EP1943039B1 - Procede pour produire un alliage d'aluminium resistant a l'usure, alliage d'aluminium obtenu selon ce procede et son utilisation - Google Patents

Procede pour produire un alliage d'aluminium resistant a l'usure, alliage d'aluminium obtenu selon ce procede et son utilisation Download PDF

Info

Publication number
EP1943039B1
EP1943039B1 EP06792791A EP06792791A EP1943039B1 EP 1943039 B1 EP1943039 B1 EP 1943039B1 EP 06792791 A EP06792791 A EP 06792791A EP 06792791 A EP06792791 A EP 06792791A EP 1943039 B1 EP1943039 B1 EP 1943039B1
Authority
EP
European Patent Office
Prior art keywords
alloy
casting
elements
weight
temperature
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.)
Not-in-force
Application number
EP06792791A
Other languages
German (de)
English (en)
Other versions
EP1943039A1 (fr
Inventor
Mathias Woydt
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.)
Bundesanstalt fuer Materialforschung und Pruefung BAM
Original Assignee
Bundesanstalt fuer Materialforschung und Pruefung BAM
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
Family has litigation
First worldwide family litigation filed litigation Critical https://patents.darts-ip.com/?family=37011951&utm_source=google_patent&utm_medium=platform_link&utm_campaign=public_patent_search&patent=EP1943039(B1) "Global patent litigation dataset” by Darts-ip is licensed under a Creative Commons Attribution 4.0 International License.
Application filed by Bundesanstalt fuer Materialforschung und Pruefung BAM filed Critical Bundesanstalt fuer Materialforschung und Pruefung BAM
Publication of EP1943039A1 publication Critical patent/EP1943039A1/fr
Application granted granted Critical
Publication of EP1943039B1 publication Critical patent/EP1943039B1/fr
Not-in-force legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

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
    • B22D21/002—Castings of light metals
    • B22D21/007—Castings of light metals with low melting point, e.g. Al 659 degrees C, Mg 650 degrees C
    • 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
    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/026—Alloys based on aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium

