EP0300927A1 - Aluminium based alloy for cans and process of manufacturing - Google Patents
Aluminium based alloy for cans and process of manufacturing Download PDFInfo
- Publication number
- EP0300927A1 EP0300927A1 EP88420210A EP88420210A EP0300927A1 EP 0300927 A1 EP0300927 A1 EP 0300927A1 EP 88420210 A EP88420210 A EP 88420210A EP 88420210 A EP88420210 A EP 88420210A EP 0300927 A1 EP0300927 A1 EP 0300927A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- alloy
- thickness
- dissolution
- content
- cold 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.)
- Granted
Links
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 37
- 239000000956 alloy Substances 0.000 title claims abstract description 37
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 11
- 238000000034 method Methods 0.000 title claims abstract description 8
- 229910052782 aluminium Inorganic materials 0.000 title description 3
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 title description 3
- 239000004411 aluminium Substances 0.000 title 1
- 229910052751 metal Inorganic materials 0.000 claims abstract description 15
- 239000002184 metal Substances 0.000 claims abstract description 15
- 238000005097 cold rolling Methods 0.000 claims abstract description 11
- 239000000203 mixture Substances 0.000 claims abstract description 11
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 9
- 238000000265 homogenisation Methods 0.000 claims abstract description 8
- 229910052749 magnesium Inorganic materials 0.000 claims abstract description 8
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 6
- 229910000838 Al alloy Inorganic materials 0.000 claims abstract description 4
- 229910052796 boron Inorganic materials 0.000 claims abstract description 4
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 12
- 238000004090 dissolution Methods 0.000 claims description 10
- 229910052742 iron Inorganic materials 0.000 claims description 9
- 238000000576 coating method Methods 0.000 claims description 5
- 238000005098 hot rolling Methods 0.000 claims description 5
- 238000010791 quenching Methods 0.000 claims description 5
- 230000000171 quenching effect Effects 0.000 claims description 5
- 239000002244 precipitate Substances 0.000 claims description 4
- 230000035800 maturation Effects 0.000 claims description 3
- 238000005266 casting Methods 0.000 claims description 2
- 229910052804 chromium Inorganic materials 0.000 claims description 2
- 238000010304 firing Methods 0.000 claims description 2
- 229910052719 titanium Inorganic materials 0.000 claims description 2
- 229910052725 zinc Inorganic materials 0.000 claims description 2
- 229910052726 zirconium Inorganic materials 0.000 claims description 2
- 238000005096 rolling process Methods 0.000 claims 1
- 238000005496 tempering Methods 0.000 abstract description 3
- 239000011572 manganese Substances 0.000 description 9
- 235000013361 beverage Nutrition 0.000 description 6
- 239000010949 copper Substances 0.000 description 6
- 239000000243 solution Substances 0.000 description 6
- 229910019752 Mg2Si Inorganic materials 0.000 description 5
- 238000001816 cooling Methods 0.000 description 4
- 229910052802 copper Inorganic materials 0.000 description 3
- 238000009749 continuous casting Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 230000003068 static effect Effects 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- 229910018134 Al-Mg Inorganic materials 0.000 description 1
- 229910021365 Al-Mg-Si alloy Inorganic materials 0.000 description 1
- 229910018125 Al-Si Inorganic materials 0.000 description 1
- 229910018467 Al—Mg Inorganic materials 0.000 description 1
- 229910018520 Al—Si Inorganic materials 0.000 description 1
- 229910018566 Al—Si—Mg Inorganic materials 0.000 description 1
- 229910019064 Mg-Si Inorganic materials 0.000 description 1
- 229910019406 Mg—Si Inorganic materials 0.000 description 1
- 229910006639 Si—Mn Inorganic materials 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000010924 continuous production Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000001627 detrimental effect Effects 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 230000007774 longterm Effects 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 239000005022 packaging material Substances 0.000 description 1
- 238000004806 packaging method and process Methods 0.000 description 1
- 238000004881 precipitation hardening Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 238000009966 trimming Methods 0.000 description 1
Images
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
Definitions
- the invention relates to an Al alloy containing essentially Si, Mn and Mg, intended for the manufacture of boxes and its process for obtaining in the form of sheets or strips.
- One way to combat competition from other packaging materials, is to reduce the thicknesses of the strips of Al alloys used for the manufacture of boxes. Given the properties that the finished boxes must have, this reduction in thickness must be compensated by an increase in the mechanical properties of the alloys used. Unless otherwise indicated, the alloys will be designated according to the nomenclature of the Aluminum Association.
- the alloys intended for the manufacture of boxes currently belong to two families of alloys according to the selected application: - 3004 (1% Mg - 1% Mn) for drawn drawn box bodies, - 5000 series alloys (Al-Mg) for the beverage can lids (Al - 4.5% Mg) or the bodies and lids of food cans (Al - 3% Mg).
- the alloys currently used are at the limits of what can be achieved in mechanical characteristics: a) 3004
- the addition of Mg is limited by two phenomena: - the appearance of seizure during stretching, - the decrease in formability.
- the hardening route during annealing of the coatings such as that described in patent application EP 121,620, involves adding Cu to the alloy.
- the present invention therefore relates to an alloy intended for the manufacture of bodies of boxes and lids which has both high mechanical characteristics and an excellent formability by drawing (shrinking and expansion) and by drawing.
- Its composition is as follows (% by weight). - the contents of Mg and Si are limited by the polygon having the following vertices: Mg% Yes% AT 0.1 0.7 B 0.4 0.7 VS 0.5 1.0 D 0.5 1.2 E 0.1 1.4
- the Mn is between 0.8% and 1.15% and preferably between 0.85 and 1.10%. It can also contain up to 0.6% Cu, up to 0.5% Fe, up to 0.3% (each) of Cr, Zr, Ti, B, Zn, and up to 0.05% each and 0.15% in total of other elements, remains Al.
