EP0886683B1 - Thixotropic aluminium-silicon-copper alloy suitable for semi-solid shaping - Google Patents
Thixotropic aluminium-silicon-copper alloy suitable for semi-solid shaping Download PDFInfo
- Publication number
- EP0886683B1 EP0886683B1 EP97914379A EP97914379A EP0886683B1 EP 0886683 B1 EP0886683 B1 EP 0886683B1 EP 97914379 A EP97914379 A EP 97914379A EP 97914379 A EP97914379 A EP 97914379A EP 0886683 B1 EP0886683 B1 EP 0886683B1
- Authority
- EP
- European Patent Office
- Prior art keywords
- alloy
- silicon
- semi
- alloys
- copper
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Lifetime
Links
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
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
- C22C21/04—Modified aluminium-silicon alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/12—Making non-ferrous alloys by processing in a semi-solid state, e.g. holding the alloy in the solid-liquid phase
Definitions
- the invention relates to the field of aluminum-silicon-copper alloys, which can possibly contain other additives such as magnesium, cast in the form of billets having a globular solidification structure conferring thixotropic properties and intended to be shaped, by forging or injection under pressure, after reheating in the semi-solid state.
- Such shaping is known as thixoforming
- Thixoforming developed from the discovery made in the early years 1970 by the team of Pr FLEMINGS at MIT that a metal, developed in some particular conditions, presents, when it is reheated in the semi-solid state, a apparent viscosity which strongly depends on the shear rate, so that it behaves like a solid during handling and like a liquid viscous when injected into a mold. This property leads, compared to traditional shaping processes, better metallurgical quality of parts produced, higher production rates, less wear of tools and molds and energy saving.
- the solidification of the metal with thixoforming must lead to a structure globular, not dendritic, which can be obtained either by mechanical agitation of the solid-liquid mixture as in US Patent 3,948,650 of the MIT, either by mixing electromagnetic as in US patents 4434837 and US 4457355 of ITT-ALUMAX or the patents EP 0351327 and EP 0439981 of ALUMINUM PECHINEY.
- the billets thus cast are cut into pieces corresponding to the quantity of metal necessary for the manufacture of the part to be formed, these pieces being heated to the semi-solid state, usually by induction heating, and transferred to shaping equipment (forging press or pressure injection machine).
- alloys intended for thixoforming to increase the resistance of the parts produced, or to facilitate machining, tried to use alloys containing 1 to 5% copper. With for example a alloy with 3% copper, no particular problem is encountered with the casting of billets, and the mechanical resistance at the level of the billet is effectively improved more than 25%. If the reheating temperature is adjusted to the semi-solid state, by lowering it by a few degrees C, to stay at a liquid fraction rate close to 50%, the thixoforming of this alloy is also easy.
- the invention aims to find a field of composition of aluminum-silicon alloys more than 5% silicon and containing 1 to 5% copper allowing get out of the dilemma set out above, i.e. allow both thixoforming without problem and to obtain parts having a high mechanical resistance and a good elongation.
- the subject of the invention is the use of an aluminum alloy of composition (% by weight): If: 5% - 7.2% Cu: 1% - 5% Mg ⁇ 1% Zn ⁇ 3% Fe ⁇ 1.5% other elements ⁇ 1% each and 3% in total, aluminum remains, such as:% Si ⁇ 7.5 - (% Cu / 3), for forming in the semi-solid state, at a rate of liquid fraction included between 35% and 55%, and with, in this state, a structure free of polyhedral crystals not remelted silicon.
- the single figure represents, in a diagram having for abscissa the content of silicon and for ordinate the copper content, the lines of equal eutectic fraction and the composition domain according to the invention.
- the alloys according to the invention remain in the usual composition ranges of AlSiCu molding alloys. We do not go below 5% silicon because the alloy becomes difficult to flow.
- the addition of copper has a significant effect on the mechanical strength and the machinability only from a content of approximately 1% and, beyond 5%, there is a very unfavorable effect on the elongation .
- Magnesium in a content of less than 1%, increases the response to heat treatment thanks to the formation of hardening particles Mg 2 Si, but, beyond 1%, there is also an unfavorable effect on the elongation.
- a eutectic silicon modifier such as sodium, strontium or antimony, which prevents the formation of coarse grains of silicon Sodium and strontium can be present alone or together, antimony being always alone.
- strontium for example, the content is between 0.005 and 0.05%.
- titanium up to 0.2% and / or boron up to 0.1%, allows a refinement of the grain and a better heat resistance.
- an alloy Ai-Si6Cu3Mg0,6 or a Al-Si6,5Cu1,5Mg0,6 alloy have a thixoforming behavior identical to that of an Al-Si7Mg0.6 alloy, that is to say that a rate of liquid fraction close to 50% with a complete fusion of the eutectic, and therefore a absence of polyhedral silicon crystals.
- the metal loss was 8 ⁇ 2%, identical to that of the alloy Ai-Si7Mg0.6.
- the apparent viscosity of pieces heated at a temperature between 2 and 5 ° C. above the eutectic plateau was measured, using a penetration test consisting in measuring the resistance to deformation F of the heated piece compressed by a tool at constant speed at the end of a stroke of determined length.
- the ratio of this force F to a constant threshold force F s is established , for a conventional value of metal loss by exudation of 8%, the metal loss being an indicator of the rate of liquid fraction for a given material.
- the rate of liquid fraction is controllable to within ⁇ 5%, taking into account the usual silicon content intervals allowed by the standards and specifications for the alloys considered, it can be estimated that, in the figure, the composition of the alloy must be such that the Si and Cu contents satisfy the relation: (2) 6.5 -% Cu / 3 ⁇ % Si ⁇ 7.5 -% Cu / 3 which corresponds to the fact that the rate of liquid fraction obtained with complete fusion of the eutectic is between 45 and 55%, or that the eutectic fraction of the alloy is between 45 and 55%.
