EP1680246A1 - Procede de production de materiaux composites a base de matrice metallique - Google Patents

Procede de production de materiaux composites a base de matrice metallique

Info

Publication number
EP1680246A1
EP1680246A1 EP04765979A EP04765979A EP1680246A1 EP 1680246 A1 EP1680246 A1 EP 1680246A1 EP 04765979 A EP04765979 A EP 04765979A EP 04765979 A EP04765979 A EP 04765979A EP 1680246 A1 EP1680246 A1 EP 1680246A1
Authority
EP
European Patent Office
Prior art keywords
metal
magnesium
composite material
matrix composite
matrix
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
Application number
EP04765979A
Other languages
German (de)
English (en)
Other versions
EP1680246B1 (fr
Inventor
Florian Moll
Lutz Oemisch
Ulrich Bischofberger
Karl Ulrich Prof. Dr.-Ing. Kainer
Norbert Hort
Hajo Dieringa
Hagen Frank
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Mahle GmbH
Original Assignee
Mahle GmbH
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Mahle GmbH filed Critical Mahle GmbH
Publication of EP1680246A1 publication Critical patent/EP1680246A1/fr
Application granted granted Critical
Publication of EP1680246B1 publication Critical patent/EP1680246B1/fr
Expired - Fee Related legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
    • B22D21/02—Casting exceedingly oxidisable non-ferrous metals, e.g. in inert atmosphere
    • B22D21/04—Casting aluminium or magnesium
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D17/00—Pressure die casting or injection die casting, i.e. casting in which the metal is forced into a mould under high pressure
    • B22D17/007—Semi-solid pressure die casting
    • 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
    • C22C1/10—Alloys containing non-metals
    • C22C1/1036—Alloys containing non-metals starting from a melt
    • 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
    • C22C1/10—Alloys containing non-metals
    • C22C1/1036—Alloys containing non-metals starting from a melt
    • C22C1/1047—Alloys containing non-metals starting from a melt by mixing and casting liquid metal matrix composites
    • C22C1/1052—Alloys containing non-metals starting from a melt by mixing and casting liquid metal matrix composites by mixing and casting metal matrix composites with reaction
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C23/00—Alloys based on magnesium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
    • C22C32/0078—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only silicides