Definitions

  • the invention relates to a new use of a wear-resistant aluminum alloy.
  • Motorized bearings with sliding elements made from an aluminum base alloy are found, for example, in a piston-piston-ring-cylinder-track assembly or crankshaft-bearing shell assembly, particularly in the form of crankshaft bearing shells, cylinder liners, piston rings, pistons and valve guides.
  • the sliding surfaces of the sliding elements can also be coated or treated thermochemically. Since the thirties of the last century, cylinder liners made of eutectic AlSi alloys ("silumin”) with coarse Si primary crystals have been known and used in motor applications. These may contain up to 1.3% by weight of iron.
  • the material matrix of these concepts is based on aluminum and silicon. For the functional design of the cylinder surface, it is essential to reset the aluminum matrix by 0.5 - 2 ⁇ m by chemical or mechanical treatments of the raceways, so that the hard silicon crystals (Hv ⁇ 12 - 14 GPa) form the supporting component.
  • the hot strength of AlSi alloys can be improved by ceramic fibers, particles and / or platelets, such as AlSiMg 30% by volume SiCp (Lanxide Corp., Al-7.0Si-0.3Mg) or A359-20% by volume.
  • SiCp (p platelet) or reinforced by particles of silicon carbide, such as DURALCAN F3S.20S, 20 wt .-% SiC) or AA6061 + 40 vol .-% Al 2 O 3 (Al-1% Mg + 30 wt .-% Al 2 O 3 (PRIMEX TM).
  • DURALCAN F3S.20S 20 wt .-% SiC
  • AA6061 + 40 vol .-% Al 2 O 3 Al-1% Mg + 30 wt .-% Al 2 O 3 (PRIMEX TM).
  • piston ring wear is negatively affected by the ceramic phases.
  • K RT 16.6 mm 2 / s of a lamellar gray cast iron with 3.7% by weight C.
  • the patent US 4,948,558 discloses a fabric system AlFeXY.
  • amorphous and crystalline aluminum phases characterize the microstructure morphology of the rapidly solidified Al special alloys.
  • these heat-resistant special alloys eg. B. Al88.5 Fe8.5 V1.3 Si1.7 or Al84.5Fe7Cr6Ti2,5, technologically complex rapidly melted by melt atomization and then compacted and extruded or represented powder metallurgy.
  • the alloys have hitherto not been mentioned in connection with wear-stressed components or with "classical” casting under the influence of gravity or pressure in molds or molds.
  • the patent US 5,318,641 ALCOA discloses in the Al-Fe-Ce material system the alloy (X8019) with a tensile strength at RT of up to 1,600 MPa with crystalline nanoparticles precipitated in a partially amorphous matrix.
  • the amorphous or partially amorphous microstructure recrystallizes above 300-450 ° C (Al90.8 Fe6.2 Nb1.0 Si2.0 (at.%), At 450 ° C), thus losing the high strengths. This goes hand in hand a grain coarsening.
  • the patent application US 2003/0185701 discloses casting parameters for the Al-Fe-V-Si material system. Thereafter, the casting temperatures are 800-1,000 ° C, being poured in a preheated to 350-500 ° C mold.
  • the inoculum for grain refining consists of ⁇ 1.0 wt.% Mg / Ni.
  • a reference to tribologically stressed surfaces is neither refilled nor disclosed, nor the casting temperatures of the invention.
  • the patent application US 2004/0261916 discloses the dispersion-strengthening material system Al-Ni-Mn, wherein the alloys consisting of 0.5-6.0 wt .-% Ni and 1.0-3.0 wt .-% Mn with up to 0.3 wt .-% Zr and / or Sc can be grainfilled.
  • a reference to tribologically stressed surfaces is neither refilled nor disclosed.
  • the dispersion strengthening system discloses Al + ⁇ 11 wt.% (Mg, Li, Si, Ti, Zr) which is enriched by cryogenic milling with up to 0.3 wt.% nitrogen.
  • Mg Li, Si, Ti, Zr
  • This will be pipes in US 2004/0255460 manufactured for the management of cryogenic media.
  • Reference to casting technologies or tribologically stressed surfaces is neither refilled nor disclosed. Sahoo, et al., Materials Science and Engineering, 2003, A355, pp. 193-200 , describe the formation of intermetallic phases in Al / Fe / V / Si alloy systems.
  • FR 2 880 086 A1 describes the use of a wear-resistant aluminum alloy in brake discs and brake drums.
  • Wear resistance, tribological carrying capacity and heat resistance of the aluminum base alloys are improved. This may be due to intermetallic phases precipitated in the microstructure, such as AlFe 3 , Al 3 Fe (Hv - 9.8 GPa, ⁇ ), Al 5 Fe 2 ( ⁇ , H v ⁇ 10.5 GPa), Al 6 Fe, Al 13 Fe 4 , Al 5 Fe 2 ( ⁇ , H v ⁇ 10.5 GPa), Al 3 (Ti, Cr), Al 3 Ti, Al 4 (Cr, Fe), Al 10 (Cr, Fe), AlSi 2 or Al 8 Fe 2 Si, which have microhardnesses of 4,000-8,000 MPa.
  • intermetallic phases precipitated in the microstructure such as AlFe 3 , Al 3 Fe (Hv - 9.8 GPa, ⁇ ), Al 5 Fe 2 ( ⁇ , H v ⁇ 10.5 GPa), Al 6 Fe, Al 13 Fe 4 , Al 5 Fe 2 ( ⁇ , H v ⁇ 10.5 GPa), Al 3 (Ti, Cr), Al
  • the silicon content should not exceed 2.0 wt%, more preferably not exceed 1.0 wt% Si.
  • the intermetallic phases are formed from eutectic ( ⁇ -Al ⁇ Al 3 Fe) and peritectic phase equilibria.
