EP1715084B1 - Anodisierte aluminiumlegierung und herstellungsverfahren dafür - Google Patents

Anodisierte aluminiumlegierung und herstellungsverfahren dafür Download PDF

Info

Publication number
EP1715084B1
EP1715084B1 EP04728648.9A EP04728648A EP1715084B1 EP 1715084 B1 EP1715084 B1 EP 1715084B1 EP 04728648 A EP04728648 A EP 04728648A EP 1715084 B1 EP1715084 B1 EP 1715084B1
Authority
EP
European Patent Office
Prior art keywords
comp
coat
aluminum alloy
eutectic
particles
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
EP04728648.9A
Other languages
English (en)
French (fr)
Other versions
EP1715084A1 (de
EP1715084A4 (de
Inventor
Yasuo c/o Showa Denko K.K. OKAMOTO
Yoshio c/o Showa Denko K.K. UMINUMA
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.)
Resonac Holdings Corp
Original Assignee
Showa Denko KK
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 JP2003391736A external-priority patent/JP4511156B2/ja
Application filed by Showa Denko KK filed Critical Showa Denko KK
Publication of EP1715084A1 publication Critical patent/EP1715084A1/de
Publication of EP1715084A4 publication Critical patent/EP1715084A4/de
Application granted granted Critical
Publication of EP1715084B1 publication Critical patent/EP1715084B1/de
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • 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
    • C—CHEMISTRY; METALLURGY
    • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
    • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
    • C25D11/00—Electrolytic coating by surface reaction, i.e. forming conversion layers
    • C25D11/02—Anodisation
    • C25D11/04—Anodisation of aluminium or alloys based thereon

