EP1778887B1 - An al-si-mg-zn-cu alloy for aerospace and automotive castings - Google Patents

An al-si-mg-zn-cu alloy for aerospace and automotive castings Download PDF

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Publication number
EP1778887B1
EP1778887B1 EP05775565.4A EP05775565A EP1778887B1 EP 1778887 B1 EP1778887 B1 EP 1778887B1 EP 05775565 A EP05775565 A EP 05775565A EP 1778887 B1 EP1778887 B1 EP 1778887B1
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European Patent Office
Prior art keywords
alloy
casting
cast product
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aluminum
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EP05775565.4A
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German (de)
English (en)
French (fr)
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EP1778887A2 (en
EP1778887A4 (en
Inventor
Jen C. Lin
Xinyan Yan
Cagatay Yanar
Larry D. Zellman
Xavier Dumant
Robert Tombari
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Alcoa Corp
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Alcoa Corp
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Priority claimed from PCT/US2005/026478 external-priority patent/WO2006014948A2/en
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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
    • C22C1/00—Making non-ferrous alloys
    • C22C1/12—Making non-ferrous alloys by processing in a semi-solid state, e.g. holding the alloy in the solid-liquid phase
    • 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
    • C22C21/10—Alloys based on aluminium with zinc 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
    • C22F1/043—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
    • C22F1/053—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 zinc as the next major constituent

Definitions

  • the present invention relates to aluminum alloys and, more particularly, it pertains to aluminum casting alloys comprising silicon (Si), magnesium (Mg), zinc (Zn), and copper (Cu).
  • Cast aluminum parts are widely used in the aerospace and automotive industries to reduce weight.
  • the most common cast alloy used, Al-Si 7 -Mg has well established strength limits.
  • cast materials in E357 the most commonly used Al-Si7-Mg alloy, can reliably guarantee Ultimate Tensile Strength of 310 MPa, (45,000 psi), Tensile Yield Strength of 260MPa (37,709 psi) with elongations of 5% or greater at room temperature.
  • material with higher strength and higher ductility is needed with established material properties for design.
  • US 2003/102059 A1 discloses an aluminum bearing-alloy used in high power engines of motor vehicles, general industrial machines etc, comprising 1.6 to 6 mass % of Si, one or more elements selected of the group consisting of Cu,
  • Si grains can be observed on the sliding surface of the aluminum bearing-alloy.
  • a fractional area of the observed Si grains having a grain size of less than 4 ⁇ m is 20 to 60% of a total area of all the observed Si grains.
  • Another fractional area of the observed Si grains having a grain size of from 4 to 20 ⁇ m is not less than 40% of the total area of all the observed Si grains.
  • the present invention provides an inventive AlSiMg casting alloy having increased mechanical properties, a shaped casting produced from the inventive alloy, and a method of forming a shaped casting produced from the inventive alloy.
  • inventive AlSiMg casting alloy composition includes Zn, Cu, and Mg in proportions suitable to produce increased mechanical properties, including but not limited to Ultimate Tensile Strength (UTS) and Tensile Yield Strength (TYS), in comparison to prior AlSi7Mg alloys, such as E357.
  • the present invention is an aluminum casting alloy in a T5 or T6 condition, consisting of:
  • the proportions of Zn, Cu, and Mg are selected to provide an AlSiMg alloy with increased strength properties, as compared to prior AlSi7Mg alloys, such as E357.
  • the term "increased strength properties” denotes an increase of approximately 20%-30% in the Tensile Yield Strength (TYS) and approximately 20%-30% in the Ultimate Tensile Strength (UTS) of T6 temper investment castings in room temperature or high temperature applications, in comparison to similarly prepared castings of E357, while maintaining similar elongations to E357.
  • the Cu content of the alloy is increased to increase the alloy's Ultimate Tensile Strength (UTS) and Tensile Yield Strength (TYS) at room temperature (22°C) and at high temperatures, wherein high temperature ranges from 100°C to 250°C, preferably being at 150°C.
  • UTS Ultimate Tensile Strength
  • TLS Tensile Yield Strength
  • the incorporation of Cu generally increases high temperature strength properties when compared to similar AlSiMg alloys without the incorporation of Cu.
  • the Cu content is minimized to increase high temperature elongation. It is further noted that Elongation (E) typically increases with higher temperatures.