  • the alloys used according to the invention differ morphologically, above all in the embodiment of the dendrites from intermetallic phases, from the silicon crystals precipitated in known AlSi alloys.
  • the silicon crystals are present in aluminum alloys as individual single crystals, while a dendritic network allows an excellent integration into the matrix for absorption for shear stresses from the tribological stress.
  • the alloys according to the invention can be clearly characterized by their production process.
  • the solid state in the aluminum, or hardly soluble alloying elements such as. Fe, Ti, Cr, Mo or V
  • grain refinement After melting and homogenizing, between 0.5% by weight and 0.8% by weight of one or more of the elements selected from among boron, Ce, Sr, Sc, Mg, Nb, Mn or Zr may be used for grain refinement be alloyed. Grain refinement primarily reduces the size of the dendrites of the intermetallic phases precipitated on solidification, but also leads to an increase in the number of nuclei / density during the primary crystallization of the aluminum.
  • a higher cooling rate of> 100 K / s achieves the same effect, so that the grain refining is advantageously to be used for larger wall thicknesses of the castings in order to obtain a uniform microstructure.
  • the still relatively large dendrites are favorable for a tribological sliding stress and for the connection of the intermetallic phases in the structure, but not for the Nachalimentierung the solidification front with melt. Therefore, an optimum in size must be sought in each case by grain refining elements optionally with the aid of magnetic stirring.
  • the formation of the dendrites from the intermetallic phases can also be prevented by magnetic stirring.
  • the magnetic stirring also improves the alimentation of the solidification front with fresh melt, thus helping to avoid voids.
  • the casting temperature in step (iii) is in the range of 1 ° C to 80 ° C, in particular in the range of 10 ° C to 50 ° C, above the melting temperature of the alloy.
  • the casting temperatures are preferably below 800 ° C.
  • an alloy with 4-8 wt .-% of Fe and / or 3-5 wt .-% of X is provided. Furthermore, it is preferred that X for the element combination (a) is specified such that a proportion of Si is less than or equal to 2 wt .-%, in particular less than or equal to 1 wt .-%.
  • X for the element combination (a) is specified such that a proportion of Si is less than or equal to 2 wt .-%, in particular less than or equal to 1 wt .-%.
  • steps (ii) and (iii) are part of a metallurgical melt casting process selected from the group of sand casting, die casting, continuous casting, strip casting, centrifugal casting and cold crucible casting.
  • the methods mentioned can be implemented particularly simply in conjunction with the method used according to the invention.
  • the existing alloy workpiece can preferably be processed by drop forging. The workpiece is completely surrounded by the closed tool, the die, and the introduced into the die engraving determines the shape of the finished molding.
  • the temperature of the mold is in the range of 450 ° C to 600 ° C.
  • the temperature of the mold is in the range of 450 ° C to 600 ° C.
  • the invention further relates to crankshaft bearing shells, cylinder liners, piston rings, pistons, valve guides, bearing bushes or bearing shells with a sliding element of the aforementioned aluminum alloy.
  • FIGS. 1 to 13 describe the manufacturing parameters with the then adjusting and the Gefugemorphologien of alloys of the invention based on AIFeVSi and AlFeCrTi in argon atmosphere.
  • the Fig. 1-3 show sample cross-sections of AlFeVSi alloys cast under different conditions.
  • the 12mm sample cross section out Fig. 1 shows an Al88.4Fe8.5V1.3Si1.7Zr0.1 alloy which was poured into a preheated to 600 ° C graphite mold at a melting temperature of 750 ° C and the Zr was added as a grain refining element.
  • the sample cross section (14mm) Fig. 3 is based on an Al88.5Fe8.5V1.3Si1.7 alloy, which was poured without preheating in a graphite mold at a melting temperature of 700 ° C.
  • Fig. 2 shows the same alloy but under the process variant that the melting temperature was 750 ° C and the graphite mold was heated to 500 ° C.
  • E RT room temperature
  • Such values of the modulus of elasticity are that is comparable to that of a high-carbon, lamellar gray cast iron ( ⁇ 3.7% by weight C, GL11) and significantly larger than that of AlSi alloys. It should be noted for both exemplified Al-casting alloys according to the invention that the high moduli of elasticity were achieved without the addition of ceramic fibers, particles or platelets.
  • the alloys according to the invention can substitute cast iron for material mechanics, since, in addition, it decreases in a similar manner with increasing temperature, as in the case of high-carbon cast iron.
  • the decrease in strength of the alloys of the invention is also shifted to higher temperatures.