- the thixoforming behavior is poor: as soon as the filling of the mold cavity begins, the heat loss by exchange with the mold wall leads to partial resolidification and an increase in the apparent viscosity which causes defects in the part. injected, such as folds, shrinkage or non-arrival.
- the range corresponding to the compositions according to the invention comprises not only the band between the straight lines representing the eutectic fractions of 55% and 45%, i.e. the fringe surrounding the straight line representing 50%, but also the area between 45% and 35% which, taking into account the lower limit of Cu to 1 %, practically corresponds to the adjacent triangle.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Conductive Materials (AREA)
- Physical Vapour Deposition (AREA)
- Manufacture Of Alloys Or Alloy Compounds (AREA)
- Powder Metallurgy (AREA)
- Forging (AREA)
- Ceramic Products (AREA)
- Silicon Compounds (AREA)
- Materials For Medical Uses (AREA)
- Chemically Coating (AREA)
- Preventing Corrosion Or Incrustation Of Metals (AREA)
Abstract
Description
L'invention concerne le domaine des alliages aluminium-silicium-cuivre, pouvant contenir éventuellement d'autres éléments d'addition tels que le magnésium, coulés sous forme de billettes présentant une structure de solidification globulaire lui conférant des propriétés thixotropes et destinés à être mis en forme, par forgeage ou injection sous pression, après réchauffage à l'état semi-solide. Une telle mise en forme est connue sous le nom de thixoformageThe invention relates to the field of aluminum-silicon-copper alloys, which can possibly contain other additives such as magnesium, cast in the form of billets having a globular solidification structure conferring thixotropic properties and intended to be shaped, by forging or injection under pressure, after reheating in the semi-solid state. Such shaping is known as thixoforming
Le thixoformage s'est développé à partir de la découverte faite au début des années 1970 par l'équipe du Pr FLEMINGS au MIT qu'un métal, élaboré dans certaines conditions particulières, présente, lorsqu'il est réchauffé à l'état semi-solide, une viscosité apparente qui dépend fortement de la vitesse de cisaillement, de sorte qu'il se comporte comme un solide au cours des manutentions et comme un liquide visqueux lorsqu'on l'injecte dans un moule. Cette propriété conduit, par rapport aux procédés traditionnels de mise en forme, à une meilleure qualité métallurgique des pièces produites, des cadences de production plus élevées, une usure moindre des outils et des moules et une économie d'énergie.Thixoforming developed from the discovery made in the early years 1970 by the team of Pr FLEMINGS at MIT that a metal, developed in some particular conditions, presents, when it is reheated in the semi-solid state, a apparent viscosity which strongly depends on the shear rate, so that it behaves like a solid during handling and like a liquid viscous when injected into a mold. This property leads, compared to traditional shaping processes, better metallurgical quality of parts produced, higher production rates, less wear of tools and molds and energy saving.
Dans ce but, la solidification du métal au thixoformage doit conduire à une structure globulaire, et non dendritique, qui peut être obtenue soit par agitation mécanique du mélange solide-liquide comme dans le brevet US 3948650 du MIT, soit par brassage électromagnétique comme dans les brevets US 4434837 et US 4457355 d'ITT-ALUMAX ou les brevets EP 0351327 et EP 0439981 d'ALUMINIUM PECHINEY. Les billettes ainsi coulées sont découpées en lopins correspondant à la quantité de métal nécessaire à la fabrication de la pièce à former, ces lopins étant réchauffés à l'état semi-solide, généralement par chauffage à induction, et transférés à l'équipement de mise en forme (presse à forger ou machine d'injection sous pression). For this purpose, the solidification of the metal with thixoforming must lead to a structure globular, not dendritic, which can be obtained either by mechanical agitation of the solid-liquid mixture as in US Patent 3,948,650 of the MIT, either by mixing electromagnetic as in US patents 4434837 and US 4457355 of ITT-ALUMAX or the patents EP 0351327 and EP 0439981 of ALUMINUM PECHINEY. The billets thus cast are cut into pieces corresponding to the quantity of metal necessary for the manufacture of the part to be formed, these pieces being heated to the semi-solid state, usually by induction heating, and transferred to shaping equipment (forging press or pressure injection machine).
Ce procédé s'est développé de manière industrielle essentiellement pour les alliages d'aluminium destinés à la fabrication de pièces pour l'industrie automobile. De fait, la quasi-totalité des livraisons a porté sur des alliages du type Al-Si7Mg à 7% de silicium et moins de 1% de magnésium, par exemple les alliages Al-Si7Mg0,3 et Al-Si7Mg0,6 (A356 et 357 selon la nomenclature de l'Aluminum Association pour les alliages de moulage). Ces alliages présentent une bonne aptitude au thixoformage. En effet, quand on les réchauffe de manière à obtenir un taux de fraction liquide de l'ordre de 50%, correspondant à un optimum des propriétés rhéologiques du métal la phase eutectique est complétement refondue alors que la fusion de la phase primaire de silicium n'est pas entamée.This process has been developed industrially mainly for alloys aluminum for the manufacture of parts for the automotive industry. In fact, the almost all deliveries related to alloys of the Al-Si7Mg type at 7% silicon and less than 1% magnesium, for example the alloys Al-Si7Mg0,3 and Al-Si7Mg0,6 (A356 and 357 according to the nomenclature of the Aluminum Association for molding alloys). These alloys have good thixoforming ability. In effect, when they are heated so as to obtain a liquid fraction rate of of the order of 50%, corresponding to an optimum of the rheological properties of the metal la eutectic phase is completely overhauled while the fusion of the primary phase silicon is not started.
