US20050000608A1 - Aluminum-silicon alloys having improved mechanical properties - Google Patents

Aluminum-silicon alloys having improved mechanical properties Download PDF

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Publication number
US20050000608A1
US20050000608A1 US10/837,665 US83766504A US2005000608A1 US 20050000608 A1 US20050000608 A1 US 20050000608A1 US 83766504 A US83766504 A US 83766504A US 2005000608 A1 US2005000608 A1 US 2005000608A1
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United States
Prior art keywords
article
silicon
aluminum
treatment
silicon alloy
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Abandoned
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US10/837,665
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English (en)
Inventor
Erhard Ogris
Peter Uggowitzer
Josef Wohrer
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Salzburger Aluminium AG
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Salzburger Aluminium AG
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Assigned to SALZBURGER ALUMINIUM AKTIENGESELLSCHAFT reassignment SALZBURGER ALUMINIUM AKTIENGESELLSCHAFT ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: WOHRER, JOSEF, UGGOWITZER, PETER, OGRIS, ERHARD
Publication of US20050000608A1 publication Critical patent/US20050000608A1/en
Priority to US12/758,381 priority Critical patent/US20100193084A1/en
Abandoned legal-status Critical Current

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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
    • 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 present invention relates to a method for improving the mechanical properties of aluminum-silicon alloys. More specifically, the present invention relates to a thermal treatment process for improving the ductility of articles of a preferably enriched/refined or purified cast or wrought aluminum-silicon alloy with an eutectic phase, which optionally contains other alloying and/or contaminating elements, said articles being subjected to an annealing treatment and subsequent aging.
  • the present invention relates to an aluminum-silicon alloy that contains at least one processing element, optionally magnesium, as well as additional alloying and/or contaminating elements with an eutectic phase consisting essentially of an ⁇ Al -matrix and silicon precipitates.
  • thermal treatment states are defined in European Standard EN 515.
  • the letter F stands for “production state”
  • T stands for “thermally treated to stable states”.
  • the particular thermal treatment state is characterized by the number that is associated with the letter T.
  • the properties of the material and, on the other hand, the costs or economic factors involved in production are important for marketing or the industrial use of objects of Al—Si alloys, since in particular long annealing treatments at high temperatures and the straightening processes that may be necessitated by so-called gravitational creep during protracted annealing are themselves costly.
  • an Al—Si alloy in State F has for the most part a low material strength R p and a relatively high value of the elongation at fracture A.
  • a thermal treatment state T5 which is to say quenched from the production temperature and thermally aged, for example at 155° C. to 190° C. for a period of 1 to 12 hours, higher strength values R p will be achieved, but at lower elongation at fracture values A of the samples.
  • the present invention provides a thermal treatment process for improving the material ductility of an article which comprises a cast or wrought aluminum-silicon alloy with an eutectic phase.
  • This process comprises subjecting the article to an annealing treatment and a subsequent aging treatment.
  • the annealing treatment is carried out as a shock annealing treatment which comprises (a) a rapid heating of the material to an annealing temperature of 400° C. to 555° C., (b) maintaining the material at this temperature for a holding period of not more than 14.8 minutes, and (c) a subsequent forced cooling of the material to essentially room temperature.
  • the aluminum-silicon alloy may further comprise one or more alloying elements and/or one or more contaminating elements.
  • the aluminum-silicon alloy may further comprises Mg, Mn and/or Fe.
  • the aluminum-silicon alloy may be enriched/refined and/or purified.
  • the holding period may be shorter than 6.8 minutes and/or the holding period may be not shorter than 1.7 minutes.
  • the holding period may be not longer than 5 minutes.
  • the aging treatment may comprise a treatment at a temperature of from 150° C. to 200° C., e.g., for from 1 to 14 hours.
  • the aging treatment may comprise a cold aging treatment at essentially room temperature.