  • Fig. 1-3 illustrate that the uniform formation of the microstructure of the Al88.5Fe8.5V1.3Si1.7 alloy over the cross section is achieved by a graphite mold preheated to 500 ° C, but these conditions promote the growth of large dendrites of Al 3 Fe (X-ray diffraction index JCPDS NR .: 001-1265) of several millimeters in length. Only the grain refining with 0.1 wt .-% Zr, a preheated to 600 ° C graphite mold in conjunction with a casting temperature of 750 ° C achieves a much finer micrograph, which is pronounced homogeneous over the cross section.
  • the alloy system Al84,4Fe7,0Cr6,0Ti2,5 also exudes a dense, but closed, primary dendrite network (see Fig. 6 ), which was analyzed by EDX as an Al 4 (Fe, Cr).
  • the SEM images reveal ( Fig. 7 (Unetched); Figure 8 (etched)) precipitates of Al 4 (V, Fe) in addition to the Al 3 Fe dendrites.
  • Fig. 7 Unetched
  • Figure 8 etched
  • the AlFeCrTi alloy exhibits a fine, "pearlitic" pattern of eutectic disintegration of the residual melt of the Al84.4Fe7.0Cr6.0Ti2.5 alloy ( Fig. 10 ).
  • Fig. 11 a LOM image of intermetallic lamellar dendrites in a rapidly cooled AlFeCrTi alloy with the residual melt.
  • the dendrite network in an Al84.4Fe7.0Cr6.0Ti2.5Mg0.1 alloy appears somewhat finer ( Fig. 12 ), which is caused in particular by their branching or ramification ( Fig. 13 ).
  • the Al84.4Fe7.0Cr6.0Ti2.5Mg0.1 alloy was cast at 750 ° C into a graphite mold (14 mm) preheated to 500 ° C.
  • the 88.5Al8.5Fe1.3V1.7Si alloys are more prone to forming star-shaped crystals as compared to the Al84.4Fe7.0Cr6.0Ti2.5Mg0.1 alloy with a dendrite network.
  • the tribological functional surfaces were lapped at R PK ⁇ 0.43 ⁇ m at Al88.4 Fe8.5 V 1.3 S.1.7 Zr0.1 and R PK ⁇ 0.37 ⁇ m at Al84.4 Fe7.0 Cr6.0 Ti2.5 Mg0.1.
  • the Fig. 14 gives the results obtained in the form of the wear coefficient of the main body (piston ring) separated from the counter body (rotating sample or cylinder bore) with the belonging to the respective pairing mixed / boundary friction number again.
  • hydrocarbons based SAE 5W-30 and SAE 0W-30 oils have a high temperature high shear viscosity (HTHS) of 3.0 mPas.
  • the GG20HCN is a 3.66 wt% carbon high carbon gray cast iron with lamellar graphite.
  • the piston ring designations "MKP81A”, “MKJet502 (WC / Cr 3 C 2 ,” superpolished ”)" and "CKS36" are brand names of Federal Mogul Burscheid GmbH.
  • Ti n O 2n-1 and Ti n-2 Cr 2 O 2n-1 ring coatings are experimental coatings for piston rings from CIE Automotive (Tarabusi, Barrio Urquizu 58, ES-48140 Igorre) AlFeXY alloys Al84.4Fe7.0Cr6.0Ti2.5Mg0.1 and 88.4Al8.5Fe1.3V1.7SiZr0.1 were vacuum degassed at 750 ° C in a graphite mold preheated to 600 ° C.
  • the wear resistance of the Al84.4Fe7Cr6Ti2.5Mg0.1 alloy, which has been compounded with 0.1% by weight Mg, achieves wear resistance and load capacity comparable to high-carbon gray cast iron compared to the molybdenum-based MKP81A piston ring.
  • Conspicuous in the table are the higher coefficients of friction with the first filling oil SAE 5W-30 under mixed / boundary friction of the AlFeXY alloys compared to the GGL20HCN.
  • the metal-free friction reducer contained in the first filling oil SAE 0W-30 (“PCX”) with an HTHS of 3.0 mPas does not affect the AlFeCrTi. Underlined against a nitrided piston ring Fig.
  • Fig. 16 is still the wear coefficient of a long-term experiment (108 km) reproduced, whereby a strong, wear-reducing run-in behavior of AlFeCrTi alloy is documented.
  • the tribological limit load capacity of 100 MPa (geometrical surface pressure) of the sliding combination "AlSi12CuNiMg / Nitrierstahl” in the BMW801 double star engine at an oil inlet temperature of 99 ° C of the fully synthetic lubricant "SS-1600" based on an adipic ester and ethylene oil is noteworthy, since it with a kinematic Viscosity ⁇ 100C ⁇ 6.2 mm 2 / s was still significantly “thinner” than today'schtiauföle with ⁇ 100C ⁇ 9-12 mm 2 / s.
  • AlFeXY wear protection and high-pressure additives in engine and gearbox oils, also due to the metallurgy of the test specimens in tribometer, are matched to iron and not to silicon.
  • valve guides require high thermal diffusivity because they dissipate heat from the valve stem into the cylinder head, with associated wear resistance. Therefore, valve guides are preferably made of copper-based alloys, as CuZn36Mn3Al2SiPb ( ⁇ CuZn40Al2 according to DIN 17660 or CW713R) with ⁇ RT -63 W / mK or K RT ⁇ 19.7 mm 2 / s. Temperatures of 500 ° C are not uncommon on the surfaces in the lower part of the outlet valve guide.
  • the aluminum alloys according to the invention offer a 3-4 times higher thermal diffusivity combined with the necessary temperature resistance without melt equilibria up to> 600 ° C.
  • Aluminum piston materials consist of AlSi12CuXX eutectic alloys or hypereutectic AlSi18CuXX alloys with up to 0.85% iron by weight.
  • the thermal diffusivities are between 55 mm 2 / s ⁇ K RT ⁇ 61.7 mm 2 / s.

