WO2020237837A1 - 一种高强韧薄壁结构件铸造铝合金及其制备方法 - Google Patents

一种高强韧薄壁结构件铸造铝合金及其制备方法 Download PDF

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WO2020237837A1
WO2020237837A1 PCT/CN2019/100504 CN2019100504W WO2020237837A1 WO 2020237837 A1 WO2020237837 A1 WO 2020237837A1 CN 2019100504 W CN2019100504 W CN 2019100504W WO 2020237837 A1 WO2020237837 A1 WO 2020237837A1
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aluminum alloy
alloy
strength
source
weight percentage
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French (fr)
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张莹
任怀德
景佰亨
李院斌
李凯
王继成
鲁强
冯力
陈彦霖
彭典明
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珠海市润星泰电器有限公司
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D17/00—Pressure die casting or injection die casting, i.e. casting in which the metal is forced into a mould under high pressure
    • B22D17/007—Semi-solid pressure die casting
    • 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
    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/026—Alloys based on aluminium
    • 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
    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/03—Making non-ferrous alloys by melting using master alloys
    • 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
    • C22F1/047—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 magnesium as the next major constituent

Definitions

  • the invention relates to the technical field of aluminum alloy processing, in particular to a high-strength and tough thin-walled structural part cast aluminum alloy and a preparation method thereof.
  • Cast aluminum alloy parts are widely used in electrical instruments, automobiles, motorcycles, and communications.
  • some workpieces such as high-load-bearing, thin-walled iron structural parts in automobile bodies are replaced by aluminum alloy pressure casting.
  • the castings are required to have high strength, high elongation and high toughness after proper heat treatment.
  • Al-Si-Cu series (domestic YL112, YL113, Japanese ADC12, ADC10, American A380, etc.), Al-Si-Mg series (domestic YL104, Japanese ADC3, American A360, etc.) conventional non-vacuum die casting (
  • the general tensile strength of aluminum alloy is 220-240MPa, and the elongation is less than or equal to 3%, which is far from meeting the performance requirements of high strength and high toughness, especially poor toughness, easy fatigue cracking during service, and low toughness.
  • the purpose of the present invention is to solve the above-mentioned problems and deficiencies, by optimizing the design of the content of Al, Si, Mg, Mn, Sr, B, Ti and Fe in the alloy, and through the steps 1S, 2S, 3S, 4S, and 5S to suppress ⁇ -
  • the AlFesi impurity phase is generated, providing a high-strength and tough thin-walled structural part cast aluminum alloy and a preparation method thereof.
  • a cast aluminum alloy with high strength and toughness and thin-walled structural parts.
  • a method for preparing a cast aluminum alloy for high-strength and toughness thin-walled structural parts includes the following steps:
  • 1S ingredients According to the group distribution, take the raw materials silicon source, magnesium source, aluminum source, titanium source, manganese source, boron source, strontium source, and iron source to prepare aluminum alloy raw materials;
  • 2S smelting and die-casting heating and smelting the raw materials prepared in step 1S to obtain a melt solution; stirring the melt solution and casting into an ingot;
  • step 2S the ingot obtained in step 2S is subjected to homogenization heat treatment at 540 to 560°C, heat preservation for 3 to 5 hours, and water cooling and quenching.
  • step 3S solid solution: the alloy obtained in step 3S is solid solution at 540 ⁇ 560°C, holding for 1 ⁇ 3h, and water quenching;
  • step 4S The alloy obtained in step 4S is artificially aged at 160-180°C for 2-8h, and after cooling, a high-strength aluminum alloy is obtained.
  • the silicon source is Al-20Si alloy
  • the magnesium source is 99.95% magnesium ingot
  • the aluminum source is 99.8% aluminum ingot
  • the titanium source is Al-10Ti alloy
  • the manganese source is Al-40Mn alloy
  • the strontium source is Al-10Sr alloy
  • the boron source is Al-5Ti-1B alloy
  • the iron source is 99.95% iron powder or aluminum-iron intermediate alloy.
  • the melting temperature is 730-760°C;
  • the stirring method includes mechanical stirring, electromagnetic stirring or ultrasonic vibration method.
  • Si element can form Al+Si eutectic liquid phase with Al in aluminum alloy, improve the die-casting fluidity of aluminum alloy, and also improve the strength and machining performance of aluminum alloy.
  • the weight percentage content range of Si can be limited to 4.00-8.00%. More preferably, the weight percentage content range of Si can be limited to 5.00-7.00%.
  • the Mg element can form a Mg2Si strengthening phase with Si in the die-cast aluminum alloy to enhance the strength of the die-cast aluminum alloy.
  • Mn element can form Mn2Si strengthening phase with Si in die-cast aluminum alloy to enhance the strength of die-cast aluminum alloy.
  • Mn content the higher the strength of die-cast aluminum alloy, but the toughness will gradually decrease.
  • the weight percentage content range of Mn can be limited to 0.10 to 1.00%.
  • the weight percentage content range of Mn can be limited to 0.20 to 0.80%. More preferably, the weight percentage content range of Mn can be limited to 0.30 to 0.60%.
  • Ti element mainly plays a role in refining ⁇ -Al grains in die-cast aluminum alloy, improves the uniformity of the structure of aluminum alloy, and improves the fluidity, strength and toughness of die-cast aluminum alloy.
  • the Ti content is less than 0.05%, and the grain refinement effect is not obvious. The higher the Ti content, the better the grain refining effect, but when the Ti content exceeds 0.20%, it will also cause the appearance of the coarse intermetallic compound TiAl3 phase, which deteriorates the strength and toughness of the die-cast aluminum alloy. Therefore, the weight percentage content range of Ti can be limited to 0.05 to 0.20%. Preferably, the weight percentage content range of Ti may be limited to 0.08 to 0.18%. More preferably, the weight percentage content range of Ti may be limited to 0.10 to 0.15%.
  • Sr element mainly plays a role in the refinement and modification of eutectic Si phase in die-cast aluminum alloy.
