EP2329053B1 - Guss aus aluminiumlegierung mit hoher heisskriechfestigkeit und ermüdungsbeständigkeit - Google Patents

Guss aus aluminiumlegierung mit hoher heisskriechfestigkeit und ermüdungsbeständigkeit Download PDF

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Publication number
EP2329053B1
EP2329053B1 EP09802550.5A EP09802550A EP2329053B1 EP 2329053 B1 EP2329053 B1 EP 2329053B1 EP 09802550 A EP09802550 A EP 09802550A EP 2329053 B1 EP2329053 B1 EP 2329053B1
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Prior art keywords
cast part
part according
content
alloys
magnesium
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English (en)
French (fr)
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EP2329053A1 (de
Inventor
Michel Garat
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Rio Tinto Alcan International Ltd
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Rio Tinto Alcan International Ltd
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Priority to PL09802550T priority Critical patent/PL2329053T3/pl
Priority to SI200931665A priority patent/SI2329053T1/sl
Publication of EP2329053A1 publication Critical patent/EP2329053A1/de
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Priority to HRP20170809TT priority patent/HRP20170809T1/hr
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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
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • C22C21/04—Modified aluminium-silicon alloys
    • 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
    • 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
    • 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
    • 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
    • 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
    • F05C2201/906—Phosphor-bronze alloy