Claims (11)

  1. Utilisation d'un alliage d'aluminium résistant à l'usure, fabriqué par un procédé qui comprend les étapes qui consistent à :
    (i) préparer un alliage d'aluminium de composition suivante :
    Fe : 3 - 10;
    X : 3 - 10;
    Y : 0 - 1,5;
    Z : 0 - 10;
    dans laquelle
    X représente un élément ou une combinaison des éléments
    (a) V et Si;
    (b) Cr et Ti;
    (c) Ce ou
    (d) Mn
    chaque fois avec la condition que la teneur en les différents éléments dans les combinaisons d'éléments (a) et (b) représente au moins 0,5 % en poids,
    Y représente un ou plusieurs éléments d'affinage des grains sélectionnés dans l'ensemble constitué de B, Ce, Sr, Sc, Mg, Nb, Mn et Zr, pour autant que ceux-ci ne soient pas déjà présents en tant que X,
    Z représente un ou plusieurs additifs céramiques améliorant la tenue à la chaleur, sélectionnés dans l'ensemble des fibres, des particules et des plaquettes,
    les données étant des données en % en poids par rapport à l'alliage, Al et les impuretés inévitablement dues à la fabrication représentant le solde de l'alliage par rapport à 100 % en poids avec la condition que la teneur en Al dans l'alliage soit d'au moins 80 % en poids,
    (ii) fusion de l'alliage d'aluminium, dissolution et homogénéisation des éléments d'alliage à une température comprise entre 650°C et 1 000°C et
    (iii) coulée du bain de fusion dans un moule de coulée à une température de coulée située dans une plage qui s'étend de la température de fusion de l'alliage à une température située à 150°C au-dessus de la température de fusion,
    pour fabriquer des éléments de coulissement dans des coussinets d'arbres de vilebrequin, des pistes de déplacement de cylindres, des bagues de piston, des pistons, des guides de soupape, des douilles de palier ou des coussinets de palier.
  2. Utilisation selon la revendication 1, dans laquelle la température de coulée de l'étape (iii) est située dans la plage de 1°C à 80°C au-dessus de la température de fusion de l'alliage.
  3. Utilisation selon la revendication 2, dans laquelle la température de coulée de l'étape (iii) est située dans la plage de 10°C à 50°C au-dessus de la température de fusion de l'alliage.
  4. Utilisation selon l'une des revendications précédentes, dans laquelle la température du moule de coulée est comprise dans la plage de 450°C à 600°C.
  5. Utilisation selon l'une des revendications précédentes, dans laquelle l'alliage contient de 4 à 8 % en poids de Fe.
  6. Utilisation selon l'une des revendications précédentes, dans laquelle l'alliage contient de 3 à 5 % en poids de X.
  7. Utilisation selon l'une des revendications précédentes, dans laquelle l'alliage contient de 0,5 à 0,8 % en poids de Y.
  8. dans laquelle l'alliage contient dans laquelle X représente la combinaison d'éléments (a) et dans laquelle la teneur en Si est inférieure ou égale à 2 % en poids.
  9. Utilisation selon la revendication 1, dans laquelle X représente la combinaison d'éléments (a) et dans laquelle la teneur en Si est inférieure ou égale à 1 % en poids.
  10. dans laquelle l'alliage contient dans laquelle les étapes (ii) et (iii) font partie d'une opération métallurgique de coulée de métal fondu sélectionnée dans l'ensemble constitué de la coulée sur sable, de la coulée sous pression, de l'extrusion, de la coulée de feuillards minces, de la coulée centrifuge et du procédé en creuset froid.
  11. Coussinet de palier d'arbre de vilebrequin, piste de déplacement de cylindre, bague de piston, piston, guide de soupape, douille de palier ou coussinet de palier dotés d'un élément de coulissement en alliage d'aluminium fabriqué par un procédé qui comprend les étapes qui consistent à :
    (i) préparer un alliage d'aluminium de composition suivante :
    Fe : 3 - 10;
    X : 3 - 10;
    Y : 0 - 1,5;
    Z : 0 - 10;
    dans laquelle
    X représente un élément ou une combinaison des éléments
    (a) V et Si;
    (b) Cr et Ti;
    (c) Ce ou
    (d) Mn
    chaque fois avec la condition que la teneur en les différents éléments dans les combinaisons d'éléments (a) et (b) représente au moins 0,5 % en poids,
    Y représente un ou plusieurs éléments d'affinage des grains sélectionnés dans l'ensemble constitué de B, Ce, Sr, Sc, Mg, Nb, Mn et Zr, pour autant que ceux-ci ne soient pas déjà présents en tant que X,
    Z représente un ou plusieurs additifs céramiques améliorant la tenue à la chaleur, sélectionnés dans l'ensemble des fibres, des particules et des plaquettes,
    les données étant des données en % en poids par rapport à l'alliage, Al et les impuretés inévitablement dues à la fabrication représentant le solde de l'alliage par rapport à 100 % en poids avec la condition que la teneur en Al dans l'alliage soit d'au moins 80 % en poids,
    (ii) fusion de l'alliage d'aluminium, dissolution et homogénéisation des éléments d'alliage à une température comprise entre 650°C et 1 000°C et
    (iii) coulée du bain de fusion dans un moule de coulée à une température de coulée située dans une plage qui s'étend de la température de fusion de l'alliage à une température située à 150°C au-dessus de la température de fusion.
EP06792791A 2005-09-30 2006-08-11 Procede pour produire un alliage d'aluminium resistant a l'usure, alliage d'aluminium obtenu selon ce procede et son utilisation Not-in-force EP1943039B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102005047037A DE102005047037A1 (de) 2005-09-30 2005-09-30 Motorische Gleitpaarung aus einer Aluminiumbasislegierung
PCT/EP2006/065258 WO2007039340A1 (fr) 2005-09-30 2006-08-11 Procede pour produire un alliage d'aluminium resistant a l'usure, alliage d'aluminium obtenu selon ce procede et son utilisation