- the Mg content must be at least 0.1%. If, on the other hand, it is such that the alloy has a composition approaching too close to the domain of existence of Mg2Si, this may not completely redissolve during dissolution; it is preferable that its maximum content is limited to 0.45%. - Similarly, the Si content must be sufficient to ensure effective hardening, which means that Si>0.7%; excess silicon will contribute all the more to hardening as it is in solid solution. Its maximum content must therefore be such that the composition of the alloy is above the Al-Si solvus surface for the dissolution conditions used.
- - manganese must be introduced in a large quantity (> 0.8%), preferably> 0.85%, to allow the formation of large precipitates Al6 (Fe, Mn) and / or ⁇ Al (Fe, Mn) Si in combination with iron during the casting and homogenization of the metal.
- These large phases (1 to 15 ⁇ m at the final thickness) and in sufficient quantity, ensure that there is no jamming during stretching. Its content must however be limited to 1.15%, preferably 1.10%, because it can, always in combination with iron, form very coarse primary crystals which will cause holes in the very thin walls ( ⁇ 100 ⁇ m) stretched beverage cans.
- - copper is added within the limit of food standards (Cu ⁇ 0.6%) to contribute to hardening.
- the manufacturing range generally includes semi-continuous casting of trays, homogenization, hot rolling, possible cold rolling, solution and quenching, possible maturation, cold rolling with or without intermediate treatment and structural hardening. This latter treatment is usually carried out during the firing of varnish-type surface coatings.
- the metal can be continuously cast in the form of strips of thickness 6 to 12 mm, which eliminates the hot rolling step; after homogenization, the continuously cast metal undergoes the same range as the metal obtained by semi-continuous casting of trays.
- the operations are preferably carried out as follows:
- the transformation range must be adapted to the desired final product but the solution must be complete (structure free of precipitates of Si and / or Mg2Si).
- the strip is hot rolled to bring it to a thickness generally between 2 and 7 mm, the temperature at the end of hot rolling having to be between 280 and 350 ° C. to ensure recrystallization of the metal during the coil cooling.
- a first cold rolling can be carried out up to a thickness of 1 to 2 mm.
- This solution treatment can be done in a through oven or alternatively in a static oven if the temperature rise rate is high enough and if the cooling allows the alloy to be metallurgically quenched.
- the dissolution temperature should allow complete dissolution of the addition elements. For this, we will choose a temperature between 540 and 590 ° C, preferably 550-570 ° C.
- the duration of the treatment varies from a few seconds to several minutes depending on the thickness of the product: in a static oven, it can be up to 1 hour.
- the metal After this treatment, the metal must be quenched to ensure maximum effectiveness of the structural hardening. For this, we will ensure that the cooling rate is greater than 100 ° C / h.
- the metal is then cold rolled to the final thickness. Alternatively, it can undergo before this step or during it, an intermediate treatment at a temperature between 100 and 220 ° C for a period of 5 min to 8 h.
- FIG. 1 represents the field of the compositions claimed in the Mg-Si plane.
- the two alloys according to the invention of the following composition are poured by the conventional semi-continuous process.
- Alloy Mg% Yes% Mn% Cu% Fe% AT 0.30 1.25 1.03 0.30 0.37 B 0.45 0.95 1.00 0.28 0.35 These alloys are homogenized for 10 h at 600 ° C followed by a 4 h stage at 500 ° C (descent in 2 h). These alloys are hot rolled to a thickness of 3.5 mm and they are coiled at a temperature of the order of 330 ° C.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Rigid Containers With Two Or More Constituent Elements (AREA)
- Containers Having Bodies Formed In One Piece (AREA)
- Forging (AREA)
- Coating With Molten Metal (AREA)
- Seeds, Soups, And Other Foods (AREA)
- Metal Rolling (AREA)
- Table Devices Or Equipment (AREA)
- Packages (AREA)
Abstract
Description
L'invention concerne un alliage d'Al contenant essentiellement du Si, du Mn et du Mg, destiné à la fabrication de boîtes et son procédé d'obtention sous forme de tôles ou bandes.
Une voie pour lutter contre la concurrence des autres matériaux d'emballage, est de diminuer les épaisseurs des bandes en alliages d'Al utilisées pour la fabrication des boîtes.
Etant donné les propriétés que doivent posséder les boîtes finies, cette diminution d'épaisseur doit être compensée par une augmentation des propriétés mécaniques des alliages utilisés.
Sauf indication contraire, les alliages seront désignés suivant la nomenclature de l'Aluminium Association.
Les alliages destinés à la fabrication de boîtes appartiennent actuellement à deux familles d'alliages selon l'application retenue :
- le 3004 (1% Mg - 1% Mn) pour les corps de boîtes emboutis étirés,
- les alliages de la série 5000 (Al-Mg) pour les couvercles de boîtes boissons (Al - 4,5% Mg) ou les corps et couvercles de boîtes alimentaires (Al - 3% Mg).
Or, les alliages utilisés actuellement sont aux limites de ce que l'on peut atteindre en caractéristiques mécaniques :
a) 3004
L'ajout de Mg est limité par deux phénomènes :
- l'apparition du grippage lors de l'étirage,
- la diminution de l'aptitude à la formabilité.
