WO2014019400A1 - Method for refining primary silicon of hypereutectic al-si alloy - Google Patents

Method for refining primary silicon of hypereutectic al-si alloy Download PDF

Info

Publication number
WO2014019400A1
WO2014019400A1 PCT/CN2013/076255 CN2013076255W WO2014019400A1 WO 2014019400 A1 WO2014019400 A1 WO 2014019400A1 CN 2013076255 W CN2013076255 W CN 2013076255W WO 2014019400 A1 WO2014019400 A1 WO 2014019400A1
Authority
WO
WIPO (PCT)
Prior art keywords
alloy
silicon
hypereutectic
primary
refining
Prior art date
Application number
PCT/CN2013/076255
Other languages
French (fr)
Chinese (zh)
Inventor
郭建
黄小婷
徐向俊
武晓霞
Original Assignee
中原工学院
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by 中原工学院 filed Critical 中原工学院
Publication of WO2014019400A1 publication Critical patent/WO2014019400A1/en

Links

Classifications

    • 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 belongs to the technical field of alloy materials, and relates to an alloy microstructure refining technology for improving the performance of a hypereutectic aluminum-silicon alloy.
  • hyper-eutectic Al-Si alloys due to the large amount of silicon, have a small density, a small coefficient of thermal expansion, and improved wear resistance.
  • the silicon element in the hypereutectic Al-Si alloy mainly exists in the form of a coarse primary silicon phase and a needle-like eutectic silicon phase.
  • the two existing forms of silicon, especially the coarse primary silicon phase Significantly reduced the mechanical properties of the alloy. Therefore, in industrial production, it is necessary to refine the primary crystalline phase or the eutectic silicon phase in the hypereutectic Al-Si alloy to improve the properties of the alloy.
  • the refinement of the silicon phase in the hypereutectic Al-Si alloy is mainly the refinement of the primary silicon phase.
  • the practical method of refining the primary silicon in the hypereutectic Al-Si alloy is to add a small amount of P element during the alloy casting.
  • the method of refining eutectic silicon is to add a small amount of Sr or Na.
  • the addition of P element to refine the primary silicon in the hypereutectic Al-Si alloy requires a higher casting temperature, and it is usually difficult to refine the primary silicon particles to below 50 microns. Further, in the alloy melt, the P element interacts with the Sr element or the Na element of the refined eutectic silicon, and loses the effect of refining the primary silicon phase or the eutectic silicon phase. Therefore, it is difficult to simultaneously refine primary crystal silicon and eutectic silicon in a hypereutectic Al-Si alloy at the same time in engineering applications.
  • Rapid solidification technology such as spray deposition technology
  • spray deposition technology can effectively suppress the growth of the silicon phase during the solidification of the hypereutectic Al-Si alloy, and simultaneously refine the primary silicon and eutectic silicon in the alloy.
  • the use of rapid solidification technology is costly and it is difficult to manufacture parts of large size or complex shape. Summary of the invention
  • the technical problem to be solved by the present invention is to refine the primary crystalline silicon phase in the hypereutectic Al-Si alloy under the conditions of conventional production techniques.
  • the following technical solution is adopted: When the hypereutectic aluminum-silicon alloy is melted, the primary silicon phase in the hypereutectic aluminum-silicon alloy is refined by using the TiB 2 particle phase.
  • the TiB 2 particle phase content required for refining the primary silicon phase is 0.5 to 4.5% (mass fraction).
  • the 0.5 to 4.5% TiB 2 particle phase required for refining the primary silicon phase is synthesized or introduced by the following method.
  • the first method when casting a eutectic aluminum-silicon alloy, adding KBF 4 and K 2 TiF 6 to the hypereutectic Al-Si alloy melt, so that KBF 4 and K 2 TiF 6 are in the hypereutectic Al-Si alloy The reaction produces TiB 2 particles.
  • the second method in the casting of the eutectic aluminum-silicon alloy, the Al-Ti intermediate alloy and the A1-B intermediate alloy are added to the melt of the hypereutectic Al-Si alloy, and the B and Ti elements introduced by the intermediate alloy react to form TiB. 2 particles.
  • the Al-Ti master alloy contains Ti with a mass fraction of 2 to 20% and a B with a mass fraction of 1 to 10%.
  • the third method in the casting of the eutectic aluminum-silicon alloy, the Al-TiB 2 master alloy is added to the melt of the hypereutectic aluminum-silicon alloy, and the Al-TiB 2 master alloy contains TiB with a mass fraction of 4-20%. 2 .
