froid, avant revêtements superficiels telles que la peinture et "cuisson" de ceux-ci.For a given mechanical strength, ductility and drawability are the essential characteristics of sheets or strips intended to be cold formed, before surface coatings such as painting and "baking" thereof.
Les alliages classiques utilisés dans ce domaine, tels que les alliages 6009, 6016, 6111, selon la désignation de l'Aluminium Association présentent encore des caractéristiques mécaniques d'utilisation et de formabilité insuffisantes.The conventional alloys used in this field, such as alloys 6009, 6016, 6111, according to the designation of the Aluminum Association still exhibit insufficient mechanical characteristics of use and formability.
L'alliage selon l'invention contient (en poids %) : de 0,1 à 0,8 Mn de 0,25 à 0,8 Mg de 0,5 à 1,3 Si jusqu'à 0,9 Cu jusqu'à 0,5 Fe jusqu'à 0,5 (chacun) et 0,15 (au total) d'autres éléments reste : Al .The alloy according to the invention contains (by weight%): from 0.1 to 0.8 Mn from 0.25 to 0.8 Mg from 0.5 to 1.3 Si up to 0.9 Cu up to at 0.5 Fe up to 0.5 (each) and 0.15 (total) of other elements remains: Al.
Cependant une composition préférentielle est la suivante : de 0,15 à 0,65 Mn de 0,3 à 0,6 Mg de 0,7 à 1,2 Si de 0,1 à 0,5 Cu jusqu'à 0,4 Fe reste Al + impuretés inévitables. La composition préférée est la suivante : de 0,25 à 0,45 Mn de 0,3 à 0,5 Mg de 0,85 à 1,10 Si de 0,1 à 0,3 Cu jusqu'à 0,3 Fe reste: A1+ impuretés inévitables.However, a preferred composition is as follows: from 0.15 to 0.65 Mn from 0.3 to 0.6 Mg from 0.7 to 1.2 Si from 0.1 to 0.5 Cu up to 0.4 Fe remains Al + unavoidable impurities. The preferred composition is as follows: from 0.25 to 0.45 Mn from 0.3 to 0.5 Mg from 0.85 to 1.10 Si from 0.1 to 0.3 Cu to 0.3 Fe rest: A1 + unavoidable impurities.
On sait que la présence de Mn est favorable à la résistance mécanique et à la déformabilité; cette action est sensible au-delà de 0,1%; cependant au-delà de 0,8% Mn, il y a formation de composés (Al,Mn,Fe) grossiers qui nuisent à la formabilité. La demanderesse a aussi trouvé que des teneurs élevées en Mn conduisent à une homogénéisation de la déformation microscopique, ce qui est favorable à une bonne répartition des déformations.It is known that the presence of Mn is favorable to mechanical strength and to deformability; this action is sensitive beyond 0.1%; however, above 0.8% Mn, coarse compounds (Al, Mn, Fe) are formed which impair formability. The Applicant has also found that high contents of Mn lead to homogenization of the microscopic deformation, which is favorable to a good distribution of the deformations.
Pour des valeurs de Mg inférieures à 0,25%, la limite élastique après cuisson des revêtements est trop faible; pour les valeurs supérieures àFor values of Mg less than 0.25%, the elastic limit after curing of the coatings is too low; for values greater than
0,8%, la formabilité devient insuffisante et la maturation trop rapide.0.8%, formability becomes insufficient and maturation too fast.
Si la teneur en Si est inférieure à 0,5%, les caractéristiques mécaniques sont trop faibles; si Si > 1,3%, des composés primaires grossiers apparaissent et nuisent à la formabilité.If the Si content is less than 0.5%, the mechanical characteristics are too low; if Si> 1.3%, coarse primary compounds appear and impair formability.
Si la teneur en Cu est supérieure à 0,9%, la tenue à la corrosionIf the Cu content is greater than 0.9%, the corrosion resistance
(intercristalline) est insuffisante.(intercrystalline) is insufficient.
