EP1012353B1 - Alliage et procede de production d'objets a partir de cet alliage - Google Patents

Alliage et procede de production d'objets a partir de cet alliage Download PDF

Info

Publication number
EP1012353B1
EP1012353B1 EP98945174A EP98945174A EP1012353B1 EP 1012353 B1 EP1012353 B1 EP 1012353B1 EP 98945174 A EP98945174 A EP 98945174A EP 98945174 A EP98945174 A EP 98945174A EP 1012353 B1 EP1012353 B1 EP 1012353B1
Authority
EP
European Patent Office
Prior art keywords
silicon
particles
alloy
aluminium
hot
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
Application number
EP98945174A
Other languages
German (de)
English (en)
Other versions
EP1012353A1 (fr
Inventor
Dieter Brungs
Heinrich Fuchs
Meinolf Hengesbach
Franz Reinken
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.)
Honsel Werke AG
Original Assignee
Honsel Werke AG
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
Priority claimed from DE19801941A external-priority patent/DE19801941A1/de
Application filed by Honsel Werke AG filed Critical Honsel Werke AG
Publication of EP1012353A1 publication Critical patent/EP1012353A1/fr
Application granted granted Critical
Publication of EP1012353B1 publication Critical patent/EP1012353B1/fr
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/10—Sintering only
    • B22F3/11—Making porous workpieces or articles
    • B22F3/1121—Making porous workpieces or articles by using decomposable, meltable or sublimatable fillers
    • B22F3/1125—Making porous workpieces or articles by using decomposable, meltable or sublimatable fillers involving a foaming process
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/115—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by spraying molten metal, i.e. spray sintering, spray 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
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/0408—Light metal alloys
    • C22C1/0416—Aluminium-based 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
    • C22C1/10—Alloys containing non-metals
    • C22C1/1036—Alloys containing non-metals starting from a melt
    • C22C1/1042—Alloys containing non-metals starting from a melt by atomising
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • 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
    • 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
    • C22C32/0052—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 carbides
    • C22C32/0063—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 carbides based on SiC
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent

Definitions

  • the invention relates to the use of an alloy with a proportion of Particles and a method of making articles from such an alloy, especially with a Wear resistance increasing addition of particles in one Aluminum alloy.
  • Aluminum alloys with a wear resistance increasing proportion of particles, in particular in the form of Silicon primary crystals are, for example, as Hypereutectic aluminum-silicon casting alloys known. From this, z. B. whole engine blocks or just Pour cylinder liners. When cooling, they separate Silicon primary crystals. The wear resistance z. B. the tread is excreted by the harder Silicon primary crystals achieved by special Treatment processes, especially etching processes superficial be exposed.
  • a disadvantage of these is hypereutectic Aluminum-silicon casting alloys that the Silicon primary crystals in the form of sharp-edged, in part needle-like crystals and in different, from the Solidification rate depending on size and distribution are available, so that the mechanical processing special tools required to get through the hard silicon primary crystals keep conditional wear within limits.
  • These hypereutectic aluminum-silicon alloys and the Manufacturing processes for cylinder liners are in the German patent 43 28 619 and the German Laid-open specification 44 38 550.
  • hypereutectic Aluminum-silicon alloy is manufactured both at Spray compacting a hypereutectic Aluminum-silicon alloy as well powder metallurgical process disadvantageous that complete made of a hypereutectic aluminum-silicon alloy existing ingots are difficult to deform and due to the precipitated silicon primary crystals and intermetallic phases high tool wear cause.
  • the invention is based on the problem, a aluminum alloy to use the the avoids disadvantages mentioned, d. H. the easy, in particular can be processed and machined by hot forming and / or machining and is still the one required, for example Wear resistance and / or uniform structure and has mechanical strength.
  • an aluminum alloy is used, the in a matrix of an easily editable and editable Aluminum alloy an addition of evenly distributed Particles, preferably silicon particles or of particles a hypereutectic aluminum-silicon alloy, whereby the individual particles have high silicon contents, preferably have up to 50 wt .-%, the silicon content in the good machinable and editable aluminum alloy, however maximum Is 12% by weight.
  • the invention is based on the consideration that in itself an aluminum melt easily soluble silicon on it must be prevented from going into solution in the matrix because when silicon primary crystals are separated from the solution the relatively large increase the wear Crystals with angular and needle-like shapes are created. So it becomes a well machinable and editable aluminum alloy so with evenly distributed silicon particles and / or with particles of a hypereutectic Aluminum-silicon alloy mixed that undissolved silicon particles and / or silicon primary crystals in the Particles of the hypereutectic aluminum-silicon alloy can remain in the aluminum alloy originally introduced in the easily editable and editable Aluminum alloy matrix not in solution Silicon particles or Silicon primary crystals are not the same as for Crystallizing, unfavorable forms but keep their original shape or become even rounded off if necessary by superficial dissolving, so that they lose their distinctive tips and corners.
  • the matrix from the well machinable and editable aluminum alloy like this is composed that none of this aluminum alloy Silicon primary crystals can crystallize and that finely divided silicon particles or Particles containing silicon primary crystals hypereutectic aluminum-silicon alloy without in the Matrix alloy have gone into solution.
  • the matrix alloy does not need as a whole to be hypereutectic to contain silicon particles, such as this with the known, wear-resistant Aluminum-silicon alloys is required but can preferably an addition of a maximum of 12% by weight of silicon in Form of silicon particles and / or silicon primary crystals in the particles of the hypereutectic Aluminum-silicon alloy included, provided that too contains an processed aluminum alloy a minimum proportion of silicon particles and / or Particles containing silicon primary crystals hypereutectic aluminum-silicon alloy, at least 5% by weight of silicon particles and / or Silicon primary crystals in the particles of the hypereutectic Aluminum-silicon alloy based on the total amount, because it was found that such a proportion did not derive from the Matrix alloy deposited silicon particles, or Silicon primary crystals suffice to get the desired one Achieve wear resistance.
  • the proportion of silicon particles in the matrix alloy is preferably 5 to 20%.
  • the matrix alloy can preferably be used as a hot-formable Wrought aluminum alloy a composition of the type Have AlMgSiCu and with an addition of even distributed silicon particles and / or particles of one hypereutectic aluminum-silicon alloy of less than 20 wt .-% based on the total amount before one Be thermoformed.
  • the wrought aluminum alloys are good thermoformable alloys, their Not even hot formability by adding Silicon particles or particles of a hypereutectic Aluminum-silicon alloy is lost. This addition of evenly distributed silicon particles or of particles a hypereutectic aluminum-silicon alloy can be relatively high, especially if part of it Silicon particles or the particles of a hypereutectic Aluminum-silicon alloy during hot forming and / or heat treatment goes into solution.
  • the grain size of the silicon particles in the aluminum alloy is preferably at most 80 microns, the grain size of Particles of a hypereutectic aluminum-silicon alloy is preferably at most 250 microns while the Silicon primary crystals in the particles of the hypereutectic Aluminum-silicon alloy is at most 20 ⁇ m.