  • the present invention is a hypereutectic Al-Si alloy with a melting using 162 grain refiner hypereutectic aluminum-silicon alloy primary silicon phase
  • under conventional casting conditions can refine the primary silicon phase to below 50 microns (See Figure 1).
  • Due to the high stability of TiB 2 particles in the melt of aluminum alloy it has long-lasting effect of refining effect, does not affect the modification and refinement effect of Sr or Na element on eutectic silicon in the alloy, and can achieve hypereutectic Simultaneous refinement of primary silicon and eutectic silicon in aluminum-silicon alloys (see Figure 2) significantly improves alloy properties.
  • Figure 1 shows the microstructure of an Al-17%Si-1.3% TiB 2 hypereutectic aluminum-silicon alloy.
  • the eutectic Si in the alloy is needle-like, and the primary Si is 35 to 45 ⁇ m granular.
  • Figure 2 shows the microstructure of Al-20%Si-2%TiB2-0.05%Sr hypereutectic Al-Si alloy.
  • the eutectic Si in the alloy is in the form of dots or fine fibers, and the primary Si is 25 to 35 ⁇ m. Detailed ways
  • a method for refining primary silicon in a hypereutectic Al-Si alloy which is fused with Al-15% Si-0.5% TiB 2 (%, mass fraction, the same below) in a ⁇ resistance furnace, 3200 g of hypereutectic Al-Si alloy .
  • the furnace temperature of the electric resistance furnace is set at 760 °C, and 1770 g of industrial pure aluminum, 1200 g of Al-40% Si intermediate alloy, 112 g of Al-lOT intermediate alloy and 120 g of A1-4B intermediate alloy are added to the graphite clay crucible in the furnace.
  • the alloy melt is degassed and refined according to a conventional smelting process of an aluminum-silicon alloy.
  • the furnace temperature of the electric resistance furnace is set at 770 °C, and industrial pure is added to the graphite clay crucible in the furnace.
  • the metallographic analysis of the alloy sample shows (see Fig. 1) that the eutectic Si in the alloy is needle-like, and the primary Si is 35 to 45 micron particles.
  • a method for refining primary silicon in a hypereutectic Al-Si alloy wherein 3600 g of Al-20%Si-2%TiB 2 -0.05% Sr hypereutectic Al-Si alloy is melted in a tantalum resistance furnace.
  • the furnace temperature of the electric resistance furnace is set at 760 °C, and 2500 g of industrial pure aluminum and 360 g of Al-20% TiB 2 intermediate alloy are added to the graphite clay crucible in the furnace.
  • the metallographic analysis of the alloy sample shows (see Fig. 2) that the eutectic Si in the alloy is in the form of dots or fine fibers, and the primary Si is 25 to 35 ⁇ m.
  • the furnace temperature of the electric resistance furnace is set at 770 °C, and industrial pure is added to the graphite clay crucible in the furnace.
  • the metallographic analysis of the alloy sample showed that the eutectic Si in the alloy was in the form of dots or fine fibers, and the primary Si was in the form of particles of 35 to 45 ⁇ m.
  • a method for refining primary silicon in a hypereutectic Al-Si alloy which is melted in a ⁇ resistance furnace by 1-19%, 8 1% ⁇ 3 ⁇ 4-0.6%, 01-0.4% ⁇ [11-0.06%81"-2 % Ding 18 2 hypereutectic Al-Si alloy 4000g.
  • the furnace temperature of the electric resistance furnace is set at 760 °C, and 2350 g of industrial pure aluminum, 373 g of ⁇ 1-15 ⁇ intermediate alloy and 267 g of A1-10B intermediate alloy are added to the graphite clay crucible in the furnace.
  • the furnace temperature of the electric resistance furnace is set at 760 °C, and 1200 g of industrial pure aluminum, 408 g of ⁇ 1-15 ⁇ intermediate alloy, 280 g of A1-10B intermediate alloy 280 g of Al-lONi intermediate alloy are added to the graphite clay crucible in the furnace.
  • the eutectic Si in the alloy was in the form of dots or fine fibers, and the primary Si was in the form of particles of 35 to 45 ⁇ m.
  • a method for refining primary silicon in a hypereutectic Al-Si alloy in which 1600 g of Al-30% Si-4.5% TiB 2 hypereutectic Al-Si alloy is melted in an induction furnace.
  • the alloy melt is refined and poured into a graphite mold at 860 °C.
  • the metallographic analysis of the alloy sample showed that the eutectic Si in the alloy was needle-like, and the primary Si in the alloy was 45-55 micron particles.
  • the alloy melt is refined and poured into a graphite mold at 850 °C.
  • the metallographic analysis of the alloy sample shows that the eutectic Si in the alloy is in the form of dots or fine fibers, and the primary Si in the alloy is in the form of particles of 40 to 50 ⁇ m.

