EP2471966B1 - Alliage AISi ductile pouvant facilement être moulé et procédé de fabrication d'une pièce moulée en utilisant l'alliage de moulage AISi - Google Patents

Alliage AISi ductile pouvant facilement être moulé et procédé de fabrication d'une pièce moulée en utilisant l'alliage de moulage AISi Download PDF

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Publication number
EP2471966B1
EP2471966B1 EP11009896.9A EP11009896A EP2471966B1 EP 2471966 B1 EP2471966 B1 EP 2471966B1 EP 11009896 A EP11009896 A EP 11009896A EP 2471966 B1 EP2471966 B1 EP 2471966B1
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EP
European Patent Office
Prior art keywords
alloy
alsi
cast
ductile
casting
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.)
Revoked
Application number
EP11009896.9A
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German (de)
English (en)
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EP2471966A1 (fr
Inventor
Hubert Dr. Koch
Marcel Dr. Rosefort
Andreas Dr. Kleine
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Trimet Aluminium SE
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Trimet Aluminium SE
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Application filed by Trimet Aluminium SE filed Critical Trimet Aluminium SE
Priority to PL11009896T priority Critical patent/PL2471966T3/pl
Publication of EP2471966A1 publication Critical patent/EP2471966A1/fr
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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
    • 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

Definitions

  • the invention relates to a readily castable, ductile AlSi alloy consisting of 6-11.8% silicon, 0.02-0.5% magnesium, 0.005-0.7% manganese, 0.0005-0.6% copper, 0.001-0.06% titanium, 0.03-0.3% iron, and max. 0.2% molybdenum and max. 0.2% zirconium, optionally 70-400 ppm strontium,
  • the invention further relates to a method for producing a thin-walled casting with a wall thickness of 1.0 - 50 mm.
  • unrefined AlSi materials solidify either lamellar or grainy, with a lamellar structure often resulting in surface defects and possibly also sticking in the mold. Therefore, the granular structure which can be refined by adding strontium or sodium is preferred.
  • the task was to develop a highly castable, ductile AlSi alloy for highly stressed high-volume parts, which already has a minimum strength Rp 0.2 of 60 MPa and an elongation of greater than 7% in the cast state, or a finite strength greater in the finished state 100 MPa or an elongation greater than 10% achieved.
  • the structure produced under the conditions described does not contain large or even plate-like precipitates, but is characterized by many small finely divided particles interdendritically incorporated into the AlSi structure.
  • large particles is meant a particle diameter of about 5 - 10 microns.
  • the microstructure consists only of the eutectic and, together with it, the most finely divided intermetallic phases crystallized.
  • FIG. 1 shows a plan view of a gray cast iron mold as a detail of the experimental setup for the production of test specimens by means of chill casting, consisting of the mold 1, a cutout for chill casting with length L, height H, and feeder. 2
  • FIG. 2a shows a Kokillengussstab 3 before processing in side view and as a cross section AA with height H and width B
  • FIG. 2 B the formation of the chill casting rod in the form of a test bar 4 after mechanical processing.
  • FIG. 3 is a Druckgussprobeplatte 5 with the longitudinal side LS and the broad side BS immediately after removal from the die mold visible.
  • the sample plate 5 comprises front overflows 5.1 to 5.4 with ejector openings 7.1 to 7.4 and rear overflows 6.1, 6.2. Furthermore, a sprue 8 and a vacuum connection 9 can be seen. From the die casting plate, the flat tensile bars for the later taken from tensile tests. The flat sides of the sample page are not processed.
