EP2516687B1 - Formteil aus cu enthaltender aluminium-legierung mit hohen mechanischer festigkeit und warmem kriechen - Google Patents

Formteil aus cu enthaltender aluminium-legierung mit hohen mechanischer festigkeit und warmem kriechen Download PDF

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Publication number
EP2516687B1
EP2516687B1 EP10799072.3A EP10799072A EP2516687B1 EP 2516687 B1 EP2516687 B1 EP 2516687B1 EP 10799072 A EP10799072 A EP 10799072A EP 2516687 B1 EP2516687 B1 EP 2516687B1
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Prior art keywords
cast part
part according
previous
alloy
content
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French (fr)
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EP2516687A1 (de
Inventor
Michel Garat
James Frederick Major
Danny Jean
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Rio Tinto Alcan International Ltd
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Rio Tinto Alcan International Ltd
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    • 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
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • 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
    • C22C21/00—Alloys based on aluminium
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • C22C21/14—Alloys based on aluminium with copper as the next major constituent with silicon
    • 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
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium
    • 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
    • C22F1/057—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 copper as the next major constituent

Definitions

  • the invention relates to copper aluminum alloy castings subjected to high mechanical stresses and working, at least in some of their areas, at high temperatures, including cylinder heads supercharged diesel or gasoline engines.
  • the alloys commonly used for the cylinder heads of automotive mass-produced vehicles are essentially silicon alloys (5 to 10% Si in general) often containing copper and magnesium in order to increase their mechanical characteristics, especially when hot. .
  • the main types used are as follows: AlSi7Mg, AlSi7CuMg, AlSi (5 to 8) Cu3Mg, AlSi10Mg, AlSi10CuMg.
  • These alloys are used with different methods of heat treatment: sometimes in the F-state without any treatment, sometimes in the T5 state with a simple income, sometimes in the T6 state with dissolution, quenching and drying. at the peak of hardening or slightly below, and often in the T7 state with dissolution, quenching and over-tempering or stabilization.
  • copper alloys of the AlCu5 type are also sometimes used. added with elements promoting the heat resistance such as Ni, Co, Ti, V and Zr: there is particularly in this category AlCu5NiCoZr and AlCu4NiTi. These alloys are very resistant to heat, especially at 300 ° C where they clearly outperform the silicon aluminum mentioned above, but suffer from two serious weaknesses: their high cracks, combined with a bad shrinkage behavior, which makes them very difficult.
  • Table 1 summarizes the characteristics at ambient temperature of these two sand-cast alloys heat-treated in the T7 state (Rp0.2 (or 0.2% TYS) being the elastic limit in MPa; Rm (or UTS) being the breaking strength in MPa, and A (or E) being elongation at break in%: Table 1 Alloy Rp0.2 (MPa) Rm (MPa) AT (%) AlCu4NiTi Unmeasurable 343 0.11 AlCu5NiCoZr 270 295 1
  • AlCu5Mg alloys such as AlCu5MgTi (designated as 204 AA), and A206 and B206 (AA), for room temperature or moderate working parts do not meet these requirements, particularly 300 ° C.
  • the alloys AlCu4NiTi and AlCu5NiCoZr (203 following AA) mentioned above are too weak and fragile at room temperature.
  • the invention is based on the finding by the applicant that it is possible to make very significant improvements to the characteristics mentioned above of the old alloy 224 (according to the AA), and thus to solve the problem posed, in particular by the addition of a limited amount of magnesium.
  • the addition of a small amount of magnesium, of the order of 0.10 to 0.15%, makes it possible to considerably increase the yield strength and the resistance of the alloy not only at room temperature but also hot, especially at 250-300 ° C and above. It is at room temperature that the relative gain is the most important: as explained in the following examples and Tables 6, 7, 8, the elastic limit goes from about 190 MPa without magnesium to about 340 MPa with only 0.09% and then at over 390 MPa with 0.13%. If we consider the average results obtained with 0.09% and 0.13% magnesium, the gains observed on the yield strength and the resistance at ambient temperature are remarkable: respectively + 96% and + 29% in relative terms.
  • the elongation is substantially reduced by half but still retains a suitable level of 6 to 8%.
  • the gains brought by the addition of magnesium remain even if they decrease.
  • the observed gains in yield strength and strength are respectively 35 and 13% in relative terms at 250 ° C, and 27 and 8% in relative terms at 300 ° C.
  • the addition of magnesium remains beneficial at least up to 300 ° C., especially as the loss of elongation fades at these high temperatures.