Definitions

  • This invention relates to aluminum alloys, bar materials, forged parts and machined parts which are capable of providing sleeve parts for use in automobiles, require the hardness and thickness of an anodized coat, shun sustaining a crack and demand wear resistance; wear-resistant aluminum alloys using the aluminum alloys mentioned above and excelling in anodized coat hardness; sleeve parts; and methods for the production thereof.
  • the casts of the ADC12, AC4C, A390 and Al-Si types and the alloys for the Al-Si type expanded materials of A4032 alloy have been hitherto formed by subjecting extruded materials and forged materials to the T6 treatment, the machining treatment and the anodizing treatment, and the parts consequently obtained have been put to use.
  • the casts of the Al-Si type and the alloys for the Al-Si type expanded materials have their Cu and Mg contents adjusted with the object of exalting the wear resistance and strength thereof.
  • the alloy materials mentioned above contain Cu in large amounts with a view to exalting their wear resistance and strength, they are supposed to encounter difficulty in acquiring the thickness and the hardness of an anodized coat.
  • Patent Document 1 JP-A HEI 10-204566 , for example.
  • Patent Document 1 The material of Patent Document 1 is characterized by containing 6 to 12% (weight %, that is applied hereinafter) of Si, 0.1 to 1.0% of Fe, 1.0 to 5.0% of Cu, 0.1 ro 1.0% of Mn, 0.4 to 2.0% of Mg, 0.01 to 0.3% of Ti and 0.005 to 0.2% of Sr, limiting the content of Ni as an impurity to less than 0.05% and having the balance formed of Al and impurities, having dispersed in the matrix thereof eutectic Si particles of an average particle diameter of 1.5 to 5.0 ⁇ m and allowing the presence therein of 5000 or more and less than 10000 eutectic Si particles of this average particle diameter per mm 2 .
  • Patent Document 1 on being anodized, has formed a film having an unduly low hardness, specifically hardness Hv only in the approximate range of 310 to 370.
  • the conventional Al-Si type alloys therefore, have been mostly such parts as are put to use without undergoing an anodizing treatment.
  • the parts, that need an anodized coat and have an ability to form the coat have been applied to products (portions) that have no need for the hardness of the coat. Thus, they have proved useful in markedly limited applications and have incurred difficulty in satisfying the demand of the market.
  • the coat when the coat is applied in a thickness 30 ⁇ m or more, the coat sustains a crack and the coated alloy product becomes no longer suitable for the intended use.
  • This invention aims to provide aluminum alloys, bar materials, forged parts and machined parts which are capable of providing sleeve parts for use in automobiles, require the hardness and thickness of an anodized coat, shun generation of a crack and demand wear resistance; wear-resistant aluminum alloys using the aluminum alloys mentioned above and excelling in anodized coat hardness; sleeve parts; and methods for the production thereof.
  • the present inventors have made a diligent study regarding the characteristic properties of the Al-Si type aluminum alloys and the anodized coats formed on the surfaces thereof. They have perfected this invention based on the knowledge acquired consequently.
  • the aluminum alloy according to this invention forms in consequence of an anodizing treatment an anodized coat having a thickness of 30 ⁇ m or more and hardness Hv of 400 or more and allows the presence, in the coat, of eutectic Si particles having particle diameters in the range of 0.4 to 5.5 ⁇ m.
  • the aluminum alloy according to this invention forms in consequence of an anodizing treatment an anodized coat having a thickness of 40 ⁇ m or more and hardness Hv of 400 or more and allows the presence, in the coat, of eutectic Si particles having particle diameters in the range of 0.8 to 5.5 ⁇ m.
  • the aluminum alloy mentioned above consists of 5 to 12% (mass %; similarly applicable hereinafter) of Si, 0.1 to 1% of Fe, less than 1% of Cu and 0.3 to 1.5% of Mg, and 0.1% or less of Ni, and has the balance formed of Al and impurities, has dispersed in the matrix thereof eutectic Si particles having particle diameters in the range of 0.4 to 5.5 ⁇ m, inclusive of 60% or more of the eutectic Si particles having particle diameters of 0.8 to 2.4 ⁇ m, and allows the presence therein of 10000 or more and less than 38000 eutectic Si particles per mm 2 .
  • the aluminum alloy mentioned above when containing 9 to 12% of Si, has 80% or more of the eutectic Si particles with particle diameters of 0.8 to 2.4 ⁇ m.
  • the aluminum alloy mentioned above consists in substantially no Cu.
  • the aluminum alloy mentioned above consists in containing at least one component selected from among 0.1 to 1% of Mn, 0.04 to 0.3% of Cr, 0.04 to 0.3% of Zr, and 0.01 to 0.1% of V and/or at least one component selected from among 0.01 to 0.3% of Ti, 0.0001 to 0.05% of B and 0.001 to 0.1% of Sr.
  • the aluminum alloy mentioned above consists in being a bar material cast by a continuous casting technique.
  • the aluminum alloy mentioned above consists in being a bar material obtained by subjecting a bar material cast by the continuous casting technique further to an extruding process or an extruding and drawing process.
  • the bar material according to this invention consists in being formed of an aluminum alloy.
  • the bar material of this invention consists in being used as a sleeve part.
  • the bar material of this invention consists in being a forged part formed by subjecting a bar material to a forging process.
  • the bar material of this invention consists in being a machined part formed by subjecting a bar material or a forced part to a machining process.
  • This invention further consists in being a wear-resistant aluminum alloy allowing the presence, in an anodized coat, of eutectic Si particles of particle diameters in the range of 0.4 to 5.5 ⁇ m, forming the coat in a thickness of 30 ⁇ m or more and with hardness Hv of 400 or more and consequently excelling in hardness of the anodized coat.
  • This invention also consists in being a wear-resistant aluminum alloy allowing the presence, in an anodized coat, of eutectic Si particles of particle diameters in the range of 0.8 to 5.5 ⁇ m, forming the coat in a thickness of 40 ⁇ m or more and with hardness Hv of 400 or more and consequently excelling in hardness of the anodized coat.
  • This invention consists in being a sleeve part resulting from subjecting a machined part to a treatment for forming an anodized coat and consequently excelling in hardness of the anodized coat.
  • this invention consists in a method for the production of a wear-resistant aluminum alloy excellent in hardness of an anodized coat, comprising casting the aluminum alloy of the composition mentioned above to a continuous casting process, subjecting the resultant cast mass to a homogenizing treatment, extruding and/or forging and/or machining the homogenized cast mass and anodizing the resultant formed cast, thereby allowing the presence, in the anodized coat, of eutectic Si particles of particle diameters in the range of 0.4 to 5.5 ⁇ m and forming the coat in a thickness of 30 ⁇ m or more and with hardness Hv of 400 or more.
  • This invention also consists in a method for the production of a sleeve part excellent in hardness of an anodized coat and formed of an aluminum alloy, comprising casting an aluminum alloy of the composition mentioned above by a continuous casting process, subjecting the resultant cast mass to a homogenizing treatment, extruding and/or forging and/or machining the homogenized cast mass and anodizing the resultant formed cast, thereby allowing the presence, in the anodized coat, of eutectic Si particles of particle diameters in the range of 0.4 to 5.5 ⁇ m and forming the coat in a thickness of 30 ⁇ m or more and with hardness Hv of 400 or more.
  • the anodized coat produced as described above cannot form a crack.
  • the thickness and hardness of the coat mentioned above do not represent mere target qualities, but indicate the qualities which can be attained by heeding and controlling the limits on the particle diameter distribution of eutectic Si particles in the anodized coat and the content of Cu therein.
  • This invention concerns an aluminum alloy which contains eutectic Si particles having particle diameters in the range of 0.4 to 5.5 ⁇ m in an anodized coat formed by an anodizing treatment and permits manufacture of sleeve parts furnished with an anodized coat excelling in hardness and possessing resistance to wear and other wear-resistant aluminum alloy products which can be properly utilized for automobile parts and other parts requiring the hardness and thickness of an anodized coat, shunning generation of a crack and demanding wear resistance.
  • This aluminum alloy acquires sufficient hardness without requiring any special anodizing treatment and, therefore, can be applied to parts that are put to use without being anodized in advance.