  • the object can after the cutting deformation or the Thermoforming be subjected to a heat treatment. It it is conceivable that this heat treatment can lead to the fact that the silicon particles embedded in the aluminum alloy and / or the particles and those contained therein Silicon primary crystals of the hypereutectic Aluminum-silicon alloy superficially with the Aluminum alloy react, creating distinctive tips and Corners are removed. This effect can already be seen in Spray compacting, with the temperature of one Aluminum alloy melt begins to be achievable. As well hot forming alone can be the desired one Change in the surface of the silicon particles and / or Silicon primary crystals in the particles of one cause hypereutectic aluminum-silicon alloy.
  • Powder metallurgy allows aluminum alloys any composition from a mixture of powders various alloy components to manufacture by a subsequent hot forming can be homogenized.
  • Silicon particles and / or particles of a hypereutectic Aluminum-silicon alloy based on a maximum of 12 wt .-% added to the total amount, so the Silicon particles or the particles of a hypereutectic Aluminum-silicon alloy in the subsequent Hot working, as described above, evenly distributed and possibly superficially dissolved or partially dissolved so that in the thermoformed object finally at least 5% by weight based on the Total amount evenly distributed, not dissolved Silicon particles and / or silicon primary crystals in the Particles of a hypereutectic aluminum-silicon alloy are present that are not the tips and corners of one hypereutectic alloy melt excreted Have silicon primary crystals, but in the same way bring about the wear resistance of the aluminum alloy, which in this case is considered to be thermoformable Wrought aluminum alloy with the composition AlMgSiCu is trained.
  • the hot forming of the ingot or compact can, for. B. by Hot rolling or by hot extrusion into bars, tubes and profiles or by hot extrusion, one If necessary, subsequent heat treatment serves to desired properties of the aluminum alloy adjust.
  • heat-formable aluminum alloy is suitable from hot rolled plates or to produce hot extruded rods and slugs through hot extrusion finished products such as cylinder liners to manufacture in the required final dimensions.
  • a compact i.e. H. a slug in shape a round or a hollow round of powder
  • Manufacture hydrostatic pressing that warmed up and afterwards is deformed by extrusion. Possibly. can one Connect heat treatment.
  • Another way to make bars or cylinders consists of a powder with alloy components or the alloy and silicon particles and / or particles one hypereutectic aluminum-silicon alloy into a shape too fill and at such pressure and such Sinter temperature that the required strength is reached and the minimum amount of silicon particles or Silicon primary crystals in the particles of one hypereutectic aluminum-silicon alloy is present. In this case too, there may be another Connect heat treatment.
  • the silicon particles or the particles of a hypereutectic aluminum-silicon alloy preferably with a hypoeutectic portion of the matrix alloy add if it is ensured that a silicon portion in the form of silicon particles and / or Silicon primary crystals in the particles of one hypereutectic aluminum-silicon alloy, in the amount of 5 wt .-% based on the total amount preserved.
  • any alloy compositions are possible, to which the Silicon particles or the particles of a hypereutectic Aluminum-silicon alloy in the manner according to the invention be added without going completely into solution, so that these added silicon particles or the particles of a hypereutectic aluminum-silicon alloy or the therein existing silicon primary crystals undissolved in the Matrix alloy are preserved and therefore none Silicon primary crystals excreted from the matrix alloy become.
  • This is in contrast to the known ones hypereutectic alloys, in which when cooling from the Melt silicon primary crystals that are excreted have an angular or angular and needle-like shape.
  • the hypereutectic alloys one Heat treatment for grain enlargement with needle formation leads, which is unfavorable for wear.
  • those of the matrix alloy are in accordance with the invention added silicon particles or particles of a hypereutectic aluminum-silicon alloy at most superficially dissolved and retained during one Heat treatment largely its original shape even then, if the silicon content in the form of silicon particles and / or Silicon primary crystals in the particles of one hypereutectic aluminum-silicon alloy no more than 12 wt .-% based on the total amount, corresponding to the Eutectic aluminum-silicon.
  • Wear-resistant cylinder liners can be easily cast Aluminum alloy used for casting cylinder blocks is particularly suitable and easy to edit, pour in, post-processing the cast Cylinder liners may no longer be required if these made from hot-rolled or hot-extruded primary material and slugs made from it by hot extrusion are manufactured.
  • a sufficient combination of materials between the Cast aluminum alloy for the cylinder block and the cast cylinder liners according to the invention can be with the in the German patent 43 28 619 achieve described methods without significant Disadvantages when using powder metallurgy produced ingots or compacts, which subsequently were thermoformed.
  • the possibly required surface treatment of the cylinder liners etching does not change the dimensional accuracy, but rather only serves to round the silicon particles or Silicon primary crystals from the added particles of one to expose hypereutectic aluminum-silicon alloy.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Powder Metallurgy (AREA)
  • Manufacture Of Alloys Or Alloy Compounds (AREA)
  • Coating By Spraying Or Casting (AREA)