Definitions

  • the invention relates to molded aluminum alloy parts 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.
  • alloys commonly used for the cylinder heads of automotive mass-produced vehicles are on the one hand alloys of the AlSi7Mg and AlSi10Mg type, optionally “doped” by an addition of 0.50% to 1% of copper, and on the other hand alloys of the AlSi5 family at 9Cu3Mg.
  • the alloys of the first type, AlSi7 (Cu) Mg and AlSi10 (Cu) Mg treated T5 (simple stabilization) and T7 (complete solution treatment, quenching and over-tempering) have sufficient mechanical properties up to about 250 ° C, but not at 300 ° C, which will nevertheless be reached by the inter-valve jumpers of the new generations of supercharged common-rail diesel engines, or even new gasoline engines with double turbocharging.
  • alloys of the type AlSi5 to 9Cu3Mg0.25 to 0.5 which have a better resistance to heat, have on the other hand a rather low ductility which makes them very vulnerable to thermal fatigue cracking.
  • FR 2 690 927 proposes aluminum-based casting alloys with good creep resistance and with additions of 0.1-0.2% Ti, 0.1-0.2% Zr and 0.2-0.4% V, especially on a type A composition basis -S5U3G.
  • Figures 1, 2 and 3 represent the breaking stress (successively with a breaking probability of 5% in bright lines on the left, 50% in dark lines in the middle and 95% in bright lines on the right) as a function of the number of cycles.
  • the invention is based on the finding by the Applicant that it is possible to make significant improvements to the characteristics mentioned above of AlSi7Cu3.5MnVZrTi alloy according to the patents FR 2,857,378 and EP 1 651 787 of the applicant, and thus solve the objective problem, in two complementary ways: the addition of a small amount of magnesium and a combined addition of vanadium.
  • Table 2 indicates, depending on the amount of magnesium added, the amounts of Al2Cu and Q-Al5Mg8Si6Cu2 hardening phases formed in the base AlSi7Cu3.5MnVZrTi, at equilibrium at 200 ° C., after a setting of solution followed by quenching.
  • the values (in this case, in atomic%) are calculated using the "Prophase" thermodynamic simulation software developed by the Applicant.
  • Table 2 Mq (% by weight) 0.00 0.05 0.07 0.10 0.14 0.19 Al2Cu 4.26 4.23 4.22 4.19 4.16 4.12 Q-Al5Mg8Si6Cu2 0.00 0.15 0.23 0.35 0.49 0.67
  • the gain on the elastic limit at 20 ° C is substantially 100 MPa (from 200 to about 300 MPa) with an addition of only 0.10%.
  • the effect of magnesium is absolutely not linear in the range 0 to 0.20%: it is indeed negligible between 0 and 0.05%, intense between 0.05 and 0.10% and a plateau is then observed to a level of substantially 0.20%.
  • magnesium no longer has a significant effect on the endurance limit, of the order of 130 MPa to 10 7 cycles, still according to the figure 6 .
  • the alloys of Al type Al Si5Cu3 and AlSi7Cu3 according to the invention do not exhibit the final quaternary eutectic Al-Si-Al2Cu-Al5Mg8Si6Cu2, melting at 507 ° C according to the HWL Philips phase diagrams (Equilibrium Diagrams of Aluminum Alloy Systems, The Aluminum Development Association, Information Bulletin 25. London.1961) or at 508 ° C according to other authors. Indeed, their melting start temperature, determined by differential scanning calorimetry (DSC), is substantially at 513 ° C., as shown in FIG. figure 9 .
  • DSC differential scanning calorimetry
  • magnesium a high diffusion coefficient eutectic element, participates in the structural hardening after tempering, by formation of intermetallic phases coherent with the aluminum matrix, in this case via the Q phase mentioned above, but progressively loses its hardening effect by coalescing said phase at 300 ° C and higher.
  • vanadium, peritectic element with very low diffusion coefficient is present in solid solution enriched in the heart of dendrites and can possibly precipitate in the form of only semi-coherent dispersoids Al-V-Si which remain stable at high temperatures above 400 ° C.
  • Vanadium addition greater than 0.21% is possible and is just as beneficial for creep resistance, but the solubility of vanadium in the liquid alloy is limited.
  • the equilibrium solubility as a function of the bath holding temperature is shown in FIG. figure 10 .
  • the bath in order to maintain a 0.25% vanadium solution, the bath must be kept at a temperature of at least 745 ° C, a relatively high value for the casting of "shell” yokes (metal mold permanent) by gravity or low pressure.
  • thermomechanical stress experienced by each particular model of part one can choose a level of tolerance adapted iron, knowing that the "high purity", especially with regard to iron, is a cost factor.
  • a level of tolerance adapted iron knowing that the "high purity", especially with regard to iron, is a cost factor.
  • the copper content of such hot-resistant alloys is typically in the range of 2 to 5%. Preferably, the range will be between 2.5%, to ensure a sufficiently high yield strength and heat resistance, and 4.2%, the approximate solubility limit of copper in a base containing from 4.5 to 10% of silicon and up to 0.25% of magnesium with dissolution at a temperature of less than or equal to 513 ° C.
  • Manganese the Applicant has already identified in previous research described in the aforementioned article, published in "Men and Foundry” of February 2008, a manganese content of 0.08 to 0.20% improved the effect of zirconium on the resistance to creep at 300 ° C.
  • Titanium acts in two joint modes: on the one hand, it promotes the refining of the primary aluminum grain, on the other hand, it contributes to creep resistance, as identified in the patent FR 2 841 164 , participating in the formation of AlSiZrTi dispersoid phases.
  • Another way to refine the eutectic AISi is to add antimony (from 0.05 to 0.25%).
  • Heat treatment the molded parts according to the invention are generally subjected to a heat treatment including dissolution, quenching and tempering.
  • the dissolution of the alloys L to T was shortened at 5 h instead of 10 h.
  • the resistance to mechanical fatigue at ambient temperature was measured in tension-compression, with a ratio R (minimum stress / maximum stress) of -1 for round test pieces with a diameter of 5 mm, also machined in the AFNOR shell blanks.
  • the creep tests at 300 ° C. were carried out on test pieces machined to a diameter of 4 mm from the same AFNOR blanks, preheated for 100 hours at 300 ° C. before the actual test.
  • the elastic limit increases by approximately 100 MPa while the fatigue life of the oligocyclic fatigue in the range extending from 220 to 270 MPa is multiplied by almost 10.
  • vanadium has no significant effect on these two properties measured at room temperature.
  • the increase of the copper content from 3.5 to 4.0% results in a gain of about 30 MPa on the yield strength and 15 MPa on the ultimate strength, but also by a loss of 1% on the lengthening, as shown by the comparison of figures 4 and 5 .
  • the figure 7 further indicates that the joint additions of magnesium between 0.07 and 0.19% and vanadium between 0.17 and 0.21% can improve by approximately 8% the yield strength.
  • the figure 8 allows to better visualize the importance of the interaction between vanadium and magnesium on the creep resistance at 300 ° C.