Si la teneur en Fe est supérieure à 0,5%, il en résulte une précipitation grossière néfaste à la formabilité. —If the Fe content is greater than 0.5%, this results in coarse precipitation which is detrimental to formability. -
Le procédé de fabrication habituellement utilisé comporte les opérations suivantes :The manufacturing process usually used includes the following operations:
- coulée d'un alliage de composition donnée sous forme de lingots ou de bandes- casting of an alloy of given composition in the form of ingots or strips
- homogénéisation éventuelle- possible homogenization
- réchauffage et laminage à chaud- reheating and hot rolling
- laminage à froid- cold rolling
- mise en solution- dissolution
- mi se en forme à froid à l ' état T4- mi is cold formed in the T4 state
- revêtement superfi ci el éventuel et sa "cui sson" , par exempl e une peinture (laquelle contribue au durcissement de l'alliage) -voir exemple US 4614552, US 4784921, US 4840852, WO 87/02712.- possible surface coating and its "cooking", for example a paint (which contributes to the hardening of the alloy) - see example US 4614552, US 4784921, US 4840852, WO 87/02712.
La demanderesse a trouvé que cette gamme pouvait être simplifiée et/ améliorée, d'une part en réduisant l'étape d'homogénéisation à réchauffage avant laminage à chaud, ou d'autre part, en introduisant u trempe rapide et une étape de pré-revenu après trempe et ava maturation.The Applicant has found that this range could be simplified and / / improved, on the one hand by reducing the homogenization step to reheating before hot rolling, or on the other hand, by introducing a rapid quenching and a pre- returned after quenching and maturing.
Ainsi, le procédé selon l'invention, comportant les opérations de coulé réchauffage, laminage à chaud et éventuellement à froid, mise en soluti et trempe, maturation et éventuellement revêtement superficiel "cuisson" de celui-ci, est caractérisé en ce que la température réchauffage avant laminage à chaud et la température d'entrée au lamino à chaud est comprise entre 460 et 520°C.Thus, the process according to the invention, comprising the casting operations reheating, hot rolling and possibly cold rolling, soluti and quenching, maturation and possibly "baking" surface coating thereof, is characterized in that the temperature reheating before hot rolling and the inlet temperature to the hot laminate is between 460 and 520 ° C.
Une montée en température à une vitesse comprise entre 10°C/h et 150°C et une température de maintien limitée entre 460°C et 520°C conduisent effet à un maximum de la densité volumique des précij stés, au Mn Al(Fe,Mn)Si leur taille maximale est inférieure à 0,2 »m et leur tail médiane est inférieure à 0,07 »m.A rise in temperature at a speed of between 10 ° C / h and 150 ° C and a limited holding temperature between 460 ° C and 520 ° C lead effect to a maximum of the volume density of the precij stes, Mn Al (Fe , Mn) If their maximum size is less than 0.2 "m and their median tail is less than 0.07" m.
Après montée en température, la durée de maintien en température e comprise entre 30 min et 24 h. La température de fin de laminage à chaud est de préférence inférieure 400°C et même 350°C.After the temperature has risen, the temperature holding time e is between 30 min and 24 h. The temperature at the end of hot rolling is preferably less than 400 ° C. and even 350 ° C.
Les fins précipités au manganèse subsistent jusqu'au stade final, et demanderesse émet l'hypothèse que la présence de ceux-ci est à l'origi de l'amélioration des caractéristiques de mise en forme à froid.The fine manganese precipitates remain until the final stage, and the applicant hypothesizes that the presence of these is at the origin of the improvement of the cold forming characteristics.
La mise en solution est de préférence réalisée entre 520 et 570°C et particulier, entre 550 et 570°C, pendant 5 min à 1 h. La vitesse moyen de trempe est de préférence supérieure à 100°C/sec.The dissolution is preferably carried out between 520 and 570 ° C and in particular, between 550 and 570 ° C, for 5 min to 1 h. The average quenching speed is preferably greater than 100 ° C / sec.
Pour les faibles durées de maintien, un four à passage peut être utilis Typiquement l'alliage mûrit à l'ambiante et atteint une dureté stationnaire en 15 jours environ, état dans lequel il est apte à subir des mises en forme.For short holding times, a pass-through oven can be used Typically the alloy matures at room temperature and reaches a stationary hardness in about 15 days, a state in which it is capable of undergoing shaping.