  • the eutectic Si phase in aluminum alloys is usually in the form of slender needles. This slender needle-like eutectic Si phase will also split the aluminum alloy matrix, which is an important reason for the lower strength and toughness of traditional die-casting aluminum alloys. .
  • the refinement and metamorphism of the eutectic Si phase is mainly the addition of Na, but the current Na element still has problems such as unstable refinement and metamorphism effect and easy to cause gas absorption.
  • the addition of 0.01 to 0.10% of Sr element can transform the eutectic Si in the die-cast aluminum alloy from slender needles to fine and uniform particles, and significantly improve the strength and toughness of the die-cast aluminum alloy.
  • the weight percentage content of Sr can be limited to 0.01-0.08%. More preferably, the weight percentage content range of Sr can be limited to 0.01-0.05%.
  • the B element mainly plays a role in refining ⁇ -Al grains in die-cast aluminum alloys, improves the uniformity of the structure of the aluminum alloy, and improves the fluidity, strength and toughness of the die-cast aluminum alloy. Therefore, the weight percentage content of B can be limited to 0.01 to 0.12%. Preferably, the weight percentage content range of B can be limited to 0.01 to 0.10%. More preferably, the weight percentage content of B can be limited to 0.01-0.05%.
  • Fe element can improve the mechanical strength and tensile properties of the alloy. Fe can also significantly improve the creep resistance and fatigue resistance of the alloy. However, excessive Fe will form coarse needle-like Al-Fe-Si rich in the aluminum alloy. Fe phase, this thick needle-like Fe-rich phase will severely split the aluminum alloy matrix, which is the main reason for the low strength and toughness of traditional die-cast aluminum alloys.
  • the inventor found through a large number of experimental studies that the content of Fe as an impurity element in the die-cast aluminum alloy is controlled within ⁇ 0.60%, preferably, the content of Fe is controlled within ⁇ 0.30%, and more preferably, the content of Fe is controlled within ⁇ 0.20%.
  • the formation of Sr-B compound consumes a large amount of Sr and B, resulting in a large amount of Mutual poisoning weakens the metamorphic effect of the two elements.
  • the present invention provides a method for preparing the above-mentioned high-strength and toughness thin-walled structural member cast aluminum alloy.
  • the preparation method includes the following steps:
  • 1S ingredients According to the group distribution, take the raw materials silicon source, magnesium source, aluminum source, titanium source, manganese source, boron source, strontium source, and iron source to prepare aluminum alloy raw materials;
  • 2S smelting and die-casting heating and smelting the raw materials prepared in step 1S to obtain a melt solution; stirring the melt solution and casting into an ingot;
  • step 2S the ingot obtained in step 2S is subjected to homogenization heat treatment at 540 to 560°C, heat preservation for 3 to 5 hours, and water cooling and quenching.
  • step 3S solid solution: the alloy obtained in step 3S is solid solution at 540 ⁇ 560°C, holding for 1 ⁇ 3h, and water quenching;
  • step 4S The alloy obtained in step 4S is artificially aged at 160-180°C for 2-8h, and after cooling, a high-strength aluminum alloy is obtained.
  • the above preparation method is carried out in the order of 1S) to 5S).
  • the silicon source is Al-20Si alloy
  • the magnesium source is 99.95% magnesium ingot
  • the aluminum source is 99.8% aluminum ingot
  • the titanium source is Al-10Ti alloy
  • the manganese source is Al-40Mn alloy
  • the strontium source is Al -10Sr alloy
  • boron source is Al-5Ti-1B alloy
  • iron source is 99.95% iron ingot or aluminum-iron master alloy
  • impurity elements are controlled to ensure high strength and high toughness of die-cast aluminum alloy.
  • step 2S the raw materials obtained in step 1S are added to an induction melting furnace, evacuated and smelted at a temperature of 730 to 760°C by evacuating argon to obtain a melt solution; using mechanical stirring, electromagnetic stirring or ultrasonic vibration methods , Stir for 8-10min, cast into ingot.
  • step 3S the ingot obtained in step 2S is subjected to homogenization heat treatment at 540 to 560°C, heat preservation for 3 to 5 hours, and water cooling and quenching.
  • step 4S the alloy obtained in step 3S is solid-solved at 540-560°C, kept for 1 to 3 hours, and quenched with water to room temperature.
  • step 5S the alloy obtained in step 4S is artificially aged at 160-180°C for 2-8 hours, and after cooling, a high-strength aluminum alloy is obtained.
  • the die-cast aluminum alloy of the present invention has the following advantages: 1)
  • the high-strength and toughness thin-walled structure cast aluminum alloy of the present invention is composed of elements such as Si, Mg, and Mn, and is optimized for the main alloy elements of Si, Mg, and Mn.
  • the introduction of Sr elements refines the coarse acicular Si particles into fine and uniform spherical particles.
  • the formation of ⁇ -AlFesi is suppressed and the aluminum is improved.
  • the uniformity of the composition of the alloy improves the fluidity, strength and plasticity of the aluminum alloy during the die-casting process; 2) The alloy further controls the ratio of B, Sr and Ti without adding expensive rare earth elements (such as Sc, Zr, etc.) High strength and toughness are achieved in the case of, which has advantages in cost; 3) Thermodynamic calculations based on the Hill solidification model show that the solid-liquid coexistence interval during solidification of the alloy (Example 3) is 70°C, which is suitable for semi-solid die casting Production; 4) The high-performance aluminum alloy of the present invention has a tensile strength of 188 ⁇ 358MPa, a yield strength of 150 ⁇ 333MPa, and an elongation of 8.0 ⁇ 23.0%. It is suitable for preparation by extrusion die-casting process and is suitable for automobiles, electronic appliances , High-strength, high-toughness, high-density aluminum alloy parts required by high-end equipment and other fields.
  • the content of each component of cast aluminum alloy for high strength and toughness thin-walled structural parts is expressed in weight percentage as follows: Al 96.73%, Si 3.00%, Mg 0.10%, Mn 0.10%, Sr 0.01%, B 0.01%, Ti 0.05%.
