EP1215295B1 - Alliage et pièce en aluminium à durcissement structural - Google Patents

Alliage et pièce en aluminium à durcissement structural Download PDF

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Publication number
EP1215295B1
EP1215295B1 EP01127698A EP01127698A EP1215295B1 EP 1215295 B1 EP1215295 B1 EP 1215295B1 EP 01127698 A EP01127698 A EP 01127698A EP 01127698 A EP01127698 A EP 01127698A EP 1215295 B1 EP1215295 B1 EP 1215295B1
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EP
European Patent Office
Prior art keywords
component
weight
alloy
aluminium
nickel
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
EP01127698A
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German (de)
English (en)
Other versions
EP1215295A1 (fr
Inventor
Andreas Dr. Barth
Mohamed Dr. Douaoui
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.)
Mercedes Benz Group AG
Original Assignee
DaimlerChrysler AG
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Filing date
Publication date
Application filed by DaimlerChrysler AG filed Critical DaimlerChrysler AG
Publication of EP1215295A1 publication Critical patent/EP1215295A1/fr
Application granted granted Critical
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Classifications

    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F02—COMBUSTION ENGINES; HOT-GAS OR COMBUSTION-PRODUCT ENGINE PLANTS
    • F02F—CYLINDERS, PISTONS OR CASINGS, FOR COMBUSTION ENGINES; ARRANGEMENTS OF SEALINGS IN COMBUSTION ENGINES
    • F02F1/00—Cylinders; Cylinder heads 
    • F02F1/24—Cylinder heads
    • 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
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F02—COMBUSTION ENGINES; HOT-GAS OR COMBUSTION-PRODUCT ENGINE PLANTS
    • F02F—CYLINDERS, PISTONS OR CASINGS, FOR COMBUSTION ENGINES; ARRANGEMENTS OF SEALINGS IN COMBUSTION ENGINES
    • F02F7/00—Casings, e.g. crankcases
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
    • F05C—INDEXING SCHEME RELATING TO MATERIALS, MATERIAL PROPERTIES OR MATERIAL CHARACTERISTICS FOR MACHINES, ENGINES OR PUMPS OTHER THAN NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES
    • F05C2201/00—Metals
    • F05C2201/02—Light metals
    • F05C2201/021—Aluminium
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
    • F05C—INDEXING SCHEME RELATING TO MATERIALS, MATERIAL PROPERTIES OR MATERIAL CHARACTERISTICS FOR MACHINES, ENGINES OR PUMPS OTHER THAN NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES
    • F05C2201/00—Metals
    • F05C2201/90—Alloys not otherwise provided for
    • F05C2201/903—Aluminium alloy, e.g. AlCuMgPb F34,37