  • the Cu content and the Mg content of the alloy is selected to increase the alloy's Ultimate Tensile Strength (UTS) and Yield Tensile Strength (YTS) at room temperature (22°C) and at high temperatures.
  • the Zn content may increase an alloy's elongation in compositions having Cu and a higher Mg concentration.
  • the Zn content can decrease the alloy's elongation in compositions having Cu and lower Mg concentrations. In addition to the incorporation of Zn effecting elongation at room temperature, similar trends are observed at high temperature.
  • the Cu composition is less than or equal to 2% and the Zn composition ranges from 3% to 5%, wherein increased Zn concentration within the disclosed range generally increases the alloy's Ultimate Tensile Strength (UTS) and Yield Tensile Strength (TYS).
  • the incorporation of Zn into alloy compositions of the present invention with a Cu concentration greater than 2% generally slightly decreases the Ultimate Tensile Strength (UTS) of the alloy.
  • the Cu, Zn and Mg content is selected to provide increased elongation.
  • the Ultimate Tensile Strength (UTS) of the alloy may be increased with the addition of Ag at less than 5 wt %.
  • the Mg, Cu and Zn concentrations are selected to have a positive impact on the Quality Index of the alloy at room and high temperatures.
  • the Quality Index is an expression of strength and elongation.
  • Mg is incorporated into the inventive alloy comprising Cu in order to increase the Quality Index of the alloy.
  • Zn can increase the Quality Index when the Mg content is high, such as on the order of .6 wt%.
  • the inventive alloy is in a T5 or T6 condition.
  • the fluidity of the alloy is also improved when compared with the E357
  • the present invention is a shaped casting in a T5 or T6 condition consisting of:
  • the present invention is a method of making a shaped aluminum alloy casting, the method comprising: preparing a molten metal mass consisting of:
  • forming the aluminum alloy product comprises casting the molten metal mass into an aluminum alloy casting by investment casting, low pressure or gravity casting, permanent or semi-permanent mold, squeeze casting, die casting, directional casting or sand mold casting.
  • the forming method may further comprise preparing a mold with chills and risers.
  • the molten metal mass is a thixotropic metal mass and forming the aluminum alloy product comprises semi-solid casting or forming.
  • Figure la presents tensile strength data for samples of aluminum alloys at room temperature containing about 7% Si, about 0.5% Mg, and further containing various amounts of Zn and Cu, directionally solidified at 1° C per second.
  • Figure 1b presents tensile strength data for samples of aluminum alloys at room temperature containing about 7% Si, about 0.5% Mg, and further containing various amounts of Zn and Cu, directionally solidified at 0.4° C per second.
  • Figure 2a presents yield strength data for samples of aluminum alloys at room temperature containing about 7% Si, about 0.5% Mg, and also containing various amounts of Zn and Cu, directionally solidified at 1° C per second.
  • Figure 2b presents yield strength data for samples of aluminum alloys at room temperature containing about 7% Si, about 0.5 % Mg, and also containing various amounts of Zn and Cu, directionally solidified at 0.4° C per second.
  • Figure 3a presents elongation data for samples of aluminum alloys at room temperature containing about 7% Si, about 0.5% Mg, and also containing various amounts of Zn and Cu, directionally solidified at 1° C per second.
  • Figure 3b presents elongation data for samples of aluminum alloys at room temperature containing about 7% Si, about 0.5% Mg, and also containing various amounts of Zn and Cu, directionally solidified at 0.4° per second.
  • Figure 4 presents the results of fluidity tests for samples of aluminum alloys containing about 7% Si, about 0.5% Mg, and also containing various amounts of Zn and Cu.
  • Figure 5 presents the quality index at room temperature, which is based on ultimate tensile strength and elongation for samples of aluminum alloys containing about 7% Si, about 0.5% Mg, and also containing various amounts of Zn and Cu.
  • Figure 6 presents a graph depicting the effects of Mg, Cu and Zn concentration on Ultimate Tensile Strength (UTS) at high temperature (approximately 150°C) of 7Si-Mg-Cu-Zn alloy test specimens produced using investment casting and T6 heat treatment.
  • UTS Ultimate Tensile Strength
  • Figure 7 presents a graph depicting the effects of Mg, Cu and Zn concentration on Elongation (E) at high temperature (approximately 150°C) of test specimens comprising 7Si-Mg-Cu-Zn produced using investment casting and T6 heat treatment.