  • the preparation method of the high-strength and toughness thin-walled structural member cast aluminum alloy includes the following steps:
  • 1S ingredients according to the above-mentioned components, take the raw materials Al-20Si alloy, 99.95% magnesium ingot, 99.8% aluminum ingot, Al-10Ti alloy, Al-40Mn alloy, Al-10Sr alloy, Al-5Ti-1B alloy, iron source It is 99.95% iron powder or aluminum-iron intermediate alloy;
  • step 2S smelting and die-casting the raw materials obtained in step 1S are added to the induction melting furnace, smelted at a temperature of 730 ⁇ 760°C by vacuuming, argon gas, and obtaining a melt solution; using mechanical stirring method, stirring for 8 ⁇ 10min , Cast into ingots;
  • step 2S the ingot obtained in step 2S is subjected to homogenization heat treatment at 540 to 560°C, heat preservation for 3 to 5 hours, and water cooling and quenching.
  • step 3S solid solution: the alloy obtained in step 3S is solid solution at 540 ⁇ 560°C, holding for 1 ⁇ 3h, and water quenching;
  • step 4S The alloy obtained in step 4S is artificially aged at 160-180°C for 2-8h, and after cooling, a high-strength aluminum alloy is obtained.
  • the content of each component of the cast aluminum alloy for high strength and toughness thin-walled structural parts is expressed in weight percentage as follows: Al 86.98%, Si 10.00%, Mg 1.00%, Mn 1.00%, Sr 0.10%, B 0.12%, Ti 0.20%, Fe 0.60 %.
  • the preparation method of the high-strength and toughness thin-walled structural member cast aluminum alloy includes the following steps:
  • 1S ingredients according to the above-mentioned components, take the raw materials Al-20Si alloy, 99.95% magnesium ingot, 99.8% aluminum ingot, Al-10Ti alloy, Al-40Mn alloy, Al-10Sr alloy, Al-5Ti-1B alloy, iron source It is 99.95% iron powder or aluminum-iron intermediate alloy;
  • step 2S smelting and die-casting the raw materials obtained in step 1S are added to the induction melting furnace, evacuated, argon is vented, and smelted at a temperature of 730 ⁇ 760°C to obtain a melt solution; using electromagnetic stirring method, stir for 8 ⁇ 10min , Cast into ingots;
  • step 2S the ingot obtained in step 2S is subjected to homogenization heat treatment at 540 to 560°C, heat preservation for 3 to 5 hours, and water cooling and quenching.
  • step 3S solid solution: the alloy obtained in step 3S is solid solution at 540 ⁇ 560°C, holding for 1 ⁇ 3h, and water quenching;
  • step 4S the alloy obtained in step 4S is artificially aged at 160-180°C for 2-8h, and after cooling, a high-strength aluminum alloy is obtained.
  • the content of each component of the cast aluminum alloy for high strength and toughness thin-walled structural parts is expressed in weight percentage as follows: Al 95.45%, Si 4.00%, Mg 0.25%, Mn 0.20%, Sr 0.01%, B 0.01%, Ti 0.08%.
  • the preparation method of the high-strength and toughness thin-walled structural member cast aluminum alloy includes the following steps:
  • 1S ingredients according to the above-mentioned components, take the raw materials Al-20Si alloy, 99.95% magnesium ingot, 99.8% aluminum ingot, Al-10Ti alloy, Al-40Mn alloy, Al-10Sr alloy, Al-5Ti-1B alloy, iron source It is 99.95% iron powder or aluminum-iron intermediate alloy;
  • 2S smelting and die-casting Put the raw materials obtained in step 1S into an induction melting furnace, smelt at a temperature of 730 ⁇ 760°C by vacuuming, argon gas, and obtain a melt solution; using ultrasonic vibration method, stirring for 8 ⁇ 10min , Cast into ingots;
  • step 2S the ingot obtained in step 2S is subjected to homogenization heat treatment at 540 to 560°C, heat preservation for 3 to 5 hours, and water cooling and quenching.
  • step 3S solid solution: the alloy obtained in step 3S is solid solution at 540 ⁇ 560°C, holding for 1 ⁇ 3h, and water quenching;
  • step 4S The alloy obtained in step 4S is artificially aged at 160-180°C for 2-8h, and after cooling, a high-strength aluminum alloy is obtained.
  • Comparative Example 1 high-strength and toughness aluminum alloys are selected as Comparative Example 1, where the high-strength and toughness aluminum alloy has the following mass percentage components: Si 8.7%, Mn 0.65%, Mg 0.5%, Ce 0.35 %, Fe 0.18%, Sr 0.03%, impurity ⁇ 0.2%, and the rest is aluminum.
  • the aluminum alloys of the above examples 1-15 are processed into standard tensile specimens, and the tensile mechanical properties at room temperature are performed on the DNS500 electronic tensile testing machine. Among them, the stretching rate is 2 mm/min.
  • the present invention can obtain a tensile strength greater than 188 MPa, a yield strength greater than 150 MPa, and an elongation greater than 8 by optimizing the alloy element ratio during the aluminum alloy preparation process and the die-casting molding process.
  • % Aluminum alloy In particular, Examples 5, 6, 7, 11, 13, and 15 achieved better results by further optimizing the ratio of main elements and trace elements.
  • the die-cast aluminum alloy of the present invention has the following advantages: 1)
  • the high-strength and toughness thin-walled structure cast aluminum alloy of the present invention is composed of elements such as Si, Mg, and Mn, and is optimized for the main alloy elements of Si, Mg and Mn
  • the introduction of Sr elements refines the coarse acicular Si particles into fine and uniform spherical particles.
  • the formation of ⁇ -AlFesi is suppressed and the aluminum is improved.