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  • Chemical & Material Sciences (AREA)
  • Mechanical Engineering (AREA)
  • Organic Chemistry (AREA)
  • Metallurgy (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Cylinder Crankcases Of Internal Combustion Engines (AREA)
  • Cookers (AREA)
  • Manufacture Of Alloys Or Alloy Compounds (AREA)
  • Manufacture And Refinement Of Metals (AREA)

Claims (15)

  1. Gussteil mit hoher statischer mechanischer Festigkeit, Ermüdungsbeständigkeit und Kriechfestigkeit bei hohen Temperaturen, insbesondere bei 300°C, aus einer Aluminiumlegierung mit folgender chemischer Zusammensetzung, ausgedrückt in Gewichtsprozent:
    Si : 3 - 11 %
    Fe: < 0.50 %
    Cu: 2.0 - 5.0 %
    Mn: 0.05 - 0.50 %
    Mg: 0.10 - 0.25 %
    Zn: < 0.30 %
    Ni: < 0.30 %
    V: 0.05 - 0.19 %
    Zr: 0.05 - 0.25 %
    Ti: 0.01 - 0.25 %
    eventuell ein oder mehrere Elemente zur Modifizierung des Eutektikums, ausgewählt unter Sr: 30 - 500 ppm, Na: 20 - 100 ppm und Ca: 30 - 120 ppm, oder Elemente zur Feinung des Eutektikums, Sb: 0.05 - 0.25 %,
    weitere Elemente jeweils < 0.05% und insgesamt 0.15 %, Rest Aluminium.
  2. Gussteil nach Anspruch 1, dadurch gekennzeichnet, dass der Siliziumgehalt 5.0 bis 9.0 % beträgt.
  3. Gussteil nach einem der Ansprüche 1 oder 2, dadurch gekennzeichnet, dass der Magnesiumgehalt 0.10 bis 0.20 % beträgt.
  4. Gussteil nach einem der Ansprüche 1 bis 3, dadurch gekennzeichnet, dass der Vanadiumgehalt 0.08 bis 0.19 % beträgt.
  5. Gussteil nach einem der Ansprüche 1 bis 4, dadurch gekennzeichnet, dass der Eisengehalt weniger als 0.30 % beträgt.
  6. Gussteil nach einem der Ansprüche 1 bis 5, dadurch gekennzeichnet, dass der Kupfergehalt 2.5 bis 4.2 % beträgt.
  7. Gussteil nach einem der Ansprüche 1 bis 6, dadurch gekennzeichnet, dass der Mangangehalt 0.08 bis 0.20 % beträgt.
  8. Gussteil nach einem der Ansprüche 1 bis 7, dadurch gekennzeichnet, dass der Zinkgehalt weniger als 0.10 % beträgt.
  9. Gussteil nach einem der Ansprüche 1 bis 8, dadurch gekennzeichnet, dass der Nickelgehalt weniger als 0.10 % beträgt.
  10. Gussteil nach einem der Ansprüche 1 bis 9, dadurch gekennzeichnet, dass der Zirkoniumgehalt 0.08 bis 0.20 % beträgt.
  11. Gussteil nach einem der Ansprüche 1 bis 10, dadurch gekennzeichnet, dass der Titangehalt 0.05 bis 0.20 % beträgt.
  12. Gussteil nach einem der Ansprüche 1 bis 11, dadurch gekennzeichnet, dass der Kupfergehalt 3.0 bis 4.0 % beträgt.
  13. Gussteil nach einem der Ansprüche 1 bis 12, dadurch gekennzeichnet, dass der Vanadiumgehalt 0.10 bis 0.19 % beträgt.
  14. Gussteil nach einem der Ansprüche 1 bis 13, dadurch gekennzeichnet, dass es ein Zylinderkopf eines Verbrennungsmotors ist.
  15. Gussteil nach einem der Ansprüche 1 bis 14, dadurch gekennzeichnet, dass es ein Einsatz für den heißen Teil eines Gussteils ist.
EP09802550.5A 2008-07-30 2009-07-01 Guss aus aluminiumlegierung mit hoher heisskriechfestigkeit und ermüdungsbeständigkeit Active EP2329053B1 (de)