Abstract

A method for refining the primary silicon of a hypereutectic Al-Si alloy adopts the TiB2 particle phase to refine the primary silicon of the hypereutectic Al-Si alloy during the general casting of the hypereutectic Al-Si alloy. According to the method, the TiB2 particle phase is adopted to refine the primary silicon of the hypereutectic Al-Si alloy during the casting of the hypereutectic Al-Si alloy, and the primary silicon can be refined to a size below 50 micrometers under the general casting condition. With high stability of the TiB2 particle in the molten Al alloy, the refining effect is lasting, and the modifying and refining effects on the eutectic silicon in the alloy by the element of Sr or Na can not be affected; and the eutectic silicon and the primary silicon of the hypereutectic Al-Si alloy can be refined at the same time, so that the performance of the alloy is greatly improved.

Description

一种细化过共晶铝硅合金中初晶硅的方法  Method for refining primary silicon in hypereutectic aluminum-silicon alloy
技术领域 Technical field
本发明属于合金材料技术领域， 涉及提高过共晶铝硅合金使用性能的 合金显微组织结构细化技术。  The invention belongs to the technical field of alloy materials, and relates to an alloy microstructure refining technology for improving the performance of a hypereutectic aluminum-silicon alloy.
背景技术 Background technique
与其它铝硅合金材料相比， 过共晶铝硅合金， 由于含有大量硅元素， 合金的密度小， 热膨胀系数减小， 耐磨性提高。 在常规铸造条件下， 过共 晶铝硅合金中硅元素主要以粗大初晶硅相和针片状的共晶硅相形式存在， 硅元素的这两种存在形式， 特别是粗大初晶硅相显著降低了合金的力学性 能。 所以在工业生产中需要对过共晶铝硅合金中的初晶硅相或共晶硅相进 行细化处理， 以提高合金性能。  Compared with other Al-Si alloy materials, hyper-eutectic Al-Si alloys, due to the large amount of silicon, have a small density, a small coefficient of thermal expansion, and improved wear resistance. Under conventional casting conditions, the silicon element in the hypereutectic Al-Si alloy mainly exists in the form of a coarse primary silicon phase and a needle-like eutectic silicon phase. The two existing forms of silicon, especially the coarse primary silicon phase Significantly reduced the mechanical properties of the alloy. Therefore, in industrial production, it is necessary to refine the primary crystalline phase or the eutectic silicon phase in the hypereutectic Al-Si alloy to improve the properties of the alloy.
目前， 过共晶铝硅合金中的硅相细化主要是初晶硅相细化， 实用的细 化过共晶铝硅合金中初晶硅的方法是， 在合金熔铸时添加少量的 P元素。 细化共晶硅的方法是添加少量的 Sr元素或 Na元素。  At present, the refinement of the silicon phase in the hypereutectic Al-Si alloy is mainly the refinement of the primary silicon phase. The practical method of refining the primary silicon in the hypereutectic Al-Si alloy is to add a small amount of P element during the alloy casting. . The method of refining eutectic silicon is to add a small amount of Sr or Na.