Les caractéristiques mécaniques des pièces réalisées à l'aide de ces alliages sont bonnes et on a la possibilité d'adapter la résistance et/ou la ductilité par l'utilisation de différents traitements thermiques. Cependant, la résistance à la rupture maximale, pour un alliage de ce type à 0,6% de magnésium, reste limitée à environ 350 MPa à l'état T6.The mechanical characteristics of the parts produced using these alloys are good and we have the possibility of adapting the resistance and / or the ductility by the use of different heat treatments. However, the maximum breaking strength, for an alloy of this type with 0.6% magnesium, remains limited to approximately 350 MPa at state T6.
Le brevet FR 2266749 de la demanderesse, publié en 1975, décrit un procédé de formage, par exemple par coulée sous pression, d'alliages d'aluminium à l'état semi-solide, avec un taux de fraction liquide supérieur à 35%. Les exemples mentionnent les alliages AS9U3 à 9% de silicium et 3% de cuivre, et AU4SG à 4% de cuivre, 0,75% de silicium et 0,5% de magnésium.The applicant's patent FR 2266749, published in 1975, describes a method of forming, for example by pressure casting, of aluminum alloys in the semi-solid state, with a liquid fraction rate higher than 35%. Examples mention AS9U3 alloys with 9% silicon and 3% copper, and AU4SG with 4% copper, 0.75% silicon and 0.5% magnesium.
Pour améliorer la résistance mécanique des alliages destinés au thixoformage, soit pour augmenter la résistance des pièces fabriquées, soit pour en faciliter l'usinage, on a essayé d'utiliser des alliages contenant de 1 à 5% de cuivre. Avec par exemple un alliage à 3% de cuivre, on ne rencontre aucun problème particulier à la coulée des billettes, et la résistance mécanique au niveau de la billette est effectivement améliorée de plus de 25%. Si on ajuste la température de réchauffage à l'état semi-solide, en l'abaissant de quelques degrés C, pour rester à un taux de fraction liquide voisin de 50%, le thixoformage de cet alliage s'opère aussi facilement. Par contre, on constate une baisse importante, de l'ordre de la moitié, de l'allongement sur la pièce traitée T6 par rapport à celui mesuré sur la billette au même état métallurgique, alors que, pour l'alliage sans cuivre, l'allongement de la billette traitée et celui de la pièce traitée sont pratiquement identiques.To improve the mechanical resistance of alloys intended for thixoforming, to increase the resistance of the parts produced, or to facilitate machining, tried to use alloys containing 1 to 5% copper. With for example a alloy with 3% copper, no particular problem is encountered with the casting of billets, and the mechanical resistance at the level of the billet is effectively improved more than 25%. If the reheating temperature is adjusted to the semi-solid state, by lowering it by a few degrees C, to stay at a liquid fraction rate close to 50%, the thixoforming of this alloy is also easy. However, we can see a significant decrease, of the order of half, in the elongation on the part treated T6 compared to that measured on the billet in the same metallurgical state, whereas, for the copper-free alloy, the elongation of the treated billet and that of the treated part are practically identical.
La demanderesse a essayé d'élucider la raison de ce comportement surprenant. Une analyse microstructurale des lopins en alliage au cuivre réchauffés à l'état semi-solide, puis trempés à l'eau, a révélé la présence d'amas fragilisants de cristaux de silicium de forme polyédrique.Ces mêmes amas ont également été mis en évidence sur la surface de rupture des éprouvettes de traction tirées de pièces thixoformées à partir de ces lopins. Une hypothèse permettant d'expliquer cette microstructure est que la phase eutectique n'a pas été complétement refondue, comme dans le cas des Al-Si7Mg sans cuivre, et que le silicium de l'eutectique a coalescé pour former des amas de cristaux grossiers.The Applicant has attempted to elucidate the reason for this surprising behavior. A microstructural analysis of copper alloy plots reheated in the semi-solid state, then soaked in water, revealed the presence of embrittling clusters of silicon crystals polyhedral shape. These same clusters have also been highlighted on the surface of rupture of tensile test pieces drawn from thixoformed parts from these plots. One hypothesis to explain this microstructure is that the phase eutectic has not been completely recast, as in the case of Al-Si7Mg without copper, and the eutectic silicon coalesced to form clusters of crystals rude.
Pour éviter ces amas de cristaux de silicium préjudiciables à l'allongement des pièces, les inventeurs ont essayé d'augmenter la température de réchauffage pour obtenir une refusion complète de la phase eutectique. Mais ceci a conduit à un taux de fraction liquide de l'ordre de 60%, entrainant un effondrement du lopin réchauffé au cours des manutentions, qui ne permettent plus le thixoformage dans des conditions industrielles acceptables.To avoid these clumps of silicon crystals detrimental to the elongation of the parts, the inventors tried to increase the reheating temperature to obtain a complete remelting of the eutectic phase. But this has led to a fraction rate liquid of the order of 60%, causing a collapse of the heated piece during handling, which no longer allows thixoforming under industrial conditions acceptable.
L'invention a pour but de trouver un domaine de composition d'alliages aluminium-silicium à plus de 5% de silicium et contenant de 1 à 5% de cuivre permettant de sortir du dilemme exposé ci-dessus, c'est à dire de permettre à la fois un thixoformage sans problème et d'obtenir des pièces présentant une haute résistance mécanique et un bon allongement.The invention aims to find a field of composition of aluminum-silicon alloys more than 5% silicon and containing 1 to 5% copper allowing get out of the dilemma set out above, i.e. allow both thixoforming without problem and to obtain parts having a high mechanical resistance and a good elongation.
L'invention a pour objet l'utilisation d'un alliage d'aluminium de composition (% en poids): Si: 5% - 7,2% Cu: 1% - 5% Mg < 1% Zn < 3% Fe< 1,5% autres éléments < 1% chacun et 3% au total, reste aluminium, tel que: %Si < 7,5 - (%Cu/3), pour le formage à l'état semi-solide, à un taux de fraction liquide compris entre 35% et 55%, et avec, à cet état, une structure exempte de cristaux polyédriques de silicium non refondus.The subject of the invention is the use of an aluminum alloy of composition (% by weight): If: 5% - 7.2% Cu: 1% - 5% Mg <1% Zn <3% Fe <1.5% other elements <1% each and 3% in total, aluminum remains, such as:% Si <7.5 - (% Cu / 3), for forming in the semi-solid state, at a rate of liquid fraction included between 35% and 55%, and with, in this state, a structure free of polyhedral crystals not remelted silicon.