  • Figure 8 presents a graph depicting the effects of Mg, Cu and Zn concentration on Quality Index (Q) at high temperature (approximately 150°C) of test specimens comprising 7Si-Mg-Cu-Zn produced using investment casting and T6 heat treatment.
  • Figure 9 presents a Table including reference alloy compositions and includes one prior art alloy (E357) for comparative purposes.
  • Figure 9 also includes Ultimate Tensile Strength (UTS), Tensile Yield Strength (TYS), Elongation (E), and Quality Index (Q) for each listed alloy composition taken from an investment cast test specimen with T6 heat treatment at a temperature on the order of 150°C.
  • UTS Ultimate Tensile Strength
  • T6 Tensile Yield Strength
  • Q Quality Index
  • Table 1 presents compositions of various alloys, with alloys 1Cu4Zn and OCu4Zn having compositions according to the present invention, and the prior art alloy, E357, which is included for comparison.
  • Table 1 Alloy Compositions Alloy Cu Zn Si Mg Fe Ti B Sr* 3Cu 0Zn 2.91 0 7.01 0.5 0.06 0.126 0.0006 0.01 3Cu 2Zn 2.9 1.83 7.1 0.49 0.06 0.127 0.0012 0.009 3Cu 4Zn 2.96 3.61 7.18 0.49 0.06 0.126 0.0007 0.008 1Cu 0Zn 1.0 0 7.03 0.5 0.02 0.12 0.0015 0.01 1Cu 2Zn 1.0 1.74 7.22 0.56 0.06 0.133 0.0003 0.009 1Cu 4Zn 0.99 3.39 7.36 0.54 0.05 0.131 0.0001 0.009 0Cu 2Zn 0 1.73 7.19 0.53 0.05 0.129 0.0014 0.006 0Cu 4Zn 0 3.41 7.19 0.53 0.05 0.127 0.0013 0.005 E357 0 0 7.03 0.53 0.05 0.127 0.0011 0.007 * within impurity levels
  • the values in columns 2-8 of Table 1 are actual weight percentages of the various elements in the samples that were tested. All the entries in column 1 except the entry in the last row are target values for copper and zinc in the alloy. The entry in the last row specifies the prior art alloy, E357.
  • the columns following the first column in Table 1 present actual weight percentages of Cu, Zn, Si, Mg, Fe, Ti, B, and Sr, respectively.
  • Samples having the compositions cited in Table 1 were cast in directional solidification test molds for mechanical properties evaluation. The resulting castings were then heat treated to a T6 condition. Samples were taken from the castings in different regions having different solidification rates. Tensile properties of the samples were then evaluated at room temperature.
  • Figure 1a presents tensile strength data for aluminum alloy samples containing about 7% Si, 0.5% Mg, and various concentrations of Cu and Zn, as indicated.
  • the samples cited in Figure 1 were solidified at about 1°C per second.
  • the dendrite arm spacing (DAS) was about 30 microns. It can be seen that the tensile strength of the alloy increases with Zn concentration up to the highest level studied, which was about 3.61 % Zn. Likewise, the tensile strength increases with increasing copper concentration up to the highest level studied, which was about 3 % Cu. All the samples having Cu and/or Zn additions had strength greater than the prior art alloy, E357.
  • Figure 1b presents data similar to Figure 1a , except that the samples shown in Figure 1b were solidified more slowly, at about 0.4°C per second, resulting in a dendrite arm spacing of about 64 microns.
  • the sample having the greatest tensile strength was the reference sample having about 3 % Cu and about 3.61 % Zn. All the samples in Figure 1b having Cu and/or Zn additions had strength greater than the prior art alloy, E357.
  • Figure 2A presents yield strength data for various aluminum alloy samples having about 7% Si, about 0.5% Mg, and various concentrations of Cu and Zn. These samples were solidified at about 1° C per second, and have a dendrite arm spacing of about 30 microns. The yield strength increased markedly with increases in Cu, and tended to increase with increases in Zn. The reference sample having the greatest yield strength had a copper concentration of about 3%, and a Zn concentration of about 4%. All the samples having added Cu or Zn exhibited greater yield strength than the prior art alloy, E357.
  • Figure 2b presents yield strength data for the same aluminum alloys as shown in Figure 2a ; however, they were solidified more slowly, at about 0.4° C per second. The corresponding dendrite arm spacing was about 64 microns.