Priority Applications (3)

Application Number Priority Date Filing Date Title
PL09802550T PL2329053T3 (pl) 2008-07-30 2009-07-01 Odlew ze stopu glinu o wysokiej wytrzymałości na zmęczenie i odporności na pełzanie wysokotemperaturowe
SI200931665A SI2329053T1 (sl) 2008-07-30 2009-07-01 Ulitek, izdelan iz aluminijeve zlitine, z visoko odpornostjo proti utrujenosti in vročemu lezenju
HRP20170809TT HRP20170809T1 (hr) 2008-07-30 2017-05-29 Lijevani komad od legure aluminija s jakom izdržljivošću na visoke temperature i otpornošću na zamor materijala

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR0804333A FR2934607B1 (fr) 2008-07-30 2008-07-30 Piece moulee en alliage d'aluminium a hautes resistances a la fatigue et au fluage a chaud
PCT/FR2009/000807 WO2010012875A1 (fr) 2008-07-30 2009-07-01 Pièce moulée en alliage d'aluminium à hautes résistances à la fatigue et au fluage à chaud

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EP2329053A1 EP2329053A1 (de) 2011-06-08
EP2329053B1 true EP2329053B1 (de) 2017-03-08

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US (1) US9982328B2 (de)
EP (1) EP2329053B1 (de)
JP (1) JP5437370B2 (de)
KR (1) KR101639826B1 (de)
BR (1) BRPI0916529B1 (de)
DK (1) DK2329053T3 (de)
ES (1) ES2625872T3 (de)
FR (1) FR2934607B1 (de)
HR (1) HRP20170809T1 (de)
HU (1) HUE033493T2 (de)
LT (1) LT2329053T (de)
MX (1) MX2011000739A (de)
PL (1) PL2329053T3 (de)
PT (1) PT2329053T (de)
SI (1) SI2329053T1 (de)
WO (1) WO2010012875A1 (de)

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JP7011942B2 (ja) * 2018-01-19 2022-02-10 昭和電工株式会社 磁気記録媒体用アルミニウム合金基板、磁気記録媒体用基板、磁気記録媒体およびハードディスクドライブ
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CN108588513A (zh) * 2018-08-10 2018-09-28 合肥工业大学 一种改性a356铝合金及其多次时效热处理方法
CN112553508B (zh) * 2019-09-10 2022-03-18 比亚迪股份有限公司 铝合金及其制备方法和铝合金结构件
CN111690850A (zh) * 2020-07-15 2020-09-22 南通鸿劲金属铝业有限公司 一种高屈服强度铸造铝合金制备工艺
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FR2934607A1 (fr) 2010-02-05
US9982328B2 (en) 2018-05-29
BRPI0916529A2 (pt) 2015-11-10
KR101639826B1 (ko) 2016-07-14
HUE033493T2 (en) 2017-12-28
PL2329053T3 (pl) 2017-08-31
ES2625872T3 (es) 2017-07-20
MX2011000739A (es) 2011-02-24
WO2010012875A1 (fr) 2010-02-04
PT2329053T (pt) 2017-05-24
FR2934607B1 (fr) 2011-04-29
SI2329053T1 (sl) 2017-07-31
JP5437370B2 (ja) 2014-03-12
KR20110050652A (ko) 2011-05-16
US20110126947A1 (en) 2011-06-02
LT2329053T (lt) 2017-07-10
JP2011529529A (ja) 2011-12-08
EP2329053A1 (de) 2011-06-08
BRPI0916529B1 (pt) 2018-06-05
HRP20170809T1 (hr) 2017-08-11
DK2329053T3 (en) 2017-05-15

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