La voie du durcissement lors du recuit des revêtements, telle que celle décrite dans la demande de brevet EP 121.620, passe par l'ajout de Cu à l'alliage. Cet ajout est limité étant donné les normes actuelles d'alimentarité (Cu < 0,6%) et la nécessaire résistance à la corrosion, ce qui fait que les propriétés mécaniques atteintes, bien que supérieures à celles du 3004 conventionnel, ne permettent pas de diminuer très significativement les épaisseurs des bandes pour corps de boîtes.
b) alliages de la série 5000
Ces alliages sont durcis grâce à la présence d'une forte teneur de Mg en solution solide qui induit un durcissement élevé par écrouissage. Mais pour les applications boîtes alimentaires, l'ajout de Mg rend le métal trop anisotrope à l'état H19 : le détourage important après emboutissage fait perdre les éventuels gains dûs à une épaisseur plus faible. De plus, la formabilité diminue lorsque l'on ajoute trop de Mg, l'alliage devenant de moins en moins emboutissable.The invention relates to an Al alloy containing essentially Si, Mn and Mg, intended for the manufacture of boxes and its process for obtaining in the form of sheets or strips.
One way to combat competition from other packaging materials, is to reduce the thicknesses of the strips of Al alloys used for the manufacture of boxes.
Given the properties that the finished boxes must have, this reduction in thickness must be compensated by an increase in the mechanical properties of the alloys used.
Unless otherwise indicated, the alloys will be designated according to the nomenclature of the Aluminum Association.
The alloys intended for the manufacture of boxes currently belong to two families of alloys according to the selected application:
- 3004 (1% Mg - 1% Mn) for drawn drawn box bodies,
- 5000 series alloys (Al-Mg) for the beverage can lids (Al - 4.5% Mg) or the bodies and lids of food cans (Al - 3% Mg).
However, the alloys currently used are at the limits of what can be achieved in mechanical characteristics:
a) 3004
The addition of Mg is limited by two phenomena:
- the appearance of seizure during stretching,
- the decrease in formability.
The hardening route during annealing of the coatings, such as that described in patent application EP 121,620, involves adding Cu to the alloy. This addition is limited given the current food grade standards (Cu <0.6%) and the necessary corrosion resistance, which means that the mechanical properties achieved, although superior to those of conventional 3004, do not allow not to significantly reduce the thicknesses of the strips for box bodies.
b) 5000 series alloys
These alloys are hardened thanks to the presence of a high content of Mg in solid solution which induces a high hardening by work hardening. But for food can applications, the addition of Mg makes the metal too anisotropic in the H19 state: the large trimming after stamping causes any gains due to a reduced thickness to be lost. In addition, the formability decreases when too much Mg is added, the alloy becoming less and less stampable.
Toutes ces raisons font que la demanderesse s'est attachée à mettre au point des alliages à durcissement structural pour application au boîtage conserve et alimentaire.
Etant donné les contraintes d'alimentarité et des gains de caractéristiques mécaniques importants à réaliser, elle a choisi les alliages Al-Mg-Si avec addition de Mn.
Cette voie a déjà été explorée par différents producteurs qui ont proposé plusieurs compositions qui, selon l'avis de la demanderesse, présentent de nombreux inconvénients.
Par exemple, les demandes de brevets EP 59.812 et 97.319 décrivent des alliages Al-Mg-Si-Mn dans lesquels le rapport Mg/Si est proche de la valeur 1,73 donnant ainsi des alliages voisins de la composition stoechiométrique Mg2Si. Ces alliages présentent cependant le risque d'une mise en solution incomplète. La présence de Mg2Si hors solution est en effet néfaste vis-à-vis de la formabilité du métal surtout pour les applications boîtes boissons où les parois sont fortement étirées et où unexcès de précipités peut créer un endommagement conduisant à la rupture lors de l'opération d'étirage.
D'autres brevets, tel que le FR 2.375.332, concernent des alliages Al-Si-Mg à fort excès de Si par rapport à la stoechiométrie Mg2Si, sans ajout significatif de Mn. De tels alliages sont impropres à l'étirage important lors de la fabrication de corps de boîtes boissons, car un fort grippage, c'est-à-dire l'adhésion de l'aluminium sur les outils d'étirage, apparaît rapidement, provoquant de nombreuses casses lors de l'étirage.For all these reasons, the Applicant has endeavored to develop alloys with structural hardening for application to canned and food packaging.
Given the constraints of food supply and the significant gains in mechanical characteristics to be achieved, it chose Al-Mg-Si alloys with the addition of Mn.
This route has already been explored by various producers who have proposed several compositions which, in the opinion of the applicant, have many drawbacks.
For example, patent applications EP 59,812 and 97,319 describe Al-Mg-Si-Mn alloys in which the Mg / Si ratio is close to the value 1.73 thus giving alloys close to the stoichiometric composition Mg2Si. However, these alloys present the risk of incomplete dissolution. The presence of Mg2Si out of solution is indeed detrimental with respect to the formability of the metal, especially for beverage can applications where the walls are strongly stretched and where an excess of precipitates can create damage leading to rupture during the operation. stretching.
Other patents, such as FR 2,375,332, relate to Al-Si-Mg alloys with a large excess of Si relative to the stoichiometry Mg2Si, without significant addition of Mn. Such alloys are unsuitable for high drawing during the manufacture of bodies of beverage cans, because a strong seizing, that is to say the adhesion of aluminum on the drawing tools, appears quickly, causing many breaks during stretching.
La présente invention concerne donc un alliage destiné à la fabrication de corps de boîtes et de couvercles qui possède à la fois des caractéristiques mécaniques élevées et une excellente aptitude à la mise en forme par emboutissage (rétreint et expansion) et par étirage.
Sa composition est la suivante (% en poids).