  • FIG. 4 the processed tensile test is shown. It was removed from the die casting sample plate in the manner described above.
  • the alloy table in FIG. 5 shows the composition in weight percent of 6 prior art alloys (Nos. 1-6) and 6 alloys with the composition of the present invention (Nos. 7-12).
  • the alloy contents were specified for the alloy constituents specified in the patent claims, the remainder being aluminum and production-related impurities to be completed in accordance with DIN EN 1676, June 2010 edition.
  • FIG. 6a, b contains the test tables with information on the casting process, the heat treatment, the strength values and the elongation values for alloys according to the prior art and for the alloys according to the invention. Details of the experiments are given at the end of the description.
  • FIG. 7a . b and 8a . b show micrographs of prior art alloys (Alloy Nos. 1 and 5) and alloys having the composition of the present invention (Alloy Nos. 7 and 11).
  • the micrographs of the alloys according to the invention (Alloy No. 7, AlSi 7 with 4 ppm phosphorus and die casting alloy No. 11 with 1 ppm phosphorus) have a refined structure, although the alloys have no Refining additives included.
  • the standard AlSi 7 alloy (alloy No. 1) exhibits a microstructure with primary silicon particles which has a lamellar structure and therefore can be expected to have unfavorable processing properties (micrograph FIG. 7a with dark primary silicon particles in the middle).
  • Even a standard AlSi 11 die-cast alloy shows an unfavorable lamellar structure (see micrograph FIG. 7b with primary silicon particles at the lower right edge) (Alloy No. 5).
  • the alloys 7 and 9a according to the invention have significantly higher conductivities with 26.4 (AlSi 7) and 22.2 (AlSi 7 Mg 0.3), which makes it possible to conclude a fine and uniform microstructure.
  • This result was based on micrographs, eg FIG. 8a . b , checked. It can be seen from this that the alloys composed according to the invention without finishing additives, for example Nos. 7 and 8, had the typical structural features of a finished structure.
  • the unrefined AlSi 7 alloy shows in the micrograph FIG. 8a naturally less quantitatively eutectic than the AlSi 11 alloy according to microsection FIG. 8b but both show a pronounced refined structure.
  • Phosphorus favors the early nucleation of silicon and leads to a granular solidification morphology. To form a fine eutectic phase with a small proportion of finely divided FeSi phases, however, excessive overcooling of the melt must be prevented.
  • the alloy was melted in a 60 kg crucible and heated to a temperature of about 730 ° C. This was followed by a degassing treatment by means of a rotor. Nitrogen was introduced as the gas. After a standing time of approx. 20 min, samples were taken according to FIG. 2a in an open mold according to FIG. 1 decanted. These samples were then analyzed according to FIG. 2 B Tension rods were removed and either cast as cast to EN 10002-1: 2001 (D) or subjected to a T6 heat treatment (535 ° C / 6h, water quenched, 180 ° C / 6h air cooled) and then tested.
  • a T6 heat treatment 535 ° C / 6h, water quenched, 180 ° C / 6h air cooled
  • the individual alloy variants were melted and brought to a temperature of 720 ° C. Casting was done on a 850 t die casting machine. The filling chamber was filled manually. The mold was provided with a vacuum vent to prevent air or mold inclusion in the sample.
  • FIG. 4 shows a tensile test made from a die casting plate FIG. 3 , These test pieces were made according to EN 10002-1: 2001 (D) with a thickness of 3 mm from the die casting plate according to FIG. 3 machined and torn on a tensile testing machine according to EN 10002-1: 2001 (D).
  • test bars with a P content ⁇ 5 ppm were always far superior in terms of elongation.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Conductive Materials (AREA)
  • Continuous Casting (AREA)

Claims (3)