  • the uniformity of the composition of the alloy improves the fluidity, strength and plasticity of the aluminum alloy during the die-casting process; 2) The alloy further controls the ratio of B, Sr and Ti without adding expensive rare earth elements (such as Sc, Zr, etc.) High strength and toughness are achieved in the case of, which has advantages in cost; 3) Thermodynamic calculations based on the Hill solidification model show that the solid-liquid coexistence interval during solidification of the alloy (Example 3) is 70°C, which is suitable for semi-solid die casting Production; 4) The high-performance aluminum alloy of the present invention has a tensile strength of 188 ⁇ 358MPa, a yield strength of 150 ⁇ 333MPa, and an elongation of 8.0 ⁇ 23.0%. It is suitable for preparation by extrusion die-casting process and is suitable for automobiles, electronic appliances , High-strength, high-toughness, high-density aluminum alloy parts required by high-end equipment and other fields.
  • the cast aluminum alloy of the high-strength and toughness thin-walled structural part of the present invention is composed of Si, Mg, Mn and other elements.
  • Ti and B are added to refine the ⁇ -Al grains, and Sr is introduced
  • the elements refine the coarse acicular Si particles into fine and uniform spherical particles.
  • the formation of ⁇ -AlFesi is inhibited, the uniformity of the structure of the aluminum alloy is improved, and the fluidity, strength and strength of the aluminum alloy during the die-casting process are improved.
  • Plasticity by further controlling the ratio of B, Sr and Ti, high strength and toughness are achieved without adding expensive rare earth elements (such as Sc, Zr, etc.), which has advantages in terms of cost; solid and liquid coexistence during the solidification of the alloy
  • the range is 70°C, which is suitable for semi-solid die-casting production; the high-performance aluminum alloy of the present invention has high mechanical strength and good elongation, is suitable for extrusion die-casting preparation, and is suitable for automobiles, electronic appliances, high-end equipment, etc. High-strength, high-toughness and high-density aluminum alloy parts required by the field.

Abstract

本发明涉及铝合金加工技术领域，尤其涉及一种高强韧薄壁结构件铸造铝合金及其制备方法。所述铝合金包括下述组分，且各组分的含量以重量百分比表示如下：Al 86.98～96.73％，Si 3.00～10.00％，Mg 0.10～1.00％，Mn 0.10～1.00％，Sr 0.01～0.10％，B 0.01～0.12％，Ti 0.05-0.20％，Fe ≤0.60％；并且，重量百分比的比值C1＝B/Sr≥1.00。本发明高强韧铝合金，在优化Si、Mg、Mn主合金元素的基础上，添加Ti、B元素细化α-Al晶粒，添加Sr元素细化变质共晶Si相，并且控制这些元素以及杂质元素的含量，使其相互配合，使的该铝合金具有高强度、良好韧性和优良的压铸工艺性能。

Description

一种高强韧薄壁结构件铸造铝合金及其制备方法
本申请要求在2019年5月24日提交中国专利局、申请号为201910438346.2、发明名称为“一种高强韧薄壁结构件铸造铝合金及其制备方法”的中国专利申请的优先权，其全部内容通过引用结合在本申请中。