Definitions

  • the present invention relates to a method for producing metal-matrix composite materials comprising at least a proportion of magnesium or a magnesium alloy and at least one production step in which thixomolding takes place.
  • the material magnesium cannot easily be used for certain applications, such as pistons in motor vehicle engines or other aggregate components, especially engines.
  • the properties mentioned can be positively influenced by reinforcing the material by means of a second, usually significantly firmer and harder phase. Ceramic or carbon-based short or long fibers or particles are usually used for this. In melt-metallurgical production, these can either be introduced in the form of a porous molded body (so-called prefomn), which is infiltrated with molten metal, or, in the case of particles, can also be introduced into the metallic matrix by stirring. Another possibility for reinforcing a metallic material with fibers or particles is to form the reinforcing component itself or also “in situ”. In addition to the melt metallurgical processes mentioned, metallic composite materials can also be produced by powder metallurgy.
  • squeeze casting When using preforms as infiltrable moldings, squeeze casting has established itself as the preferred casting method.
  • the molten metal is pressed into the porous fiber or particle body at somewhat lower mold filling speeds, but somewhat higher pressures than in conventional die casting. This creates an almost pore-free composite with closed fiber-matrix connections.
  • Ceramic particles When stirring in, ceramic particles are usually supplied as a loose bed of the moving metal melt by trickling or blowing.
  • Composite melts of this type can be cast directly in the form of castings or bars.
  • the composite material In the in situ process, the composite material is created by a reaction between two or several alloy elements of the metallic matrix or phases of the overall system, usually with the formation of a new, usually intermetallic phase.
  • Mg-Mg 2 Si The production and characterization of the Mg-Mg 2 Si system has been described several times. For example, reference is made to the disclosure of DE 41 25 014 A1.
  • the emergence of the intermetallic phase in terms of reinforcement can be assigned to the in-situ process. This is usually done by infiltration of Si pre-containing fiber preforms or by excretion of primary magnesium silicide from hypereutectic Mg-Si alloys. While the primary coarse withdrawal after falling below the liquidus line, block-shaped Mg 2 Si precipitates form, the Mg of pure Si 2 Si formed at the reactive conversion in a preform globular one. Mg 2 Si which is ectectically excreted usually shows the characteristic "Chinese script" structure.
  • the metallic material is fed as granulate to the thixomolding machine and moved in the direction of the spray nozzle inside a heated cylinder by a screw conveyor.
  • the temperature which lies between the liquidus and solidus temperature of the metal, it partially liquefies, while the remaining solid portion is globular.
  • the behavior of the thixotropic material is pseudoplastic, which means that the viscosity decreases with increasing shear.
  • Thixomolding is particularly suitable for the manufacture of very thin-walled components with a high degree of dimensional accuracy, since the favorable temperature level between the liquidus and solidus means that there are hardly any signs of shrinkage and distortion.
  • the infiltration ability of preforms with high fiber and particle contents in classic die casting is not readily available, the method of squeeze casting is preferably used for this, which in turn requires special casting systems.
  • the difficulties that can arise with die-cast infiltration are primarily due to the high filling speed of the process and the low pressure that can be exerted on the melt due to the small gate. However, this is required in order to overcome the normally very low tendency towards wetting between the metallic melt and the ceramic molded body.
  • the preform must be heated significantly above the melt temperature in order to avoid premature solidification of the melt on the fiber body.
  • the method of stirring is primarily reserved for the particulate reinforcements, since the use of fibers can lead to a sharp increase in the viscosity of the melt, which makes homogeneous distribution of the fibers very difficult or even impossible.
  • the stirring result depends on the particle size used, the stirrer speed and the temperature. Inadequate choice of parameters can lead to clumping, flushing of the particles into the slag or their sedimentation on the crucible bottom. If the particles and the melt are a reactive system, reaction reactions may occur at the interfaces due to the long contact time between the two phases, which damage the particles.
  • An example of this is the magnesium-aluminum oxide system, where magnesium oxide and aluminum are formed during the reaction between the two partners with the decomposition of the particle substance.
  • the object of the present invention is to provide a method for producing metal-matrix composites of the type mentioned at the outset, which enables the production of light-metal composites, in particular for use in components subject to high temperatures, which is more variable and less expensive than previously is known method and avoids the disadvantages associated with these.
  • the solution to this problem is provided by a method according to the invention for producing metal-matrix composite materials of the type mentioned at the outset with the characterizing features of claim 1.
  • the light-metal composite material is produced using the thixomolding method, with a Mg 2 Si Phase with a volume content of at least 2% is stored.
  • the particular advantages of the method according to the present invention result from the combination of the thixomolding method with the method for the in-situ production of a metallic composite material.
  • Mg-Mg 2 Si composite materials with a volume content of at least 2% Mg 2 Si are to be produced, preferably by adding a granulate of silicon or a silicon alloy and a granulate of magnesium or a magnesium alloy together to the thixomolding process and there under Shear form an at least partially liquid melt that solidifies in the form of a magnesium body.
  • Advantages of the process are the wide range of the adjustable volume contents of Mg 2 Si, the possibility to do without fiber or particle preforms and the quantity and size of the Si particles determine the quantity and size of the Mg 2 Si crystals that form to be able to individually change properties such as the thermal expansion coefficient, the modulus of elasticity, the tensile and elastic limit and the wear behavior. In this way, Si contents can be set that cannot be produced by melt metallurgy. The material cast in this way can be fed to subsequent forming operations, such as a forging process.
