EP1442150B1 - Alliages aluminium-silicium possedant des proprietes mecaniques ameliorees - Google Patents

Alliages aluminium-silicium possedant des proprietes mecaniques ameliorees Download PDF

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Publication number
EP1442150B1
EP1442150B1 EP02774155A EP02774155A EP1442150B1 EP 1442150 B1 EP1442150 B1 EP 1442150B1 EP 02774155 A EP02774155 A EP 02774155A EP 02774155 A EP02774155 A EP 02774155A EP 1442150 B1 EP1442150 B1 EP 1442150B1
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Prior art keywords
silicon
article
annealing
average
eutectic
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EP02774155A
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German (de)
English (en)
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EP1442150A1 (fr
Inventor
Erhard Ogris
Peter Uggowitzer
Josef Wöhrer
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Salzburger Aluminium AG
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Salzburger Aluminium AG
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Priority to SI200230502T priority Critical patent/SI1442150T1/sl
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    • 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
    • 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

Definitions

  • the invention relates to a method for improving the mechanical properties of aluminum-silicon alloys.
  • the invention relates to a heat treatment process for improving the material ductility of articles consisting of a preferably refined aluminum-silicon alloy containing cast iron or wrought alloy with eutectic phase fraction, which subjects the articles to an annealing treatment followed by aging become.
  • the invention relates to an article preferably comprising at least one finishing element, optionally magnesium and further alloy and / or impurity elements containing aluminum-silicon alloy having a eutectic phase portion consisting essentially of an ⁇ - Al - matrix and silicon precipitates.
  • Aluminum forms a simple eutectic system with silicon, with the eutectic point at a Si concentration of 12.5% by weight and a temperature of 577 ° C.
  • the residual melt can solidify eutectically, whereby in this silicon precipitates in a plate-like coarse form. It has long been the art to add sodium or strontium to such alloys and thereby hinder the growth of the silicon crystals upon solidification, which is referred to as refining, and is performed throughout to improve mechanical properties, particularly elongation at break.
  • an Al-Si alloy in state F usually has low material strength values R p and relatively high elongation at break values A.
  • a heat treatment state corresponding to T6 with a solution annealing at a temperature of for example 540 ° C with a period of 12 hours and a subsequent heat aging can significantly increase the strength of the material at approximately the same elongation at break of the samples or ductility of the material, compared with state F, be achieved.
  • the long solution annealing time makes it possible, for example, to advantageously diffuse magnesium atoms in the material, whereby, after quenching and heat aging of the article, finely divided Mg 2 Si precipitates are formed in the ⁇ - Al matrix, which precipitates significantly increase material strength.
  • Solution annealing treatments at high temperatures of long duration have the disadvantage of, as previously mentioned, gravitational creep of the part and a complex temperature-time treatment process. In many cases, therefore, for economic reasons, it is not necessary to achieve the highest strength and good ductility of the material by T6, and a treatment state T5 for the article is selected. The significantly lower material strength due to T5 must be compensated if necessary by design changes of the component.
  • the invention now aims to provide a new economical method of heat treatment, with which the ductility of the material can be significantly increased, without causing major drops in material strength compared with T6 or a much higher ductility and higher material strength compared with T5 is reached.
  • the object of the invention is achieved in that the solution annealing treatment as a flash annealing consisting of a rapid heating to an annealing temperature of 400 ° C - 555 ° C, a holding at this temperature with a holding time of at most 14.8 minutes and a subsequent forced cooling to substantially Room temperature is performed.
  • the solution annealing treatment as a flash annealing consisting of a rapid heating to an annealing temperature of 400 ° C - 555 ° C, a holding at this temperature with a holding time of at most 14.8 minutes and a subsequent forced cooling to substantially Room temperature is performed.
  • the advantages achieved by the invention are to be seen essentially in the fact that with a simple high-temperature - Kurzzeitglühung highest ductility values of the material can be achieved. Furthermore, a so-called impingement annealing causes little to no distortion of the component or delay of the article, so that, if necessary, no straightening of the same is required.