Claims (9)

  1. Utilisation d'un alliage d'aluminium d'une matrice d'alliage d'aluminium corroyé facilement déformable à chaud du type Al Mg Si Cu avec une composition à partir de laquelle aucun cristal primaire de silicium ne peut se séparer à l'état cristallin, avec un additif augmentant la résistance à l'usure de particules de silicium réparties uniformément et/ou de particules d'un alliage d'aluminium-silicium hypereutectique pour la fabrication de chemises de cylindres proches de la cote finale ainsi que de cylindres hydrauliques ou pneumatiques par extrusion à chaud, moyennant quoi les particules individuelles ont des teneurs élevées en silicium, atteignant de préférence 50% en poids, et l'additif représente au maximum 12% en poids du silicium sous forme de particules de silicium et/ou de cristaux primaires de silicium dans les particules de l'alliage d'aluminium-silicium hypereutectique, alors que l'alliage d'aluminium usiné pour faire l'objet contient, après la déformation à chaud ou après un traitement thermique ultérieur, une portion minimale de particules de silicium qui n'ont pas été dissoutes et qui n'ont pas été éliminées de l'alliage de la matrice et/ou de cristaux primaires de silicium dans les particules de l'alliage d'aluminium-silicium hypereutectique d'au moins 5% en poids par rapport à la quantité totale.
  2. Utilisation de l'alliage d'aluminium selon la revendication 1, avec une taille de grain des particules de silicium de 80 µm maximum, avec la taille de grains des particules d'un alliage d'aluminium-silicium hypereutectique de 250 µm maximum de préférence et avec les cristaux primaires de silicium dans les particules de l'alliage d'aluminium-silicium hypereutectique de 20 µm maximum.
  3. Utilisation de l'alliage d'aluminium selon la revendication 1, dans laquelle une billette est fabriquée par compactage par pulvérisation d'une fonte d'un alliage d'aluminium déformable à chaud et du silicium sous forme de particules de silicium et/ou de cristaux primaires de silicium dans les particules d'un alliage d'aluminium-silicium hypereutectique est ajouté à l'alliage d'aluminium dans le jet de pulvérisation à 12% en poids maximum par rapport à la quantité totale.
  4. Utilisation de l'alliage d'aluminium déformable à chaud selon la revendication 1 ou 2, dans laquelle une billette est fabriquée à partir d'une poudre d'alliage de matrice avec un additif de particules de silicium réparties uniformément et/ou de cristaux primaires de silicium dans les particules d'un alliage d'aluminium-silicium hypereutectique de 12% en poids maximum et cette billette est ultérieurement déformée à chaud.
  5. Utilisation de l'alliage d'aluminium déformable à chaud selon la revendication 1 ou 2, dans laquelle une billette est fabriquée à partir d'un mélange de poudres de divers composants d'alliage avec un additif de particules de silicium réparties uniformément et/ou de cristaux primaires de silicium dans les particules d'un alliage d'aluminium-silicium hypereutectique de 12% en poids maximum et cette billette est ultérieurement déformée à chaud.
  6. Utilisation de l'alliage d'aluminium selon l'une des revendications 1 à 5, dans laquelle des pastilles sont fabriquées à partir de plaques laminées à chaud ou de barres extrudées à chaud et à partir desquelles les chemises de cylindres ou les cylindres hydrauliques ou pneumatiques sont fabriqués aux dimensions finales par extrusion à chaud.
  7. Utilisation de l'alliage d'aluminium selon la revendication 4 ou 5, dans laquelle une pièce pressée en forme de rond plein ou de rond creux est fabriquée à partir de poudre par compression hydrostatique, réchauffée puis usinée ultérieurement, éventuellement avec un traitement thermique ultérieur.
  8. Utilisation de l'alliage d'aluminium selon la revendication 4 ou 5, dans laquelle une poudre d'un alliage d'aluminium ou de composants d'alliage et de particules de silicium ou de particules d'un alliage d'aluminium-silicium hypereutectique est introduite dans un moule d'extrusion à chaud, soumise à une compression hydrostatique dans le moule fermé et ultérieurement extrudée à chaud après ouverture du moule.
  9. Utilisation de l'alliage d'aluminium selon la revendication 4 ou 5, dans laquelle la poudre d'un alliage d'aluminium ou de composants d'alliage et de particules de silicium et/ou de particules d'un alliage d'aluminium-silicium hypereutectique est chargée dans un moule, frittée sous pression et à température élevée et éventuellement soumise à un traitement thermique ultérieur.
EP98945174A 1997-08-30 1998-08-07 Alliage et procede de production d'objets a partir de cet alliage Expired - Lifetime EP1012353B1 (fr)