  • the addition of magnesium considerably improves the hot creep resistance, reducing by approximately 2, for example, the deformation observed after 300 h at 300 ° C. under a stress of 30 MPa.
  • the addition of magnesium therefore does not affect the hot stability, contrary to the philosophy that led to the definition of alloys AlCu5NiCoZr (203 following the AA) and AlCu5MnVZr (224 following the AA) conventional that are devoid of magnesium .
  • the alloy according to the invention treated T7 can be compared with the AlSi7Cu3.5Mg0.15MnVZrTi also treated T7, which was also developed by the applicant and is its most creep-resistant knowledge of the series of aluminum silicon alloys considered in the previous table.
  • the curve of the figure 3 shows the very great superiority of the AlCu4.7MnMgVZrTi, which deforms substantially 4 times less under the same conditions.
  • the magnesium content can be increased beyond the area already experienced in the examples. If only very high strength and hardness are sought, with a reduced ductility requirement, a maximum level of 0.38% can be envisaged, knowing that the burn temperature will be lowered and the heat treatment will have to be adapted. The minimum to obtain a significant curing effect is of the order of 0.05%. A smaller range is from 0.07% to 0.30% and the preferred range, corresponding to the resistance-ductility-creep tradeoffs quantified in the examples while having an industrially acceptable width is 0.08-0.20%, or even 0.09-1.03%.
  • the other elements are to be considered as impurities.
  • Table 4 A series of three alloy compositions described in Table 4 was developed in a 35 kg electric furnace, all elements being expressed in% by weight.
  • Table 4 landmark Yes Fe Cu mn mg Ti V Zr 0 Mg 0.09 0.14 4.83 0.34 0.00 0.18 0.21 0.14 0.09 Mg 0.08 0.14 4.74 0.33 0.09 0.22 0.17 0.13 0.13 Mg 0.09 0.14 4.81 0.33 0.13 0.20 0.17 0.13
  • FIG. figure 1 Du "(6.5 mm) diameter shell specimens of the Rio Tinto Alcan type, represented in FIG. figure 1 for tensile tests and ASTM B108 1 ⁇ 2 "(12.7 mm) shell test pieces to be used as blanks for 4 mm diameter creep specimens.
  • figure 1 is more particularly a cluster 10 of 4 test tubes 11 of Rio Tinto Alcan cast into shell with a diameter of the barrel 1 ⁇ 4 "(6.35 mm) .This cluster 10 takes, scale 1/2, the design of the ASTM specimen B108.
  • the burning temperature of the various compositions was first determined by performing differential enthalpic analyzes (AED) on pellets machined in the cast specimens. The rate of rise in temperature was 20 ° C / minute. The AED curves are represented at figure 2 . The burn temperatures observed corresponding to the melting peaks obviously depend on the magnesium content as shown in Table 5: Table 5 Content in Mg (%) Burning temperature (° C) 0 542.7 0.09 538.2 0.13 533.9
  • the burn temperature gradually shifts to lower temperatures when the Mg content increases from 0% to 0.09% and then to 0.13%.
  • the blanks intended for the creep tests were subjected, prior to this heat treatment, to hot isostatic compaction at 1000 bar at 485 ° C. for 2 hours in order to eliminate any microporosity which could seriously affect the tests given the small diameter of the specimen.
  • Static mechanical characteristics were measured at room temperature and at 250 ° C and 300 ° C. In the latter two cases, the specimens were preheated for 100 hours at the temperature before being tracted.
  • Table 6 Mechanical characteristics at room temperature Alloy Rp0.2 rm AT Mg (%) MPa MPa % 0 187.8 349.3 15.3 0.09 344.5 435.0 8.2 0.13 393.4 466.4 6.6 Alloy Rp0.2 rm AT Mg (%) MPa MPa % 0 134.7 199.5 10.7 0.09 172.2 223.7 7.3 0.13 191.4 228.8 12.2 Alloy Rp0.2 rm AT Mg (%) MPa MPa % 0 98.3 147.1 14.5 0.09 130.2 167.2 11.2 0.13 120.0 149.4 18.3
  • Table 9 summarizes the results: Table 9: Creep at 300 ° C. under 30 MPa Magnesium content (%) Deformation (in%) after 300h 0 0.26 0.09 0.13 0.13 0.14
  • a part may then be molded from the advantageous alloy defined above, this part may in particular be a cylinder head or an insert of a cylinder head or of another part requiring a high static mechanical resistance at room temperature and at room temperature. hot and high resistance to creep when hot, in particular at 300 ° C.
  • the part is advantageously treated T7, even if a T6 treatment is also possible.
  • Ablation molding is particularly suitable for molding high-tread alloys. Initially, it is sand casting that does not much upset the withdrawal, and then after removal of the mold the end of the solidification is carried out without rigid mold at all. In addition to providing a high solidification rate, the process also leads to high temperature gradients because the spray is generally progressive, starting on selected areas and advancing towards the end points of solidification where it is possible to attach. the weights. This advantageously also favors the use of alloys with low feed capacity of the shrink, such as copper aluminum alloys, including the alloy according to the invention.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (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)
  • Supercharger (AREA)