  • the holding period may be from 1.7 to less than 6.8 minutes and the aging treatment may comprise a treatment at a temperature of from 150° C. to 200° for from 1 to 14 hours, or a cold aging treatment at essentially room temperature.
  • the article may have been made by a thixocasting method.
  • the present invention also provides an article which is obtainable by the above process, including the various aspects thereof.
  • the present invention also provides an article which comprises an aluminum-silicon alloy with an eutectic phase.
  • a Si may be less than 2 ⁇ m 2 .
  • the aluminum-silicon alloy may further comprise one or more alloying elements and/or one or more contaminating elements.
  • the alloy may further comprises Mg, Mn and/or Fe.
  • the aluminum-silicon alloy may further comprise at least one processing element.
  • the present invention further provides an article which comprises an aluminum-silicon alloy with an eutectic phase.
  • the eutectic phase consists essentially of an ⁇ Al -matrix and silicon precipitates comprising silicon particles.
  • the average free path length between the silicon particles, ⁇ Si , in the eutectic phase is not higher than 4 ⁇ m.
  • the average free path length may be less than 3 ⁇ m, e.g., less than 2 ⁇ m.
  • the aluminum-silicon alloy may further comprise one or more alloying elements and/or one or more contaminating elements.
  • the alloy may further comprises Mg, Mn and/or Fe.
  • the aluminum-silicon alloy may further comprise at least one processing element.
  • the present invention further provides an article which comprises an aluminum-silicon alloy with an eutectic phase.
  • the eutectic phase consists essentially of an ⁇ Al -matrix and silicon precipitates which comprise silicon particles.
  • the average spheroidization density may be greater than 20.
  • the aluminum-silicon alloy may further comprise one or more alloying elements and/or one or more contaminating elements.
  • the alloy may further comprises Mg, Mn and/or Fe.
  • the aluminum-silicon alloy may further comprise at least one processing element.
  • the present invention also provides any of the above articles, including the various aspects thereof, which is made by a thixocasting method and is heat treated by a process according to the present invention as set forth above, including the various aspects thereof.
  • the solution annealing is conducted as shock annealing which comprises rapid heating of the material to an annealing temperature of 400° C. to 555° C., maintaining it at this temperature for a period of at most 14.8 minutes, and subsequent forced cooling, essentially to room temperature.
  • the advantages that are obtained are that the highest ductility values are achieved for the material by a simple short-time high-temperature annealing.
  • the so-called shock annealing causes little or no component deformation or warping of the article, so that there is no need to straighten it.
  • the short-time annealing treatment is very economical and can be incorporated very easily into a production sequence, for example by using a continuous heating furnace. Material strength can be adjusted by an adapted thermal aging technology. With the majority of Al—Si alloys, the greatest increase will be achieved if, as can be provided for, the shock annealing is effected with a holding time of less than 6.8 minutes, preferably for a period ranging from 1.7 up to optionally at most 5 minutes.
  • the article is thermally aged after the shock annealing, it is advantageous to do this at a temperature in the range between 150° C. and 200° C., for a period ranging from 1 to 14 hours.
  • shock annealing be effected as cold aging, essentially at room temperature.
  • An additional advantage of the present invention is achieved in that the silicon precipitates are spheroidized in the eutectic phase and have a cross-sectional area A Si , of less than 4 ⁇ m 2 .
  • the advantages of a microstructure of this kind are essentially that crack initiation in the material is significantly reduced and ductility of the material is improved by spheroidization of the Si precipitates and by their fineness.
  • the spheroidization and small size result in a favourable morphology of the brittle eutectic silicon and lead to significantly higher values for the material's elongation at fracture.
  • the stress peaks on the Si—Al phase boundary surface are reduced.
  • a transcrystalline break was also found during tests, and this indicates the highest ductility of the material.
  • the silicon precipitates in the eutectic phase are spheroidized and have an average cross-sectional area of less than 2 ⁇ m 2 .
  • the silicon particles are subjected to a diffusion-controlled growth, and the initially favourable high spheroidization density ⁇ Si becomes smaller.