  • the reference sample having the greatest yield strength had a copper concentration of about 3%, and a Zn concentration of about 4%. All the samples having added Cu or Zn exhibited greater yield strength than the prior art alloy, E357.
  • Figure 3a presents elongation data for the prior art alloy, E357, and various alloys having added Cu and Zn.
  • the solidification rate was about 1°C per second, and the dendrite arm spacing was about 30 microns.
  • the best elongation is obtained for the alloys having 0% Cu.
  • increasing the Zn concentration from 2% to about 4% caused increased elongation.
  • the alloys having Zn between 2% and 4% had elongations greater than that of the prior art alloy, E357.
  • Figure 3b presents elongation data for the alloys shown in Figure 3a , but solidified more slowly, at 0.4° C per second.
  • the dendrite arm spacing was about 64 microns.
  • the alloys having about 0% Cu had the greatest elongation. Indeed the greatest elongation was obtained for the prior art alloy, E357.
  • the alloy with 0% Cu and Zn in a range from 2% to 4 % was only slightly inferior to E357 in this regard.
  • the alloys having Zn in the range from 2% to 4 % are of interest because their tensile strength and yield strength values are superior to E357.
  • Figure 4 presents the results of casting in a fluidity mold. As before, the tests were performed on aluminum alloys containing about 7% Si, about 0.5% Mg, and with various amounts of Cu and Zn. Most of the alloys in Figure 4 having additions of Cu or Zn have fluidity superior to that of the prior art alloy, E357. Indeed, the best fluidity of all was obtained for the reference alloy with 3% Cu, 4% Zn. Fluidity is crucial for shaped castings because it determines the ability of the alloy to flow through small passages in the mold to supply liquid metal to all parts of the casting.
  • Figure 5 presents data for the Quality Index (Q) for the alloys tested.
  • the Quality Index (Q) is a calculated index that includes the Ultimate Tensile Strength (UTS) plus a term involving the logarithm of the Elongation (E).
  • the two plots in Figure 5 are for the two dendrite arm spacings employed for the preceding studies. The 30 micron spacing is found in samples cooled at 1° C per second, and the 64 micron spacing is found in samples cooled at 0.4° C per second. It can be seen from Figure 5 that, generally, the best Quality Index (Q) is obtained for high concentrations of Zn, and for low concentrations of Cu.
  • Table 2 presents compositions of various alloys, with alloys 7Si1Cu0.5Mg3Zn and 5Si1Cu0.6Mg3Zn being according to the present invention, wherein the concentrations of Cu, Mg and Zn were selected to provide improved mechanical properties at room temperature and high temperature.
  • the values in columns 2-7 of Table 2 are actual weight percentages of the various elements in the samples that were tested.
  • the balance of each alloy consists essentially of aluminum. It is noted that Sr is included as a grain refiner, within impurity levels.
  • Test specimens where produced from the above compositions for mechanical testing.
  • the test specimens where formed by investment casting in the form of 1 ⁇ 4" thick test plates.
  • the cooling rate via investment casting is less than about .5° C per second and provides a dendritic arm spacing (DAS) on the order of approximately 60 microns or greater.
  • DAS dendritic arm spacing
  • T6 temper comprises solution heat treat, quench and artificial aging.
  • the test plates where sectioned and their mechanical properties tested. Specifically, the test specimens comprising the alloy compositions listed in Table 2 where tested for Ultimate Tensile Strength (UTS) at room temperature (22°C).
  • UTS Ultimate Tensile Strength
  • TYS MPa at High Temperature 150 ⁇ °C 279.465 + 29.792 * Mg wt % + 14.0 Cu wt % + 0.4823 Zn wt % - 0.503 Si wt % + 6.566 Mg wt % Zn wt % - 1.998 Cu wt % Zn wt % - 3.686 Sr wt % .
  • the Ultimate.Tensile Strength (UTS) in MPa is plotted for alloy compositions at high temperature (150°C) of varying Mg and Cu concentrations as a function of increasing Zn concentration (wt %).