- les teneurs en Mg et Si sont limitées par le polygone ayant les sommets suivants :
Il peut en outre contenir jusqu'à 0,6% de Cu, jusqu'à 0,5% de Fe, jusqu'à 0,3% (chacun) de Cr, Zr, Ti, B, Zn, et jusqu'à 0,05% chacun et 0,15% au total d'autres éléments, reste Al.
Ces limites de compositions sont justifiées de la façon suivante :
- pour assurer le durcissement par précipitation, il faut que la teneur en Mg soit au moins de 0,1%. Si par contre, elle est telle que l'alliage a une composition s'approchant de trop près du domaine d'existence de Mg2Si, celui-ci risque de ne pas se redissoudre totalement lors de la mise en solution ; il est préférable que sa teneur maximale soit limitée à 0,45%.
- de même la teneur en Si doit être suffisante pour assurer un durcissement efficace, ce qui impose que Si > 0,7% ; le silicium en excès contribuera d'autant plus au durcissement qu'il sera en solution solide. Sa teneur maximale devra donc être telle que la composition de l'alliage soit au-dessus de la surface solvus Al-Si pour les conditions de mise en solution utilisées
- le manganèse doit être introduit en quantité importante (> 0,8%), de préférence > 0,85%, pour permettre la formation de gros précipités Al6 (Fe, Mn) et/ou α Al (Fe, Mn) Si en combinaison avec le fer lors de la coulée et de l'homogénéisation du métal. Ces phases de taille importante (1 à 15 µm à l'épaisseur finale) et en quantité suffisante, assurent une absence de grippage lors de l'étirage. Sa teneur doit cependant être limitée à 1,15%, de préférence 1,10%, car il peut, toujours en combinaison avec le fer, former des cristaux primaires très grossiers qui provoqueront des trous dans les parois très minces (≃ 100 µm) des boîtes boissons étirées.
- le cuivre est ajouté dans la limite des normes d'alimentarité (Cu < 0,6%) pour contribuer au durcissement. Au-delà, il provoque des problèmes de corrosion, malgré le revêtement existant sur les boîtes et couvercles.
La gamme de fabrication comporte généralement la coulée semi-continue de plateaux, homogénéisation, laminage à chaud, laminage à froid éventuel, mise en solution et trempe, maturation éventuelle, laminage à froid avec ou sans traitement intermédiaire et durcissement structural. Ce dernier traitement est habituellement effectué lors de la cuisson des revêtements superficiels type vernis.
Alternativement, le métal peut être coulé en continu sous forme de bandes d'épaisseur 6 à 12 mm, ce qui supprime l'étape de laminage à chaud; après homogénéisation, le métal coulé en continu subit la même gamme le métal obtenu par coulée semi-continue de plateaux.
En vue d'obtenir les caractéristiques optimales, les opérations sont, de préférence, conduites de la façon suivante :
La gamme de transformation doit être adaptée au produit final souhaité mais la mise en solution doit être complète (structure exempte de précipités de Si et/ou Mg2Si).
Pour faciliter la mise en solution ainsi que pour contrôler la taille du grain, il est nécessaire de réaliser une homogénéisation à double palier . Cette homogénéisation doit être précédée d'une montée lente en température.
On choisira donc une homogénéisation avec un premier palier entre 550 et 620°C, de préférence 580 à 600°C pendant une durée de 6 à 24 h, suivi d'un second palier entre 450 et 530°C, de préférence 480-510°C pendant une durée maximale de 4 h ; la descente à la température du second palier sera contrôlée entre 20°/h et 100°/h.
Après cette étape, on lamine à chaud la bande pour l'amener à une épaisseur généralement comprise entre 2 et 7 mm, la température de fin de laminage à chaud devant être comprise entre 280 et 350°C pour assurer une recristallisation du métal lors du refroidissement de la bobine.The present invention therefore relates to an alloy intended for the manufacture of bodies of boxes and lids which has both high mechanical characteristics and an excellent formability by drawing (shrinking and expansion) and by drawing.
Its composition is as follows (% by weight).
- the contents of Mg and Si are limited by the polygon having the following vertices:
It can also contain up to 0.6% Cu, up to 0.5% Fe, up to 0.3% (each) of Cr, Zr, Ti, B, Zn, and up to 0.05% each and 0.15% in total of other elements, remains Al.
These composition limits are justified as follows:
- to ensure precipitation hardening, the Mg content must be at least 0.1%. If, on the other hand, it is such that the alloy has a composition approaching too close to the domain of existence of Mg2Si, this may not completely redissolve during dissolution; it is preferable that its maximum content is limited to 0.45%.
- Similarly, the Si content must be sufficient to ensure effective hardening, which means that Si>0.7%; excess silicon will contribute all the more to hardening as it is in solid solution. Its maximum content must therefore be such that the composition of the alloy is above the Al-Si solvus surface for the dissolution conditions used.
- manganese must be introduced in a large quantity (> 0.8%), preferably> 0.85%, to allow the formation of large precipitates Al6 (Fe, Mn) and / or α Al (Fe, Mn) Si in combination with iron during the casting and homogenization of the metal. These large phases (1 to 15 μm at the final thickness) and in sufficient quantity, ensure that there is no jamming during stretching. Its content must however be limited to 1.15%, preferably 1.10%, because it can, always in combination with iron, form very coarse primary crystals which will cause holes in the very thin walls (≃ 100 µm) stretched beverage cans.
- copper is added within the limit of food standards (Cu <0.6%) to contribute to hardening. Beyond that, it causes corrosion problems, despite the existing coating on the boxes and lids.
The manufacturing range generally includes semi-continuous casting of trays, homogenization, hot rolling, possible cold rolling, solution and quenching, possible maturation, cold rolling with or without intermediate treatment and structural hardening. This latter treatment is usually carried out during the firing of varnish-type surface coatings.