Publications (2)

Publication Number Publication Date
EP1943039A1 EP1943039A1 (fr) 2008-07-16
EP1943039B1 true EP1943039B1 (fr) 2011-07-13

Family

ID=37011951

Family Applications (1)

Application Number Title Priority Date Filing Date
EP06792791A Not-in-force EP1943039B1 (fr) 2005-09-30 2006-08-11 Procede pour produire un alliage d'aluminium resistant a l'usure, alliage d'aluminium obtenu selon ce procede et son utilisation

Country Status (5)

Country Link
US (1) US20080219882A1 (fr)
EP (1) EP1943039B1 (fr)
AT (1) ATE516094T1 (fr)
DE (1) DE102005047037A1 (fr)
WO (1) WO2007039340A1 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2017009132A1 (fr) 2015-07-13 2017-01-19 Federal-Mogul Wiesbaden Gmbh Palier lisse, matériau de palier lisse, procédé de fabrication d'un matériau de palier lisse, et utilisation d'un matériau de palier lisse pour un palier lisse

Families Citing this family (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102009039838A1 (de) 2008-09-05 2010-04-29 Ks Kolbenschmidt Gmbh Verfahren zur Herstellung eines Kolbens einer Brennkraftmaschine, bestehend aus einer verbesserten Aluminiumsilizium-Legierung
JP2013525608A (ja) 2010-04-26 2013-06-20 サパ アーベー 階層状の微細構造を有する損傷耐性アルミ材
DE102011004133B4 (de) 2011-02-15 2015-11-19 Federal-Mogul Wiesbaden Gmbh Verfahren zur Herstellung eines bleifreien, plattierten Aluminiumgleitlagers
GB201102849D0 (en) 2011-02-18 2011-04-06 Univ Brunel Method of refining metal alloys
US9657844B2 (en) 2011-09-14 2017-05-23 Honeywell International Inc. High temperature aluminum valve components
JP6367567B2 (ja) * 2014-01-31 2018-08-01 吉川工業株式会社 耐食性溶射皮膜、その形成方法およびその形成用溶射装置
DE102015200632A1 (de) 2015-01-16 2016-07-21 Federal-Mogul Nürnberg GmbH Verfahren zur Herstellung eines Motorbauteils, Motorbauteil und Verwendung eines Kornfeiners zur Herstellung eines Motorbauteils
CN106086498B (zh) * 2016-08-26 2018-07-03 安徽永昌金属制品有限公司 铝合金轮毂重力熔炼铸造工艺
DE102018127401A1 (de) * 2018-11-02 2020-05-07 AM Metals GmbH Hochfeste Aluminiumlegierungen für die additive Fertigung von dreidimensionalen Objekten
CN110819852A (zh) * 2019-10-30 2020-02-21 全球能源互联网研究院有限公司 一种耐热性好的高导电率软铝单丝及其制备方法
US11608546B2 (en) 2020-01-10 2023-03-21 Ut-Battelle Llc Aluminum-cerium-manganese alloy embodiments for metal additive manufacturing
CN112453359B (zh) * 2020-12-12 2022-08-05 安徽瑞荣汽车零部件有限公司 一种高强度铝合金汽车电机壳体

Family Cites Families (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4715893A (en) * 1984-04-04 1987-12-29 Allied Corporation Aluminum-iron-vanadium alloys having high strength at elevated temperatures
US4898612A (en) * 1988-08-31 1990-02-06 Allied-Signal Inc. Friction-actuated extrusion of rapidly solidified high temperature Al-base alloys and product
JP2619118B2 (ja) 1990-06-08 1997-06-11 健 増本 粒子分散型高強度非晶質アルミニウム合金
DE19532244C2 (de) 1995-09-01 1998-07-02 Peak Werkstoff Gmbh Verfahren zur Herstellung von dünnwandigen Rohren (I)
US6454657B1 (en) * 1998-12-31 2002-09-24 Spicer Driveshaft, Inc. End yoke for a universal joint assembly
US6478682B1 (en) * 1999-11-05 2002-11-12 Ntn Corporation Constant velocity universal joint
US6520859B2 (en) * 2000-12-27 2003-02-18 Spicer Driveshaft, Inc. Universal joint bearing insert formed from ceramic or composite materials
US6848163B2 (en) 2001-08-31 2005-02-01 The Boeing Company Nanophase composite duct assembly
US20040261916A1 (en) 2001-12-21 2004-12-30 Lin Jen C. Dispersion hardenable Al-Ni-Mn casting alloys for automotive and aerospace structural components
US20040156739A1 (en) 2002-02-01 2004-08-12 Song Shihong Gary Castable high temperature aluminum alloy
WO2003080881A1 (fr) * 2002-03-26 2003-10-02 Council Of Scientific And Industrial Research Processus de production d'alliages al-fe-v-si
US7435306B2 (en) 2003-01-22 2008-10-14 The Boeing Company Method for preparing rivets from cryomilled aluminum alloys and rivets produced thereby
EP1469213A1 (fr) * 2003-04-17 2004-10-20 Ford Global Technologies, LLC, A subsidary of Ford Motor Company Système tribologique pour arbre d'entraínement
FR2880086B1 (fr) 2004-12-23 2008-08-22 Renault Sas Piece de friction mecanique pour systeme de freinage et d'embrayage comportant une zone d'alliage d'aluminium et de fer