  • the short-time annealing treatment also has a high economy and can be easily incorporated into a manufacturing sequence, for example by means of a continuous furnace, an adjustment of the material strength can be done mostly by a coordinated technology of thermal aging.
  • the impact annealing is carried out with a holding time of less than 6.8 minutes, preferably with a period of 1.7 to optionally no more than 5 minutes, in the vast majority of Al-Si alloys achieved greatest ductility increases.
  • a heat aging of the object is carried out after the impact annealing, it is advantageous to set it at a temperature in the range between 150 ° C and 200 ° C with a duration of 1 to 14 hours.
  • the silicon precipitates are spheroidized in the eutectic phase portion and have an average sectional area of less than 2 microns 2 .
  • a solution annealing according to the prior art which is provided as a long-term annealing with 2 to 12 hours for a diffusion of hardening alloy components and their accumulation in the solid solution, as a side effect, although a spheroidization of the silicon particles, but these particles are due to the long Annealing time very large and roughly distributed, which can adversely affect the fracture behavior of the material.
  • a eutectic silicon network according to the invention can be spheroidized by a short-term pulse annealing even in small periods of a few minutes, whereby an advantageous microstructure of the material can be achieved. It is important that the temperature for the impact annealing as high as possible, but below the lowest melting phase, preferably 5 to 20 ° C below.
  • the silicon particles are subjected to a diffusion-controlled growth with increasing annealing time, wherein the initially low spheroidization density, ⁇ Si , decreases.
  • the work has shown that substantially all of the eutectic-containing Al-Si alloys can be provided with a structure according to the invention and the articles formed therefrom have high ductility values of the material. Particularly efficient are the increase in the quality and an improvement in the elongation at break when the object is produced in the thixocasting process.
  • the state values F, T4x3, T5, T6x3 and T6 are again compared with respect to the R p0.2 and the elongation at break A in the form of bars . Comparatively speaking, marked increases in the elongation at break values are again given.
  • the material can be cold (T4x3) or hot (T6x3) after 3 minutes of impact annealing in order to obtain superior elongation at break properties according to the invention.
  • Fig. 3 and Fig. 4 show scanning electron microscope - recordings of Si precipitates.
  • suitable binary images Up to an annealing time of 2 hours inclusive, the images were taken with the scanning electron microscope, after the cuts were previously etched for 30 seconds with a solution of 99.5% water and 0.5% hydrofluoric acid. After 4 hours of annealing, the cuts were etched with the cellar solution and the images could be taken with the light microscope. All images were then digitally reworked with the program Adobe Photoshop 5.0 and evaluated with the image analysis program Leica QWin V2.2, whereby the minimum detection area was 0.1 ⁇ m 2 .
  • Fig. 1 shows scanning electron microscope - recordings of Si precipitates.
  • FIG. 3 shows the material AlSi7Mg0,3 after a usual T6 annealing time of 12 hours by means of an SEM image.
  • Fig. 4 is the Microstructure of the same material after a 3-minute impact annealing treatment.
  • a spheroidization of the silicon precipitates can be seen after a short time (FIG. 4) and the diffusion-controlled growth of the same after long annealing times (FIG. 3).
  • FIG. 5 and FIG. 6 the average sectional area A Si of the silicon particles in the case of the Schliffprobung as a function of the annealing time at 540 ° C is shown. From the graph of FIG. 5 with a logarithmic time axis, the increase of the average sectional area of the Si particles indicating the particle size can be clearly seen. From the detailed illustration in FIG. 6, the diffusion-related increase in the mean silicon areas can be taken within the first 60 minutes. The increase in the average time of the silicon particles with the annealing time is highly dependent on the initial size of the Si particles in the eutectic.
  • FIG. 8 shows the decrease in the average spheroidization density, ⁇ Si , as a function of the annealing time.
  • the steep decrease of the average spheroidization density begins at 1.7 minutes and leads from a value of ⁇ Si ⁇ 10 to a pronounced loss of ductility. At higher annealing temperatures, this value can be reached after only 14 to 25 minutes, with a density value greater than 20 being required for superior high elongation at break values.
  • FIG. 9 shows the measured values with regard to yield strength and elongation at break, which result from Tab. 1, from 8 differently composed Al-Si alloys on the basis of a bar graph. For all alloys an increase in material ductility is achieved according to the invention. ⁇ U> Tab.