Elle a également pour objet un procédé selon la revendication 7 de thixoformage de pièces présentant une
haute résistance mécanique et un bon allongement à partir de cet alliage.
Dans ce domaine, on peut définir 3 compositions particulières telles que:
La figure unique représente, dans un diagramme ayant pour abscisse la teneur en silicium et pour ordonnée la teneur en cuivre, les droites d'égale fraction eutectique et le domaine de composition selon l'invention.The single figure represents, in a diagram having for abscissa the content of silicon and for ordinate the copper content, the lines of equal eutectic fraction and the composition domain according to the invention.
Les alliages selon l'invention restent dans les domaines de composition habituels des alliages de moulage AlSiCu. On ne descend pas en dessous de 5% de silicium car l'alliage devient difficile à couler. L'addition de cuivre n'a un effet significatif sur la résistance mécanique et l'usinabilité qu'à partir d'une teneur d'environ 1% et, au delà de 5%, on a un effet très défavorable sur l'allongement. Le magnésium, à une teneur inférieure à 1%, accroít la réponse au traitement thermique grâce à la formation de particules durcissantes Mg2Si, mais, au-delà de 1%, on a également un effet défavorable sur l'allongement.The alloys according to the invention remain in the usual composition ranges of AlSiCu molding alloys. We do not go below 5% silicon because the alloy becomes difficult to flow. The addition of copper has a significant effect on the mechanical strength and the machinability only from a content of approximately 1% and, beyond 5%, there is a very unfavorable effect on the elongation . Magnesium, in a content of less than 1%, increases the response to heat treatment thanks to the formation of hardening particles Mg 2 Si, but, beyond 1%, there is also an unfavorable effect on the elongation.
Des teneurs relativement élevées peuvent être observées pour le zinc et le fer dans le cas où l'on part de métal secondaire issu de reyclage. Ces teneurs sont évidemment beaucoup plus réduites si l'on part de métal primaire.Relatively high levels can be observed for zinc and iron in case where we start from secondary metal from recycling. These contents are obviously much more reduced if we start from primary metal.
On peut aussi ajouter, comme on le fait habituellement dans les alliages AlSi de fonderie, un agent de modification du silicium de l'eutectique, tel que le sodium, le strontium ou l'antimoine, qui évite la formation de grains trop grossiers de silicium Le sodium et le strontium peuvent être présents seuls ou ensemble, l'antimoine étant toujours seul. Pour le strontium par exemple, la teneur est comprise entre 0,005 et 0,05%. De même, une addition de titane jusqu'à 0,2% et/ou de bore jusqu'à 0,1%, permet un affinage du grain et une meilleure résistance à chaud.We can also add, as we usually do in AlSi alloys of foundry, a eutectic silicon modifier, such as sodium, strontium or antimony, which prevents the formation of coarse grains of silicon Sodium and strontium can be present alone or together, antimony being always alone. For strontium for example, the content is between 0.005 and 0.05%. Likewise, an addition of titanium up to 0.2% and / or boron up to 0.1%, allows a refinement of the grain and a better heat resistance.
Afin de maintenir, pour les alliages au cuivre, les mêmes propriétés rhéologiques au
cours du thixoformage que pour les alliages de composition identique mais sans
cuivre, tout en obtenant également une refusion complète du silicium eutectique dans
le lopin réchauffé à l'état semi-solide, gage d'un bon allongement de la pièce finie, les
inventeurs ont eu l'idée de modifier la teneur en silicium en fonction de la teneur en
cuivre. Ils ont ainsi constaté qu'on pouvait obtenir un comportement au thixoformage
identique à celui d'un alliage Al-Si7 pour un alliage Al-SiCu si les teneurs en Si et Cu
de cet alliage satisfont à la relation:
La droite représentant cette relation sur la figure est donc la droite des compositions correspondant à 50% de fraction eutectique. Ainsi, un alliage Ai-Si6Cu3Mg0,6 ou un alliage Al-Si6,5Cu1,5Mg0,6 ont un comportement au thixoformage identique à celui d'un alliage Al-Si7Mg0,6, c'est à dire qu'on peut obtenir au réchauffage un taux de fraction liquide voisin de 50% avec une fusion complète de l'eutectique, et donc une absence de cristaux polyédriques de silicium.The line representing this relation in the figure is therefore the line of the compositions corresponding to 50% of eutectic fraction. Thus, an alloy Ai-Si6Cu3Mg0,6 or a Al-Si6,5Cu1,5Mg0,6 alloy have a thixoforming behavior identical to that of an Al-Si7Mg0.6 alloy, that is to say that a rate of liquid fraction close to 50% with a complete fusion of the eutectic, and therefore a absence of polyhedral silicon crystals.
On a vérifié, pour les 2 compositions mentionnées, que la perte métal était de 8 ± 2%, identique à celle de l'alliage Ai-Si7Mg0,6. On a mesuré la viscosité apparente de lopins réchauffés à une température située entre 2 et 5°C au dessus du palier eutectique, à l'aide d'un test de pénétration consistant à mesurer la résistance à la déformation F du lopin réchauffé, comprimé par un outil à vitesse constante au terme d'une course de longueur déterminée. On établit le rapport de cette force F à une force-seuil Fs constante, pour une valeur conventionnelle de perte métal par exsudation de 8%, la perte métal étant un indicateur du taux de fraction liquide pour un matériau donné.It was verified, for the 2 compositions mentioned, that the metal loss was 8 ± 2%, identical to that of the alloy Ai-Si7Mg0.6. The apparent viscosity of pieces heated at a temperature between 2 and 5 ° C. above the eutectic plateau was measured, using a penetration test consisting in measuring the resistance to deformation F of the heated piece compressed by a tool at constant speed at the end of a stroke of determined length. The ratio of this force F to a constant threshold force F s is established , for a conventional value of metal loss by exudation of 8%, the metal loss being an indicator of the rate of liquid fraction for a given material.