技术领域
本发明涉及铝合金加工技术领域，尤其涉及一种高强韧薄壁结构件铸造铝合金及其制备方法。
背景技术
铸造铝合金件在电气仪表、汽车摩托车、通讯等领域应用广泛。随着汽车、机械等领域对铸件薄壁化、轻量化的要求越来越高，一些工件如汽车车身中的高承载、薄壁铁质结构件改由铝合金压力铸造成形，这要求合金不仅应满足常规的无热裂、无偏析现象，能进行薄壁铸件的充填及成型，还尤其要求铸件在经过合适的热处理后具有高强度、高延伸率以及高韧性。
当前国内外应用广泛的Al-Si-Cu系(国内YL112、YL113，日本ADC12、ADC10，美国A380等)、Al-Si-Mg系(国内YL104，日本ADC3、美国A360等)常规非真空压铸(铝合金一般抗拉强度为220-240MPa、延伸率≤3％，远满足不了高强度高韧性的性能要求，尤其是韧性差、服役过程容易疲劳开裂、韧性低。
针对高强高韧压铸铝合金的研究现状，迫切需要在普通铸造工艺下，通过设计优化Al-Si系压铸合金成分、通过组织细化变质处理来改善合金的组织结构，开发出铸造性能优良、高强高塑高韧的铸造铝合金，以满足高承载、薄壁压铸结构件的性能要求。
发明内容
本发明的目的在于针对上述存在问题和不足，通过优化设计合金中Al、Si、Mg、Mn、Sr、B、Ti和Fe的含量，通过步骤1S、2S、3S、4S、5S，抑制β-AlFesi杂质相生成，提供一种高强韧薄壁结构件铸造铝合金及其制备方法。
根据本发明的一个方面，提供一种高强韧薄壁结构件铸造铝合金，所述铝合金包括下述组分，且各组分的含量以重量百分比表示如下：Al 86.98～96.73％，Si 3.00～10.00％，Mg 0.10～1.00％，Mn 0.10～1.00％，Sr 0.01～0.10％，B 0.01～0.12％，Ti 0.05-0.20％，Fe≤0.60％；并且，重量百分比的比值C1＝B/Sr≥1.00。
其中，各组分的含量以重量百分比表示如下：Al 89.79～95.45％，Si 4.00～8.00％，Mg 0.25～0.75％，Mn 0.20～0.80％，Sr 0.01～0.08％，B 0.01～0.10％，Ti 0.08-0.18％，Fe≤0.30％；并且，重量百分比的比值C1＝B/Sr≥1.00。
其中，各组分的含量以重量百分比表示如下：Al 91.35～94.23％，Si 5.00～7.00％，Mg 0.35～0.60％，Mn 0.30～0.60％，Sr 0.01～0.05％，B 0.01～0.05％，Ti 0.10-0.15％，Fe≤0.20％；并且，重量百分比的比值C1＝B/Sr≥1。
其中，重量百分比的比值C1＝B/Sr的范围为1.00～1.50。
其中，重量百分比的比值C2＝Ti/B的范围为2.40～7.50。
其中，重量百分比的比值C2＝Ti/B的范围为3.00～5.00。
根据本发明的另一方面，还提供了一种高强韧薄壁结构件铸造铝合金的制备方法，所述制备方法包括以下步骤：
1S配料：按组分配取原料硅源、镁源、铝源、钛源、锰源、硼源、锶源、铁源，配制铝合金原料；
2S熔炼及压铸：将步骤1S配制的原料加热熔炼，得熔体溶液；将所述熔体溶液进行搅拌，并铸造成铸锭；
3S均匀化：将步骤2S得到的铸锭在540～560℃下进行均匀化热处理，保温3～5h，水冷淬火。
4S固溶：将步骤3S得到的合金在540～560℃下进行固溶，保温1～3h，水淬；
5S时效：将步骤4S得到的合金在160～180℃下进行人工时效，保温2～8h，冷却后得高强韧铝合金。
其中，在步骤1S中，所述硅源为Al-20Si合金，所述镁源为99.95％的镁锭，所述铝源为99.8％的铝锭，所述钛源为Al-10Ti合金，所述锰源为Al-40Mn合金，所述锶源为Al-10Sr合金，所述硼源为Al-5Ti-1B合金，所述铁源为99.95％的铁粉或铝铁中间合金。
其中，在步骤2S中，熔炼温度为730～760℃；所述搅拌方法包括机械搅拌、电磁搅拌或 超声振动方法。
根据本发明的第三个方面，提供一种前述铝合金在半固态压铸生产中的应用。
该高性能压铸铝合金中各元素的作用及含量说明如下：
Si元素在铝合金中能与Al形成Al+Si共晶液相，提高铝合金的压铸流动性，同时还能提高铝合金的强度和机械加工性能。Si含量越高，共晶液相越多，铝合金的压铸流动性越好，但压铸铝合金的韧性会下降。因此，为了保证铝合金具有足够的压铸流动性和韧性，Si的重量百分比含量范围可以限定为3.00～10.00％。优选地，Si的重量百分比含量范围可以限定为4.00～8.00％。更优选地，Si的重量百分比含量范围可以限定为5.00～7.00％。
Mg元素在压铸铝合金中能与Si形成Mg2Si强化相，增强压铸铝合金的强度，Mg含量越高，压铸铝合金的强度也越高，但韧性会逐渐下降。因此，为了保证压铸铝合金的强度和韧性，Mg的重量百分比含量范围可以限定为0.10～1.00％。优选地，Mg的重量百分比含量范围可以限定为0.25～0.75％。更优选地，Mg的重量百分比含量范围可以限定为0.35～0.60％。
Mn元素在压铸铝合金中能与Si形成Mn2Si强化相，增强压铸铝合金的强度，Mn含量越高，压铸铝合金的强度也越高，但韧性会逐渐下降。并且，Mn的含量过多则将形成大量的不可溶粗大金属间化合物，从而降低铝合金的流动性，从而影响铝合金的强度和韧性。因此，Mn的重量百分比含量范围可以限定为0.10～1.00％。优选地，Mn的重量百分比含量范围可以限定为0.20～0.80％。更优选地，Mn的重量百分比含量范围可以限定为0.30～0.60％。
Ti元素在压铸铝合金中主要起到细化α-Al晶粒的作用，改善铝合金的组织成分均匀性，提高压铸铝合金的流动性、强度和韧性。Ti含量小于0.05％，晶粒细化效果不明显。Ti含量越高，晶粒细化效果越好，但Ti含量超过0.20％时，也会导致粗大金属间化合物TiAl3相的出现，恶化压铸铝合金的强度和韧性。因此，Ti的重量百分比含量范围可以限定为0.05～0.20％。优选地，Ti的重量百分比含量范围可以限定为0.08～0.18％。更优选地，Ti的重量百分比含量范围可以限定为0.10～0.15％。