Après formage et éventuellement un revêtement de surface, l'alliage peut subir un durcissement par revenu au cours du traitement de cuisson du revêtement (vers 180°C pendant 30 min). Il a cependant été remarqué que dans le cas d'un alliage homogénéisé de façon classique, la pratique d'un pré-revenu entre 70 et 150°C pendant 0,5 à 5 h après la trempe conduit à une augmentation notable du coefficient d'écrouissage n (après maturation) et à une augmentation significative des caractéristiques de résistance mécanique (après cuisson des revêtements). Le coefficient d'écrouissage est égal à n = d(Lnςr-)/d £. , <j— étant la contrainte de Von Misés et cl. la déformation équivalente de Von Misés pour des déformations en traction comprises entre 5 et 20% (C=Ln (l/lo)).After forming and optionally a surface coating, the alloy can undergo a hardening by tempering during the baking treatment of the coating (around 180 ° C. for 30 min). It has however been noted that in the case of an alloy homogenized in a conventional manner, the practice of a pre-annealing between 70 and 150 ° C for 0.5 to 5 h after quenching leads to a significant increase in the coefficient d 'hardening n (after maturation) and a significant increase in the mechanical strength characteristics (after curing of the coatings). The coefficient of work hardening is equal to n = d (Lnςr -) / d £. , <j— being the constraint of Von Misés et cl. the equivalent Von Mises deformation for tensile deformations between 5 and 20% (C = Ln (l / lo)).
La figure 1 représente les évolutions du coefficient d'écrouissage n à l'état mûri en fonction de la limite élastique à l'état durci avec et sans pré-revenu, dans les conditions reportées à l'Exemple 2.FIG. 1 represents the changes in the work hardening coefficient n in the ripened state as a function of the elastic limit in the hardened state with and without pre-tempering, under the conditions reported in Example 2.
L'invention sera mieux comprise à l'aide des exemples suivants :The invention will be better understood using the following examples:
Exemple 1Example 1
Les alliages dont la composition est reportée au Tableau I ont étéThe alloys whose composition is given in Table I have been
2 élaborés en lingots, de 1,25x0,6 m de section, scalpés, réchauffés2 prepared in ingots, 1.25x0.6 m in section, scalped, reheated
(vitesse de montée : 46°C/h; température de maintien: 480°C) et laminés à chaud avec une température d'entrée de 480°C et une température de sortie de 310°C jusqu'à une épaisseur de 4mm, puis à froid jusqu'à une épaisseur de 1,2mm.(rise speed: 46 ° C / h; holding temperature: 480 ° C) and hot rolled with an inlet temperature of 480 ° C and an outlet temperature of 310 ° C up to a thickness of 4mm, then cold to a thickness of 1.2mm.
La mise en solution en four à passage a été effectuée dans les conditions données au Tableau II, refroidissement brouillard puis les tôles ont subi un vieillissement de 15 jours à la température ambiante avant essais.The dissolution in a passing oven was carried out under the conditions given in Table II, mist cooling and then the sheets were aged for 15 days at room temperature before testing.
Les caractéristiques mécaniques (sens long) et les déformations à rupture . f en expansion biaxiale obtenues sont reportés au Tableau III. Le test d'expansion biaxiale consiste à déformer une tôle 300x300x1,2 mm maintenue par un flan circulaire de diamètre 250 mm par une pression hydraulique. La déformation est mesurée au sommet du dôme formé. On peut constater que l'alliage suivant l'invention présente des caractéristiques de formabilité améliorées par rapport à celles des alliages obtenus selon l'art antérieur. On constate également un léger durcissement qui n'est pas spécifiquement recherché dans l'invention.Mechanical characteristics (long sense) and breaking strains. f biaxial expansion obtained are shown in Table III. The biaxial expansion test consists in deforming a 300x300x1.2 mm sheet held by a circular blank with a diameter of 250 mm by hydraulic pressure. The deformation is measured at the top of the dome formed. It can be seen that the alloy according to the invention has improved formability characteristics compared to those of the alloys obtained according to the prior art. There is also a slight hardening which is not specifically sought in the invention.