Pour les deux compositions mentionnées, on trouve un rapport F/Fs de l'ordre de 0,45, semblable à celui mesuré sur un lopin d'alliage Al-Si7Mg0,6.For the two compositions mentioned, there is an F / Fs ratio of the order of 0.45, similar to that measured on a piece of Al-Si7Mg0.6 alloy.
Comme le taux de fraction liquide est contrôlable à environ ± 5% près, compte tenu
des intervalles habituels de teneur en silicium admis par les normes et spécifications
pour les alliages considérés, on peut estimer que, sur la figure, la composition de
l'alliage doit être telle que les teneurs en Si et Cu satisfassent à la relation:
De plus, on a constaté qu'on pouvait, pour ces alliages au cuivre, obtenir un bon
comportement au thixoformage en réchauffant les lopins jusqu'à un taux de fraction
liquide nettement plus bas que 50%. Ainsi, pour un alliage à 5% de Si et 3% de Cu,
on peut descendre jusqu'à 40% de fraction liquide et, pour un alliage à 5% de Si et
1,5% de Cu, jusqu'à environ 35%. Par contre, en essayant un alliage à 4% de silicium
et 3% de cuivre, on a constaté d'abord qu'à cause du grand intervalle de solidification
(625 - 560°C), la coulée de billettes thixotropes se fait avec difficulté, entraínant des
défauts de coulée tels que des arrachements et des percées. Par ailleurs, le
comportement au thixoformage est mauvais: dès que le remplissage de la cavité du
moule commence, la perte thermique par échange avec la paroi du moule conduit à
une resolidification partielle et une augmentation de la viscosité apparente qui entraíne
des défauts dans la pièce injectée, tels que des replis, retassures ou non-venues.
Ainsi, en se reportant à la figure représentant les teneurs en silicium et cuivre, sur
laquelle on a fait figurer les droites d'égale fraction eutectique, on constate que le
domaine correspondant aux compositions selon l'invention comprend non seulement
la bande comprise entre les droites représentant les fractions eutectiques de 55% et
45%, c'est à dire la frange entourant la droite représentant 50%, mais aussi la zone
comprise entre 45% et 35% qui, compte-tenu de la limite inférieure de Cu à 1%,
correspond pratiquement au triangle adjacent.In addition, it has been found that, for these copper alloys, it is possible to obtain good thixoforming behavior by heating the pieces up to a rate of liquid fraction clearly lower than 50%. Thus, for an alloy with 5% Si and 3% Cu, we can go down to 40% of liquid fraction and, for an alloy with 5% Si and 1.5% Cu, up to around 35 %. On the other hand, by trying an alloy with 4% of silicon and 3% of copper, it was noted initially that because of the large interval of solidification (625 - 560 ° C), the casting of thixotropic billets is done with difficulty , resulting in casting defects such as tears and breakthroughs. Furthermore, the thixoforming behavior is poor: as soon as the filling of the mold cavity begins, the heat loss by exchange with the mold wall leads to partial resolidification and an increase in the apparent viscosity which causes defects in the part. injected, such as folds, shrinkage or non-arrival.
Thus, with reference to the figure representing the silicon and copper contents, on which the lines of equal eutectic fraction have been shown, it can be seen that the range corresponding to the compositions according to the invention comprises not only the band between the straight lines representing the eutectic fractions of 55% and 45%, i.e. the fringe surrounding the straight line representing 50%, but also the area between 45% and 35% which, taking into account the lower limit of Cu to 1 %, practically corresponds to the adjacent triangle.
Claims (12)
- Use of an alloy of aluminium of composition (by weight) :
Si: 5% - 7.2%; Cu: 1% - 5%; Mg: < 1%; Zn: < 3%; Fe: < 1.5%; and possibly Sr: 0.005 - 0.05%; Ti: up to 0.2%; B: up to 0.1%, with other elements < 1% each and < 3% in total, the rest being aluminium with the condition that %Si < 7.5 -(%Cu/3),
for forming, in the semi-solid state, with a liquid fraction of between 35 and 55% and with a structure free of polyhedral crystals of unremelted silicon. - Use of an alloy according to Claim 1 such that Si is between 5 and 7% and Cu between 1% and 1.5%.
- Use of an alloy according to Claim 1 such that Si is between 5 and 6.3% and Cu between 2.5% and 3.5%.
- Use of an alloy according to Claim 1 such that Si is between 5 and 6% and Cu between 3.5% and 4.5%.
- Use of an alloy according to one of Claims 1 to 4 containing between 0.005 and 0.05% of strontium.
- Use of an alloy according to one of Claims 1 to 5 containing up to 0.2% titanium and/or up to 0.1% boron.
- A method of producing aluminium alloy articles by forming, in the semi-solid state and with a liquid fraction of between 35 and 55% and with a structure free of polyhedral crystals of unremelted silicon, an alloy of composition (by weight):
Si: 5% - 7.2%; Cu: 1% - 5%; Mg: < 1%; Zn: < 3%; Fe: < 1.5%; and possibly Sr: 0.005 - 0.05%; Ti: up to 0.2%; B: up to 0.1%, with other elements < 1% each and < 3% in total, the rest being aluminium with the condition that %Si < 7.5 -(%Cu/3). - A method according to Claim 7 characterised in that Si is between 5 and 7% and Cu between 1% and 1.5%.