  • a cast body is preferably produced from the metal-matrix composite material, which is then processed further.
  • the cast body is subsequently formed in at least one process step.
  • Such a forming process can include, for example, at least one forging process.
  • the present invention furthermore relates to metal-matrix composite materials which have been produced by the process according to the invention.
  • the present invention furthermore relates to the use of metal-matrix composite materials produced by a method having the features of one of claims 1 to 11 for the production of components for motor vehicles.
  • These are preferably motor vehicle components made of light metal composites which are exposed to high temperature loads, for example engine parts such as pistons or the like.
  • Metal-matrix composite materials that were produced by the method according to the invention can be used, for example, for the production of pistons or other engine parts for engines operated with diesel fuel or gasoline fuel.
  • the metal-matrix composite materials are furthermore suitable, for example, for the production of liners for shafts, cylinders and other rotationally symmetrical parts, in particular in engines. They are also suitable for the production of other motor vehicle parts subject to wear, such as brake discs.
  • the volume content of the Mg 2 Si phase in the metal matrix is preferably in the range between about 5 and about 40 percent by volume receive an addition of Si.
  • the reaction 2 Mg + Si - Mg 2 Si is essential.
  • an addition of at least about 2 percent by weight of Si and preferably a maximum of about 15 percent by weight of Si is suitable.
  • the resulting volume percentages of Mg 2 Si are listed in Table 1 below, which represent exemplary proportions of Mg 2 Si phase in the metal-matrix composite.
  • Mg 2 Si is a comparatively high-melting phase with a melting point close to 1,100 ° C. This phase is therefore suitable as a reinforcement to improve the high-temperature properties of the matrix material. This applies to creep behavior as well as parameters such as thermal conductivity and thermal expansion coefficient. In addition to other physical and mechanical properties, these values can be set specifically for an application. The exact numerical values depend, among other things, on the base alloy, the volume fraction of Mg 2 Si, further precipitations in the matrix alloy, and also on the operating temperature or the operating temperature range. These data are to be determined experimentally for the respective application.
  • Mg 2 Si precipitates Another influencing factor is the form of the Mg 2 Si precipitates. They are usually found as so-called "Chinese script" excretions, ie as needle-shaped excretions, which are very similar in shape to Chinese characters. However, the addition of alloying elements such as Ca results in primary polygonal excretions that look like one Both types of excretion also have an effect on mechanical and physical properties.
  • the parameters selected in the further processing have a significant effect on the property profile. If reshaping takes place, for example, by extrusion, the alignment of planes of the Mg crystallites parallel to the extrusion direction leads to anisotropy.
  • the magnitude of the anisotropy depends on various factors, in particular on the forming ratio, the temperature in the tool, the preheating, heat control after pressing and thus the dynamic and static recrystallization.
  • the alloy composition including the influence of impurities is also an influencing factor.
  • the temperature control in the production of metal matrix composites by the method according to the invention is directly related to the selected alloy, the shot weight and the tool, in particular its component geometry, sprue etc., the geometry of the screw and cylinder during thixomolding, the feed rate and also the shooting speed. These parameters must be determined empirically for each component and are also dependent on the type of machine and its data profile. Similarly, the properties also depend on the solid phase component. This influences the mechanical properties of the matrix alloy alone as well as that of the composite material, i.e. H. the combination of matrix and reinforcement.
  • the reaction 2 Mg + Si ⁇ Mg 2 Si means that although the alloys build up a high proportion of the liquid phase more quickly, an increase in the solid phase due to the formation of Mg 2 Si occurs at the same time.
  • the reaction not only takes place in the cylinder screw area of the Thixomolding machine, but can also take place in the workpiece after casting. This behavior can be expected especially in areas with material accumulations. Under certain circumstances, a reprint can therefore be applied more successfully, since the exothermic reaction means that some of the matrix alloy is still in the molten phase. Conclusions can be drawn from this by examining metallographic sections.
  • the melting interval plays a major role.
  • the AZ91 alloy is listed, whose melting range is in the range from 440 to 600 ° C. It is known from the literature that for this alloy a high proportion of liquid phase in the range of 95% leads to an improvement in the mechanical properties in the component. With such a liquid phase component, one can speak of an undercooled melt. After injection into the tool, the result of the method according to the invention is therefore a high nucleation rate with a very high number of germs. This leads to the development of a very fine structure, which has very good mechanical properties due to the Hall-Petsch relationship. Due to the subcooling of the melt, the overall shrinkage is very low. The lower the proportion of liquid phase, the lower it is.
  • the grain size of the granules is usually not a determining size. Depending on the machine and the selected component, a different screw geometry can then be selected. The grain size and the grain shape must be matched to the screw geometry. This is completely independent of the alloy or the composite material. The grain size ratio Mg-Si must then be coordinated. However, this is usually only useful for a previously defined screw geometry.
  • Granules can be added, for example, by means of a simple conveyor device at the same time or shortly after the granules are fed (both materials are still solid), which can also be attached to the machine.
  • a machine of conventional design can be used, such as is available on the market from the companies Thixomat or Japan Steel Works.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Composite Materials (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Manufacture Of Alloys Or Alloy Compounds (AREA)
  • Powder Metallurgy (AREA)