  • reference line 15 indicates a plot of reference alloy comprising approximately .6 wt % Mg and 3 wt % Cu
  • reference line 20 indicates a plot of a reference alloy comprising a proximately .5 wt % Mg and 3 wt % Cu
  • reference line 25 indicates a plot of a reference alloy comprising approximately .6 wt % Mg and 2 wt % Cu
  • reference line 30 indicates a plot of an alloy comprising approximately .5 wt % Mg and 2 wt % Cu
  • reference line 35 is a plot of an alloy comprising approximately .6 wt % Mg and 1 wt % Cu
  • reference line 40 is a plot of an alloy comprising approximately .5 wt % Mg and 1 wt % Cu
  • reference line 45 is a plot of an alloy comprising approximately .6 wt % Mg and 0 wt % Cu
  • reference line 50 is a plot of an alloy comprising
  • alloys comprising .6 wt % Mg have a greater high temperature Ultimate Tensile Strength (UTS), depicted by the alloy plots indicated by reference lines 15, 25, 35, and 45, than alloys having similar compositions having a Mg concentration on the order of about .5 wt %, as depicted by the alloy plots indicated by reference lines 20, 30, 40, and 50.
  • UTS Ultimate Tensile Strength
  • reference line 55 indicates a plot of a reference alloy comprising approximately .6 wt % Mg and 3 wt % Cu
  • reference line 60 indicates a plot of a reference alloy comprising approximately .5 wt % Mg and 3 wt % Cu
  • reference line 65 indicates a plot of an alloy comprising approximately .6 wt % Mg and 2 wt % Cu
  • reference line 70 indicates a plot of an alloy comprising approximately .5 wt % Mg and 2 wt % Cu
  • reference line 75 is a plot of an alloy comprising approximately .6 wt % Mg and 1 wt % Cu
  • reference line 80 is a plot of an alloy comprising approximately .5 wt % Mg and 1 wt % Cu
  • reference line 85 is a plot of an alloy comprising approximately .5 wt % Mg and 1 wt % Cu
  • reference line 85 is a plot of an alloy comprising approximately .5 wt
  • increases in Zn content can increase the alloy's elongation when the magnesium content is low, such as on the order of .5 wt %, as plotted in reference lines 60, 70, 80, and 90.
  • Increases in Zn content can decrease the elongation of the alloy when the magnesium content is high, such as on the order of .6 wt %, as plotted in reference lines 55, 65, 75, and 85.
  • Magnesium has a positive impact on elongation when the Zn content is more than 2.5 wt % and has a negative impact when the Zn content is less than 2.5 wt %.
  • the Mg concentration in both alloys is equal to 3.0 wt %
  • the Quality Index (Q) is increased if the Zn content of the alloy is greater than or equal to 2.5 wt%.
  • the Mg concentration has a similar effect on the alloys with less than 3.0 wt % Cu.
  • reference line 95 indicates a plot of a reference alloy comprising approximately .5 wt % Mg and 3 wt % Cu
  • reference line 100 indicates a plot of an alloy comprising approximately .5 wt % Mg and 2 wt % Cu
  • reference line 105 indicates a plot of a reference alloy comprising approximately .6 wt % Mg and 3 wt % Cu
  • reference line 110 indicates a plot of an alloy comprising approximately .5 wt % Mg and 1 wt % Cu
  • reference line 115 is a plot of an alloy comprising approximately .6 wt % Mg and 2 wt % Cu
  • reference line 120 is a plot of an alloy comprising approximately .5 wt % Mg and 0
  • Cu generally decreases elongation and therefore in some embodiments may decrease the alloy's Quality Index (Q).
  • Q Quality Index
  • Mg typically has a positive impact on Quality Index of the alloys including Cu and Zn, wherein Zn content is greater than or equal to 1.2 wt %.
  • the Mg concentration in both alloys is equal to 3.0 wt %
  • the Quality Index (Q) is increased if the Zn content of the alloy is greater than or equal to 1.2 wt %.
  • the Mg concentration has a similar effect on the alloy with less than 3.0 wt % Cu.
  • AlSiMg alloys comprising increased Cu concentrations such as the alloy plots indicated by reference lines 95, 100, 105, and 120, have decreasing Quality Index (Q) values as the concentration of Cu is increased.
  • the incorporation of Zn can increase the Quality Index (Q) of the alloy when the Mg content is on the order of about .6 wt %, and the Cu is content is less than about 2.5 wt %, as depicted by the alloy plots indicated by reference numbers 115, 125, and 130.
  • inventive alloy compositions listed in Table 3 are illustrative of the inventive composition, the invention should not be deemed limited thereto as any composition having the constituents and ranges recited in the Claims of this disclosure are within the scope of this invention.
  • Further reference alloy compositions are listed within the Table depicted in Figure 9.