Alternatively, the metal can be continuously cast in the form of strips of thickness 6 to 12 mm, which eliminates the hot rolling step; after homogenization, the continuously cast metal undergoes the same range as the metal obtained by semi-continuous casting of trays.
In order to obtain the optimum characteristics, the operations are preferably carried out as follows:
The transformation range must be adapted to the desired final product but the solution must be complete (structure free of precipitates of Si and / or Mg2Si).
To facilitate dissolution and to control the size of the grain, it is necessary to carry out a double-stage homogenization. This homogenization must be preceded by a slow rise in temperature.
We will therefore choose a homogenization with a first level between 550 and 620 ° C, preferably 580 to 600 ° C for a period of 6 to 24 h, followed by a second level between 450 and 530 ° C, preferably 480-510 ° C for a maximum duration of 4 h; the descent to the temperature of the second level will be controlled between 20 ° / h and 100 ° / h.
After this step, the strip is hot rolled to bring it to a thickness generally between 2 and 7 mm, the temperature at the end of hot rolling having to be between 280 and 350 ° C. to ensure recrystallization of the metal during the coil cooling.
Selon les caractéristiques souhaitées, on peut réaliser un premier laminage à froid jusqu'à une épaisseur de 1 à 2 mm. Cependant, il est possible d'effectuer le traitement de mise en solution immédiatement après laminage à chaud.
Ce traitement de mise en solution peut être fait dans un four à passage ou alternativement en four statique si la vitesse de montée en température est suffisamment élevée et si le refroidissement permet de tremper métallurgiquement l'alliage.
La température de mise en solution devra permettre la mise en solution complète des éléments d'addition. Pour cela, on choisira une température comprise entre 540 et 590°C, de préférence 550-570°C. La durée du traitement varie de quelques secondes à plusieurs minutes selon l'épaisseur du produit : en four statique, elle peut aller jusqu'à 1 h.
Après ce traitement, le métal doit être trempé pour assurer une efficacité maximale du durcissement structural. Pour cela, on s'assurera que la vitesse de refroidissement est supérieure à 100°C/h.
Le métal est ensuite laminé à froid jusqu'à l'épaisseur finale. Alternativement, il peut subir avant cette étape ou au cours de celle-ci, un traitement intermédiaire à une température entre 100 et 220°C pendant une durée de 5 mn à 8 h.Depending on the desired characteristics, a first cold rolling can be carried out up to a thickness of 1 to 2 mm. However, it is possible to carry out the solution treatment immediately after hot rolling.
This solution treatment can be done in a through oven or alternatively in a static oven if the temperature rise rate is high enough and if the cooling allows the alloy to be metallurgically quenched.
The dissolution temperature should allow complete dissolution of the addition elements. For this, we will choose a temperature between 540 and 590 ° C, preferably 550-570 ° C. The duration of the treatment varies from a few seconds to several minutes depending on the thickness of the product: in a static oven, it can be up to 1 hour.
After this treatment, the metal must be quenched to ensure maximum effectiveness of the structural hardening. For this, we will ensure that the cooling rate is greater than 100 ° C / h.
The metal is then cold rolled to the final thickness. Alternatively, it can undergo before this step or during it, an intermediate treatment at a temperature between 100 and 220 ° C for a period of 5 min to 8 h.
On peut aussi réaliser une maturation après mise en solution, c'est-à-dire laisser le métal vieillir à la température ambiante pendant plusieurs jours avant de la laminer à froid.One can also carry out a maturation after dissolving, ie let the metal age at room temperature for several days before cold rolling.
la présente invention est illustrée par l'exemple décrit ci-après et illustrée par la fig.1, qui représente le domaine des compositions revendiquées dans le plan Mg-Si.the present invention is illustrated by the example described below and illustrated by FIG. 1, which represents the field of the compositions claimed in the Mg-Si plane.
On coule par le procédé classique semi-continu les deux alliages selon l'invention de composition suivante (% en poids).
On lamine à chaud ces alliages jusqu'à une épaisseur de 3,5 mm et on les bobine à une température de l'ordre de 330°C. On les lamine ensuite à froid jusqu'à 1,5 mm et on effectue à cette épaisseur une mise en solution en four à passage (température du métal : 560°C pendant 5 mm) suivie d'une trempe à l'air (refroidissement jusqu'à 100°C en 30 sec.).
On effectue alors les deux gammes suivantes sur chacune des compositions :The two alloys according to the invention of the following composition (% by weight) are poured by the conventional semi-continuous process.
These alloys are hot rolled to a thickness of 3.5 mm and they are coiled at a temperature of the order of 330 ° C. They are then cold rolled to 1.5 mm and this solution is dissolved in a passing oven (metal temperature: 560 ° C for 5 mm) followed by air quenching (cooling up to 100 ° C in 30 sec.).