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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)
  • Manufacture Of Alloys Or Alloy Compounds (AREA)
  • Investigating And Analyzing Materials By Characteristic Methods (AREA)
  • Conductive Materials (AREA)
  • Silicon Compounds (AREA)
  • Heat Treatment Of Articles (AREA)
  • Powder Metallurgy (AREA)
  • Manufacture And Refinement Of Metals (AREA)
  • Crystals, And After-Treatments Of Crystals (AREA)
  • Refinement Of Pig-Iron, Manufacture Of Cast Iron, And Steel Manufacture Other Than In Revolving Furnaces (AREA)
  • Ceramic Products (AREA)
  • Laminated Bodies (AREA)

Claims (11)

  1. Procédé de traitement thermique pour l'amélioration de la ductilité d'objets en un alliage de fonderie ou de corroyage à base d'aluminium et de silicium, de préférence affiné ou raffiné, contenant éventuellement d'autres éléments d'addition et/ou des impuretés comme le magnésium, le manganèse, le fer et autres éléments similaires, avec une phase eutectique, lesquels objets sont soumis à un recuit suivi d'un durcissement par précipitation, caractérisé en ce que le traitement de recuit se déroule sous la forme d'un recuit flash, qui consiste en un échauffement rapide à une température de recuit comprise entre 400 et 555°C, un maintien à cette température pendant une durée maximum de 14,8 minutes, puis un refroidissement forcé jusqu'à atteindre sensiblement la température ambiante.
  2. Procédé selon la revendication 1, caractérisé en ce que le recuit flash est effectué avec un temps de maintien en température inférieur à 6,8 minutes, de préférence compris entre 1,7 minute minimum et éventuellement 5 minutes maximum.
  3. Procédé selon la revendication 1 ou la revendication 2, caractérisé en ce que le durcissement par précipitation de l'objet suivant le recuit flash se déroule à chaud, à une température comprise entre 150°C et 200°C pendant une durée comprise entre 1 et 14 heures.
  4. Procédé selon la revendication 1 ou la revendication 2, caractérisé en ce que le durcissement par précipitation de l'objet suivant le traitement de recuit flash se déroule à froid, c'est-à-dire à température sensiblement ambiante.
  5. Objet en alliage d'aluminium et de silicium contenant de préférence un élément de raffinage, éventuellement d'autres éléments d'addition et/ou des impuretés comme le magnésium, le manganèse, le fer et autres éléments similaires, avec une phase eutectique se composant pour l'essentiel d'une matrice αAl et de précipités de silicium, caractérisé en ce que les précipités de silicium présents dans la phase eutectique sont sphéroïdisés et présentent une section moyenne ASi inférieure à 4 µm2, avec A si = 1 n ∑ k = 1 n A ≤ 4  μ m 2
    Figure imgb0010
    ASi = section moyenne des particules de silicium, en µm2
    A = section moyenne des particules de silicium par image, en µm2
    n = nombre de photos ayant fait l'objet de mesures.
  6. Objet selon la revendication 5, caractérisé en ce que les précipités de silicium présents dans la phase eutectique sont sphéroïdisés et présentent une section moyenne inférieure à 2 µm2.
  7. Objet en alliage d'aluminium et de silicium contenant de préférence un élément de raffinage, éventuellement d'autres éléments d'addition et/ou des impuretés comme le magnésium, le manganèse, le fer et autres éléments similaires, avec une phase eutectique se composant pour l'essentiel d'une matrice αAl et de précipités de silicium, caractérisé en ce que le libre parcours moyen λSi entre les particules de silicium présentes dans la phase eutectique, défini comme étant la racine carrée d'une surface de mesure carrée divisée par le nombre de particules de silicium qu'elle contient, est inférieur à 4 µm, avec λ si = 1 n ∑ k = 1 n A Quadrat N Silizium ≤ 4 ⁢ μm
    Figure imgb0011
    λSi = distance moyenne entre les particules de Si
    Acarré = surface de référence carrée, en µm2
    Nsilicium = nombre de particules de silicium
    n = nombre d'images ayant fait l'objet de mesures.
  8. Objet selon la revendication 7, caractérisé en ce que le libre parcours moyen est inférieur à 3 µm, de préférence inférieur à 2 µm.
  9. Objet en alliage d'aluminium et de silicium contenant de préférence un élément de raffinage, éventuellement d'autres éléments d'addition et/ou des impuretés comme le magnésium, le manganèse, le fer et autres éléments similaires, avec une phase eutectique se composant pour l'essentiel d'une matrice αAl et de précipités de silicium, caractérisé en ce que la densité de sphéroïdisation ξSi, définie comme étant le nombre de particules de silicium eutectiques sphéroïdisées par 100 µm2, est supérieure à 10, avec ξ si = 1 n ∑ k = 1 n N si A × 100 ≥ 10
    Figure imgb0012
    ξSi = densité de sphéroïdisation moyenne des particules de silicium eutectique
    Nsilicium = nombre de particules de silicium
    A = surface de référence, en µm2
    n = nombre d'images ayant fait l'objet de mesures.
  10. Objet selon la revendication 9, caractérisé en ce que la densité de sphéroïdisation moyenne est supérieure à 20.
  11. Objet selon l'une quelconque des revendications 5 à 10, fabriqué suivant le procédé des revendications 1 à 4, caractérisé en ce qu'il est fabriqué par thixomoulage.
EP02774155A 2001-11-05 2002-11-05 Alliages aluminium-silicium possedant des proprietes mecaniques ameliorees Expired - Lifetime EP1442150B1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
SI200230502T SI1442150T1 (sl) 2001-11-05 2002-11-05 Aluminij-silicijeve zlitine z izboljšanimi mehanskimi lastnostmi

Applications Claiming Priority (3)

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AT0173301A AT411269B (de) 2001-11-05 2001-11-05 Aluminium-silizium-legierungen mit verbesserten mechanischen eigenschaften
AT17332001 2001-11-05
PCT/AT2002/000309 WO2003040423A1 (fr) 2001-11-05 2002-11-05 Alliages aluminium-silicium possedant des proprietes mecaniques ameliorees