Les précipités au Mn ont une taille médiane à 0,06 nm avec une dimension maximale de 0,18 uni. *The Mn precipitates have a median size at 0.06 nm with a maximum dimension of 0.18 µm. *
TABLEAU ITABLE I
TABLEAU IITABLE II
TABLEAU I I I TABLE III
* selon l 'invention.* according to the invention.
Exemple 2Example 2
Un alliage de composition pondérale suivante (en %)An alloy with the following weight composition (in%)
Si: 1,08 Fe: 0,10 Cu : 0,05 Mn: 0,38 Mg: 0,40 a été coulé en plateaux de 1,25 x 0,6 m , homogénéisé à 520°C pendantSi: 1.08 Fe: 0.10 Cu: 0.05 Mn: 0.38 Mg: 0.40 was poured into 1.25 x 0.6 m trays, homogenized at 520 ° C for
33 h, laminé à chaud jusqu'à 4 mm d'épaisseur entre 494 et 304°C, laminé à froid jusqu'à 1,2 mm d'épaisseur, mis en solution dans un four à air avec une montée en 30 min à 560°C et maintien de 5 min à cette température et trempe à l'eau à 20°C33 h, hot rolled up to 4 mm thick between 494 and 304 ° C, cold rolled up to 1.2 mm thick, dissolved in an air oven with rise in 30 min at 560 ° C and maintained for 5 min at this temperature and quenched with water at 20 ° C
10 min après la trempe, des échantillons ont subi un pré-revenu de 2 h à10 min after quenching, samples underwent a pre-annealing of 2 h at
100°C, d'autres échantillons de comparaison n'étant pas traités.100 ° C, other comparison samples not being treated.
Les essais de traction ont été effectués 14 jours après la trempe et certains échantillons ont été contrôlés après un revenu de 30 min àThe tensile tests were carried out 14 days after quenching and certain samples were checked after an income of 30 min at
180°C, simulant les conditions de cuisson des revêtements.180 ° C, simulating the cooking conditions of the coatings.
Les résultats obtenus sont reportés sur le Tableau IV ci-après et représentés graphiquement sur la figure 1.The results obtained are reported in Table IV below and shown graphically in Figure 1.
On peut constater les effets bénéfiques du pré-revenu sur le coefficient n à l'état mûri (T4) et sur les caractéristiques mécaniques après cuisson des revêtements. We can see the beneficial effects of pre-tempering on the coefficient n in the matured state (T4) and on the mechanical characteristics after curing of the coatings.
Exemple 3 Example 3
Des produits ont été traités conformément à l'Exemple 2, sauf en ce qui concerne différentes vitesses de refroidissement lors de la trempe.Products were treated in accordance with Example 2, except for different cooling rates during quenching.
Les résultats obtenus sont reportés au Tableau V.The results obtained are reported in Table V.
TABLEAU VTABLE V
580 140 I 271 I 32,4 I 24,4 I 161 580 140 I 271 I 32.4 I 24.4 I 161
11
On constate que les vitesses de trempe élevées sont nettement favorables à l'obtention des caractéristiques mécaniques élevées à l'état durci, 0 avec une augmentation de l'allongement réparti à l'état T4. It can be seen that the high quenching speeds are clearly favorable for obtaining high mechanical characteristics in the hardened state, 0 with an increase in the elongation distributed in the T4 state.

Claims

REVENDICATIONS
1. Alliage d'aluminium pour bandes et tôles destinées à l'emboutissage caractérisé en ce qu'il contient en poids % : de 0,1 à 0,8 Mn de 0,25 à 0,8 Mg de 0,5 à 1,3 Si jusqu'à 0,9 Cu jusqu'à 0,5 Fe jusqu'à 0,5 (chacun) et 0,15 (au total) d'autres éléments reste Al .1. Aluminum alloy for strips and sheets intended for stamping, characterized in that it contains by weight%: from 0.1 to 0.8 Mn from 0.25 to 0.8 Mg from 0.5 to 1 , 3 If up to 0.9 Cu up to 0.5 Fe up to 0.5 (each) and 0.15 (total) of other elements remains Al.