  • This invention concerns an aluminum alloy which contains of eutectic Si particles having particle diameters in the range of 0.8 to 5.5 ⁇ m in an anodized coat formed by an anodizing treatment and permits manufacture of sleeve parts furnished with an anodized coat excelling further in hardness and possessing wear resistance and other wear-resistant aluminum alloy products.
  • the aluminum alloy of this invention is characterized by consisting of 5 to 12% (mass %; similarly applicable hereinafter) of Si, 0.1 to 1% of Fe, less than 1% of Cu and 0.3 to 1.5% of Mg and 0.1 % or less of Ni, and having the balance formed of Al and impurities, having dispersed in the matrix thereof eutectic Si particles of particle diameters in the range of 0.4 to 5.5 ⁇ m, inclusive of 60% or more of the eutectic Si particles existing with particle diameters of 0.8 to 2.4 ⁇ m, and allowing the presence therein of 10000 or more and less than 38000 eutectic Si particles per mm 2 , thereby permitting manufacture of sleeve parts furnished with an anodized coat excelling further in hardness and possessing a wear resistance and other wear-resistant aluminum alloy products.
  • the aluminum alloy of this invention when containing 9 to 12% of Si, has 80% or more of the eutectic Si particles with particle diameters of 0.8 to 2.4 ⁇ m and therefore permits manufacture of sleeve parts furnished with an anodized coat excelling further in hardness and possessing wear resistance and other wear-resistant aluminum alloy products.
  • the aluminum alloy of this invention contains substantially no Cu and therefore acquires a further exalted ability to undergo an anodizing treatment and permits provision of sleeve parts furnished with an anodized coat excelling further in hardness and possessing wear resistance and other wear-resistant aluminum alloy products.
  • the aluminum alloy of this invention contains one or two or more components selected from among 0.1 to 1% of Mn, 0.04 to 0.3% of Cr, 0.04 to 0.3% of Zr and 0.01 to 0.1% of V and, owing to the inclusion of Mn, Cr, Zr and V, induces precipitation of the Al-Mn type, Al-Mn-Fe-Si type, Al-Cr type, Al-Cr-Fe-Si type, Al-Zr type or Al-V type particles and thereby effects refinement of recrystallized particles, acquires exalted workability and permits formation of sleeve parts of complicated shapes and other wear-resistant aluminum alloy products.
  • Mn, Cr, Zr and V results in inducing precipitation of the particles of the Al-Mn type, Al-Mn-Fe-Si type, Al-Cr type, Al-Cr-Fe-Si type, Al-Zr type and Al-V type, suppressing recrystallization of the sleeve parts by a heat treatment given after the formation thereof and exalting the ductility and toughness of the sleeve parts.
  • the aluminum alloy of this invention contains at least one component selected from among 0.01 to 0.3% of Ti, 0.0001 to 0.05% of B and 0.001 to 0.1% of Sr and, when containing Ti and B, induces refinement of the texture of the cast mass, prevents the alloy mass from sustaining a crack during the course of forging, allows the aluminum alloy of this invention to be cast stably, further imparts exalted workability to the cast mass and permits manufacture of sleeve parts of complicated shapes.
  • the inclusion of Sr results in allowing the eutectic Si particles to be refined and consequently enabling the aluminum alloy of this invention to acquire improvement in ductility and toughness.
  • the aluminum alloy of this invention is a bar material cast by a continuous casting process. This aluminum alloy, therefore, permits manufacture of sleeve parts excelling in hardness and possessing wear resistance and other wear-resistant aluminum alloy products.
  • the aluminum alloy of this invention is a bar material resulting from subjecting a bar material cast by a continuous casting process to an extruding process or an extruding and drawing process. Even when the subsequent process omits a forging step or comprises a forging step of a small processing ratio, it enjoys a sufficient processing ratio and acquires exalted ductility and toughness. It also permits easy manufacture of a bar material having a diameter of 20 mm or less which is not easily obtained by the continuous casting technique.
  • the formed article which uses the bar material of the aluminum alloy of this invention mentioned above constitutes a product excellent in hardness and possessing wear resistance.
  • the bar material of the aluminum alloy of this invention mentioned above permits manufacture of a sleeve part possessing an anodized coat of excellent hardness and excelling in wear resistance.
  • the bar material of the aluminum alloy of this invention mentioned above undergoes a forging treatment.
  • the forged part consequently obtained permits manufacture of sleeve parts furnished with an anodized coat excelling in hardness and possessing wear resistance and other wear-resistant aluminum alloy products.
  • the bar material or forged part of the aluminum alloy of this invention mentioned above undergoes a machining treatment.
  • the machined part consequently obtained permits manufacture of sleeve parts furnished with an anodized coat excelling in hardness and possessing wear resistance and other wear-resistant aluminum alloy products.
  • the aluminum alloy of this invention contains in an anodized coat eutectic Si particles of particle diameters in the range of 0.4 to 5.5 ⁇ m and forms the coat in a thickness of 30 ⁇ m or more and with hardness Hv of 400 or more.
  • the aluminum alloy of this invention contains in an anodized coat eutectic Si particles of particle diameters in the range of 0.8 to 5.5 ⁇ m and forms the coat in a thickness of 40 ⁇ m or more and with hardness Hv of 400 or more.
  • the machined part of the aluminum alloy of this invention has undergone a treatment for the formation of an anodized coat. It, therefore, constitutes a sleeve part that is furnished with an anodized coat excelling in hardness and possessing wear resistance.
  • the method for the production of an aluminum alloy according to this invention comprises casting an aluminum alloy of the composition mentioned above in accordance with a continuous casting process, subjecting the resultant cast mass to a homogenizing treatment, extruding and/or forging and/or machining the homogenized cast mass and anodizing the resultant formed cast, thereby containing in an anodized coat eutectic Si particles of particle diameters in the range of 0.4 to 5.5 ⁇ m and forming the coat in a thickness of 30 ⁇ m or more and with hardness Hv of 400 or more.
  • the method therefore, permits easy manufacture of wear-resistant aluminum alloy products excelling in hardness of an anodized coat.
  • the method for the production of an aluminum alloy according to this invention comprises casting an aluminum alloy of the composition mentioned above in accordance with a continuous casting process, subjecting the resultant cast mass to a homogenizing treatment, extruding and/or forging and/or machining the homogenized cast mass and anodizing the resultant formed cast, thereby containing in an anodized coat eutectic Si particles of particle diameters in the range of 0.4 to 5.5 ⁇ m and forming the coat in a thickness of 30 ⁇ m or more and with hardness Hv of 400 or more.
  • the method therefore, permits easy manufacture of sleeve parts excelling in hardness of an anodized coat.
  • the aluminum alloy according to this invention is characterized by inducing in consequence of an anodizing treatment the formation of an anodized coat having a thickness of 30 ⁇ m or more, preferably 40 ⁇ m or more, and hardness Hv of 400 or more and the presence of eutectic Si particles of particle diameters in the range of 0.4 to 5.5 ⁇ m, preferably 0.8 to 5.5 ⁇ m, in the coat.
  • the aluminum alloy mentioned above in one preferred example of the composition thereof, consists of 5 to 12% (mass %; similarly applicable hereinafter, preferably 5 to 11%) of Si, 0.1 to 1% of Fe, less than 1% (preferably less than 0.5% and more preferably substantially no content) of Cu and 0.3 to 1.5% (preferably 0.4 to 1%) of Mg, and 0.1% or less of Ni, and has the balance formed of Al and impurities.
  • the aluminum alloy mentioned above preferably contains at least one component selected from among 0.1 to 1% of Mn, 0.04 to 0.3% of Cr; 0.04 to 0.3% of Zr and 0.01 to 0.1% of V.
  • it further contains one or two or more components selected from among 0.01 to 0.3% of Ti, 0.0001 to 0.05% ofB and 0.001 to 0.1% of Sr.
  • the aluminum alloy of this composition excels in workability and ability to yield to an anodizing treatment and acquires an ability to retain the hardness (Hv: 400 or more) of the anodized coat mentioned above.
  • this aluminum alloy acquires sufficient hardness without undergoing any special anodizing treatment and therefore fits application to parts that are put to use without requiring an anodizing treatment.
  • Si while coexisting with Mg induces precipitation of Mg 2 Si particles and exalts the strength of the aluminum alloy and, owing to the distribution of eutectic Si, adds to strength and wear-resistance.