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EP1442150B1 true EP1442150B1 (fr) 2007-01-03

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US (2) US20050000608A1 (fr)
EP (1) EP1442150B1 (fr)
JP (1) JP2005508446A (fr)
KR (1) KR20050043748A (fr)
CN (1) CN100366782C (fr)
AT (2) AT411269B (fr)
CA (1) CA2465683C (fr)
DE (1) DE50209192D1 (fr)
DK (1) DK1442150T3 (fr)
ES (1) ES2280578T3 (fr)
HK (1) HK1071171A1 (fr)
HU (1) HUP0401962A2 (fr)
PT (1) PT1442150E (fr)
SI (1) SI1442150T1 (fr)
WO (1) WO2003040423A1 (fr)

Cited By (1)

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DE102011105447A1 (de) 2011-06-24 2012-12-27 Audi Ag Verfahren zur Wärmebehandlung von Aluminium-Druckgussteilen sowie hiermit hergestellte Aluminium-Druckgussteile und eine hierfür geeignete Gießzelle

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US8950468B2 (en) 2007-05-11 2015-02-10 The Boeing Company Cooling system for aerospace vehicle components
DE102008024524A1 (de) * 2008-05-21 2009-11-26 Bdw Technologies Gmbh Verfahren und Anlage zur Herstellung eines Gussbauteils
CN107586939A (zh) * 2017-09-13 2018-01-16 中信戴卡股份有限公司 一种用于铝合金铸旋车轮的热处理方法
CN109706411A (zh) * 2019-02-18 2019-05-03 东莞宏幸智能科技有限公司 一种铝合金零部件生产用固熔炉
CN115961223A (zh) * 2022-12-19 2023-04-14 湖南中创空天新材料股份有限公司 一种去除残余应力的方法

Family Cites Families (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0747807B2 (ja) * 1992-03-17 1995-05-24 スカイアルミニウム株式会社 成形加工用アルミニウム合金圧延板の製造方法
JPH07166285A (ja) * 1993-06-08 1995-06-27 Shinko Alcoa Yuso Kizai Kk 焼付硬化型Ａｌ合金板及びその製造方法
JPH11613A (ja) * 1997-06-13 1999-01-06 Kawasaki Steel Corp 成形性および塗装焼付硬化性に優れたアルミニウム合金板の製造方法
US6040059A (en) * 1997-11-18 2000-03-21 Luk Gmbh & Co. Component made of an aluminium silicon cast alloy
US5985349A (en) * 1998-11-12 1999-11-16 Kraft Foods, Inc. Method for manufacture of grated cheese
DE19901508A1 (de) * 1999-01-16 2000-08-17 Bayerische Motoren Werke Ag Verfahren zur Herstellung von Gußteilen aus Aluminiumlegierungen
DE19925666C1 (de) * 1999-06-04 2000-09-28 Vaw Motor Gmbh Zylinderkopf- und Motorblockgußteil
JP2001316747A (ja) * 1999-08-31 2001-11-16 Asahi Tec Corp 非Ｃｕ系鋳造Ａｌ合金とその熱処理方法
JP3857503B2 (ja) * 2000-07-26 2006-12-13 大同メタル工業株式会社 アルミニウム系軸受合金
DE60336534D1 (de) * 2002-01-11 2011-05-12 Gen Hospital Corp Vorrichtung zur OCT Bildaufnahme mit axialem Linienfokus für verbesserte Auflösung und Tiefenschärfe

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102011105447A1 (de) 2011-06-24 2012-12-27 Audi Ag Verfahren zur Wärmebehandlung von Aluminium-Druckgussteilen sowie hiermit hergestellte Aluminium-Druckgussteile und eine hierfür geeignete Gießzelle

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AT411269B (de) 2003-11-25
ES2280578T3 (es) 2007-09-16
HUP0401962A2 (hu) 2005-01-28
HK1071171A1 (en) 2005-07-08
US20050000608A1 (en) 2005-01-06
ATA17332001A (de) 2003-04-15
KR20050043748A (ko) 2005-05-11
CA2465683C (fr) 2011-01-18
SI1442150T1 (sl) 2007-06-30
US20100193084A1 (en) 2010-08-05
CN1602368A (zh) 2005-03-30
EP1442150A1 (fr) 2004-08-04
CN100366782C (zh) 2008-02-06
JP2005508446A (ja) 2005-03-31
ATE350507T1 (de) 2007-01-15
CA2465683A1 (fr) 2003-05-15
DK1442150T3 (da) 2007-05-14
DE50209192D1 (de) 2007-02-15
PT1442150E (pt) 2007-04-30
WO2003040423A1 (fr) 2003-05-15

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