The following two ranges are then carried out on each of the compositions:
- revenu 6 h à 180°C
- laminage à froid jusqu'à 0,33 mm
- tempering 6 h at 180 ° C
- cold rolling up to 0.33 mm
- laminage à froid jusqu'à 1 mm
- revenu 1 h à 140°C
- laminage à froid jusqu'à 0,33 mm
- cold rolling up to 1 mm
- tempering 1 h at 140 ° C
- cold rolling up to 0.33 mm
- caractéristiques mécaniques de traction dans le sens long
- taux de cornes à 45° : S x (%)
- indice d'emboutissabilité Ericksen : I E (mm)
sont données dans le tableau suivant,
comparativement aux alliages classiques de même épaisseur
- rate of horns at 45 °: S x (%)
- Ericksen stampability index: IE (mm)
are given in the following table,
compared to conventional alloys of the same thickness
Après traitement de cuisson des revêtements (10 mm à 204°C), on obtient les propriétés suivantes :
Avec une forme de fond conventionnelle et une épaisseur de paroi de 0,125 mm, on obtient les performances suivantes sur les boîtes revétues :
- pression de retournement du fond : P = 0,79 MPa
- force d'écrasement : F = 3989 N
Ces valeurs sont à comparer aux valeurs obtenues avec le matériau conventionnel, le 3004 H19 de même épaisseur
- pression de retournement du fond : P = 0.67 MPa
- force d'écrasement : F = 3869 N
Les valeurs beaucoup plus élévées obtenues avec les alliages de la présente invention permettent d'envisager :
- la réduction des épaisseurs des bandes pour corps de boîtes embouties étirées,
- l'utilisation du même alliage pour réaliser le corps de boîte boisson et le couvercle ; seules les gammes de transformation seront différentes selon la partie de la boîte à réaliser.After baking the coatings (10 mm at 204 ° C), the following properties are obtained:
With a conventional bottom shape and a wall thickness of 0.125 mm, the following performances are obtained on coated boxes:
- bottom turning pressure: P = 0.79 MPa
- crushing force: F = 3989 N
These values are to be compared with the values obtained with the conventional material, the 3004 H19 of the same thickness.
- bottom turning pressure: P = 0.67 MPa
- crushing force: F = 3869 N
The much higher values obtained with the alloys of the present invention make it possible to envisage:
- the reduction of the thicknesses of the strips for bodies of drawn drawn boxes,
- the use of the same alloy to produce the beverage can body and the lid; only the transformation ranges will be different depending on the part of the box to be produced.
Claims (7)
les teneurs en Mg et Si sont comprises dans le polygone ABCDE de coordonnées :
- la teneur en Cu est inférieure ou égale à 0,6%
- les éléments Cr, Zn, Zr, Ti, B peuvent exister à des teneurs inférieures à 0,3% chacun
- le fer est limité à 0,5% maximum
- les autres éléments sont limités à 0.05% chacun et 0,15% au total.
- reste Al.1 - Aluminum alloy for the manufacture of boxes, characterized in that its composition is as follows (by weight%):
the contents of Mg and Si are included in the polygon ABCDE of coordinates:
- the Cu content is less than or equal to 0.6%
- the elements Cr, Zn, Zr, Ti, B may exist at contents of less than 0.3% each
- the iron is limited to 0.5% maximum
- the other elements are limited to 0.05% each and 0.15% in total.
- remains Al.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| AT88420210T ATE66699T1 (en) | 1987-06-23 | 1988-06-21 | ALUMINUM-BASED ALLOY FOR BEVERAGE CANS AND PROCESS FOR THEIR PRODUCTION. |
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| FR8709168A FR2617188B1 (en) | 1987-06-23 | 1987-06-23 | AL-BASED ALLOY FOR CASING AND PROCESS FOR OBTAINING |
| FR8709168 | 1987-06-23 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| EP0300927A1 true EP0300927A1 (en) | 1989-01-25 |
| EP0300927B1 EP0300927B1 (en) | 1991-08-28 |
Family
ID=9352645
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| EP88420210A Expired - Lifetime EP0300927B1 (en) | 1987-06-23 | 1988-06-21 | Aluminium based alloy for cans and process of manufacturing |
Country Status (6)
| Country | Link |
|---|---|
| EP (1) | EP0300927B1 (en) |
| AT (1) | ATE66699T1 (en) |
| DE (1) | DE3864473D1 (en) |
| ES (1) | ES2024683B3 (en) |
| FR (1) | FR2617188B1 (en) |
| GR (1) | GR3002615T3 (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0714993A1 (en) * | 1994-11-29 | 1996-06-05 | Alusuisse-Lonza Services AG | Deep drawable and weldable AlMgSi type aluminium alloy |
| DE10163039C1 (en) * | 2001-12-21 | 2003-07-24 | Daimler Chrysler Ag | Hot and cold formable component made of an aluminum alloy and process for its production |
| EP1484421A1 (en) * | 2003-06-05 | 2004-12-08 | Pechiney Rhenalu | Use of a rolled or extruded aluminium alloy product having a good corrosion resistance |
| FR2873717A1 (en) * | 2004-07-27 | 2006-02-03 | Boxal France Soc Par Actions S | PROCESS FOR MANUFACTURING AEROSOL BOXES |
| CN104561686A (en) * | 2014-12-31 | 2015-04-29 | 东莞市东兴铝业有限公司 | Aluminum alloy material capable of resisting cold and hot coagulation changes and preparation process for aluminum alloy material |
| WO2016000937A1 (en) * | 2014-07-04 | 2016-01-07 | Aleris Rolled Products Germany Gmbh | Aluminium alloy for use in the building industry |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR2375332A1 (en) * | 1976-12-24 | 1978-07-21 | Alusuisse | MANUFACTURING PROCESS OF WELL TRANSFORMABLE ALUMINUM SHEETS, POOR IN HORNS AND OF HIGH MECHANICAL STRENGTH |