2. Alliage selon la revendication 1 caractérisé en ce qu'il contient : de 0,15 à 0,65 Mn de 0,3 à 0,6 Mg de 0,7 à 1,2 Si de 0,1 à 0,5 Cu jusqu'à 0,4 Fe.2. Alloy according to claim 1 characterized in that it contains: from 0.15 to 0.65 Mn from 0.3 to 0.6 Mg from 0.7 to 1.2 Si from 0.1 to 0.5 Cu up to 0.4 Fe.
3. Alliage selon la revendication 2 caractérisé en ce qu'il contient : de 0,25 à 0,45 Mn de 0,3 à 0,5 Mg de 0,85 à 1,10 Si de 0,1 à 0,3 Cu jusqu'à 0,3 Fe.3. Alloy according to claim 2 characterized in that it contains: from 0.25 to 0.45 Mn from 0.3 to 0.5 Mg from 0.85 to 1.10 Si from 0.1 to 0.3 Cu up to 0.3 Fe.
4. Alliage suivant l'une des revendications 1 à 3 caractérisé en ce qu'il contient des précipités au Mn, type Al (Mn, Fe) Si, dont la taille médiane est inférieure à 0,07 »m et la taille maximale inférieure à 0,20 »m.4. Alloy according to one of claims 1 to 3 characterized in that it contains precipitates with Mn, type Al (Mn, Fe) Si, whose median size is less than 0.07 ”m and the maximum size less at 0.20 ”m.
5. Méthode d'obtention de tôles ou bandes en alliage d'Al suivant l'une des revendications 1 à 4, comportant un réchauffage et un laminage à chaud (et éventuellement à froid), une mise en solution et trempe et une maturation à la température ambiante caractérisée en ce que la température de réchauffage et de début de laminage à chaud est comprise entre 460 et 500°C. 5. Method for obtaining sheets or strips of Al alloy according to one of claims 1 to 4, comprising heating and hot rolling (and optionally cold), dissolving and quenching and maturing at the ambient temperature characterized in that the temperature for reheating and the start of hot rolling is between 460 and 500 ° C.
6. Méthode selon la revendication 5 caractérisée en ce que la durée de maintien à température est comprise entre 30 min et 48 h.6. Method according to claim 5 characterized in that the duration of temperature maintenance is between 30 min and 48 h.
7. Méthode selon l'une des revendications 5 ou 6 caractérisée en ce que la vitesse de montée en température est comprise entre 10°C/h et 150°C/h.7. Method according to one of claims 5 or 6 characterized in that the rate of temperature rise is between 10 ° C / h and 150 ° C / h.
8. Méthode selon Tune des revendications 5 à 7 caractérisée en ce que la température de fin de laminage à chaud est inférieure à 400°C, et de préférence inférieure à 350°C.8. Method according to one of claims 5 to 7 characterized in that the end temperature of hot rolling is less than 400 ° C, and preferably less than 350 ° C.
9. Méthode selon Tune des revendications 5 à 8 caractérisée en ce que la mise en solution a lieu entre 520 et 570°C, pendant 5 min à 1 h.9. Method according to one of claims 5 to 8 characterized in that the dissolution takes place between 520 and 570 ° C, for 5 min to 1 h.
10. éthode selon Tune des revendications 5 à 9 caractérisée en ce que la maturation à l'ambiante est au moins de 15 jours.10. Method according to one of claims 5 to 9 characterized in that the ambient maturation is at least 15 days.
11. éthode d'obtention de tôles ou bandes en alliage d'Al suivant Tune des revendications 1 à 4 comportant au moins une homogénéisation ou un réchauffage des lingots, un laminage à chaud (et éventuellement à froid), une mise en solution et trempe, une maturation, une mise en forme et un traitement de cuisson des revêtements caractérisée en ce qu'un pré-revenu est pratiqué entre la trempe et la maturation.11. method for obtaining sheets or strips of Al alloy according to one of claims 1 to 4 comprising at least one homogenization or reheating of the ingots, hot rolling (and possibly cold), dissolving and quenching , a maturation, a shaping and a baking treatment of the coatings characterized in that a pre-tempering is practiced between the quenching and the maturation.