Applications Claiming Priority (5)

Application Number Priority Date Filing Date Title
DE19737957 1997-08-30
DE19737957 1997-08-30
DE19801941 1998-01-20
DE19801941A DE19801941A1 (de) 1997-08-30 1998-01-20 Legierung und Verfahren zum Herstellen von Gegenständen aus dieser Legierung
PCT/EP1998/005017 WO1999011834A1 (fr) 1997-08-30 1998-08-07 Alliage et procede de production d'objets a partir de cet alliage

Publications (2)

Publication Number Publication Date
EP1012353A1 EP1012353A1 (fr) 2000-06-28
EP1012353B1 true EP1012353B1 (fr) 2002-11-27

Family

ID=26039578

Family Applications (1)

Application Number Title Priority Date Filing Date
EP98945174A Expired - Lifetime EP1012353B1 (fr) 1997-08-30 1998-08-07 Alliage et procede de production d'objets a partir de cet alliage

Country Status (5)

Country Link
US (1) US6531089B1 (fr)
EP (1) EP1012353B1 (fr)
JP (1) JP2001515141A (fr)
AT (1) ATE228580T1 (fr)
WO (1) WO1999011834A1 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102004007704A1 (de) * 2004-02-16 2005-08-25 Mahle Gmbh Werkstoff auf der Basis einer Aluminium-Legierung, Verfahren zu seiner Herstellung sowie Verwendung hierfür

Families Citing this family (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US6761852B2 (en) * 2002-03-11 2004-07-13 Advanced Materials Technologies Pte. Ltd. Forming complex-shaped aluminum components
DE10313957A1 (de) * 2002-06-27 2004-01-22 Bwg Gmbh & Co. Kg Verfahren zum Beschichten einer Fläche eines Gleisbauteils sowie Gleisbauteil
DE10241028B3 (de) * 2002-09-05 2004-07-29 Erbslöh Ag Verfahren zur Herstellung von bogenförmigen (gerundeten) Strukturbauteilen aus einem Strangpreßprofil
US20070102071A1 (en) * 2005-11-09 2007-05-10 Bac Of Virginia, Llc High strength, high toughness, weldable, ballistic quality, castable aluminum alloy, heat treatment for same and articles produced from same
JP2008180218A (ja) * 2006-12-28 2008-08-07 Yamaha Motor Co Ltd 内燃機関用部品およびその製造方法
EP2178664A1 (fr) * 2007-07-18 2010-04-28 Alcan Technology & Management AG Matériau aluminium duplex à base d'aluminium présentant une première et une seconde phase et procédé de production d'un matériau aluminium duplex
US10718320B1 (en) * 2017-04-06 2020-07-21 Clayton Note High pressure axial piston pump with multiple discharge ports