Sr元素在压铸铝合金中主要起到对共晶Si相的细化变质作用。共晶Si相在铝合金中通常都是呈细长的针状，这种细长的针状共晶Si相也会割裂铝合金基体，是导致传统压铸铝合金强度和韧性较低的重要原因。现有技术对共晶Si相的细化变质主要是添加Na，但目前Na元素还存在细化变质效果不稳定、容易引发吸气等问题。发明人通过大量实验研究发现，Sr元素对本发明所述压铸铝合金的共晶Si相具有良好的细化变质作用，其效果明显好于传统的Na元素，还有稳定好、持续时间长、再现性好等优点，还可以避免传统Na元素细化变质引 起的吸气问题。添加0.01～0.10％的Sr元素，可使压铸铝合金中共晶Si的形态从细长的针状转变为细小均匀的颗粒状，显著提高压铸铝合金的强度和韧性。优选地，Sr的重量百分比含量范围可以限定为0.01～0.08％。更优选地，Sr的重量百分比含量范围可以限定为0.01～0.05％。
B元素在压铸铝合金中主要起到细化α-Al晶粒的作用，改善铝合金的组织成分均匀性，提高压铸铝合金的流动性、强度和韧性。因此，B的重量百分比含量范围可以限定为0.01～0.12％。优选地，B的重量百分比含量范围可以限定为0.01～0.10％。更优选地，B的重量百分比含量范围可以限定为0.01～0.05％。
Fe元素可以改善合金的机械强度和拉伸性能，Fe还能明显提高合金的抗蠕变性能以及抗疲劳性能，但是过量的Fe会在铝合金中形成粗大的针状Al-Fe-Si系富Fe相，这种粗大针状富Fe相会严重割裂铝合金基体，是导致传统压铸铝合金强度和韧性较低的主要原因。发明人通过大量实验研究发现，压铸铝合金中杂质元素Fe的含量控制在≤0.60％，优选地，Fe的含量控制在≤0.30％，更优选地，Fe的含量控制在≤0.20％。
进一步深入研究，发明人发现，Sr与B有交互作用，当控制重量百分比的比值C1＝B/Sr≥1.00，二者间交互作用形成细小的SrB6化合物颗粒相，数量很少，存在于枝晶α中心；当C1＝B/Sr<1.00时，颗粒尺寸变大、数量增多，且大多出现在共晶区，Sr-B化合物的形成消耗了大量的Sr和B，导致了Sr，B间的互毒化，削弱了二元素的变质效果。优选地，控制重量百分比的比值C1＝B/Sr的范围为1.00～1.50，这种互毒化作用最弱，二元素可以达到良好的变质效果，从而使压铸铝合金具有极好的机械强度及韧性。
进一步研究发明人还发现，在合金细化过程中，Al-Ti-B比Al-Ti合金细化效率更高，Ti用量更少，加入少量就会使锻造组织产生很大的变化，但是在静止过程中，由于B的沉淀，细化作用很快消退。通过调整Ti元素与B元素的含量比可以减慢B元素的沉淀，使细化作用更持久，从而使压铸铝合金具有极好的机械强度及韧性。因此，控制重量百分比的比值C2＝Ti/B的范围为2.40～7.50，优选地，控制重量百分比的比值C2＝Ti/B的范围为3.00～5.00。
另外，本发明提供了一种上述高强韧薄壁结构件铸造铝合金的制备方法，所述制备方法包括以下步骤：
1S配料：按组分配取原料硅源、镁源、铝源、钛源、锰源、硼源、锶源、铁源，配制铝合金原料；
2S熔炼及压铸：将步骤1S配制的原料加热熔炼，得熔体溶液；将所述熔体溶液进行搅拌，并铸造成铸锭；
3S均匀化：将步骤2S得到的铸锭在540～560℃下进行均匀化热处理，保温3～5h，水冷淬火。
4S固溶：将步骤3S得到的合金在540～560℃下进行固溶，保温1～3h，水淬；
5S时效：将步骤4S得到的合金在160～180℃下进行人工时效，保温2～8h，冷却后得高强韧铝合金。
上述制备方法按照1S)～5S)的顺序依次进行。
步骤1S中，硅源为Al-20Si合金，镁源为99.95％的镁锭，铝源为99.8％的铝锭，钛源为Al-10Ti合金，锰源为Al-40Mn合金，锶源为Al-10Sr合金，硼源为Al-5Ti-1B合金，铁源为99.95％的铁锭或铝铁中间合金，控制杂质元素，确保压铸铝合金获得高强度和高韧性。
步骤2S中，将步骤1S所得的原料加入到感应熔炼炉中，通过抽真空，通氩气，在730～760℃的温度下熔炼，得熔体溶液；采用机械搅拌、电磁搅拌或超声振动方法，搅拌8～10min，铸造成铸锭。
步骤3S中，将步骤2S得到的铸锭在540～560℃下进行均匀化热处理，保温3～5h，水冷淬火。
步骤4S中，将步骤3S得到的合金在540～560℃下进行固溶，保温1～3h，水淬至室温。
步骤5S中，将步骤4S得到的合金在160～180℃下进行人工时效，保温2～8h，冷却后得高强韧铝合金。
本发明中的压铸铝合金与其他铝合金相比有以下优点：1)本发明高强韧薄壁结构件铸造铝合金由Si、Mg、Mn等元素组成，在优化Si、Mg、Mn主合金元素的基础上，添加Ti、B元素细化α-Al晶粒，引入Sr元素使粗大的针状Si颗粒细化变质为细小均匀的球形颗粒，同时通过成分调控，抑制β-AlFesi生成，改善铝合金的组织成分均匀性，提高压铸过程中铝合金的流动性、强度和塑性；2)该合金通过进一步控制B、Sr和Ti的比例，在不添加昂贵的稀土元素(例如Sc、Zr等)的情况下实现了高强韧，在成本方面具有优势；3)基于希尔凝固模型的热力学计算表明，该合金(实施例3)凝固过程中的固液共存区间为70℃，适合进行半固态压铸生产；4)本发明的高性能铝合金，抗拉强度为188～358MPa，屈服强度为150～333MPa，伸长率为8.0～23.0％，适合于挤压压铸工艺制备，满足于汽车、电子电器、高端装备等领域所需的高强度、高韧性、高致密度铝合金零部件。
具体实施方式
为使本发明实施例的目的、技术方案和优点更加清楚，下面将对本发明实施例中的技术方案进行清楚、完整地描述，显然，所描述的实施例是本发明一部分实施例，而不是全部的实施例。基于本发明中的实施例，本领域普通技术人员在没有做出创造性劳动前提下所获得的所有其他实施例，都属于本发明保护的范围。需要说明的是，在不冲突的情况下，本发明中的实施例及实施例中的特征可以相互任意组合。
实施例1
高强韧薄壁结构件铸造铝合金各组分的含量以重量百分比表示如下：Al 96.73％，Si 3.00％，Mg 0.10％，Mn 0.10％，Sr 0.01％，B 0.01％，Ti 0.05％。该高强韧薄壁结构件铸造铝合金的制备方法包括以下步骤：
1S配料：按上述组分配取原料Al-20Si合金，99.95％的镁锭，99.8％的铝锭，Al-10Ti合金，Al-40Mn合金，Al-10Sr合金，Al-5Ti-1B合金，铁源为99.95％的铁粉或铝铁中间合金；