12.Méthode selon la rev.ll caractérisée en ce que le pré-revenu est effectué dans un domaine de température allant de 70 à 150°C, pour une durée comprise entre 0,5 et 5 heures.12. Method according to rev.ll characterized in that the pre-annealing is carried out in a temperature range from 70 to 150 ° C, for a period of between 0.5 and 5 hours.
13.Méthode d'obtention d'une tôle ou bande d'alliage d'Al suivant Tune des revendications 11 ou 12 caractérisée en ce que la vitesse moyenne de refroidissement lors de la trempe est supérieure à 100°C/sec 13. Method for obtaining a sheet or strip of Al alloy according to one of claims 11 or 12 characterized in that the average cooling rate during quenching is greater than 100 ° C / sec
EP95901489A 1993-11-17 1994-11-15 Aluminium-silicon-magnesium alloy having improved ductility and deep-drawing properties, and method for producing same Revoked EP0679199B1 (en)

Applications Claiming Priority (5)

Application Number Priority Date Filing Date Title
FR9313966A FR2712605B1 (en) 1993-11-17 1993-11-17 Process for obtaining Al-Si-Mg alloys with improved ductility and stampability and product thus obtained.
FR9313966 1993-11-17
FR9401603A FR2713664B1 (en) 1993-11-17 1994-02-08 Al-Si-Mg alloy with improved ductility and stampability and process for obtaining it.
FR9401603 1994-02-08
PCT/FR1994/001330 WO1995014113A1 (en) 1993-11-17 1994-11-15 Aluminium-silicon-magnesium alloy having improved ductility and deep-drawing properties, and method for producing same

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EP0679199A1 true EP0679199A1 (en) 1995-11-02
EP0679199B1 EP0679199B1 (en) 1999-06-02

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JP (1) JPH08505904A (en)
KR (1) KR960700353A (en)
BR (1) BR9406554A (en)
CA (1) CA2152402C (en)
DE (1) DE69418855T2 (en)
FR (1) FR2713664B1 (en)
WO (1) WO1995014113A1 (en)

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WO2006037588A1 (en) * 2004-10-05 2006-04-13 Aleris Aluminum Koblenz Gmbh Method of heat treating an aluminium alloy member and apparatus therefor
US7491278B2 (en) 2004-10-05 2009-02-17 Aleris Aluminum Koblenz Gmbh Method of heat treating an aluminium alloy member and apparatus therefor
WO2018185425A1 (en) * 2017-04-06 2018-10-11 Constellium Neuf-Brisach Improved method for producing a motor vehicle body structure component
WO2018206696A1 (en) * 2017-05-11 2018-11-15 Aleris Aluminum Duffel Bvba Method of manufacturing an al-si-mg alloy rolled sheet product with excellent formability

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WO2006037588A1 (en) * 2004-10-05 2006-04-13 Aleris Aluminum Koblenz Gmbh Method of heat treating an aluminium alloy member and apparatus therefor
US7491278B2 (en) 2004-10-05 2009-02-17 Aleris Aluminum Koblenz Gmbh Method of heat treating an aluminium alloy member and apparatus therefor
WO2018185425A1 (en) * 2017-04-06 2018-10-11 Constellium Neuf-Brisach Improved method for producing a motor vehicle body structure component
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WO2018206696A1 (en) * 2017-05-11 2018-11-15 Aleris Aluminum Duffel Bvba Method of manufacturing an al-si-mg alloy rolled sheet product with excellent formability
US11384418B2 (en) 2017-05-11 2022-07-12 Aleris Aluminum Duffel Bvba Method of manufacturing an Al—Si—Mg alloy rolled sheet product with excellent formability

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CA2152402C (en) 2003-09-23
EP0679199B1 (en) 1999-06-02
JPH08505904A (en) 1996-06-25
KR960700353A (en) 1996-01-19
DE69418855D1 (en) 1999-07-08
FR2713664A1 (en) 1995-06-16
BR9406554A (en) 1996-02-06
DE69418855T2 (en) 1999-10-07
FR2713664B1 (en) 1996-05-24
WO1995014113A1 (en) 1995-05-26
CA2152402A1 (en) 1995-05-26

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