| FR2432555A1 (en) * | 1978-08-04 | 1980-02-29 | Coors Container Co | ALIMINUM ALLOY AND PROCESS FOR PRODUCING A STRIP FOR BOXES AND LIDS |
| EP0057959A1 (en) * | 1981-02-06 | 1982-08-18 | Vereinigte Deutsche Metallwerke Ag | Wrought aluminium alloy |
| EP0059812A1 (en) * | 1981-03-02 | 1982-09-15 | Sumitomo Light Metal Industries Limited | Method for producing an aluminium alloy forming sheet |
-
1987
- 1987-06-23 FR FR8709168A patent/FR2617188B1/en not_active Expired
-
1988
- 1988-06-21 ES ES88420210T patent/ES2024683B3/en not_active Expired - Lifetime
- 1988-06-21 AT AT88420210T patent/ATE66699T1/en active
- 1988-06-21 EP EP88420210A patent/EP0300927B1/en not_active Expired - Lifetime
- 1988-06-21 DE DE8888420210T patent/DE3864473D1/en not_active Expired - Fee Related
-
1991
- 1991-08-29 GR GR91400484T patent/GR3002615T3/en unknown
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR2375332A1 (en) * | 1976-12-24 | 1978-07-21 | Alusuisse | MANUFACTURING PROCESS OF WELL TRANSFORMABLE ALUMINUM SHEETS, POOR IN HORNS AND OF HIGH MECHANICAL STRENGTH |
| FR2432555A1 (en) * | 1978-08-04 | 1980-02-29 | Coors Container Co | ALIMINUM ALLOY AND PROCESS FOR PRODUCING A STRIP FOR BOXES AND LIDS |
| EP0057959A1 (en) * | 1981-02-06 | 1982-08-18 | Vereinigte Deutsche Metallwerke Ag | Wrought aluminium alloy |
| EP0059812A1 (en) * | 1981-03-02 | 1982-09-15 | Sumitomo Light Metal Industries Limited | Method for producing an aluminium alloy forming sheet |
Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| 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 |
| DE10163039C1 (en) * | 2001-12-21 | 2003-07-24 | Daimler Chrysler Ag | Hot and cold formable component made of an aluminum alloy and process for its production |
| EP1484421A1 (en) * | 2003-06-05 | 2004-12-08 | Pechiney Rhenalu | Use of a rolled or extruded aluminium alloy product having a good corrosion resistance |
| EP1484420A1 (en) * | 2003-06-05 | 2004-12-08 | Pechiney Rhenalu | Use of a rolled or extruded aluminium alloy product having a high corrosion resistance |
| FR2855833A1 (en) * | 2003-06-05 | 2004-12-10 | Pechiney Rhenalu | LAMINATED OR ALUMINUM ALLOY WIRE WITH GOOD CORROSION RESISTANCE |
| FR2873717A1 (en) * | 2004-07-27 | 2006-02-03 | Boxal France Soc Par Actions S | PROCESS FOR MANUFACTURING AEROSOL BOXES |
| EP1624083A3 (en) * | 2004-07-27 | 2007-05-16 | Boxal France | Process for manufacturing aerosol cans |
| US7520044B2 (en) | 2004-07-27 | 2009-04-21 | Boxal France | Aerosol can fabrication process |
| WO2016000937A1 (en) * | 2014-07-04 | 2016-01-07 | Aleris Rolled Products Germany Gmbh | Aluminium alloy for use in the building industry |
| CN104561686A (en) * | 2014-12-31 | 2015-04-29 | 东莞市东兴铝业有限公司 | Aluminum alloy material capable of resisting cold and hot coagulation changes and preparation process for aluminum alloy material |
Also Published As
| Publication number | Publication date |
|---|---|
| FR2617188B1 (en) | 1989-10-20 |
| FR2617188A1 (en) | 1988-12-30 |
| GR3002615T3 (en) | 1993-01-25 |
| DE3864473D1 (en) | 1991-10-02 |
| ES2024683B3 (en) | 1992-03-01 |
| EP0300927B1 (en) | 1991-08-28 |
| ATE66699T1 (en) | 1991-09-15 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| EP2997171B1 (en) | Aluminium alloy sheet for metallic bottle or can or aerosol bottle | |
| WO2014167191A1 (en) | Method for transforming al-cu-li alloy sheets improving formability and corrosion resistance | |
| FR2843754A1 (en) | Balanced aluminum-copper-magnesium-silicon alloy product for fuselage sheet or lower-wing sheet of aircraft, contains copper, silicon, magnesium, manganese, zirconium, chromium, iron, and aluminum and incidental elements and impurities | |
| FR2584094A1 (en) | HIGH STRENGTH TITANIUM ALLOY MATERIAL HAVING IMPROVED OUVABILITY AND PROCESS FOR PRODUCING THE SAME | |
| EP0259232B1 (en) | Easily workable and weldable aluminium alloy, and process for its manufacture | |
| FR3026747A1 (en) | ALUMINUM-COPPER-LITHIUM ALLOY ISOTROPES FOR THE MANUFACTURE OF AIRCRAFT FUSELAGES | |
| FR2737225A1 (en) | AL-CU-MG ALLOY WITH HIGH FLOW RESISTANCE | |
| EP0660882B1 (en) | Method for manufacturing a thin sheet for producing canning components | |
| WO2018073533A1 (en) | Thin sheets made of an aluminium-magnesium-scandium alloy for aerospace applications | |
| FR2543578A1 (en) | PRODUCTION OF METALLIC ARTICLES BY SUPERPLASTIC DEFORMATION | |
| EP0300927B1 (en) | Aluminium based alloy for cans and process of manufacturing | |
| FR2773819A1 (en) | Aluminum-copper-manganese alloy for impact extruded and drawn aerosol can manufacture | |
| FR2679257A1 (en) | Aluminium and lithium alloy and process for its manufacture | |
| EP0070790B1 (en) | Process for manufacturing hollow bodies for pressure containers from an aluminium alloy | |
| WO2005010222A2 (en) | Thin strips or foils of alfesi alloy | |
| EP0375572B1 (en) | Aluminium alloy for cupping, containing silicon, magnesium and copper | |
| FR2836154A1 (en) | THIN BANDS IN ALUMINUM-IRON ALLOY | |
| EP0149946B1 (en) | Nickel base alloy | |
| FR2496702A1 (en) | ALUMINUM ALLOY OPENING PRODUCT CONTAINING AFFINED INTERMETALLIC PHASES, PREPARATION AND USE THEREOF | |
| JP3708616B2 (en) | Manufacturing method of Ai alloy plate for DI can body excellent in formability | |