2S熔炼及压铸：将步骤1S所得的原料加入到感应熔炼炉中，通过抽真空，通氩气，在730～760℃的温度下熔炼，得熔体溶液；采用机械搅拌方法，搅拌8～10min，铸造成铸锭；
3S均匀化：将步骤2S得到的铸锭在540～560℃下进行均匀化热处理，保温3～5h，水冷淬火。
4S固溶：将步骤3S得到的合金在540～560℃下进行固溶，保温1～3h，水淬；
5S时效：将步骤4S得到的合金在160～180℃下进行人工时效，保温2～8h，冷却后得高强韧铝合金。
实施例2
高强韧薄壁结构件铸造铝合金各组分的含量以重量百分比表示如下：Al 86.98％，Si 10.00％，Mg 1.00％，Mn 1.00％，Sr 0.10％，B 0.12％，Ti 0.20％，Fe 0.60％。该高强韧薄壁结构件铸造铝合金的制备方法包括以下步骤：
1S配料：按上述组分配取原料Al-20Si合金，99.95％的镁锭，99.8％的铝锭，Al-10Ti合金，Al-40Mn合金，Al-10Sr合金，Al-5Ti-1B合金，铁源为99.95％的铁粉或铝铁中间合金；
2S熔炼及压铸：将步骤1S所得的原料加入到感应熔炼炉中，通过抽真空，通氩气，在730～760℃的温度下熔炼，得熔体溶液；采用电磁搅拌方法，搅拌8～10min，铸造成铸锭；
3S均匀化：将步骤2S得到的铸锭在540～560℃下进行均匀化热处理，保温3～5h，水冷淬火。
4S固溶：将步骤3S得到的合金在540～560℃下进行固溶，保温1～3h，水淬；
5S时效：将步骤4S得到的合金在160～180℃下进行人工时效，保温2～8h，冷却后得 高强韧铝合金。
实施例3
高强韧薄壁结构件铸造铝合金各组分的含量以重量百分比表示如下：Al 95.45％，Si 4.00％，Mg 0.25％，Mn 0.20％，Sr 0.01％，B 0.01％，Ti 0.08％。该高强韧薄壁结构件铸造铝合金的制备方法包括以下步骤：
1S配料：按上述组分配取原料Al-20Si合金，99.95％的镁锭，99.8％的铝锭，Al-10Ti合金，Al-40Mn合金，Al-10Sr合金，Al-5Ti-1B合金，铁源为99.95％的铁粉或铝铁中间合金；
2S熔炼及压铸：将步骤1S所得的原料加入到感应熔炼炉中，通过抽真空，通氩气，在730～760℃的温度下熔炼，得熔体溶液；采用超声振动方法，搅拌8～10min，铸造成铸锭；
3S均匀化：将步骤2S得到的铸锭在540～560℃下进行均匀化热处理，保温3～5h，水冷淬火。
4S固溶：将步骤3S得到的合金在540～560℃下进行固溶，保温1～3h，水淬；
5S时效：将步骤4S得到的合金在160～180℃下进行人工时效，保温2～8h，冷却后得高强韧铝合金。
对比例
为了进一步说明本发明的有益效果，选择其他高强韧铝合金作为对比实施1，其中，该高强韧铝合金有以下质量百分比的组分组成：Si 8.7％，Mn 0.65％，Mg 0.5％，Ce 0.35％，Fe 0.18％，Sr 0.03％，杂质≤0.2％，其余为铝。
测试例
力学性能测试：按中华人民共和国国家标准GMN/T16865-2013，将上述实施例1～15的铝合金加工成标准拉伸试样，并在DNS500型电子拉伸试验机上进行室温拉伸力学性能，其中，拉伸速率为2毫米/分钟。
实施例1～15和对比例的铝合金的力学性能测试结果如表1所示，其中，性能检测测试均已以相同条件相同时间进行表征：
表1
  1 2 3 4 5 6 7 8
Mg 0.10 1.00 0.25 0.75 0.35 0.60 0.60 0.55
Si 3.00 10.00 4.00 8.00 5.00 7.00 7.00 6.00
Mn 0.10 1.00 0.20 0.80 0.30 0.60 0.60 0.40
Fe 0 0.60 0 0.30 0 0.20 0.20 0.15
Sr 0.01 0.10 0.01 0.08 0.01 0.05 0.02 0.03
B 0.01 0.12 0.01 0.10 0.01 0.05 0.03 0.05
Ti 0.05 0.20 0.08 0.18 0.10 0.15 0.10 0.15
Al 96.73 86.98 95.45 89.79 94.23 91.35 91.45 92.67
C1＝B/Sr 1.00 1.20 1.00 1.25 1.00 1.00 1.50 1.67
C2＝Ti/B 5.00 1.67 8.00 1.80 10.00 3.00 3.33 3.00
屈服强度MPa 150.16 333.86 198.23 325.23 246.73 308.32 310.25 290.37
抗拉强度MPa 188.32 358.43 230.15 346.74 282.35 337.47 344.12 329.46
延伸率％ 14 8 13 10 12 19 16 13
续表1
  9 10 11 12 13 14 15 对比例
Mg 0.75 0.70 0.60 0.40 0.35 0.45 0.50
Si 5.50 5.00 7.00 7.00 5.50 5.00 6.50
Mn 0.60 0.50 0.45 0.30 0.30 0.50 0.55
Fe 0.20 0.18 0.10 0.20 0.15 0.10 0.10
Sr 0.05 0.06 0.02 0.03 0.02 0.02 0.03
B 0.06 0.08 0.02 0.05 0.02 0.04 0.03
Ti 0.20 0.12 0.15 0.12 0.10 0.10 0.12
Al 92.64 93.36 91.66 91.90 93.56 93.79 92.17
C1＝B/Sr 1.20 1.33 1.00 1.67 1.00 2.00 1.00
C2＝Ti/B 3.33 1.50 7.50 2.40 5.00 2.50 4.00
屈服强度MPa 320.86 315.27 300.84 267.89 252.13 272.34 295.34 210.50
抗拉强度MPa 342.35 340.56 327.39 293.85 291.67 293.21 315.28 315.30
延伸率％ 11 11 15 13 22 13 21 5.89