  • the Si content is in the range of 5 to 12%, preferably 5 to 11%. If the Si content falls short of 5%, the shortage will prevent this effect of Si from being manifested fully satisfactorily. If it exceeds 12%, the excess will result in inducing precipitation of a primary crystal of Si and exerting an adverse effect to bear on the ability to undergo an anodizing treatment.
  • the Fe content is in the range of 0.1 to 1% (preferably 0.1 to 0.5% and more preferably 0.21 to 0.3%).
  • the reason for this range is that the Fe content is capable of inducing precipitation of the particles of the Al-Fe type or Al-Fe-Si type and, during the heat treatment after the formation of a sleeve part, repressing recrystallization and exalting the ductility and the toughness of the sleeve part.
  • the Fe content is capable of refining recrystallized particles during the course of extrusion, exalting the forgeability of the material in the subsequent step and consequently permitting manufacture of sleeve parts of complicated shapes.
  • the Fe content falls short of 0.1%, the shortage will prevent the effect of Fe from being manifested satisfactorily. If it exceeds 1%, the excess will result in increasing the precipitation of coarse crystals of the Al-Fe type or Al-Fe-Si type, exerting an adverse effect to bear on the ability of the aluminum ally to succumb to an anodizing treatment and impairing the ductility and the toughness of the aluminum alloy.
  • the Cu content is less than 1% (preferably 0.9% or less and more preferably less than 0.5%) or substantially absent.
  • the inclusion of Cu results in inducing precipitation of CuAl 2 particles and consequently contributing to the strength and hardness of the aluminum alloy. If the Cu content is 1% or more, the excess will result in decreasing the hardness of the anodized coat. For the purpose of further increasing the hardness of the coat, the Cu content is preferred to be less than 0.5% and more preferably to be substantially nil.
  • Cu is dissolved during the course of an anodizing treatment. Since the Cu ions formed by this dissolution are precious metal ions, Cu is precipitated again on the surface of the aluminum alloy matrix and is suffered to render the formation of an anodized coat difficult and degrade the denseness of the coat. By controlling the Cu content, it is made possible to exalt the formability and the denseness of the anodized coat and increase the hardness of the coat.
  • Mg and Si are effective in inducing precipitation of Mg 2 Si particles and contributing to the strength of the aluminum alloy.
  • the Mg content is in the range of 0.3 to 1.5% and more preferably in the range of 0.4 to 1%. If the Mg content falls short of 0.3%, the shortage will result in decreasing the effect. If it exceeds 1.5%, the excess will results in lowering the workability of the aluminum alloy.
  • the inclusion of at least one component selected from among 0.1 to 1% (preferably 0.2 to 0.4%) of Mn, 0.04 to 0.3% (preferably 0.15 to 0.25%) of Cr, 0.04 to 0.3% (preferably 0.1 to 0.2%) of Zr and 0.01 to 0.1% (preferably 0.05 to 0.1%) of V in the composition of the aluminum alloy mentioned above is effective in inducing precipitation of the particles of the Al-Mn type, Al-Mn-Fe-Si type, Al-Cr type, Al-Cr-Fe-Si type, Al-Zr type or Al-V type, suppressing recrystallization during the heat treatment after the formation of a sleeve part and exalting the ductility and toughness of the sleeve part.
  • the inclusion is effective in refining the recrystallized particles during the course of the extrusion, exalting the forgeability of the extruded material in the subsequent step and consequently enabling the sleeve part to be formed in a complicated shape. If the Mn content falls short of 0.1%, the Cr content falls short of 0.04%, the Zr content falls short of 0.04% and the V content falls short of 0.01%, these shortages will result in preventing the effects of these elements from being manifested satisfactorily.
  • the Mn content exceeds 1%
  • the Cr content exceeds 0.3%
  • the Zr content exceeds 0.3%
  • the V content exceeds 0.1%
  • the inclusion of at least one component selected from among 0.01 to 0.3% (preferably 0.01 to 0.2% and more preferably 0.002 to 0.1%) of Ti, 0.0001 to 0.05% (preferably 0.005 to 0.01%) of B and 0.001 to 0.2% (preferably 0.005 to 0.1% and more preferably 0.005 to 0.05%) of Sr is favorable for the following reason.
  • the inclusion of Ti and B is effective in refining the texture of a cast mass, preventing the cast mass from being fractured during the course of casting and exalting the workability of the cast mass and consequently permitting sleeve parts to be formed in complicated shapes. If the Ti content falls short of 0.01%, the shortage will result in preventing the effects of its inclusion from being manifested sufficiently.
  • the Ni content is 0.1% or less.
  • the aluminum alloy can be precluded from sustaining a crack by allowing the presence of eutectic Si particles in the anodized coat and enabling the aluminum alloy to excel in hardness of the coat and acquire an increased thickness.
  • the eutectic Si particles dispersed in the alloy matrix have particle diameters of 0.4 to 5.5 ⁇ m (preferably 0.8 to 5.5 ⁇ m). It is proper and necessary that 60% or more (preferably 80% or more) of the eutectic Si particles have particle diameters of 0.8 to 2.4 ⁇ m and that the matrix allow the presence therein of 10000 or more and less than 38000 eutectic Si particles per mm 2 .
  • the expression "the eutectic Si particles have particle diameters of 0.4 to 5.5 ⁇ m” means that the substantial particle diameter distribution is in the range of 0.4 to 5.5 ⁇ m. For example, it means that 95% or more, preferably 98% or more, of the eutectic Si particles have particle diameters falling in the range of 0.4 to 5.5 ⁇ m.
  • the eutectic Si particles in the anodized coat have particle diameters of 0.4 to 5.5 ⁇ m as described above. If the particle diameters fall short of 0.4 ⁇ m, particularly 0.3 ⁇ m, the shortage will result in heightening the voltage of the bath used for the anodizing treatment, increasing the resistance to the anodization, rendering the flow of electric current difficult and permitting no easy formation of the coat. If the particle diameters exceed 5.6 ⁇ m, particularly 6.0 ⁇ m, the excess will result in forming a cause for degrading the ability of the aluminum alloy to succumb to an anodizing treatment and aggravating the surface coarseness of the formed coat.
  • eutectic Si particles those that have particle diameters of 0.8 to 2.4 ⁇ m account for a proportion of 60% or more as described above. If this proportion falls short of 60%, particularly within 50% inclusive, the shortage will result in increasing the difference between the portion allowing easy flow of electric current and the portion not allowing easy flow of electric current during the course of the anodizing treatment, disrupting the uniformity of flow of the electric current and consequently preventing the formed coat from acquiring a uniform thickness.
  • the proportion mentioned above is preferred to be 80% or more.
  • the alloy matrix contains 10000 or more and less than 38000 eutectic Si particles of particle diameters of 0.8 to 2.4 ⁇ m per mm 2 .
  • the flow of the electric current during the course of the anodizing treatment is fixed and the produced coat is allowed to have a uniform thickness.
  • the eutectic Si particles dispersed in the aluminum alloy matrix allow more difficult flow of electric current than the matrix, since the difficulty can be suppressed, the anodized coat can be formed in a uniform thickness.
  • the degradation of the hardness of the coat can be suppressed further because the possibility of the eutectic Si surviving dissolution during the course of the anodizing treatment and persisting in the coat can be diminished and the possibility of the residual eutectic Si particles in the coat degrading the denseness of the coat surrounding the eutectic Si particles can be suppressed.
  • the aluminum alloy of the composition mentioned above is cast by the continuous casting process, such as the gas pressure hot top continuous casting process, the resultant cast mass is subjected to the homogenizing treatment, and the homogenized alloy mass is either directly machined or subjected to a proper processing selected from among extruding, forging and machining operations.
  • the resultant formed aluminum alloy is made possible to obtain an aluminum alloy product which excels in hardness of the anodized coat and allows the coat to acquire an increased thickness without sustaining a crack.
  • the state of the generation of the eutectic Si in the alloy is affected by the temperature of the melt of the alloy and the speed of casting while the melt of the alloy of the given composition is solidified by the continuous casting process.