Family Cites Families (16)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3765877A (en) * 1972-11-24 1973-10-16 Olin Corp High strength aluminum base alloy
JPS5920444A (ja) 1982-07-22 1984-02-02 Honda Motor Co Ltd 繊維強化複合部材
JPS6050138A (ja) * 1983-08-30 1985-03-19 Riken Corp 硬質粒子分散型耐熱耐摩耗性高力アルミニウム合金部材とその製造方法
JPS6050137A (ja) 1983-08-30 1985-03-19 Riken Corp 硬質粒子分散型耐熱耐摩耗性高力アルミニウム合金部材
US4969428A (en) * 1989-04-14 1990-11-13 Brunswick Corporation Hypereutectic aluminum silicon alloy
US5022455A (en) * 1989-07-31 1991-06-11 Sumitomo Electric Industries, Ltd. Method of producing aluminum base alloy containing silicon
US5366691A (en) * 1990-10-31 1994-11-22 Sumitomo Electric Industries, Ltd. Hyper-eutectic aluminum-silicon alloy powder and method of preparing the same
US5234514A (en) * 1991-05-20 1993-08-10 Brunswick Corporation Hypereutectic aluminum-silicon alloy having refined primary silicon and a modified eutectic
JP2703840B2 (ja) * 1991-07-22 1998-01-26 東洋アルミニウム 株式会社 高強度の過共晶Ａ１―Ｓｉ系粉末冶金合金
US5372775A (en) 1991-08-22 1994-12-13 Sumitomo Electric Industries, Ltd. Method of preparing particle composite alloy having an aluminum matrix
US5513688A (en) 1992-12-07 1996-05-07 Rheo-Technology, Ltd. Method for the production of dispersion strengthened metal matrix composites
US5545487A (en) * 1994-02-12 1996-08-13 Hitachi Powdered Metals Co., Ltd. Wear-resistant sintered aluminum alloy and method for producing the same
JPH08218141A (ja) 1995-02-09 1996-08-27 Mitsubishi Materials Corp 耐キャビテーション損傷性および耐摩耗性にすぐれたＡｌ合金熱間粉末鍛造部材
DE19532244C2 (de) * 1995-09-01 1998-07-02 Peak Werkstoff Gmbh Verfahren zur Herstellung von dünnwandigen Rohren (I)
US5851320A (en) * 1996-01-05 1998-12-22 Norsk Hydro, A. S. Wear-resistant aluminum alloy and compressor piston formed therefrom
DE69814498T2 (de) 1997-02-12 2003-11-20 Yamaha Motor Co Ltd Kolben für eine Brennkraftmaschine und Verfahren seiner Herstellung

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102004007704A1 (de) * 2004-02-16 2005-08-25 Mahle Gmbh Werkstoff auf der Basis einer Aluminium-Legierung, Verfahren zu seiner Herstellung sowie Verwendung hierfür
US7892482B2 (en) 2004-02-16 2011-02-22 Mahle Gmbh Material on the basis of an aluminum alloy, method for its production, as well as use therefor

Also Published As

Publication number Publication date
ATE228580T1 (de) 2002-12-15
EP1012353A1 (fr) 2000-06-28
US6531089B1 (en) 2003-03-11
WO1999011834A1 (fr) 1999-03-11
JP2001515141A (ja) 2001-09-18