从上述实施例和对比例我们可以看出，本发明通过优化铝合金制备过程中的合金元素配比以及压铸成型的工艺，可以获得抗拉强度大于188MPa、屈服强度大于150MPa、伸长率大于8％的铝合金。特别是实施例5、6、7、11、13和15，通过进一步优化主元素和微量元素的比例取得了更好的效果。
本发明中的压铸铝合金与其他铝合金相比有以下优点：1)本发明高强韧薄壁结构件铸造铝合金由Si、Mg、Mn等元素组成，在优化Si、Mg、Mn主合金元素的基础上，添加Ti、B元素细化α-Al晶粒，引入Sr元素使粗大的针状Si颗粒细化变质为细小均匀的球形颗粒， 同时通过成分调控，抑制β-AlFesi生成，改善铝合金的组织成分均匀性，提高压铸过程中铝合金的流动性、强度和塑性；2)该合金通过进一步控制B、Sr和Ti的比例，在不添加昂贵的稀土元素(例如Sc、Zr等)的情况下实现了高强韧，在成本方面具有优势；3)基于希尔凝固模型的热力学计算表明，该合金(实施例3)凝固过程中的固液共存区间为70℃，适合进行半固态压铸生产；4)本发明的高性能铝合金，抗拉强度为188～358MPa，屈服强度为150～333MPa，伸长率为8.0～23.0％，适合于挤压压铸工艺制备，满足于汽车、电子电器、高端装备等领域所需的高强度、高韧性、高致密度铝合金零部件。
最后应说明的是：在本文中，术语“包括”、“包含”或者其任何其他变体意在涵盖非排他性的包含，从而使得包含一系列要素的过程、方法、物品或者设备不仅包括那些要素，而且还包括没有明确列出的其他要素，或者是还包括为这种过程、方法、物品或者设备所固有的要素。在没有更多限制的情况下，由语句“包括一个…”限定的要素，并不排除在包括所述要素的过程、方法、物品或者设备中还存在另外的相同要素。
以上实施例仅用以说明本发明的技术方案，而非对其限制。尽管参照前述实施例对本发明进行了详细的说明，本领域的普通技术人员应当理解：其依然可以对前述各实施例所记载的技术方案进行修改，或者对其中部分技术特征进行等同替换；而这些修改或者替换，并不使相应技术方案的本质脱离本发明各实施例技术方案的精神和范围。
工业实用性
本发明高强韧薄壁结构件铸造铝合金由Si、Mg、Mn等元素组成，在优化Si、Mg、Mn主合金元素的基础上，添加Ti、B元素细化α-Al晶粒，引入Sr元素使粗大的针状Si颗粒细化变质为细小均匀的球形颗粒，同时通过成分调控，抑制β-AlFesi生成，改善铝合金的组织成分均匀性，提高压铸过程中铝合金的流动性、强度和塑性；通过进一步控制B、Sr和Ti的比例，在不添加昂贵的稀土元素(例如Sc、Zr等)的情况下实现了高强韧，在成本方面具有优势；该合金凝固过程中的固液共存区间为70℃，适合进行半固态压铸生产；本发明的高性能铝合金具有较高的机械强度以及良好的伸长率，适合于挤压压铸工艺制备，满足于汽车、电子电器、高端装备等领域所需的高强度、高韧性、高致密度铝合金零部件。

Claims (10)

  1. 一种高强韧薄壁结构件铸造铝合金，其特征在于，所述铝合金包括下述组分，且各组分的含量以重量百分比表示如下：Al 86.98～96.73％，Si 3.00～10.00％，Mg 0.10～1.00％，Mn 0.10～1.00％，Sr 0.01～0.10％，B 0.01～0.12％，Ti 0.05-0.20％，Fe≤0.60％；并且，重量百分比的比值C1＝B/Sr≥1.00。
  2. 根据权利要求1所述的高强韧薄壁结构件铸造铝合金，其特征在于，所述铝合金包括下述组分，且各组分的含量以重量百分比表示如下：Al 89.79～95.45％，Si 4.00～8.00％，Mg 0.25～0.75％，Mn 0.20～0.80％，Sr 0.01～0.08％，B 0.01～0.10％，Ti 0.08-0.18％，Fe≤0.30％；并且，重量百分比的比值C1＝B/Sr≥1.00。
  3. 根据权利要求1所述的高强韧薄壁结构件铸造铝合金，其特征在于，所述铝合金包括下述组分，且各组分的含量以重量百分比表示如下：Al 91.35～94.23％，Si 5.00～7.00％，Mg 0.35～0.60％，Mn 0.30～0.60％，Sr 0.01～0.05％，B 0.01～0.05％，Ti 0.10-0.15％，Fe≤0.20％；并且，重量百分比的比值C1＝B/Sr≥1.00。
  4. 根据权利要求1所述的高强韧薄壁结构件铸造铝合金，其特征在于，重量百分比的比值C1＝B/Sr的范围为1.00～1.50。
  5. 根据权利要求1所述的高强韧薄壁结构件铸造铝合金，其特征在于，重量百分比的比值C2＝Ti/B的范围为2.40～7.50。
  6. 根据权利要求5所述的高强韧薄壁结构件铸造铝合金，其特征在于，重量百分比的比值C2＝Ti/B的范围为3.00～5.00。
  7. 一种如权利要求1～6任一所述的高强韧薄壁结构件铸造铝合金的制备方法，其特征在于，所述制备方法包括以下步骤：
    1S配料：按组分配取原料硅源、镁源、铝源、钛源、锰源、硼源、锶源、铁源，配制铝合金原料；
    2S熔炼及压铸：将步骤1S配制的原料加热熔炼，得熔体熔液；将所述熔体溶液进行搅拌，并铸造成铸锭；
    3S均匀化：将步骤2S得到的铸锭在540～560℃下进行均匀化热处理，保温3-5h，水冷淬火。
    4S固溶：将步骤3S得到的合金在540～560℃下进行固溶，保温1～3h，水淬；
    5S时效：将步骤4S得到的合金在160～180℃下进行人工时效，保温2～8h，冷却后 得高强韧铝合金。
  8. 根据权利要求7所述的高强韧薄壁结构件铸造铝合金的制备方法，其特征在于，在步骤1S中，所述硅源为Al-20Si合金，所述镁源为99.95％的镁锭，所述铝源为99.8％的铝锭，所述钛源为Al-10Ti合金，所述锰源为Al-40Mn合金，所述锶源为Al-10Sr合金，所述硼源为Al-5Ti-1B合金，所述铁源为99.95％的铁粉或铝铁中间合金。
  9. 根据权利要求7所述的高强韧薄壁结构件铸造铝合金的制备方法，其特征在于，在步骤2S中，熔炼温度为730～760℃；所述搅拌方法包括机械搅拌、电磁搅拌或超声振动方法。
  10. 一种根据权利要求1～6任一所述的高强韧薄壁结构件铸造铝合金在半固态压铸生产中的应用。
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