  • the aluminum alloy contemplated by this invention can be obtained by controlling the temperature of the melt and the speed of casting, thereby enabling the eutectic Si particles to acquire particle diameters in the range of 0.4 to 5.5 ⁇ m. Further, by controlling the temperature of the melt and the speed of casting, thereby enabling 60% or more of the eutectic Si particles to possess particle diameters of 0.8 to 2.4 ⁇ m, it is made possible to obtain the aluminum alloy aimed at by this invention.
  • the speed of solidification must be controlled to a rather higher level than ever because the aluminum alloy of this invention has a small Cu content, forms a small region of solid-liquid coexistence during solidification, and becomes liable to solidify.
  • the speed of solidification is preferred to be in the range of 200 to 350 mm/min.
  • the gas pressure hot top continuous casting process presses the gap between the melt and the mold with a gas and therefore permits the speed of casting to be increased. It is, therefore, at an advantage in permitting easy production of the aluminum alloy of this invention having the particle diameters of the eutectic Si controlled in a given state.
  • the state of generation of the eutectic Si in the alloy succumbs to the influences of the temperature of homogenization and the time of homogenization during the course of the homogenizing treatment and controls the particle diameter of the eutectic Si and controls the shape of the eutectic Si particles as well.
  • the cast mass is enabled to have the workability thereof exalted as compared with the acerate form prior to the anodizing treatment. Further, the ability of the aluminum alloy to succumb to an anodizing treatment is exalted.
  • the homogenizing treatment is carried out at a temperature of 450°C or more and lower than 500°C (preferably 480°C or more) for a period of four hours or more.
  • the primary crystal Si is preferred to be in the following state (position of distribution of particles, average particle diameter, and ratio of occupation of area) or to be substantially absent from the outer peripheral part of the cast mass which is destined to form a sleeve part in consequence of an anodizing treatment. If the primary crystal Si is present in the part subjected to the anodizing treatment, it will prevent the flow of electric current from being fixed during the course of the anodizing treatment, render the thickness of the coat uneven, decrease the denseness of the coat and lower the hardness of the coat.
  • Position of distribution of particles of primary crystal Si Absent of the primary crystal Si from the outer periphery of the cast mass through the position of 20% or less of the radius of the cast mass (0.2% or less of the ratio of occupation of area).
  • Average particle diameter of primary crystal Si 30 ⁇ m or less.
  • Ratio of occupation of area by primary crystal Si 0.8% or less.
  • the procedure of setting the Si content at 12% or less and controlling the conditions of the amount of gas pressure, the speed of casting and the temperature of the melt during the course of a gas pressure hot top continuous casting operation is at an advantage in enabling the primary crystal Si to assume the state mentioned above.
  • the aluminum alloy mentioned above may be cast through the continuous casting process to form cast billets and the cast billets may be subjected to a homogenizing treatment and then machined directly without being modified. Otherwise, the cast billets may be subjected to properly selected processes, such as extruding, forging and machining operations. Alternatively, the aluminum alloy may be cast to manufacture bar materials and the bar materials may be manufactured into formed articles having given shapes.
  • the manufacture of bar materials into formed articles may be accomplished by properly combining various processes, such as machining and forging operations.
  • the bar materials are preferred to undergo an extruding or drawing process prior to the forging or machining process.
  • the bar materials which have undergone the extruding or drawing process are at an advantage in enjoying exalted ductility and excelling in workability and imparting ductility to end products. While round bars measuring 20 mm or less in diameter are not easily obtained by the continuous casting method, they can be easily obtained through the extruding or drawing process.
  • the extruding process does not need to be particularly restricted but may be properly attained by using an extruding device of 2500 tons, for example, and extruding a given bar material at the highest extruding rate of 8 m/min.
  • the anodizing treatment that is performed on a formed article does not need to be particularly restricted but may be properly accomplished by using an aqueous 15-wt% sulfuric acid solution as the electrolytic bath.
  • the coat may be obtained in a given thickness by adjusting the temperature of the bath, the electric voltage and the time of the treatment.
  • the aluminum alloy of this invention and the sleeve parts manufactured therefrom can be effectively used in sleeve portions of more exacting requirements because their matrix parts excel in hardness and their coats enjoy an exalted ability to resist wear. They are suitable for the following uses, for example.
  • the wear-resistant aluminum alloy that is consequently obtained does not restrict the uses to be found therefor.
  • it is particularly suitable for brake caliper pistons, air suspension quality compressor pistons and other parts that require a coat excelling in hardness and defying infliction of a crack.
  • the aluminum alloys having the compositions shown in Table1 were manufactured by the gas pressure hot top continuous casting method into cast billets (8 inches in diameter). These cast billets were subjected to a homogenizing treatment at 490°C for 12 hours and extruded by an indirect extruding device to form extruded bars 44 mm in diameter. The extruded bars were subjected to a T6 treatment performed by an ordinary method. The extruded bars resulting from this treatment were used as test materials and were tested for ability to succumb an anodizing treatment, hardness of coat, presence or absence of the occurrence of a crack in the coat, wear resistance and mechanical properties based on the standards shown below. The results of the test were rated. The test materials were further tested for determining the cross section, eutectic Si particles in an anodized coat and state of distribution of particle diameters by the use of an image analysis system under the following conditions.
  • the determination was performed by cutting a given sample in an arbitrary size, embedding the cut sample in an abrading resin, micro-abrading the resin till eutectic Si particles became detectable and visually examining the abraded surface.
  • a cross section of a given extruded bar perpendicular to the direction of extrusion was cut till it formed a smooth surface having a fixed surface roughness.
  • the cross section was used as a sample for rating the ability.
  • an aqueous 15-wt% sulfuric acid solution was used as the electrolytic bath and the anodizing treatment was performed, with the bath temperature, voltage and time so set as to form an anodized coat of a target thickness of 40 ⁇ m on the sample surface.
  • the determination was performed by cutting a given sample which had undergone an anodizing treatment in an arbitrary size, embedding the cut sample in a resin, micro-abrading the resin till the coat thickness became detectable, and determining and rating the hardness of the coat.
  • the results are shown in Table 3.
  • a JIS No. 4 test piece was taken from the central part of an extruded material in parallel to the direction of extrusion and tested for tensile strength.
  • the results are shown in Table 2.
  • Example 1 The same procedure as in Example 1 was repeated, with the compositions changed as shown in Table 1. The conditions of forming an anodized coat were the same as in Example 1.
  • Examples 4 to 13 of this invention invariably excelled in ability to succumb to an anodizing treatment, hardness of coat, freedom from infliction of a crack in the coat and wear resistance, and were possessed of tensile strengths exceeding 310 N/mm 2 and proof strengths exceeding 230 N/mm 2 as respect mechanical properties.
  • Comparative Example 1 was deficient in the ability to succumb to an anodizing treatment because it had a small Si content. Further, Comparative Examples 1, 2, 4, 5 and 8 were deficient in the ability to succumb to an anodizing treatment and in hardness of the coat because they had large Cu contents.
  • Examples 1 to 3 are Reference Examples.
  • Test material Composition (mass %) Si Fe Cu Mn Mg Cr Ti Sr Al Ex. 1 5.0 0.2 0.3 0.2 0.4 0.1 0.01 0.01 Balance Ex. 2 5.0 0.2 0.4 0.2 0.4 0.1 0.01 0.01 Balance Ex. 3 5.0 0.2 0.9 0.2 0.4 0.1 0.01 0.01 Balance Ex. 4 5.0 0.2 0.9 0.2 0.8 0.1 0.01 0.01 Balance Ex. 5 7.5 0.2 0.4 0.2 0.4 0.1 0.01 0.01 Balance Ex. 6 7.5 0.2 0.9 0.2 0.4 0.1 0.01 0.01 Balance Ex. 7 7.5 0.2 0.95 0.2 0.8 0.1 0.01 0.01 Balance Ex.