Abstract

L'invention concerne un procédé permettant de produire des matériaux composites à base de matrice métallique, comprenant au moins une proportion de magnésium ou d'un alliage de magnésium, ainsi qu'au moins une étape de production, dans laquelle s'effectue un thixomoulage. Selon l'invention, une phase Mg2Si à teneur volumétrique d'au moins 2 % est intégrée dans une matrice métallique comprenant de préférence du magnésium ou un alliage de magnésium. Le procédé selon l'invention utilise la méthode du thixomoulage pour produire in situ un matériau composite métallique et présente l'avantage qu'il se produit une grande variation des teneurs volumétriques ajustables de la phase Mg2Si dans le matériau composite, ce qui permet d'effectuer des modifications individuelles du matériau composite. Ledit matériau composite à base de matrice métallique selon l'invention s'utilise notamment pour produire des éléments d'automobiles, sollicités en température, comme par exemple des pistons ou similaires.
EP04765979A 2003-11-07 2004-10-16 Procede de production de materiaux composites a base de matrice metallique Expired - Fee Related EP1680246B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE10352453A DE10352453A1 (de) 2003-11-07 2003-11-07 Verfahren zur Herstellung von Metall-Matrix-Verbundwerkstoffen
PCT/EP2004/011688 WO2005046911A1 (fr) 2003-11-07 2004-10-16 Procede de production de materiaux composites a base de matrice metallique

Publications (2)

Publication Number Publication Date
EP1680246A1 true EP1680246A1 (fr) 2006-07-19
EP1680246B1 EP1680246B1 (fr) 2007-07-11

Family

ID=34530186

Family Applications (1)

Application Number Title Priority Date Filing Date
EP04765979A Expired - Fee Related EP1680246B1 (fr) 2003-11-07 2004-10-16 Procede de production de materiaux composites a base de matrice metallique

Country Status (7)

Country Link
US (1) US8282748B2 (fr)
EP (1) EP1680246B1 (fr)
JP (1) JP4444963B2 (fr)
KR (1) KR101110947B1 (fr)
CN (1) CN100402191C (fr)
DE (2) DE10352453A1 (fr)
WO (1) WO2005046911A1 (fr)

Families Citing this family (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US6973955B2 (en) 2003-12-11 2005-12-13 Novelis Inc. Heated trough for molten metal
US8715066B2 (en) 2010-06-14 2014-05-06 Automated Cash Systems, Llc System and method for electronic fund transfers for use with gaming systems
US9728039B2 (en) * 2010-06-14 2017-08-08 Automated Cash Systems, Inc. Enabling financial transactions for electronic gaming machines
US20140023547A1 (en) * 2011-04-08 2014-01-23 Stu Co., Ltd. Magnesium alloy chips and process for manufacturing molded article using same
CN103045891B (zh) * 2013-01-04 2015-03-11 南昌大学 一种原位Al2Y颗粒增强镁基复合材料的制备方法
US11410499B2 (en) * 2014-05-13 2022-08-09 Automated Cashless Systems, Inc. Financial gaming passport for cashless mobile gaming
US11508213B2 (en) * 2014-05-13 2022-11-22 Automated Cashless Systems, Inc. Enabling financial transactions for electronic gaming machines
CN104148608B (zh) * 2014-08-06 2018-08-03 南昌大学 一种基于超声制备半固态Mg2Si颗粒增强Mg-Al-Mn复合材料流变模型的建立方法
AT518825A1 (de) * 2016-05-31 2018-01-15 Lkr Leichtmetallkompetenzzentrum Ranshofen Gmbh Verfahren zur Herstellung eines Profils aus einer Metalllegierung
US11908277B2 (en) * 2021-05-24 2024-02-20 Automated Cashless Systems, Inc. Financial gaming passport for cashless mobile gaming