Definitions

  • the invention relates to an aluminum casting alloy according to claim 1 and a method for producing a component according to claim 3.
  • This alloy is especially intended for pistons in internal combustion engines.
  • the relatively high silicon content leads to good wear resistance and high strength even at high temperatures.
  • the other alloying elements prevent the formation of sharp primary silicon crystals, which form the starting points of fatigue fractures under alternating load.
  • white components only have limited elongation at break.
  • From CH-A-168 202 alloys are known having a composition in wt.% Of 8 to 15% Si, 0.1 to 0.6% Mg and up to 1% Ni or Co.
  • iron is added to reduce adhesion between the component and the mold of the alloy, but at higher concentrations it increases the brittleness of the component.
  • the cobalt here shows the functional property to reduce the adhesive properties of the component to the mold, without increasing the brittleness.
  • the iron content can be greatly reduced.
  • the object of the invention is thus to provide an alloy from which components result which have a high heat resistance, a high elongation at break, a high ductility with a low tendency to corrosion.
  • the object is achieved by an alloy according to claim 1 and a method for producing a component according to claim 3.
  • the alloy of the invention according to claim 1 has a silicon content of between 5% and 10%.
  • a lower silicon content would affect the castability of the alloy.
  • a higher silicon content leads to material embrittlement. More preferably, the silicon content is between 6.5% and 7.5%.
  • the alloying element magnesium forms, together with the silicon, Mg 2 Si crystals (magnesium silicide), which increase the strength.
  • Mg 2 Si crystals magnesium silicide
  • the resulting component has too low a strength, above 0.35% magnesium, the Mg 2 Si crystals lead to too high brittleness.
  • the alloying element nickel forms together with the aluminum intermetallic phases, such as. B. Al 3 Ni (nickel aluminide) which increase the thermal stability and melt congruently at temperatures above 800 ° C (in contrast to Al 2 Cu (copper aluminide), which forms in copper-containing alloys and melts below 600 ° C).
  • the phases containing aluminum and nickel do not adversely affect the ductility of the material.
  • the nickel content of the alloy according to the invention is between 0.3% and 3%, preferably between 0.5% and 2.5%.
  • Cobalt as an alloying element to the alloy according to the invention.
  • Cobalt also forms intermetallic compounds based on aluminum and cobalt, similar to the compounds based on aluminum and nickel, which increase the heat resistance.
  • the alloy according to the invention may contain cobalt between 0.6% by weight and 3% by weight.
  • Iron which reduces the elongation at break, can be dispensed with in the alloy according to the invention.
  • Another object of the invention is a method for producing a component according to claim 3.
  • the component is cast from an alloy, which is already described in claim 1 and has the advantages that result from this alloy.
  • a heat treatment of the component preferably after a solution annealing leads to a precipitation hardening (hot curing) of an Al matrix (by which the component is formed) by targeted intermetallic phases such.
  • B. said Mg 2 Si or Al 3 Ni are excreted.
  • the precipitation hardening takes place in a temperature interval between 160 ° C and 240 ° C for a period of 0.2 h to 10 h.
  • the precipitation hardening is particularly preferably carried out in a temperature interval between 180 ° C. and 220 ° C. for a period of 0.5 h to 8 h.
  • the duration of the temperature treatment depends on the temperature, at higher temperatures, the heat treatment is shortened considerably.
  • the component which is represented by the alloy according to the invention is preferably designed as a sand casting or chill casting component, since this facilitates the already mentioned heat treatment.
  • a component that is produced by die casting the heat treatment due to air bubbles is not readily possible. In this case, a procedurally more complex Vakuumdruckg tellvon would be applied.
  • the component according to the invention is designed as a cylinder head or as a cylinder crankcase in an internal combustion engine.
  • these components especially in cylinder heads very high pressures occur at high temperatures.
  • these components have very complex geometries such. B. on the valve webs in the cylinder head or on the cooling channels in the cylinder crankcase.
  • These constructions act as notches and break points especially at the high temperatures, pressures and alternating loads. A particularly high elongation at break in combination with an increased heat resistance offers a considerable advantage here.
  • a cylinder head of an internal combustion engine is cast in the cube casting process with the alloy according to the invention.
  • the casting parameters correspond to the usual process-related process control.
  • the component After casting and after cooling, the component has a coarse grain structure of mixed crystals, since aluminum has a very low solubility with respect to most alloying elements at room temperature. For this reason, a solution annealing of the component takes place for about 4 -5 h at a temperature of about 540 ° C. In this step, the alloying elements in the aluminum matrix dissolve. The component is then quenched in water leaving the alloying elements dissolved in the aluminum matrix.
  • the phases that form during precipitation hardening are intermetallic compounds, which include, among other things, Mg 2 Si, which determines the strength of the component increases and Al 3 Ni (or other ternary and / or quaternary intermetallic compounds based on aluminum and nickel) increases due to its high melting temperature, the heat resistance of the component.
  • the strength and the ductility of the component is adjustable by the temperature control and the duration of the temperature treatment, which, as mentioned, is due to the precipitated crystal (eg the intermetallic compounds Mg 2 Si and Al 3 Ni).
  • the size of the Mg2Si and Al3Ti precipitates which are also affected by the heat treatment, affects the component properties, as explained below.
  • FIGS. 1 and 2 schematically show the strength ⁇ of the component (left y-axis) and the elongation at break ⁇ (right-hand y-axis, dashed) as a function of the duration of the heat treatment t.
  • Figures 1 and 2 differ in the temperature T of the heat treatments, T of Figure 1 is smaller than T of Figure 2.
  • the solid curves 1 and 3 show schematically the course of strength ⁇ , the dashed lines 2 and 4 the course of Elongation at break ⁇ .
  • T6 the component strength reaches a maximum after a certain duration of the heat treatment.
  • This state is generally called T6
  • the component has a very fine structure of the precipitates here.
  • the elongation at break in the T6 state reaches a minimum. If the heat treatment is continued after reaching the T6 state, a so-called overcure occurs, which is referred to as T7 state.
  • the T7 state has the advantage that, due to the coarser structure of the precipitates that occurs in this state, the elongation at break increases again.
  • T6 and T7 are fixed technical terms, T does not stand for temperature in these terms.
  • task T7 is aimed at with the highest possible elongation at break.
  • the alloying elements silicon and magnesium cause an increase in strength and a shift of the curves 1 and 3 upwards. In turn, these elements shift the curves 2 and 4 downwards, which has a negative effect on the elongation at break. Surprisingly, it was found that both nickel and cobalt shift as the alloying elements curves 1 and 3 upwards, without exerting a negative effect on the elongation at break.