Claims (17)

  1. Formteil mit hoher statischer mechanischer Festigkeit bei Raumtemperatur und im warmen Zustand und mit hoher Beständigkeit gegen Warmfließen, insbesondere bei 300°C oder mehr, gegossen aus einer Aluminiumlegierung mit folgender chemischer Zusammensetzung, ausgedrückt in Gewichtsprozent:
    Si: 0.02 - 0.50%
    Fe: 0.02 - 0.30%
    Cu: 3.5 - 4.9%
    Mn: < 0.70%
    Mg: 0.05 - 0.20%
    Zn: < 0.30%
    Ni: < 0.30%
    V: 0.05 - 0.30%
    Zr: 0.05 - 0.25%
    Ti: 0.01 - 0.35%
    weitere Elemente insgesamt < 0,15% und jeweils weniger als 0.05%,
    Rest Aluminium.
  2. Formteil nach Anspruch 1, dadurch gekennzeichnet, dass der Magnesiumgehalt 0.07 - 0.20% beträgt.
  3. Formteil nach einem der Ansprüche 1 bis 2, dadurch gekennzeichnet, dass der Magnesiumgehalt 0.08 - 0.20% und bevorzugt 0.09 - 0.13% beträgt.
  4. Formteil nach einem der Ansprüche 1 bis 3, dadurch gekennzeichnet, dass der Kupfergehalt 3.8 - 4.9% und bevorzugt 4.0 - 4.8% beträgt.
  5. Formteil nach einem der vorhergehenden Ansprüche, dadurch gekennzeichnet, dass der Vanadiumgehalt 0.08 - 0.25% und bevorzugt 0.10 - 0.20% beträgt.
  6. Formteil nach einem der vorhergehenden Ansprüche, dadurch gekennzeichnet, dass der Zirkoniumgehalt 0.08 - 0.20% beträgt.
  7. Formteil nach einem der vorhergehenden Ansprüche, dadurch gekennzeichnet, dass der Titangehalt 0.05 - 0.25% und bevorzugt 0.10 - 0.20% beträgt.
  8. Formteil nach einem der vorhergehenden Ansprüche, dadurch gekennzeichnet, dass der Siliziumgehalt 0.02 - 0.20% und bevorzugt 0.02 - 0.06% beträgt.
  9. Formteil nach einem der vorhergehenden Ansprüche, dadurch gekennzeichnet, dass der Eisengehalt 0.02 - 0.20%, bevorzugt 0.02 - 0.12% und besonders bevorzugt 0.02 - 0.06% beträgt.
  10. Formteil nach einem der vorhergehenden Ansprüche, dadurch gekennzeichnet, dass der Mangangehalt 0.20 - 0.50% beträgt.
  11. Formteil nach einem der vorhergehenden Ansprüche, dadurch gekennzeichnet, dass der Zinkgehalt weniger als 0.10% und bevorzugt weniger als 0.03% beträgt.
  12. Formteil nach einem der vorhergehenden Ansprüche, dadurch gekennzeichnet, dass der Nickelgehalt weniger als 0.10% und bevorzugt weniger als 0.03% beträgt.
  13. Formteil nach einem der vorhergehenden Ansprüche, welches einer Wärmebehandlung vom Typ T7 oder T6 unterzogen wurde.
  14. Einsatz umfassend ein Formteil nach einem der Ansprüche 1 bis 13.
  15. Einsatz nach Anspruch 14, dadurch gekennzeichnet, dass der Einsatz im Wesentlichen aus dem Formteil besteht.
  16. Zylinderkopf umfassend ein Formteil nach einem der Ansprüche 1 bis 13 oder einen Einsatz nach irgendeinem der Ansprüche 14 und 15.
  17. Verfahren zum Formen eines Einsatzes nach irgendeinem der Ansprüche 14 und 15 oder eines Zylinderkopfes nach Anspruch 16, welches folgende Schritte aufweist:
    - Bereitstellen einer aus einem Zuschlagstoff und einem wasserlöslichen Bindemittel hergestellten Gussform;
    - Eingießen der Legierung in die Form;
    - Aufspritzen von Wasser auf die Form, um die Form zu zerlegen und den Einsatz bzw. den Zylinderkopf zu kühlen.
EP10799072.3A 2009-12-22 2010-12-07 Formteil aus cu enthaltender aluminium-legierung mit hohen mechanischer festigkeit und warmem kriechen Active EP2516687B1 (de)