  • Figure 9 also includes the Tensile Yield Strength (TYS), Ultimate Tensile Strength (UTS), Elongation (E), and Quality Index (Q) of the listed alloy compositions listed, wherein the TYS, UTS, E, and Q were taken from T6 temper test samples at room temperature (22°C).
  • the final row of the Table in Figure 9 includes the composition and room temperature (22°C) mechanical properties (Tensile Yield Strength (TYS), Ultimate Tensile Strength (UTS), Elongation (E), and Quality Index (Q)) of an E357 alloy test specimen at T6 temper (E357-T6) that was formed by investment casting, wherein the E357 alloy test specimen is prior art that has been incorporated for comparative purposes. Still referring to Figure 9 , E357 has an Ultimate Tensile Strength (UTS) at 22°C on the order of 275 MPa and an Elongation (E) of approximately 5%.
  • TTS Tinsile Yield Strength
  • UTS Ultimate Tensile Strength
  • E Elongation
  • Q Quality Index
  • the inventive aluminum alloy has an Ultimate Tensile Strength (UTS) for investment castings with a T6 heat treatment at applications on the order of 150°C that is 20% to 30% greater than similiarly prepared castings of E357.
  • UTS Ultimate Tensile Strength
  • UTS Ultimate Tensile Strength
  • Alloys according to the present invention may be cast into useful products by investment casting, low pressure or gravity casting, permanent or semi-permanent mold, squeeze casting, high pressure die casting, or sand mold casting.

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EP05775565.4A 2004-07-28 2005-07-28 An al-si-mg-zn-cu alloy for aerospace and automotive castings Expired - Lifetime EP1778887B1 (en)

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US59205104P 2004-07-28 2004-07-28
PCT/US2005/026478 WO2006014948A2 (en) 2004-07-28 2005-07-28 An al-si-mg-zn-cu alloy for aerospace and automotive castings

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KR101756016B1 (ko) 2016-04-27 2017-07-20 현대자동차주식회사 다이캐스팅용 알루미늄 합금 및 이를 이용하여 제조한 알루미늄 합금의 열처리 방법
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CN107868889B (zh) * 2016-09-23 2020-04-24 比亚迪股份有限公司 铝合金及其制备方法和应用以及车辆车身骨架连接件和电动汽车
CN106636813A (zh) * 2016-12-12 2017-05-10 余姚市庆达机械有限公司 一种耐腐蚀的铝合金及其制备方法
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CN107828999A (zh) * 2017-12-18 2018-03-23 广州致远新材料科技有限公司 一种压铸铝合金的热处理方法及压铸铝合金材料
CN110144499B (zh) * 2019-06-21 2020-12-08 广东省材料与加工研究所 一种用于5g通迅基站壳体的压铸铝合金及其制备方法
CN113462932B (zh) * 2021-07-05 2023-03-24 南昌航空大学 一种用于半固态流变压铸的高导热铝合金材料及其制备方法
CN114381640B (zh) * 2021-12-17 2022-11-22 深圳南科强正轻合金技术有限公司 一种流变铸造用高强铝合金材料及其应用方法
CN114752822B (zh) * 2022-05-25 2023-02-24 深圳南科强正轻合金技术有限公司 一种压铸铝合金及其制备方法
CN114875280B (zh) * 2022-07-07 2022-10-28 中国航发北京航空材料研究院 耐热铝硅合金材料、制造方法及耐热铝硅合金铸件
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JP7666489B2 (ja) 2022-11-14 2025-04-22 トヨタ自動車株式会社 鋳造用アルミニウム合金、アルミニウム合金部材、及びアルミニウム合金部材の製造方法
CN115679162A (zh) * 2022-11-18 2023-02-03 江西万泰铝业有限公司 一种新能源汽车免热处理铝合金材料及低碳制备方法
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CA2574962A1 (en) 2006-02-09
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CN101018881B (zh) 2011-11-30
CN101018881A (zh) 2007-08-15
NO20071075L (no) 2007-04-30
JP2008514807A (ja) 2008-05-08
EP1778887A2 (en) 2007-05-02
EP1778887A4 (en) 2010-06-02
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NO339946B1 (no) 2017-02-20
AU2005269483B2 (en) 2010-12-23
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AU2005269483A1 (en) 2006-02-09
JP5069111B2 (ja) 2012-11-07

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