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  • Engineering & Computer Science (AREA)
  • Chemical & Material Sciences (AREA)
  • Mechanical Engineering (AREA)
  • Combustion & Propulsion (AREA)
  • General Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Cylinder Crankcases Of Internal Combustion Engines (AREA)

Claims (8)

  1. Alliage de fonte d'aluminium durcissable, caractérisé en ce que l'alliage contient, outre l'aluminium, en tant qu'éléments fonctionnels
    de 5 à 7,5% en poids de silicium,
    de 0,2 à 0,35% en poids de magnésium,
    de 0,3 à 3% en poids de nickel
    et/ou de 0,6 à 3% en poids de cobalt,
    le reste étant Al,
    ainsi que des impuretés produites lors de la fabrication.
  2. Alliage de fonte d'aluminium durcissable selon la revendication 1, caractérisé en ce que l'alliage contient, outre l'aluminium, en tant qu'éléments fonctionnels,
    de 6,5 à 7,5% en poids de silicium,
    de 0,2 à 0,35% en poids de magnésium,
    de 0,5 à 2,5% en poids de nickel,
    le reste étant Al,
    ainsi que des impuretés produites lors de la fabrication.
  3. Procédé en vue de la fabrication d'une pièce faite en alliage d'aluminium, caractérisé en ce que, pour la pièce, on choisit un alliage qui présente, outre l'aluminium, en tant qu'éléments fonctionnels,
    de 5 à 7,5% en poids de silicium,
    de 0,2 à 0,35% en poids de magnésium,
    de 0,3 à 3% en poids de nickel
    et/ou de 0,6 à 3% en poids de cobalt,
    le reste étant Al,
    ainsi que des impuretés produites lors de la fabrication,
    et
    en ce que la pièce contient des phases, qui présentent de l'aluminium et du nickel et/ou de l'aluminium et du cobalt et qui sont présentes sous la forme de composés intermétalliques binaires et/ou ternaires et/ou quaternaires.
  4. Procédé selon la revendication 3, caractérisé en ce que,
    • pour la pièce, on choisit un alliage qui présente, outre l'aluminium, en tant qu'éléments fonctionnels,
    de 6,5 à 7,5% en poids de silicium,
    de 0,2 à 0,35% en poids de magnésium,
    de 0,5 à 2,5% en poids de nickel,
    et
    • en ce que la pièce contient des phases, qui présentent de l'aluminium et du nickel et qui sont présentes sous la forme de composés intermétalliques binaires et/ou ternaires et/ou quaternaires.
  5. Procédé selon la revendication 3 ou 4, caractérisé en ce que la pièce subit un durcissement à chaud à une température comprise entre 160°C et 240°C pendant une période de 0,2 à 10 heures.
  6. Procédé selon l'une quelconque des revendications 3 à 5, caractérisé en ce que la pièce subit un durcissement à chaud à une température comprise entre 180°C et 220°C pendant une période de 0,5 à 8 heures.
  7. Procédé selon l'une quelconque des revendications 3 à 6, caractérisé en ce que la pièce est fabriquée dans un procédé de coulage en sable ou de coulage en coquille ou de coulage sous pression de vide.
  8. Procédé selon l'une quelconque des revendications 3 à 7, caractérisé en ce que l'on forme une tête de cylindre ou un carter de manivelle de cylindre d'un moteur à combustion interne.
EP01127698A 2000-12-15 2001-11-21 Alliage et pièce en aluminium à durcissement structural Expired - Lifetime EP1215295B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE10062547 2000-12-15
DE10062547A DE10062547A1 (de) 2000-12-15 2000-12-15 Aushärtbare Aluminium-Gusslegierung und Bauteil

Publications (2)

Publication Number Publication Date
EP1215295A1 EP1215295A1 (fr) 2002-06-19
EP1215295B1 true EP1215295B1 (fr) 2006-06-14