| EP0547175A1 (en) | Aluminum alloy sheet stock | |
| FR2496701A1 (en) | OPEN ALUMINUM ALLOY FOR THE MANUFACTURE OF HEAT EXCHANGE FINS AND TUBES, METHOD FOR MANUFACTURING THE SAME, AND USE THEREOF | |
| FR3122187A1 (en) | 5xxx aluminum sheets with high formability | |
| FR2507210A1 (en) | METHOD FOR MANUFACTURING A HIGH ELASTIC LIMIT ALUMINUM SHEET | |
| JPS63149348A (en) | Aluminum alloy for wrapping and manufacture thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PUAI | Public reference made under article 153(3) epc to a published international application that has entered the european phase |
Free format text: ORIGINAL CODE: 0009012 |
|
| AK | Designated contracting states |
Kind code of ref document: A1 Designated state(s): AT BE CH DE ES GB GR IT LI LU NL SE |
|
| 17P | Request for examination filed |
Effective date: 19890328 |
|
| RAP1 | Party data changed (applicant data changed or rights of an application transferred) |
Owner name: CEGEDUR PECHINEY RHENALU |
|
| RAP1 | Party data changed (applicant data changed or rights of an application transferred) |
Owner name: PECHINEY RHENALU |
|
| 17Q | First examination report despatched |
Effective date: 19901220 |
|
| GRAA | (expected) grant |
Free format text: ORIGINAL CODE: 0009210 |
|
| AK | Designated contracting states |
Kind code of ref document: B1 Designated state(s): AT BE CH DE ES GB GR IT LI LU NL SE |
|
| REF | Corresponds to: |
Ref document number: 66699 Country of ref document: AT Date of ref document: 19910915 Kind code of ref document: T |
|
| ITF | It: translation for a ep patent filed | ||
| GBT | Gb: translation of ep patent filed (gb section 77(6)(a)/1977) | ||
| REF | Corresponds to: |
Ref document number: 3864473 Country of ref document: DE Date of ref document: 19911002 |
|
| REG | Reference to a national code |
Ref country code: ES Ref legal event code: FG2A Ref document number: 2024683 Country of ref document: ES Kind code of ref document: B3 |
|
| PLBE | No opposition filed within time limit |
Free format text: ORIGINAL CODE: 0009261 |
|
| STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT |
|
| 26N | No opposition filed | ||
| REG | Reference to a national code |
Ref country code: GR Ref legal event code: FG4A Free format text: 3002615 |
|
| PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: GR Payment date: 19940427 Year of fee payment: 7 |
|
| PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: DE Payment date: 19940518 Year of fee payment: 7 Ref country code: CH Payment date: 19940518 Year of fee payment: 7 |
|
| PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: AT Payment date: 19940519 Year of fee payment: 7 |
|
| PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: GB Payment date: 19940523 Year of fee payment: 7 |
|
| PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: SE Payment date: 19940524 Year of fee payment: 7 |
|
| PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: BE Payment date: 19940601 Year of fee payment: 7 |
|
| PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: ES Payment date: 19940606 Year of fee payment: 7 |
|
| PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: NL Payment date: 19940630 Year of fee payment: 7 Ref country code: LU Payment date: 19940630 Year of fee payment: 7 |
|
| EPTA | Lu: last paid annual fee | ||
| EAL | Se: european patent in force in sweden |
Ref document number: 88420210.2 |
|
| PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: LU Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 19950621 Ref country code: GB Effective date: 19950621 Ref country code: AT Effective date: 19950621 |
|
| PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: SE Effective date: 19950622 Ref country code: ES Free format text: LAPSE BECAUSE OF EXPIRATION OF PROTECTION Effective date: 19950622 |
|
| PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: LI Effective date: 19950630 Ref country code: CH Effective date: 19950630 Ref country code: BE Effective date: 19950630 |
|
| BERE | Be: lapsed |
Owner name: PECHINEY RHENALU Effective date: 19950630 |
|
| PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: GR Free format text: THE PATENT HAS BEEN ANNULLED BY A DECISION OF A NATIONAL AUTHORITY Effective date: 19951231 |
|
| PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: NL Effective date: 19960101 |
|
| GBPC | Gb: european patent ceased through non-payment of renewal fee |
Effective date: 19950621 |
|
| REG | Reference to a national code |
Ref country code: CH Ref legal event code: PL Ref country code: GR Ref legal event code: MM2A Free format text: 3002615 |
|
| NLV4 | Nl: lapsed or anulled due to non-payment of the annual fee |
Effective date: 19960101 |
|
| PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: DE Effective date: 19960301 |
|
| EUG | Se: european patent has lapsed |
Ref document number: 88420210.2 |
|
| REG | Reference to a national code |
Ref country code: ES Ref legal event code: FD2A Effective date: 19990601 |
|
| PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: IT Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES;WARNING: LAPSES OF ITALIAN PATENTS WITH EFFECTIVE DATE BEFORE 2007 MAY HAVE OCCURRED AT ANY TIME BEFORE 2007. THE CORRECT EFFECTIVE DATE MAY BE DIFFERENT FROM THE ONE RECORDED. Effective date: 20050621 |