在常规生产技术条件下， 加入 P元素细化过共晶铝硅合金中的初晶硅， 需要使用较高的浇铸温度，通常初晶硅颗粒难以细化到 50微米以下。此外， 在合金熔体中， P元素与细化共晶硅的 Sr元素或 Na元素发生相互作用，而 失去细化初晶硅相或共晶硅相的作用。 因此， 目前工程应用上难以同时细 化过共晶铝硅合金中初晶硅和共晶硅。  Under the conditions of conventional production technology, the addition of P element to refine the primary silicon in the hypereutectic Al-Si alloy requires a higher casting temperature, and it is usually difficult to refine the primary silicon particles to below 50 microns. Further, in the alloy melt, the P element interacts with the Sr element or the Na element of the refined eutectic silicon, and loses the effect of refining the primary silicon phase or the eutectic silicon phase. Therefore, it is difficult to simultaneously refine primary crystal silicon and eutectic silicon in a hypereutectic Al-Si alloy at the same time in engineering applications.
采用快速凝固技术， 如喷射沉积技术， 可以有效抑制过共晶铝硅合金 凝固时硅相长大， 实现同时细化合金中的初晶硅和共晶硅。 但使用快速凝 固技术成本高， 且难以制造尺寸大或形状复杂的零部件。 发明内容 Rapid solidification technology, such as spray deposition technology, can effectively suppress the growth of the silicon phase during the solidification of the hypereutectic Al-Si alloy, and simultaneously refine the primary silicon and eutectic silicon in the alloy. However, the use of rapid solidification technology is costly and it is difficult to manufacture parts of large size or complex shape. Summary of the invention
本发明所要解决的技术问题是在常规生产技术条件下， 对过共晶铝硅 合金中的初晶硅相进行细化。  The technical problem to be solved by the present invention is to refine the primary crystalline silicon phase in the hypereutectic Al-Si alloy under the conditions of conventional production techniques.
为了解决上述技术问题采用以下技术方案： 在过共晶铝硅合金熔配时， 利用 TiB2颗粒相细化过共晶铝硅合金中初晶硅相。 In order to solve the above technical problem, the following technical solution is adopted: When the hypereutectic aluminum-silicon alloy is melted, the primary silicon phase in the hypereutectic aluminum-silicon alloy is refined by using the TiB 2 particle phase.
在含硅量为 15~30% (质量分数） 的过共晶铝硅合金中， 细化初晶硅相 所需的 TiB2颗粒相含量为 0.5~4.5% (质量分数）。 In the hypereutectic Al-Si alloy containing 15 to 30% by mass (mass fraction), the TiB 2 particle phase content required for refining the primary silicon phase is 0.5 to 4.5% (mass fraction).
过共晶铝硅合金中， 细化初晶硅相所需的 0.5~4.5%TiB2颗粒相由下述 方法合成或引入。 In the hypereutectic aluminum-silicon alloy, the 0.5 to 4.5% TiB 2 particle phase required for refining the primary silicon phase is synthesized or introduced by the following method.
第一种方法： 在熔铸过共晶铝硅合金时， 向过共晶铝硅合金熔体中加 入 KBF4和 K2TiF6， 使 KBF4和 K2TiF6在过共晶铝硅合金中反应生成 TiB2 颗粒。 The first method: when casting a eutectic aluminum-silicon alloy, adding KBF 4 and K 2 TiF 6 to the hypereutectic Al-Si alloy melt, so that KBF 4 and K 2 TiF 6 are in the hypereutectic Al-Si alloy The reaction produces TiB 2 particles.
第二种方法： 在熔铸过共晶铝硅合金时， 向过共晶铝硅合金熔体中加 入 Al-Ti中间合金和 A1-B中间合金， 由中间合金引入的 B、 Ti元素反应生 成 TiB2颗粒。 Al-Ti中间合金中含有质量分数为 2~20%的 Ti、 A1-B中间合 金中含有质量分数为 1~10%的 B。 The second method: in the casting of the eutectic aluminum-silicon alloy, the Al-Ti intermediate alloy and the A1-B intermediate alloy are added to the melt of the hypereutectic Al-Si alloy, and the B and Ti elements introduced by the intermediate alloy react to form TiB. 2 particles. The Al-Ti master alloy contains Ti with a mass fraction of 2 to 20% and a B with a mass fraction of 1 to 10%.
第三种方法： 在熔铸过共晶铝硅合金时， 向过共晶铝硅合金熔体中加 入 Al- TiB2中间合金， Al- TiB2中间合金中含有质量分数为 4~20% 的 TiB2。 The third method: in the casting of the eutectic aluminum-silicon alloy, the Al-TiB 2 master alloy is added to the melt of the hypereutectic aluminum-silicon alloy, and the Al-TiB 2 master alloy contains TiB with a mass fraction of 4-20%. 2 .