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2017009132A1 (fr) 2015-07-13 2017-01-19 Federal-Mogul Wiesbaden Gmbh Palier lisse, matériau de palier lisse, procédé de fabrication d'un matériau de palier lisse, et utilisation d'un matériau de palier lisse pour un palier lisse
DE102015213052A1 (de) 2015-07-13 2017-01-19 Federal-Mogul Wiesbaden Gmbh Gleitlager, Gleitlagerwerkstoff, Verfahren zur Herstellung eines Gleitlagerwerkstoffes und Verwendung eines Gleitlagerwerkstoffes für ein Gleitlager

Also Published As

Publication number Publication date
EP1943039A1 (fr) 2008-07-16
DE102005047037A1 (de) 2007-04-19
US20080219882A1 (en) 2008-09-11
ATE516094T1 (de) 2011-07-15
WO2007039340A1 (fr) 2007-04-12

Similar Documents

Publication Publication Date Title
EP1943039B1 (fr) Procede pour produire un alliage d'aluminium resistant a l'usure, alliage d'aluminium obtenu selon ce procede et son utilisation
DE112004001160B4 (de) Aluminiumlegierung für einen Gussmotorblock, Gusszylinderblock für einen Verbrennungsmotor sowie Verwendung der Aluminiumlegierung
DE3817350C2 (fr)
US4938810A (en) Heat-resistant, wear-resistant, and high-strength aluminum alloy powder and body shaped therefrom
DE19532244C2 (de) Verfahren zur Herstellung von dünnwandigen Rohren (I)
DE3725495C2 (fr)
DE102007023323B4 (de) Verwendung einer Al-Mn-Legierung für hochwarmfeste Erzeugnisse
EP0867517B1 (fr) Composite à matrice en alliage d'aluminium et procédé de fabrication
EP0670441A1 (fr) Palier à glissement
DE102009016111B4 (de) Druckgusskörper aus einer übereutektischen Aluminium-Silizium-Gusslegierung und Verfahren zu dessen Herstellung
EP0871791A1 (fr) Procede de fabrication de tuyaux minces
US5494540A (en) Abrasion-resistant aluminum alloy and method of preparing the same
DE3344450A1 (de) Motormaentel auf basis von aluminiumlegierungen und intermetallischen verbindungen und verfahren zu deren herstellung
DE19532253C2 (de) Verfahren zur Herstellung von dünnwandigen Rohren (II)
WO2009068132A1 (fr) Bloc moteur comportant des chemises de cylindre coulées à plusieurs couches de matériau et procédé de fabrication des chemises de cylindre
JPH0578767A (ja) 高耐摩耗性アルミニウム青銅合金、該合金を用いた摺動部材
EP1412113B1 (fr) Pieces en metal fritte ayant une repartition homogene de composantes a fusion non homogene, et procede destine a leur production
US6706126B2 (en) Aluminum alloy for sliding bearing and its production method
DE102004005458B4 (de) Zylinderblock für eine Brennkraftmaschine und Verfahren zur Herstellung eines Zylinderblocks
DE3835253A1 (de) Gegenstand aus einer aluminium-silizium-legierung und verfahren zu seiner herstellung
US6899844B2 (en) Production method of aluminum alloy for sliding bearing
DE10357096B4 (de) Monolithisches Aluminium-Zylinderkurbelgehäuse für hochbeanspruchte Dieselmotoren
DE102012018934A1 (de) Verfahren zur Herstellung eines Halbzeugs aus einer Aluminium-Eisen-Legierung sowie nach dem Verfahren erhältliche Halbzeuge
DE102012112422A1 (de) Bauteil und Verfahren zur Herstellung eines Bauteils
JPS60215162A (ja) アルミニウム合金製ピストン

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: 20080422

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IS IT LI LT LU LV MC NL PL PT RO SE SI SK TR