- A method according to Claim 7 characterised in that Si is between 5 and 6.3% and Cu between 2.5% and 3.5%.
- A method according to Claim 7 characterised in that Si is between 5 and 6% and Cu between 3.5% and 4.5%.
- A method according to one of Claims 7 to 10 characterised in that the alloy contains between 0.005 and 0.05% of strontium.
- A method according to one of Claims 7 to 11 characterised in that the alloy contains up to 0.2% titanium and/or up to 0.1% boron.
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
FR9603703A FR2746414B1 (en) | 1996-03-20 | 1996-03-20 | THIXOTROPE ALUMINUM-SILICON-COPPER ALLOY FOR SHAPING IN SEMI-SOLID CONDITION |
FR9603703 | 1996-03-20 | ||
PCT/FR1997/000439 WO1997035040A1 (en) | 1996-03-20 | 1997-03-12 | Thixotropic aluminium-silicon-copper alloy suitable for semi-solid shaping |
Publications (2)
Publication Number | Publication Date |
---|---|
EP0886683A1 EP0886683A1 (en) | 1998-12-30 |
EP0886683B1 true EP0886683B1 (en) | 1999-08-18 |
Family
ID=9490523
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP97914379A Expired - Lifetime EP0886683B1 (en) | 1996-03-20 | 1997-03-12 | Thixotropic aluminium-silicon-copper alloy suitable for semi-solid shaping |
Country Status (16)
Country | Link |
---|---|
US (1) | US5879478A (en) |
EP (1) | EP0886683B1 (en) |
JP (1) | JP2000506938A (en) |
AT (1) | ATE183549T1 (en) |
AU (1) | AU715447B2 (en) |
BR (1) | BR9708091A (en) |
CA (1) | CA2249464C (en) |
CZ (1) | CZ293598A3 (en) |
DE (2) | DE69700436T2 (en) |
ES (1) | ES2136468T3 (en) |
FR (1) | FR2746414B1 (en) |
HU (1) | HUP9902156A3 (en) |
NO (1) | NO984366L (en) |
PL (1) | PL185416B1 (en) |
SK (1) | SK128098A3 (en) |
WO (1) | WO1997035040A1 (en) |
Families Citing this family (24)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
KR100247143B1 (en) * | 1998-02-04 | 2000-04-01 | 박호군 | THIXOFORMABLE SIC/(2í í í AL+SI)COMPOSITE AND METHOD FOR MANUFACTURING THEREOF |
FR2788788B1 (en) * | 1999-01-21 | 2002-02-15 | Pechiney Aluminium | HYPEREUTECTIC ALUMINUM-SILICON ALLOY PRODUCT FOR SHAPING IN SEMI-SOLID CONDITION |
US6428636B2 (en) | 1999-07-26 | 2002-08-06 | Alcan International, Ltd. | Semi-solid concentration processing of metallic alloys |
WO2001009401A1 (en) * | 1999-07-28 | 2001-02-08 | Sm Schweizerische Munitionsunternehmung Ag | Method for producing a metal-alloy material |
US6446325B1 (en) | 1999-12-22 | 2002-09-10 | International Business Machines Corporation | Method of making a swagable metal arm tip for a ceramic actuator arm |
KR20020096279A (en) * | 2001-06-19 | 2002-12-31 | 현대자동차주식회사 | an aluminum alloy |
US6719859B2 (en) | 2002-02-15 | 2004-04-13 | Northwest Aluminum Company | High strength aluminum base alloy |
US6908590B2 (en) * | 2002-03-19 | 2005-06-21 | Spx Corporation | Aluminum alloy |
CN100338248C (en) * | 2003-11-20 | 2007-09-19 | 北京有色金属研究总院 | Aluminium alloy for semi solid state shaping and preparation method of its semi solid state blank material |
US7165598B2 (en) * | 2004-03-15 | 2007-01-23 | Spx Corporation | Magnesium alloy and methods for making |
CN101018881B (en) * | 2004-07-28 | 2011-11-30 | 美铝公司 | An Al-Si-Mg-Zn-Cu alloy for aerospace and automotive castings |
FR2887182B1 (en) * | 2005-06-15 | 2007-09-21 | Salomon Sa | RADIUS FOR A TRACTION ROLL WHEEL AND TRACTION RAY WHEEL |
GB0514751D0 (en) * | 2005-07-19 | 2005-08-24 | Holset Engineering Co | Method and apparatus for manufacturing turbine or compressor wheels |
US20080299001A1 (en) * | 2007-05-31 | 2008-12-04 | Alcan International Limited | Aluminum alloy formulations for reduced hot tear susceptibility |
CN100464898C (en) * | 2007-06-18 | 2009-03-04 | 北京科技大学 | Process for making SiC particle reinforced composite material electronic package shell using semi-soild-state technology |
US8047258B1 (en) | 2008-07-18 | 2011-11-01 | Brunswick Corporation | Die casting method for semi-solid billets |
WO2010033650A1 (en) * | 2008-09-17 | 2010-03-25 | Cool Polymers, Inc. | Multi-component metal injection molding |
CN102319876B (en) * | 2011-08-31 | 2013-05-01 | 苏州有色金属研究院有限公司 | Near-net-shape casting production method for automotive aluminum alloy parts |
US10174409B2 (en) | 2011-10-28 | 2019-01-08 | Alcoa Usa Corp. | High performance AlSiMgCu casting alloy |
US9555468B2 (en) * | 2012-09-12 | 2017-01-31 | Lucio Megolago Albani | Process and plant for producing components made of an aluminium alloy for vehicles and white goods, and components obtained thereby |
EP3084027B1 (en) | 2013-12-20 | 2018-10-31 | Alcoa USA Corp. | HIGH PERFORMANCE AlSiMgCu CASTING ALLOY |
CN103831417A (en) * | 2014-03-11 | 2014-06-04 | 扬州宏福铝业有限公司 | Continuous semisolid forming method for high-silicon aluminum alloy encapsulation shell |
CN110592438A (en) * | 2019-09-03 | 2019-12-20 | 滨州联信新材料科技有限公司 | Formula and preparation method of high-performance A356 aluminum alloy |
CN112646993A (en) * | 2020-12-15 | 2021-04-13 | 有研工程技术研究院有限公司 | Aluminum alloy material suitable for high solid-phase semi-solid rheocasting |
Family Cites Families (12)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US1924725A (en) * | 1932-09-21 | 1933-08-29 | Aluminum Co Of America | Aluminum alloys |
GB555425A (en) * | 1942-02-18 | 1943-08-23 | Magnal Products Ltd | Improvements in and relating to aluminium alloys |