Family Cites Families (15)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3415697A (en) * 1965-01-08 1968-12-10 Reynolds Metals Co Method and composition for exothermic fluxless brazing of aluminum and aluminum base alloys
JP2780778B2 (ja) * 1988-03-04 1998-07-30 水澤化学工業株式会社 チクソトロピー的性質付与剤
DE4125014A1 (de) * 1990-09-22 1992-03-26 Metallgesellschaft Ag Bauteile fuer motoren und fahrzeuge
JPH04231168A (ja) 1990-12-28 1992-08-20 Toyota Central Res & Dev Lab Inc 金属基複合材料の製造方法
JPH0681068A (ja) * 1992-09-01 1994-03-22 Honda Motor Co Ltd 耐熱Ｍｇ合金の鋳造方法
US5902424A (en) * 1992-09-30 1999-05-11 Mazda Motor Corporation Method of making an article of manufacture made of a magnesium alloy
JP2981977B2 (ja) 1995-10-09 1999-11-22 本田技研工業株式会社 チクソキャスティング法
EP0773302B1 (fr) * 1995-10-09 2002-07-31 Honda Giken Kogyo Kabushiki Kaisha Procédé de coulée de gelées métalliques
JP4352472B2 (ja) 1998-06-26 2009-10-28 株式会社豊田中央研究所 マグネシウム基複合材料
JP3494020B2 (ja) * 1998-07-03 2004-02-03 マツダ株式会社 金属の半溶融射出成形方法及びその装置
DE10135198A1 (de) * 2001-07-19 2003-02-06 Bayerische Motoren Werke Ag Verfahren und Vorrichtung zum Thixospritzgießen metallischen Materials und Anwendung des Verfahrens
WO2003027341A1 (fr) 2001-09-25 2003-04-03 Center For Advanced Science And Technology Incubation, Ltd. Materiau composite a base de magnesium
WO2003027342A1 (fr) * 2001-09-25 2003-04-03 Center For Advanced Science And Technology Incubation, Ltd. Materiau composite a base de magnesium
JP2003211260A (ja) 2002-01-18 2003-07-29 Sodick Plastech Co Ltd 軽金属材料の射出方法および軽金属射出成形機の射出装置
US7052526B2 (en) * 2002-02-15 2006-05-30 Toudai Tlo, Ltd. Magnesium base composite material and its manufacturing method

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See references of WO2005046911A1 *

Also Published As

Publication number Publication date
CN1863626A (zh) 2006-11-15
KR20070008518A (ko) 2007-01-17
CN100402191C (zh) 2008-07-16
DE502004004318D1 (de) 2007-08-23
US20070104606A1 (en) 2007-05-10
JP2007510545A (ja) 2007-04-26
US8282748B2 (en) 2012-10-09
WO2005046911A1 (fr) 2005-05-26
JP4444963B2 (ja) 2010-03-31
EP1680246B1 (fr) 2007-07-11
KR101110947B1 (ko) 2012-02-20
DE10352453A1 (de) 2005-06-02