17Q First examination report despatched

Effective date: 20090304

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

GRAC Information related to communication of intention to grant a patent modified

Free format text: ORIGINAL CODE: EPIDOSCIGR1

DAX Request for extension of the european patent (deleted)
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): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IS IT LI LT LU LV MC NL PL PT RO SE SI SK TR

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: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

Free format text: LANGUAGE OF EP DOCUMENT: GERMAN

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 502006009828

Country of ref document: DE

Effective date: 20110901

REG Reference to a national code

Ref country code: NL

Ref legal event code: VDEP

Effective date: 20110713

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: 20111114

Ref country code: SE

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: 20110713

Ref country code: IS

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: 20111113

Ref country code: FI

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: 20110713

Ref country code: NL

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: 20110713

Ref country code: LT

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: 20110713

REG Reference to a national code

Ref country code: IE

Ref legal event code: FD4D

BERE Be: lapsed

Owner name: BUNDESANSTALT FUR MATERIALFORSCHUNG UND -PRUFUNG

Effective date: 20110831

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

Ref country code: SI

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: 20110713

Ref country code: GR

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: 20111014

Ref country code: PL

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: 20110713

Ref country code: LV

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: 20110713

Ref country code: CY

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: 20110713

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

Ref country code: MC

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

Effective date: 20110831

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

PLBI Opposition filed

Free format text: ORIGINAL CODE: 0009260

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

Ref country code: CH

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

Effective date: 20110831

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: 20110713

Ref country code: LI

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

Effective date: 20110831

Ref country code: CZ

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: 20110713

Ref country code: SK

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: 20110713

PLAX Notice of opposition and request to file observation + time limit sent

Free format text: ORIGINAL CODE: EPIDOSNOBS2

26 Opposition filed

Opponent name: KS KOLBENSCHMIDT GMBH

Effective date: 20120413

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

Ref country code: EE

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: 20110713

Ref country code: BE

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

Effective date: 20110831

Ref country code: RO

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: 20110713

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

Effective date: 20111013

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

Ref country code: DK

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: 20110713

REG Reference to a national code

Ref country code: DE

Ref legal event code: R026

Ref document number: 502006009828

Country of ref document: DE

Effective date: 20120413

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

Ref country code: GB

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

Effective date: 20111013

PLAF Information modified related to communication of a notice of opposition and request to file observations + time limit

Free format text: ORIGINAL CODE: EPIDOSCOBS2

REG Reference to a national code

Ref country code: DE

Ref legal event code: R082

Ref document number: 502006009828

Country of ref document: DE

Representative=s name: ZIMMERMANN & PARTNER, DE

Ref country code: DE

Ref legal event code: R082

Ref document number: 502006009828

Country of ref document: DE

Representative=s name: ZIMMERMANN & PARTNER PATENTANWAELTE MBB, DE

PLBB Reply of patent proprietor to notice(s) of opposition received

Free format text: ORIGINAL CODE: EPIDOSNOBS3

REG Reference to a national code

Ref country code: AT

Ref legal event code: MM01

Ref document number: 516094

Country of ref document: AT

Kind code of ref document: T

Effective date: 20110811

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: 20110811

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: 20111024

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: 20110811

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

Ref country code: BG

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: 20111013

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

Ref country code: TR

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: 20110713

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

Ref country code: HU

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: 20110713

PLCK Communication despatched that opposition was rejected

Free format text: ORIGINAL CODE: EPIDOSNREJ1

APBM Appeal reference recorded

Free format text: ORIGINAL CODE: EPIDOSNREFNO

APBP Date of receipt of notice of appeal recorded

Free format text: ORIGINAL CODE: EPIDOSNNOA2O

APAH Appeal reference modified

Free format text: ORIGINAL CODE: EPIDOSCREFNO

APBQ Date of receipt of statement of grounds of appeal recorded

Free format text: ORIGINAL CODE: EPIDOSNNOA3O

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 10

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 11

REG Reference to a national code

Ref country code: DE

Ref legal event code: R100

Ref document number: 502006009828

Country of ref document: DE

APBU Appeal procedure closed

Free format text: ORIGINAL CODE: EPIDOSNNOA9O

PLBN Opposition rejected

Free format text: ORIGINAL CODE: 0009273

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: OPPOSITION REJECTED

27O Opposition rejected

Effective date: 20170419

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: FR

Payment date: 20170822

Year of fee payment: 12

Ref country code: DE

Payment date: 20170831

Year of fee payment: 12

Ref country code: IT

Payment date: 20170828

Year of fee payment: 12

REG Reference to a national code

Ref country code: DE

Ref legal event code: R119

Ref document number: 502006009828

Country of ref document: DE

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: 20180811

Ref country code: DE

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

Effective date: 20190301

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: 20180831