LU69788A1 (en) * | 1974-04-04 | 1976-03-17 | Pechiney Aluminium | |
SU523953A1 (en) * | 1975-01-13 | 1976-08-05 | Ярославское Объединение "Автодизель" | Aluminum-based foundry alloy |
US4457355A (en) * | 1979-02-26 | 1984-07-03 | International Telephone And Telegraph Corporation | Apparatus and a method for making thixotropic metal slurries |
CA1235048A (en) * | 1983-05-23 | 1988-04-12 | Yoji Awano | Method for producing aluminum alloy castings and the resulting product |
FR2557144A1 (en) * | 1983-12-22 | 1985-06-28 | Fonderie Alcoa Mg Sa | ALUMINUM ALLOY HAVING IMPROVED PROPERTIES |
US4865808A (en) * | 1987-03-30 | 1989-09-12 | Agency Of Industrial Science And Technology | Method for making hypereutetic Al-Si alloy composite materials |
FR2634677B1 (en) * | 1988-07-07 | 1990-09-21 | Pechiney Aluminium | PROCESS FOR THE MANUFACTURE BY CONTINUOUS CASTING OF THIXOTROPIC METAL PRODUCTS |
FR2656552B1 (en) * | 1990-01-04 | 1995-01-13 | Pechiney Aluminium | PROCESS FOR THE MANUFACTURE OF THIXOTROPIC METAL PRODUCTS BY CONTINUOUS CASTING WITH ELECTROMAGNETIC BREWING IN POLYPHASE CURRENT. |
GB2243620B (en) * | 1990-03-27 | 1994-06-29 | Atsugi Unisia Corp | Improvements in and relating to forming aluminium-silicon alloy |
JP2901218B2 (en) * | 1992-07-16 | 1999-06-07 | 大同メタル工業 株式会社 | Aluminum alloy bearing |
-
1996
- 1996-03-20 FR FR9603703A patent/FR2746414B1/en not_active Expired - Fee Related
-
1997
- 1997-02-26 US US08/806,399 patent/US5879478A/en not_active Expired - Fee Related
- 1997-03-12 JP JP9533188A patent/JP2000506938A/en active Pending
- 1997-03-12 DE DE69700436T patent/DE69700436T2/en not_active Expired - Fee Related
- 1997-03-12 SK SK1280-98A patent/SK128098A3/en unknown
- 1997-03-12 HU HU9902156A patent/HUP9902156A3/en unknown
- 1997-03-12 WO PCT/FR1997/000439 patent/WO1997035040A1/en not_active Application Discontinuation
- 1997-03-12 PL PL97329008A patent/PL185416B1/en not_active IP Right Cessation
- 1997-03-12 DE DE0886683T patent/DE886683T1/en active Pending
- 1997-03-12 EP EP97914379A patent/EP0886683B1/en not_active Expired - Lifetime
- 1997-03-12 AT AT97914379T patent/ATE183549T1/en not_active IP Right Cessation
- 1997-03-12 CZ CZ982935A patent/CZ293598A3/en unknown
- 1997-03-12 ES ES97914379T patent/ES2136468T3/en not_active Expired - Lifetime
- 1997-03-12 AU AU21645/97A patent/AU715447B2/en not_active Ceased
- 1997-03-12 CA CA002249464A patent/CA2249464C/en not_active Expired - Fee Related
- 1997-03-12 BR BR9708091A patent/BR9708091A/en not_active Application Discontinuation
-
1998
- 1998-09-18 NO NO984366A patent/NO984366L/en not_active Application Discontinuation
Also Published As
Publication number | Publication date |
---|---|
DE886683T1 (en) | 1999-05-06 |
BR9708091A (en) | 1999-07-27 |
CA2249464C (en) | 2004-12-14 |
WO1997035040A1 (en) | 1997-09-25 |
ES2136468T3 (en) | 1999-11-16 |
HUP9902156A3 (en) | 2001-11-28 |
JP2000506938A (en) | 2000-06-06 |
CZ293598A3 (en) | 1999-10-13 |
HUP9902156A2 (en) | 1999-11-29 |
ATE183549T1 (en) | 1999-09-15 |
EP0886683A1 (en) | 1998-12-30 |
NO984366L (en) | 1998-11-18 |
DE69700436T2 (en) | 2000-02-03 |
FR2746414B1 (en) | 1998-04-30 |
AU2164597A (en) | 1997-10-10 |
US5879478A (en) | 1999-03-09 |
CA2249464A1 (en) | 1997-09-25 |
FR2746414A1 (en) | 1997-09-26 |
SK128098A3 (en) | 1999-05-07 |
AU715447B2 (en) | 2000-02-03 |
NO984366D0 (en) | 1998-09-18 |
PL329008A1 (en) | 1999-03-01 |
DE69700436D1 (en) | 1999-09-23 |
PL185416B1 (en) | 2003-05-30 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
EP0886683B1 (en) | Thixotropic aluminium-silicon-copper alloy suitable for semi-solid shaping | |
JP3415987B2 (en) | Molding method of heat-resistant magnesium alloy molded member | |
FR2827614A1 (en) | Welded weldable products of high resistance aluminum alloy used in aircraft contain cerium preferably added as a mischmetal | |
WO2003051998A1 (en) | Thermoplastic polymer composition comprising a hyperbranched polymer and articles made using said composition | |
CA2820768A1 (en) | Thick products made of 7xxx alloy and manufacturing process | |
CN109468503B (en) | Aluminum alloy material and production process thereof | |
EP1147237B1 (en) | Hypereutectic aluminium-silicon alloy product for semisolid forming | |
EP0756017B1 (en) | Aluminium-copper-magnesium alloy with high creep resistance | |
EP1453986A1 (en) | Safety component moulded in al-si alloy | |
FR2954355A1 (en) | COPPER ALUMINUM ALLOY MOLDED MECHANICAL AND HOT FLUID MOLDED PART | |
FR2833616A1 (en) | Structural or safety component for a motor vehicle is cast under pressure from an aluminum alloy | |
CH644402A5 (en) | PROCESS FOR THE MANUFACTURE OF HOLLOW BODIES IN AN ALUMINUM ALLOY AND PRODUCT OBTAINED BY THIS PROCESS. | |
FR2472618A1 (en) | ALUMINUM ALLOY CASTING BAR FOR WORK PRODUCTS HAVING IMPROVED MECHANICAL PROPERTIES AND WORKABILITY, AND METHOD OF MANUFACTURING THE SAME | |
FR2808536A1 (en) | Production of a semi-molten billet of aluminum alloy for use as a transport unit by introducing a work distortion by cold forging | |
CA2244145C (en) | Metal alloy mass for semi-solid forming | |
JPH0635624B2 (en) | Manufacturing method of high strength aluminum alloy extruded material | |
FR2505877A1 (en) | METHOD FOR IMPROVING THE FORMABILITY OF ALUMINUM-MAGNESIUM-SILICON ALLOYS AND NEW ALUMINUM-MAGNESIUM-SILICON ALLOYS | |