Similar Documents

Publication Publication Date Title
DE112005000511B4 (de) Magnesiumknetlegierung mit verbesserter Extrudierbarkeit und Formbarkeit
EP1978120B1 (fr) Alliage de fonte, d'aluminium et de silice et son procédé de fabrication
DE102016103261B4 (de) Verfahren zum Bilden einer gegossenen Kraftfahrzeugkomponente
DE3817350C2 (fr)
DE69921925T2 (de) Hochfeste Aluminiumlegierungsschmiedestücke
DE112010002575B4 (de) Recycelte Magnesiumlegierung, Verfahren zur Verbesserung der Korrosionsbeständigkeit einer recycelten Magnesiumlegierung und Magnesiumlegierung
DE60100370T2 (de) Druckgussmagnesiumlegierung
DE102016210354A1 (de) Verfahren zum herstellen von aluminium- oder magnesiumbasierten verbundwerkstoff-motorblöcken oder anderen teilen mit in situ geformten verstärkten phasen durch squeeze-casting oder halbfeste metallumformung und post-wärmebehandlung
DE102016118729A1 (de) Ein neues Hochdruck-Spritzgussverfahren für Aluminiumlegierungen für Anwendungen bei hoher Temperatur und in korrosiver Umgebung
DE102009015316B4 (de) Metallbehandlung zur Eliminierung von Warmrissdefekten in Aluminiumlegierungen mit niedrigem Siliziumgehalt
WO2008138614A1 (fr) UTILISATION D'UN ALLIAGE Al-Mn POUR DES PRODUITS RÉSISTANTS AUX HAUTES TEMPÉRATURES
WO2017076801A1 (fr) Procédé de fabrication d'un élément en fonte de métal léger et élément en fonte de métal léger
DE3344450C2 (fr)
DE102009036056A1 (de) Al-Druckgusslegierung für dickwandige Druckgussteile
DE102019130108A1 (de) Verfahren zur Herstellung eines Aluminiumgussteils und hierdurch hergestelltes Aluminiumgussteil
EP1680246B1 (fr) Procede de production de materiaux composites a base de matrice metallique
DE60114281T2 (de) Guss- und Schmiedprodukt unter Verwendung einer Kupfer-basis Legierung
EP1407056B1 (fr) Procede de production d'une piece moulee realisee en matiere gamma-ti-al intermetallique
WO2005045081A1 (fr) Alliage d'aluminium, composant realise avec cet alliage et procede de production de ce composant
DE60316679T2 (de) Bremsprodukt, Bremssystem und Verfahren zur deren Herstellung
EP1012353B1 (fr) Alliage et procede de production d'objets a partir de cet alliage
DE3835253A1 (de) Gegenstand aus einer aluminium-silizium-legierung und verfahren zu seiner herstellung
EP1611980A1 (fr) Procédé de production d'un affineur de grains pour métaux, affineur de grains et métal ou alliage métallique
DE102014002583B3 (de) Verfahren zur Herstellung eines verschleißbeständigen Leichtmetall-Bauteils
DE2929812C2 (de) Rad für Kraftfahrzeuge

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: 20060327

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): DE FR GB IT

17Q First examination report despatched

Effective date: 20060914

DAX Request for extension of the european patent (deleted)
RBV Designated contracting states (corrected)

Designated state(s): DE FR GB IT

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): DE FR GB IT

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

Free format text: NOT ENGLISH

REF Corresponds to:

Ref document number: 502004004318

Country of ref document: DE

Date of ref document: 20070823

Kind code of ref document: P

GBT Gb: translation of ep patent filed (gb section 77(6)(a)/1977)

Effective date: 20071008

ET Fr: translation filed
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

Effective date: 20080414

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 12

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: GB

Payment date: 20151022

Year of fee payment: 12

Ref country code: IT

Payment date: 20151030

Year of fee payment: 12

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FR

Payment date: 20151022

Year of fee payment: 12

REG Reference to a national code

Ref country code: DE

Ref legal event code: R119

Ref document number: 502004004318

Country of ref document: DE

Ref country code: DE

Ref legal event code: R409

Ref document number: 502004004318

Country of ref document: DE

REG Reference to a national code

Ref country code: DE

Ref legal event code: R082

Ref document number: 502004004318

Country of ref document: DE

Ref country code: DE

Ref legal event code: R081

Ref document number: 502004004318

Country of ref document: DE

Owner name: VOLKSWAGEN AG, DE

Free format text: FORMER OWNERS: VOLKSWAGEN AG, 38440 WOLFSBURG, DE; MAHLE GMBH, 70376 STUTTGART, DE

REG Reference to a national code

Ref country code: DE

Ref legal event code: R409

Ref document number: 502004004318

Country of ref document: DE

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20161016

REG Reference to a national code

Ref country code: FR

Ref legal event code: ST

Effective date: 20170630

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: 20161102

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20161016

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: 20161016

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 20201031

Year of fee payment: 17

REG Reference to a national code

Ref country code: DE

Ref legal event code: R119

Ref document number: 502004004318

Country of ref document: DE

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: DE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20220503