  • the highest ductility of an article of an Al—Si alloy was found if the mean spheroidization density ⁇ Si , defined as the number of spheroidized eutectic silicon particles per 100 ⁇ m 2 , has a value that is greater than 10, and preferably greater than 20.
  • FIG. 1 Bar chart showing mechanical values for a material as a function of the thermal treatment state
  • FIG. 2 As in FIG. 1
  • FIG. 3 SEM image of a cut
  • FIG. 4 As in FIG. 3
  • FIG. 5 Mean area of the Si precipitates as a function of the annealing time
  • FIG. 6 As in FIG. 5
  • FIG. 7 Mean free path length between the Si particles
  • FIG. 8 Mean spheroidization density
  • FIG. 9 Bar chart showing material mechanical properties of various Al—Si alloys
  • Table 1 Numerical values for FIG. 9 .
  • a bar chart shows the Rp 0.2 limiting values and the values for elongation at fracture A of samples manufactured from a test component produced from an AlSi 7 Mg 0.3 alloy, said component having been produced by the thixocasting method.
  • the values for thermal treatment state T6 (12 hours 540° C.+4 hours 160° C.) of the material are compared to those that were achieved with the T6x method according to the present invention after shock annealing for 1 minute (T6x1), after 3 minutes (T6x3) and after 5 minutes (T6x5) at a temperature of 540° C. All the samples were heat-aged (4 hours) at a temperature of 160° C.
  • the results of the tensile test show that the samples display significantly higher values for elongation at fracture after shock annealing, the T6x3 effecting an increase of A by approximately 60% as compared to T6.
  • the state values F, T4x3, T5, T6x3 and T6 are compared in a bar chart with respect to Rp 0.2 and elongation at fracture A. When compared, they display marked increases of the values for elongation at fracture.
  • the material can be cold-aged (T4x3) or heat-aged (T6x3) after shock annealing for 3 minutes in order to obtain superior elongation at fracture characteristics according to the present invention.
  • FIG. 3 and FIG. 4 show scanning electron microscope images of Si precipitates. With respect to the imaging and evaluation method, it must be noted that it is essential to have binary images available in order to permit quantitative evaluation.
  • the images were taken with a scanning electron microscope for an annealing period of 2 hours inclusive, after which the cut was etched for 30 seconds using a solution of 99.5% water and 0.5% hydrofluoric acid. After annealing for 4 hours, the cut was etched with the Keller solution and the images could be taken by an optical microscope. All the images were processed digitally using Adobe Photoshop 5, and evaluated with the Leica QWin V2.2 image analysis software; the minimal detection area amounted to 0.1 ⁇ m.
  • FIG. 1 shows scanning electron microscope images of Si precipitates.
  • FIG. 3 shows the AlSi 7 Mg 0.3 after a normal T6 annealing time of 12 hours, using an SEM image.
  • FIG. 4 shows the microstructure of the same material after shock annealing for three minutes. It is clear that even after a very short time there is spheroidization of the silicon precipitates ( FIG. 4 ) and the diffusion-controlled growth thereof after long annealing times can be seen ( FIG. 3 ).
  • FIG. 5 and FIG. 6 show the mean cross-sectional area A Si of the silicon particles during cut testing as a function of the annealing time at 540° C.
  • the increase of average cross-sectional area of the silicon particles, which characterizes the size of the particles, can be clearly seen from the details of FIG. 5 with the logarithmic time axis.
  • the increase of the average silicon surface within the first 60 minutes, which is governed by diffusion, can be clearly seen from FIG. 6 .
  • the average size of the silicon particles, which increases with annealing time, is to a large extent dependent on the initial size of the silicon particles in the eutectic.
  • FIG. 8 shows the decrease of the average spheroidization density, ⁇ Si , as a function of annealing time.
  • the sharp decrease of the average spheroidization density begins as soon as at 1.7 minutes and starting at a value of ⁇ 10 for ⁇ Si , results in a pronounced loss of ductility. At higher annealing temperatures, this value may already be reached after 14 to 25 minutes, and a density value of greater than 20 has to be provided for superior values of elongation at fracture.
  • the bar chart of FIG. 9 shows the measured values for yield strength and elongation at fracture which are listed in Table 1 for eight Al—Si alloys of different composition. In all of these alloys, an increase in the ductility of the material is achieved according to the present invention.