Priority Applications (1)

Application Number Priority Date Filing Date Title
PL10799072T PL2516687T3 (pl) 2009-12-22 2010-12-07 Odlew ze stopu aluminium z miedzią, posiadający dużą wytrzymałość mechaniczną i trwałość w próbie pełzania na gorąco

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR0906218A FR2954355B1 (fr) 2009-12-22 2009-12-22 Piece moulee en alliage d'aluminium au cuivre a haute resistance mecanique et au fluage a chaud
PCT/FR2010/000812 WO2011083209A1 (fr) 2009-12-22 2010-12-07 Pièce moulée en alliage d'aluminium au cuivre à haute résistance mécanique et au fluage à chaud

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EP2516687A1 EP2516687A1 (de) 2012-10-31
EP2516687B1 true EP2516687B1 (de) 2016-08-10

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US (1) US20120258010A1 (de)
EP (1) EP2516687B1 (de)
JP (1) JP5758402B2 (de)
KR (1) KR101757013B1 (de)
BR (1) BR112012016917A2 (de)
CA (1) CA2812236C (de)
ES (1) ES2601809T3 (de)
FR (1) FR2954355B1 (de)
MX (1) MX2012006988A (de)
PL (1) PL2516687T3 (de)
WO (1) WO2011083209A1 (de)

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US10266933B2 (en) * 2012-08-27 2019-04-23 Spirit Aerosystems, Inc. Aluminum-copper alloys with improved strength
FR3007423B1 (fr) * 2013-06-21 2015-06-05 Constellium France Element de structure extrados en alliage aluminium cuivre lithium
US9643651B2 (en) 2015-08-28 2017-05-09 Honda Motor Co., Ltd. Casting, hollow interconnecting member for connecting vehicular frame members, and vehicular frame assembly including hollow interconnecting member
DE102016200535A1 (de) * 2016-01-18 2017-07-20 Bayerische Motoren Werke Aktiengesellschaft Verfahren zum Herstellen einer Aluminium-Gusslegierung
CN107419148A (zh) * 2017-05-05 2017-12-01 安徽彩晶光电有限公司 用于液晶电视支架的复合铝合金
CN112281034A (zh) * 2020-10-16 2021-01-29 中国航发北京航空材料研究院 一种铸造铝合金及其制备方法
US20220170138A1 (en) * 2020-12-02 2022-06-02 GM Global Technology Operations LLC Aluminum alloy for casting and additive manufacturing of engine components for high temperature applications
CN114058917A (zh) * 2021-10-29 2022-02-18 安徽省恒泰动力科技有限公司 应用于汽车发动机缸体的铝合金及其制备方法
CN114293077B (zh) * 2021-12-29 2022-09-30 北京理工大学 一种用于航空航天结构件的高强铝铜合金及制备方法
CN116005022B (zh) * 2023-02-08 2024-06-07 内蒙古蒙泰集团有限公司 一种高性能铸造铝硅合金及其制备方法

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Publication number Publication date
CA2812236A1 (fr) 2011-07-14
CA2812236C (fr) 2018-03-27
FR2954355B1 (fr) 2012-02-24
PL2516687T3 (pl) 2017-07-31
ES2601809T3 (es) 2017-02-16
US20120258010A1 (en) 2012-10-11
EP2516687A1 (de) 2012-10-31
KR20120114316A (ko) 2012-10-16
BR112012016917A2 (pt) 2016-04-12
JP2013515169A (ja) 2013-05-02
WO2011083209A1 (fr) 2011-07-14
JP5758402B2 (ja) 2015-08-05
MX2012006988A (es) 2012-07-03
KR101757013B1 (ko) 2017-07-11
FR2954355A1 (fr) 2011-06-24

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