EP3610048B1 (en) | Low-density aluminium-copper-lithium alloy products | |
JPH0340647B2 (en) | ||
EP0064468B1 (en) | Process for manufacturing foils consisting of hypoeutectic aluminium-iron alloys | |
WO1996002682A1 (en) | Hot chamber castable zinc alloy | |
FR3134119A1 (en) | Recycled 6xxx alloy sheet and manufacturing process | |
FR3132306A1 (en) | Aluminum-Copper-Lithium Alloy Enhanced Thin Sheet | |
BE517473A (en) |
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 |
|
17P | Request for examination filed |
Effective date: 19980821 |
|
AK | Designated contracting states |
Kind code of ref document: A1 Designated state(s): AT BE CH DE ES FR GB GR IT LI LU NL PT |
|
GRAG | Despatch of communication of intention to grant |
Free format text: ORIGINAL CODE: EPIDOS AGRA |
|
GRAG | Despatch of communication of intention to grant |
Free format text: ORIGINAL CODE: EPIDOS AGRA |
|
GRAH | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOS IGRA |
|
TCAT | At: translation of patent claims filed | ||
17Q | First examination report despatched |
Effective date: 19990203 |
|
DET | De: translation of patent claims | ||
GRAH | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOS IGRA |
|
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 FR GB GR IT LI LU NL PT |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: GR Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 19990818 |
|
REF | Corresponds to: |
Ref document number: 183549 Country of ref document: AT Date of ref document: 19990915 Kind code of ref document: T |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: EP |
|
REF | Corresponds to: |
Ref document number: 69700436 Country of ref document: DE Date of ref document: 19990923 |
|
ITF | It: translation for a ep patent filed |
Owner name: ING. A. GIAMBROCONO & C. S.R.L. |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: NV Representative=s name: WILLIAM BLANC & CIE CONSEILS EN PROPRIETE INDUSTRI |
|
REG | Reference to a national code |
Ref country code: ES Ref legal event code: FG2A Ref document number: 2136468 Country of ref document: ES Kind code of ref document: T3 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: PT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 19991118 |
|
RAP2 | Party data changed (patent owner data changed or rights of a patent transferred) |
Owner name: ALUMINIUM PECHINEY |
|
NLT2 | Nl: modifications (of names), taken from the european patent patent bulletin |
Owner name: ALUMINIUM PECHINEY |
|
GBT | Gb: translation of ep patent filed (gb section 77(6)(a)/1977) |
Effective date: 20000118 |
|
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 | ||
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: DE Payment date: 20010215 Year of fee payment: 5 Ref country code: AT Payment date: 20010215 Year of fee payment: 5 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: GB Payment date: 20010219 Year of fee payment: 5 Ref country code: CH Payment date: 20010219 Year of fee payment: 5 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: LU Payment date: 20010227 Year of fee payment: 5 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: FR Payment date: 20010316 Year of fee payment: 5 Ref country code: ES Payment date: 20010316 Year of fee payment: 5 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: NL Payment date: 20010330 Year of fee payment: 5 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: BE Payment date: 20010410 Year of fee payment: 5 |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: IF02 |
|
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: 20020312 Ref country code: GB Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20020312 Ref country code: AT Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20020312 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: ES Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20020313 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: LI Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20020331 Ref country code: CH Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20020331 Ref country code: BE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20020331 |
|
BERE | Be: lapsed |
Owner name: *ALUMINIUM PECHINEY Effective date: 20020331 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: NL Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20021001 Ref country code: DE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20021001 |
|
GBPC | Gb: european patent ceased through non-payment of renewal fee |
Effective date: 20020312 |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: PL |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: FR Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20021129 |
|
NLV4 | Nl: lapsed or anulled due to non-payment of the annual fee |
Effective date: 20021001 |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: ST |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: RN |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: IC |
|
REG | Reference to a national code |
Ref country code: ES Ref legal event code: FD2A Effective date: 20030410 |
|
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 Effective date: 20050312 |