Family

ID=7667285

Family Applications (1)

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EP01127698A Expired - Lifetime EP1215295B1 (fr) 2000-12-15 2001-11-21 Alliage et pièce en aluminium à durcissement structural

Country Status (3)

Country Link
US (1) US6676775B2 (fr)
EP (1) EP1215295B1 (fr)
DE (2) DE10062547A1 (fr)

Families Citing this family (15)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102004013777B4 (de) * 2004-03-20 2005-12-29 Hydro Aluminium Deutschland Gmbh Verfahren zur Herstellung eines Gussteils aus einer AL/Si-Gusslegierung
US8062250B2 (en) * 2004-08-10 2011-11-22 Unomedical A/S Cannula device
DE102005037738B4 (de) * 2005-08-10 2009-03-05 Daimler Ag Aluminium-Gusslegierung mit hoher dynamischer Festigkeit und Wärmeleitfähigkeit
DE102007033827A1 (de) * 2007-07-18 2009-01-22 Technische Universität Clausthal Aluminium-Gusslegierung und deren Verwendung
AT509343B1 (de) * 2010-07-02 2011-08-15 Voecklabrucker Metallgiesserei Alois Dambauer & Co Ges M B H Aluminiumlegierung
AU2012308416C1 (en) 2011-09-16 2016-11-24 Ball Corporation Impact extruded containers from recycled aluminum scrap
AU2014251206B2 (en) 2013-04-09 2018-03-08 Ball Corporation Aluminum impact extruded bottle with threaded neck made from recycled aluminum and enhanced alloys
US20180044155A1 (en) 2016-08-12 2018-02-15 Ball Corporation Apparatus and Methods of Capping Metallic Bottles
WO2018125199A1 (fr) 2016-12-30 2018-07-05 Ball Corporation Alliage d'aluminium pour récipients extrudés par choc et procédé pour le fabriquer
WO2018152230A1 (fr) 2017-02-16 2018-08-23 Ball Corporation Appareil et procédés de formation et d'application de fermetures inviolables sur le col fileté de récipients métalliques
MX2020002563A (es) 2017-09-15 2020-07-13 Ball Corp Sistema y metodo de formar una tapa metalica para un contenedor roscado.
DE102021114484A1 (de) 2021-06-07 2022-12-08 Audi Aktiengesellschaft Aluminium-Gusslegierung
DE102021131935A1 (de) 2021-12-03 2023-06-07 Audi Aktiengesellschaft Aluminium-Druckgusslegierung
DE102021131973A1 (de) 2021-12-03 2023-06-07 Audi Aktiengesellschaft Aluminium-Druckgusslegierung
MX2024009465A (es) 2022-02-04 2024-08-09 Ball Corp Metodo para formar un rizo y contenedor metalico roscado que incluye el mismo.

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GB394746A (en) * 1932-02-05 1933-07-06 Lightalloys Ltd Aluminium alloys and methods of treating same
FR2343895A1 (fr) * 1976-03-10 1977-10-07 Pechiney Aluminium Procede de fabrication de corps creux en alliages d'aluminium au silicium par filage de grenailles
US4243438A (en) 1978-07-21 1981-01-06 Sumitomo Aluminium Smelting Co., Ltd. Production of aluminum impact extrusions
US4274438A (en) * 1979-02-21 1981-06-23 Westinghouse Electric Corp. Method of diagnostic valve testing
JPH03120334A (ja) * 1989-09-29 1991-05-22 Showa Alum Corp 押出性に優れた低熱膨張アルミニウム合金
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DE4215160C2 (de) * 1992-05-08 1995-01-26 Vaw Ver Aluminium Werke Ag Verwendung einer Aluminium-Gußlegierung
JP3142659B2 (ja) 1992-09-11 2001-03-07 ワイケイケイ株式会社 高力、耐熱アルミニウム基合金
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WO1998010109A1 (fr) * 1996-09-03 1998-03-12 Toyota Jidosha Kabushiki Kaisha Alliage, alliage d'aluminium et element d'alliage d'aluminium ayant une excellente resistance a la fatigue thermique
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Also Published As

Publication number Publication date
US20020088509A1 (en) 2002-07-11
DE50110140D1 (de) 2006-07-27
DE10062547A1 (de) 2002-06-20
US6676775B2 (en) 2004-01-13
EP1215295A1 (fr) 2002-06-19

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