  • Test material Diameter of eutectic Si particles ( ⁇ m) Number (pieces/ mm 2 ) Distribution of diameters of eutectic Si particles (%) Proportion of 0.8 to 2.4 ⁇ m (%) Hardness of coat Ability to yield anodization treatment Thickness of coat ( ⁇ m) Crack Max. Min. Ave. ⁇ 0.8 ( ⁇ m) ⁇ 1.6 ( ⁇ m) ⁇ 2.4 ( ⁇ m) ⁇ 3.2 ( ⁇ m) ⁇ 4.0 ( ⁇ m) ⁇ 4.8 ( ⁇ m) ⁇ 5.5 ( ⁇ m) 5.6 ⁇ ( ⁇ m) (Hv) Ex.
  • An aluminum alloy having the composition shown in Table 5 was manufactured by the gas pressure hot top continuous casting method disclosed in JP-B SHO 54-42827 into bar materials of a diameter of 72 mm.
  • the bar materials were then subjected to a homogenizing treatment at 490°C for four hours and subjected to a T6 treatment according to an ordinary method under the conditions shown in Table 6 (a solution treatment at 500 to 510°C for two to three hours, followed by water cooling and further by an aging treatment at 180 to 190°C for five to six hours) to obtain test materials.
  • the continuous casting (continuously cast) bar materials were similarly subjected to a homogenizing treatment, then to a shaving treatment to remove the cast skin, cut to given lengths, and the cut lengths were subjected to an annealing treatment and a bonde treatment, and forged into double wall cups measuring 68 mm in outside diameter of the outer cup, 52 mm in inside diameter of the outer cup, 32 mm in outside diameter of the inner cup, 15 mm in inside diameter of the inner cup, 40 mm in height and 10 mm in bottom thickness.
  • test materials were subjected to a T6 treatment according to the ordinary method under the conditions shown in Table 8 (a solution treatment at 500 to 510°C for two to three hours, following by water cooling and further by an aging treatment at 180 to 190°C for five to six hours) to obtain forged parts as test materials.
  • the test materials were further machined and thereafter tested for ability to succumb to an anodizing treatment, hardness of coat, the presence or absence of a crack in the coat, wear resistance and mechanical properties under the following standards. They were also tested for the cross section of test material, eutectic Si particles in the anodized coat and distribution of particle diameters by the use of an image analysis system under the conditions shown below.
  • the determination was performed through cutting a given sample in an arbitrary size, embedding the cut sample in a resin and micro-abrading the resin till eutectic Si particles became detectable.
  • An aluminum alloy having the composition shown in Table 5 was manufactured by the horizontal continuous casting method disclosed in JP-A SHO 61-33735 into bar materials of a diameter of 30 mm.
  • the bar materials were then subjected to a homogenizing treatment at 490°C for four hours and to a T6 treatment according to an ordinary method under the conditions shown in Table 6 (a solution treatment at 500 to 510°C for two to three hours, followed by water cooling and further by an aging treatment at 180 to 190°C for five to six hours) to obtain test materials.
  • the continuously cast bar materials were similarly subjected to a homogenizing treatment and then to a shaving treatment to remove the cast skin, and cut to given lengths, and the cut lengths were subjected to an annealing treatment and a bonde treatment, and forged into cups measuring 32 mm in outside diameter, 15 mm in inside diameter, 27 mm in height and 8 mm in bottom thickness.
  • These cups were subjected to a T6 treatment according to the ordinary method under the conditions shown in Table 8 (a solution treatment at 500 to 510°C for two to three hours, following by water cooling and further by an aging treatment at 180 to 190°C for five to six hours) to obtain forged parts as test materials.
  • test materials were further machined and thereafter tested for ability to succumb to an anodizing treatment, hardness of coat, presence or absence of a crack in the coat, wear resistance and mechanical properties under the following standards. They were also tested for the cross section of test material, eutectic Si particles in the anodized coat and distribution of particle diameters by the use of an image analysis system under the conditions shown below.
  • the determination was performed by cutting a given sample in an arbitrary size, embedding the cut sample in a resin, micro-abrading the resin till eutectic Si particles became detectable.
  • An aluminum alloy having the composition shown in Table 5 was manufactured using the gas-pressure hot top continuous casting method disclosed in JP-B SHO 54-42827 into billets (8 inches in diameter). Then, the cast billets were subjected to a homogenizing treatment at 490°C for four hours. Subsequently, the cast mass was heated to 350°C and then extruded by the use of an indirect extruding device to manufacture extruded bars 32 mm in diameter and subjected to a T6 treatment according to an ordinary method under the conditions shown in Table 6 (a solution treatment at 500 to 510°C for two to three hours, followed by water cooling, and further by an aging treatment at 180 to 190°C for five to six hours) to obtain extruded bars as test materials.
  • the indirectly extruded bars were drawn into bars 39.2 mm in diameter, subjected to a T6 treatment by an ordinary method under the conditions shown in Table 6 (a solution treatment at 500 to 510°C for two to three hours, followed by water cooling and further by an aging treatment at 180 to 190°C for five to six hours) to obtain drawn bars as test materials.
  • the drawn bars 39.2 mm in diameter manufactured from the extruded bars were cut into given lengths, subjected to an annealing treatment and a bonde treatment, and forged into cups measuring 32 mm in outside diameter, 15 mm in inside diameter, 27 mm in height and 8 mm in bottom thickness.
  • the determination was performed by cutting a given sample in an arbitrary size, embedding the cut sample in a resin, micro-abrading the resin till eutectic Si particles became detectable.
  • a cross section of a given extruded bar perpendicular to the direction of extrusion was cut till it formed a smooth surface having a fixed surface roughness.
  • the cross section was used as a sample for rating the ability.
  • an aqueous 15-wt% sulfuric acid solution was used as the electrolytic bath and the anodizing treatment was performed with the bath temperature, electric voltage and time so set as to form an anodized coat of a target thickness of 30 ⁇ m on the sample surface.
  • the determination was performed through cutting a given sample in an arbitrary size, embedding the cut sample in a resin and micro-abrading the resin till eutectic Si particles became detectable.
  • the hardness of the coat was measured and rated.
  • the results of the samples that had not undergone a forging treatment are shown in Table 6 and those of the samples that had undergone the forging treatment are shown in Table 8.
  • a JIS No. 4 test piece was taken from the central part of an extruded material in parallel to the direction of extrusion and tested for tensile strength.
  • the passage of the commendable tensile strength of 310 N/mm 2 and proof strength of 230 N/mm 2 was taken as the standard. The results are shown in Table 6.
  • the continuously cast materials, extruded materials and drawn materials of Examples 101 to 104, 121 to 125, 141 to 144 and 150 to 153 having the compositions shown in Table 5 and the forced products thereof (Example 201 to 204, 221 to 225, 241 to 244 and 250 to 253) were manufactured by machining into brake caliper pistons. These brake caliper pistons were subjected to a T6 treatment by following the ordinary method to form anodized coats of 38 ⁇ m or more on their surfaces. These brake caliper pistons were incorporated into brake master cylinders of four wheelers and were made to repeat braking operations to determine the conditions of seizure and locking.
  • the brake caliper pistons of Example 101 to 153 and Examples 201 to 253 and those of the Comparative Examples produced no sign of problem.
  • the brake caliber pistons of Examples 11 to 153 and Examples 201 to 253 sustained absolutely no scar, whereas those of the Comparative Examples sustained streaky scratches.
  • the brake caliper pistons using the aluminum alloys of Comparative Examples 125 and 126 and having the compositions shown in Table 5 could not be put to the test because they sustained cracks on their
  • Examples No 103, 104, 109 to 112, 210 are Reference Examples.
  • Hot top continuous forging 10.0 0.25 0.9 - 0.4 - - - Ex. 142 Horizontal continuous forging do. do. do. do. do. do. Ex. 143 Extruding do. do. do. do. do. do. do. do. Ex. 144 Extruding/drawing do. do. do. do. do. do. do. do. Ex. 145 Hot top continuous forging 10.0 0.25 0.9 - 0.8 - - - Ex. 146 Hot top continuous forging 10.0 0.25 0.9 0.2 0.4 - - - Ex. 147 Hot top continuous forging 10.0 0.25 0.9 0.2 0.8 0.1 - - Ex.
  • the aluminum alloy according to this invention derives from an anodizing treatment that results in the presence of eutectic Si particles in the anodized coat, is endowed with excellent wear resistance and can be used for:

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Electrochemistry (AREA)
  • Forging (AREA)

Claims (7)

  1. Anodierte Aluminiumlegierung, umfassend eine anodierte Beschichtung, die eine Dicke von 30 µm oder mehr und eine Härte Hv von 400 oder mehr aufweist und eutektische Si-Partikel eines Partikeldurchmessers im Bereich von 0,4 bis 5,5 µm enthält,
    wobei die Aluminiumlegierung, ausgedrückt in Massen-%, was im Folgenden in ähnlicher Weise anwendbar ist, aus 5 bis 12 % Si, 0,1 bis 1 % Fe, weniger als 1 % Cu, 0,3 bis 1,5 % Mg und 0,1 % oder weniger Ni besteht und der Rest aus Al und Verunreinigungen gebildet wird, sie in einer Matrix davon eutektische Si-Teilchen eines Teilchendurchmessers im Bereich von 0,4 bis 5,5 µm aufweist, einschließlich 60 % oder mehr der eutektischen Si-Teilchen eines Teilchendurchmessers von 0,8 bis 2,4 µm, und worin 10000 oder mehr und weniger als 38000 eutektische Si-Teilchen pro mm2 vorhanden sind, oder
    wobei die Aluminiumlegierung aus 5 bis 12 % (Massen-%; im Folgenden in ähnlicher Weise anwendbar) Si, 0,1 bis 1 % Fe, weniger als 1 % Cu, 0,3 bis 1,5 % Mg, 0,1 % oder weniger Ni; mindestens einer Komponente, die unter 0,1 bis 1 % Mn, 0,04 bis 0,3 % Cr, 0,04 bis 0,3 % Zr und 0,01 bis 0,1 % V ausgewählt ist, und/oder mindestens einer Komponente, die unter 0,01 bis 0,3 % Ti, 0,001 bis 0,05 % B und 0,001 bis 0,1 % Sr ausgewählt ist, besteht, und worin der Rest aus Al und Verunreinigungen gebildet wird, sie in einer Matrix davon eutektische Si-Teilchen eines Teilchendurchmessers im Bereich von 0,4 bis 5,5 µm enthält, einschließlich 60 % oder mehr der eutektischen Si-Teilchen eines Teilchendurchmessers von 0,8 bis 2,4 µm, und worin 10000 oder mehr und weniger als 38000 eutektische Si-Teilchen pro mm2 vorhanden sind.
  2. Anodierte Aluminiumlegierung nach Anspruch 1, wobei die Dicke der anodierten Beschichtung 40 µm oder mehr ist und die Teilchendurchmesser der eutektischen Si-Teilchen im Bereich von 0,8 bis 0,5 µm liegen.
  3. Anodierte Aluminiumlegierung nach Anspruch 1 oder 2, die 80 % oder mehr der eutektischen Si-Teilchen eines Teilchendurchmessers von 0,8 bis 2,4 µm aufweist, wenn 9 bis 12 % Si enthalten sind.
  4. Anodierte Aluminiumlegierung nach einem der Ansprüche 1 bis 3, die im Wesentlichen kein Cu enthält.
  5. Anodierte Aluminiumlegierung nach einem der Ansprüche 1 bis 4, worin die Aluminiumlegierung ein durch kontinuierliches Gießen erhaltenes Blockgussmaterial ist.
  6. Anodierte Aluminiumlegierung nach einem der Ansprüche 1 bis 5, wobei die Aluminiumlegierung ein Blockmaterial ist, das durch ein kontinuierliches Gießverfahren und anschließendes Extrudieren oder Extrudieren und Ziehen hergestellt wurde.
  7. Verfahren zum Herstellen einer anodierten Aluminiumlegierung nach Anspruch 1, welches das Gießen einer Aluminiumlegierung der in Anspruch 1 definierten Zusammensetzung durch ein kontinuierliches Gießvervahren unter Bildung einer Gussmasse, das Homogenisieren der Gussmasse bei einer Temperatur von 450°C oder mehr und niedriger als 500°C während 4 Stunden oder mehr unter Bildung einer homogenisierten Gussmasse und das anschließende Extrudieren und/oder Formen und/oder Maschinieren der homogenisierten Gussmasse unter Bildung einer geformten Gussmasse und die Anodierungsbehandlung der geformten Gussmasse umfasst, wodurch in der anodierten Beschichten eutektische Si-Teilchen mit Teilchendurchmessern im Bereich von 0,4 bis 5,5 µm enthalten sind und die Beschichtung in einer Dicke von 30 µm oder mehr und mit einer Härte Hv von 400 oder mehr gebildet wird.
EP04728648.9A 2003-11-21 2004-04-21 Anodisierte aluminiumlegierung und herstellungsverfahren dafür Expired - Lifetime EP1715084B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2003391736A JP4511156B2 (ja) 2002-11-22 2003-11-21 アルミニウム合金の製造方法と、これにより製造されるアルミニウム合金、棒状材、摺動部品、鍛造成形品および機械加工成形品
PCT/JP2004/005677 WO2005049896A1 (ja) 2003-11-21 2004-04-21 アルミニウム合金、棒状材、鍛造成形品、機械加工成形品、それを用いた陽極酸化皮膜硬さに優れた耐摩耗性アルミニウム合金、摺動部品、及びそれらの製造方法

Publications (3)

Publication Number Publication Date
EP1715084A1 EP1715084A1 (de) 2006-10-25
EP1715084A4 EP1715084A4 (de) 2007-05-09
EP1715084B1 true EP1715084B1 (de) 2019-01-16

Family

ID=34616418

Family Applications (1)

Application Number Title Priority Date Filing Date
EP04728648.9A Expired - Lifetime EP1715084B1 (de) 2003-11-21 2004-04-21 Anodisierte aluminiumlegierung und herstellungsverfahren dafür

Country Status (2)

Country Link
EP (1) EP1715084B1 (de)
WO (1) WO2005049896A1 (de)