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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)
  • Thermal Sciences (AREA)
  • Physics & Mathematics (AREA)
  • Manufacture Of Alloys Or Alloy Compounds (AREA)
  • Investigating And Analyzing Materials By Characteristic Methods (AREA)
  • Conductive Materials (AREA)
  • Heat Treatment Of Articles (AREA)
  • Silicon Compounds (AREA)
  • Crystals, And After-Treatments Of Crystals (AREA)
  • Powder Metallurgy (AREA)
  • Manufacture And Refinement Of Metals (AREA)
  • Ceramic Products (AREA)
  • Laminated Bodies (AREA)
  • Refinement Of Pig-Iron, Manufacture Of Cast Iron, And Steel Manufacture Other Than In Revolving Furnaces (AREA)
US10/837,665 2001-11-05 2004-05-04 Aluminum-silicon alloys having improved mechanical properties Abandoned US20050000608A1 (en)

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US12/758,381 US20100193084A1 (en) 2001-11-05 2010-04-12 Aluminum-silicon alloys having improved mechanical properties

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AT0173301A AT411269B (de) 2001-11-05 2001-11-05 Aluminium-silizium-legierungen mit verbesserten mechanischen eigenschaften
AT1733/2001 2001-11-05
PCT/AT2002/000309 WO2003040423A1 (de) 2001-11-05 2002-11-05 Aluminium-silizium-legierungen mit verbesserten mechanischen eigenschaften

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

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
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
US11118254B2 (en) * 2017-09-13 2021-09-14 Citic Dicastal Co., Ltd Thermal treatment method for aluminum alloy cast-spun wheel
US11148827B2 (en) 2007-05-11 2021-10-19 The Boeing Company Cooling system for aerospace vehicle components
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

Families Citing this family (2)

* Cited by examiner, † Cited by third party
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DE102008024524A1 (de) * 2008-05-21 2009-11-26 Bdw Technologies Gmbh Verfahren und Anlage zur Herstellung eines Gussbauteils
DE102011105447B4 (de) * 2011-06-24 2019-08-22 Audi Ag Verfahren zur Herstellung von Aluminium-Druckgussteilen

Citations (1)

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US20020034454A1 (en) * 2000-07-26 2002-03-21 Daido Metal Co. Ltd. Aluminum bearing alloy

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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
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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
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Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US11148827B2 (en) 2007-05-11 2021-10-19 The Boeing Company Cooling system for aerospace vehicle components
US11118254B2 (en) * 2017-09-13 2021-09-14 Citic Dicastal Co., Ltd Thermal treatment method for aluminum alloy cast-spun wheel
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

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CA2465683C (en) 2011-01-18
DE50209192D1 (de) 2007-02-15
CN100366782C (zh) 2008-02-06
EP1442150B1 (de) 2007-01-03
WO2003040423A1 (de) 2003-05-15
ES2280578T3 (es) 2007-09-16
ATA17332001A (de) 2003-04-15
CN1602368A (zh) 2005-03-30
JP2005508446A (ja) 2005-03-31
HUP0401962A2 (hu) 2005-01-28
PT1442150E (pt) 2007-04-30
EP1442150A1 (de) 2004-08-04
DK1442150T3 (da) 2007-05-14
US20100193084A1 (en) 2010-08-05
ATE350507T1 (de) 2007-01-15
AT411269B (de) 2003-11-25
KR20050043748A (ko) 2005-05-11
CA2465683A1 (en) 2003-05-15
SI1442150T1 (sl) 2007-06-30
HK1071171A1 (en) 2005-07-08

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