  1. Alliage AlSi ductile possédant une bonne coulabilité, constitué par :
    de 6 à 11,8 % de silicium ;
    de 0,02 à 0,5 % de magnésium ;
    de 0,005 à 0,7 % de manganèse ;
    de 0,0005 à 0,6 % de cuivre ;
    de 0,001 à 0,06 % de titane ;
    de 0,03 à 0,3 % de fer ;
    et au maximum 0,2 % de molybdène et au maximum 0,2 % de zirconium ;
    et le cas échéant, de 70 à 400 ppm de strontium ;
    le reste étant de l'aluminium et des impuretés liées à la fabrication conformément à la norme DIN EN 1676, édition de juin 2010, caractérisé en ce que l'alliage présente, pour la suppression de la phase primaire de silicium, une teneur en phosphore de 0,00001 à 0,0005 %, et la teneur respective en magnésium est liée à la teneur en silicium conformément à l'équation suivante :
    Mg ≤ 1,018 à 0,083% de Si.
  2. Alliage AlSi ductile possédant une bonne coulabilité qui, à l'état de fonte et non enrichi, présente une résistance minimale Rp0,2 de 60 MPa et un allongement supérieur à 7 %, selon la revendication 1, caractérisé en ce que la conductibilité, à l'état de fonte, que l'on mesure avec la sonde de Fôrster, dans le cas des alliages AlSi, est supérieure à 26 m/Ω mm2, et dans le cas des alliages AlSiMg, est supérieure à 22 m/Ω mm2.
  3. Procédé pour la fabrication d'une pièce coulée à paroi mince (épaisseur de paroi de 1,0 à 50 mm) avec un alliage AlSi ductile possédant une bonne coulabilité selon l'une quelconque des revendications précédentes 1 à 2, caractérisé en ce qu'on coule l'alliage dans la coulée en lingotière à une température de la paroi de la lingotière dans la plage de 80 à 250 °C et avec un temps de solidification locale dans la plage de 5 à 30 secondes, ou dans le procédé de coulée sous pression avec un temps de solidification locale dans la plage de 5 à 40 millisecondes avec un espace entre les bras dendritiques DAS de 5 µm à 60 µm.
EP11009896.9A 2010-12-17 2011-12-16 Alliage AISi ductile pouvant facilement être moulé et procédé de fabrication d'une pièce moulée en utilisant l'alliage de moulage AISi Revoked EP2471966B1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
PL11009896T PL2471966T3 (pl) 2010-12-17 2011-12-16 Łatwo odlewalny, ciągliwy stop alsi oraz sposób wytwarzania odlewu z użyciem stopu odlewniczego alsi

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
DE102010550116 2010-12-17

Publications (2)

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EP2471966A1 EP2471966A1 (fr) 2012-07-04
EP2471966B1 true EP2471966B1 (fr) 2014-09-03

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EP11009896.9A Revoked EP2471966B1 (fr) 2010-12-17 2011-12-16 Alliage AISi ductile pouvant facilement être moulé et procédé de fabrication d'une pièce moulée en utilisant l'alliage de moulage AISi

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EP (1) EP2471966B1 (fr)
ES (1) ES2527727T3 (fr)
PL (1) PL2471966T3 (fr)

Families Citing this family (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103911528A (zh) * 2013-01-06 2014-07-09 德尔福技术有限公司 用于压铸工艺的高耐腐蚀性铝合金
DE102014226389A1 (de) * 2014-12-18 2016-06-23 Bayerische Motoren Werke Aktiengesellschaft Verfahren zum zerstörungsfreien Ermitteln von Werkstoffkennwerten
CN107923004B (zh) * 2015-08-13 2021-12-14 美铝美国公司 改善的3xx铝铸造合金及其制备方法
CN106676296A (zh) * 2016-12-29 2017-05-17 新疆众和股份有限公司 一种zld102铝合金的生产工艺
DE102021131973A1 (de) 2021-12-03 2023-06-07 Audi Aktiengesellschaft Aluminium-Druckgusslegierung
CN114855033A (zh) * 2022-05-20 2022-08-05 重庆渝江压铸有限公司 一种高延伸率铝合金及其制备方法
CN115418537B (zh) * 2022-10-31 2023-03-24 小米汽车科技有限公司 一种免热处理压铸铝合金及其制备方法和应用
DE102024121750A1 (de) * 2024-07-31 2026-02-05 Bayerische Motoren Werke Aktiengesellschaft Legierung

Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE10323741B3 (de) * 2003-05-24 2004-10-14 Daimlerchrysler Ag Hoch- und warmfeste, zähe Al-Gusslegierungen

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JP4148801B2 (ja) * 2003-03-06 2008-09-10 住友軽金属工業株式会社 切削性に優れた耐摩耗Ａｌ−Ｓｉ系合金及びその鋳造方法
US6923935B1 (en) * 2003-05-02 2005-08-02 Brunswick Corporation Hypoeutectic aluminum-silicon alloy having reduced microporosity

Patent Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE10323741B3 (de) * 2003-05-24 2004-10-14 Daimlerchrysler Ag Hoch- und warmfeste, zähe Al-Gusslegierungen

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EP2471966A1 (fr) 2012-07-04
PL2471966T3 (pl) 2015-03-31
ES2527727T3 (es) 2015-01-29

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