Families Citing this family (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102007012423A1 (de) 2007-03-15 2008-09-18 Bayerische Motoren Werke Aktiengesellschaft Aluminium-Gusslegierung
JP5300118B2 (ja) 2007-07-06 2013-09-25 日産自動車株式会社 アルミニウム合金鋳物の製造方法
JP4564082B2 (ja) 2008-06-20 2010-10-20 大同メタル工業株式会社 摺動部材
JP2010018875A (ja) * 2008-07-14 2010-01-28 Toyota Central R&D Labs Inc 高強度アルミニウム合金、高強度アルミニウム合金鋳物の製造方法および高強度アルミニウム合金部材の製造方法
DE102009012073B4 (de) * 2009-03-06 2019-08-14 Andreas Barth Verwendung einer Aluminiumgusslegierung
US10654135B2 (en) * 2010-02-10 2020-05-19 Illinois Tool Works Inc. Aluminum alloy welding wire
JP2011236470A (ja) * 2010-05-11 2011-11-24 Daido Metal Co Ltd Ａｌ基軸受合金及びその製造方法
EP2811041B1 (de) * 2012-02-01 2016-07-06 UACJ Corporation Aluminiumlegierung mit hervorragender abriebfestigkeit, extrudierbarkeit und schmiedebearbeitbarkeit
PL3121302T3 (pl) * 2015-04-15 2019-03-29 Daiki Aluminium Industry Co., Ltd. Stop aluminium do odlewania kokilowego oraz odlew kokilowy ze stopu aluminium z jego użyciem
DE102018216224A1 (de) * 2018-07-02 2020-01-02 Volkswagen Aktiengesellschaft Motor für ein Kraftfahrzeug aufweisend ein eine Leichtmetalllegierung umfassendes Bauteil sowie Zylinderkopf und Zylinderkurbelgehäuse
JP7358759B2 (ja) * 2019-03-27 2023-10-12 株式会社レゾナック スクロール部材およびスクロール鍛造品の製造方法
CN111534845A (zh) * 2020-06-10 2020-08-14 上海宝敦金属表面处理厂(普通合伙) 一种阀体用局部阳极氧化设备
CN111690970A (zh) * 2020-06-10 2020-09-22 上海宝敦金属表面处理厂(普通合伙) 一种阀体局部阳极氧化方法
CN118241086B (zh) * 2024-05-28 2024-07-23 中铝材料应用研究院有限公司 铝合金活塞及其制备方法

Family Cites Families (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP3261056B2 (ja) * 1997-01-14 2002-02-25 住友軽金属工業株式会社 陽極酸化皮膜の形成容易性および皮膜厚の均一性に優れた高強度耐摩耗性アルミニウム合金押出材およびその製造方法
JP2000026996A (ja) * 1998-07-13 2000-01-25 Yamaha Motor Co Ltd アルミニウム部品及びその製造方法
JP2003086979A (ja) * 2001-09-14 2003-03-20 Sky Alum Co Ltd 電気又は電子機器の冷却構造

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
None *

Also Published As

Publication number Publication date
WO2005049896A1 (ja) 2005-06-02
EP1715084A1 (de) 2006-10-25
EP1715084A4 (de) 2007-05-09

Similar Documents

Publication Publication Date Title
EP1715084B1 (de) Anodisierte aluminiumlegierung und herstellungsverfahren dafür
EP2518171B1 (de) Aluminiumlegierung zur anodisierung und aluminiumlegierungskomponente
JP3261056B2 (ja) 陽極酸化皮膜の形成容易性および皮膜厚の均一性に優れた高強度耐摩耗性アルミニウム合金押出材およびその製造方法
CA2105968C (en) Aluminum-based alloy cast product and process for producing the same
EP2085491B1 (de) Verschleissfester aluminiumlegierungswerkstoff mit hervorragender bearbeitbarkeit und herstellungsverfahren dafür
US10458009B2 (en) Free-machining wrought aluminium alloy product and manufacturing process thereof
EP3208356B1 (de) Magnesiumlegierung, magnesiumlegierungsplatte, magnesiumlegierungsteil und verfahren zur herstellung einer magnesiumlegierung
HU219635B (hu) Forgácsolható alumíniumötvözet
CN111349827B (zh) 压缩机滑动部件用铝合金、压缩机滑动部件锻造品及其制造方法
JP4511156B2 (ja) アルミニウム合金の製造方法と、これにより製造されるアルミニウム合金、棒状材、摺動部品、鍛造成形品および機械加工成形品
WO2020261611A1 (ja) 快削性銅合金、及び、快削性銅合金の製造方法
US10724123B2 (en) Extruded 6XXX alloy product that is suitable for turning and has low roughness after anodisation
EP3170594B1 (de) Aluminiumlegierungspulver zum warmschmieden einer gleitkomponente, herstellungsverfahren dafür, aluminiumlegierungsschmiedeprodukt für gleitkomponente und verfahren zur herstellung davon
US20050109429A1 (en) Aluminum alloy, bar-like material, forge-formed article, machine-formed article, wear-resistant aluminum alloy with excellent anodized coat using the same and production methods thereof
KR20200072618A (ko) 강도와 내마모성이 우수한 알루미늄 합금
EP3176274B1 (de) Stranggepresstes material aus einer aluminiumlegierung mit hervorragender bearbeitbarkeit und herstellungsverfahren dafür
JP4412594B2 (ja) アルミニウム合金、棒状材、鍛造成形品、機械加工成形品、それを用いた陽極酸化皮膜硬さに優れた耐摩耗性アルミニウム合金、摺動部品、及びそれらの製造方法
JP2848368B2 (ja) 耐摩耗性及び靭性に優れたコンプレッサー部品用アルミ合金の製造方法
KR101556070B1 (ko) 알루미늄 합금 부재
JP2907389B2 (ja) 靭性に優れた耐摩耗性加工用アルミニウム合金材
JP2004269937A (ja) 切削性に優れた耐摩耗Ａｌ−Ｓｉ系合金及びその鋳造方法
JP7318281B2 (ja) コンプレッサー摺動部品用アルミニウム合金およびコンプレッサー摺動部品鍛造品
EP4372114A1 (de) Mehrkomponentenaluminiumlegierungen mit verbesserten heissrisseneigenschaften und verringerter porosität
JPH0256401B2 (de)
JP2868017B2 (ja) パワーステアリングシステム部品の製造方法

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: 20060619

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): DE FR GB IT

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

Designated state(s): DE FR GB IT

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 21/02 20060101AFI20070328BHEP

A4 Supplementary search report drawn up and despatched

Effective date: 20070411

17Q First examination report despatched

Effective date: 20071025

REG Reference to a national code

Ref country code: DE

Ref legal event code: R079

Ref document number: 602004053640

Country of ref document: DE

Free format text: PREVIOUS MAIN CLASS: C25D0011040000

Ipc: C22C0021020000

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

RIC1 Information provided on ipc code assigned before grant

Ipc: C22F 1/043 20060101ALI20180430BHEP

Ipc: C22C 21/02 20060101AFI20180430BHEP

Ipc: C25D 11/04 20060101ALI20180430BHEP

INTG Intention to grant announced

Effective date: 20180606

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

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602004053640

Country of ref document: DE

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602004053640

Country of ref document: DE

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

Ref country code: GB

Payment date: 20190418

Year of fee payment: 16

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: 20191017

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

Effective date: 20200421

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: 20200421

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

Ref country code: FR

Payment date: 20230309

Year of fee payment: 20

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

Ref country code: IT

Payment date: 20230310

Year of fee payment: 20

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

Ref country code: DE

Payment date: 20230228

Year of fee payment: 20

REG Reference to a national code

Ref country code: DE

Ref legal event code: R071

Ref document number: 602004053640

Country of ref document: DE