Similar Documents

Publication Publication Date Title
DE3817350C2 (fr)
DE2423597A1 (de) Verbesserte aluminiumlegierungsprodukte und verfahren zu deren herstellung
DE1775322A1 (de) Gleitlager mit feinverteiltem Aluminium als Grundmaterial und Verfahren und zu dessen Herstellung
DE10232159B4 (de) Verschleißfester gestreckter Körper aus Aluminiumlegierung, Herstellungsverfahren dafür und dessen Verwendung für Kolben für eine Auto-Klimaanlage
DE3344450C2 (fr)
DE2551294B2 (de) Verfahren zur Herstellung dispersionsverfestigter Aluminiumlegierungsprodukte
DE1255928B (de) Verfahren zur Erzielung eines langanhaltenden Veredelungseffektes in Aluminium-Silicium-Legierungen
EP0554808B1 (fr) Procédé de fabrication des pièces métalliques
DE2103875A1 (de) Verfahren zur Herstellung einer Nickelbasis-Superlegierung
DE1583748A1 (de) Herstellung von poly-poroesen Mikrostrukturen
EP1012353B1 (fr) Alliage et procede de production d'objets a partir de cet alliage
DE3047524A1 (de) "aluminium-titan-bor-vorlegierung"
DE2060605A1 (de) Auf pulvermetallurgischem Wege hergestellte,gesinterte,hitze- und korrosionsbestaendige,ausscheidungshaertbare Nickel-Chrom-Legierung mit einem Gehalt an einem schwer schmelzbaren Carbid
CH623359A5 (fr)
DE2242235C3 (de) Superplastische Aluminiumlegierung
DE102012211699A1 (de) Aluminiumlegierung zum kontinuierlichen Gießen und Verfahren zum Herstellen derselben
DE19533529A1 (de) Verfahren zum Gießen eines Motorblockes aus Aluminium
WO1995005490A1 (fr) Agent de traitement d'un materiau en fusion, sa production et son utilisation
EP1680246B1 (fr) Procede de production de materiaux composites a base de matrice metallique
DE756272C (de) Verfahren zur Herstellung von Gegenstaenden aus Aluminium-Silizium-Legierungen
DE3835253A1 (de) Gegenstand aus einer aluminium-silizium-legierung und verfahren zu seiner herstellung
DE19801941A1 (de) Legierung und Verfahren zum Herstellen von Gegenständen aus dieser Legierung
EP1047803B1 (fr) Alliage d'aluminium pour palier lisse
DE10101572A1 (de) Magnesiumlegierungen mit einer ausgezeichneten Fließfähigkeit und daraus hergestellte Werkstoffe
DE3008358B1 (de) Verwendung von aus Aluminiumgusslegierungen und Aluminiumknetlegierungen vermischten Altschrotten zur Herstellung von Walzhalbzeugen

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: 20000328

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AT DE ES FR GB IE SE

RAP1 Party data changed (applicant data changed or rights of an application transferred)

Owner name: HONSEL GMBH & CO. KG

17Q First examination report despatched

Effective date: 20000912

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

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 DE ES FR GB IE SE

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

Ref country code: IE

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: 20021127

REF Corresponds to:

Ref document number: 228580

Country of ref document: AT

Date of ref document: 20021215

Kind code of ref document: T

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

Free format text: NOT ENGLISH

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

Free format text: GERMAN

REF Corresponds to:

Ref document number: 59806462

Country of ref document: DE

Date of ref document: 20030109

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

Effective date: 20030331

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 FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20030529

ET Fr: translation filed
REG Reference to a national code

Ref country code: IE

Ref legal event code: FD4D

Ref document number: 1012353E

Country of ref document: IE

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

Ref country code: AT

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

Effective date: 20030807

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: 20030828

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

Ref country code: SE

Payment date: 20110823

Year of fee payment: 14

Ref country code: GB

Payment date: 20110824

Year of fee payment: 14

Ref country code: FR

Payment date: 20110829

Year of fee payment: 14

Ref country code: DE

Payment date: 20110831

Year of fee payment: 14

REG Reference to a national code

Ref country code: SE

Ref legal event code: EUG

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

Effective date: 20120807

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

Ref country code: SE

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

Effective date: 20120808

REG Reference to a national code

Ref country code: FR

Ref legal event code: ST

Effective date: 20130430

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: 20130301

Ref country code: GB

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

Effective date: 20120807

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: 20120831

REG Reference to a national code

Ref country code: DE

Ref legal event code: R119

Ref document number: 59806462

Country of ref document: DE

Effective date: 20130301