本发明是在过共晶铝硅合金熔配时， 利用 1 62颗粒细化过共晶铝硅合 金中初晶硅相， 在常规熔铸条件下可以使初晶硅相细化至 50微米以下 （见 附图 1 )。 由于 TiB2颗粒在铝合金熔体中稳定性高， 具有细化效果长效性， 不影响 Sr元素或 Na元素对合金中共晶硅的变质细化作用， 能实现过共晶 铝硅合金中初晶硅和共晶硅同时细化 （见附图 2)， 显著提高合金性能。 附图说明 When the present invention is a hypereutectic Al-Si alloy with a melting using 162 grain refiner hypereutectic aluminum-silicon alloy primary silicon phase, under conventional casting conditions can refine the primary silicon phase to below 50 microns (See Figure 1). Due to the high stability of TiB 2 particles in the melt of aluminum alloy, it has long-lasting effect of refining effect, does not affect the modification and refinement effect of Sr or Na element on eutectic silicon in the alloy, and can achieve hypereutectic Simultaneous refinement of primary silicon and eutectic silicon in aluminum-silicon alloys (see Figure 2) significantly improves alloy properties. DRAWINGS
图 1为 Al-17%Si-1.3%TiB2过共晶铝硅合金显微组织。 Figure 1 shows the microstructure of an Al-17%Si-1.3% TiB 2 hypereutectic aluminum-silicon alloy.
合金中共晶 Si为针片状， 初晶 Si为 35~45微米颗粒状。 The eutectic Si in the alloy is needle-like, and the primary Si is 35 to 45 μm granular.
图 2为 Al-20%Si-2%TiB2-0.05%Sr过共晶铝硅合金显微组织。 Figure 2 shows the microstructure of Al-20%Si-2%TiB2-0.05%Sr hypereutectic Al-Si alloy.
合金中共晶 Si为点状或细小的纤维状， 初晶 Si为 25~35微米颗粒状。 具体实施方式 The eutectic Si in the alloy is in the form of dots or fine fibers, and the primary Si is 25 to 35 μm. Detailed ways
实施例 1  Example 1
一种细化过共晶铝硅合金中初晶硅的方法， 在坩埚电阻炉中熔配 Al-15%Si-0.5%TiB2 ( %， 质量分数， 以下相同） 过共晶铝硅合金 3200g。 A method for refining primary silicon in a hypereutectic Al-Si alloy, which is fused with Al-15% Si-0.5% TiB 2 (%, mass fraction, the same below) in a 坩埚 resistance furnace, 3200 g of hypereutectic Al-Si alloy .
( 1 ) 坩埚电阻炉炉温设定 760°C， 在炉内石墨粘土坩埚中加入工业纯 铝 1770g， Al-40%Si中间合金 1200g， Al-lOTi中间合金 112g， A1-4B中间 合金 120g。  (1) The furnace temperature of the electric resistance furnace is set at 760 °C, and 1770 g of industrial pure aluminum, 1200 g of Al-40% Si intermediate alloy, 112 g of Al-lOT intermediate alloy and 120 g of A1-4B intermediate alloy are added to the graphite clay crucible in the furnace.
(2 ) 上述合金熔化并升温到设定温度后， 按铝硅合金的常规熔炼工艺 对合金熔体除气和精炼。  (2) After the above alloy is melted and heated to a set temperature, the alloy melt is degassed and refined according to a conventional smelting process of an aluminum-silicon alloy.
(3 ) 精炼后于 740 °C浇入金属模中。  (3) After refining, it is poured into a metal mold at 740 °C.
合金试样金相分析显示， 合金中共晶 Si为针片状， 初晶 Si为 45~55微 米颗粒状。  Metallographic analysis of the alloy sample showed that the eutectic Si in the alloy was needle-like, and the primary Si was 45 to 55 micrometers.
实施例 2  Example 2
一种细化过共晶铝硅合金中初晶硅的方法， 在坩埚电阻炉中熔配 Method for refining primary silicon in hypereutectic aluminum-silicon alloy, melting in tantalum resistance furnace
Al-17%Si-1.3%TiB2过共晶铝硅合金 4000g。 Al-17% Si-1.3% TiB 2 hypereutectic aluminum silicon alloy 4000g.
( 1 ) 坩埚电阻炉炉温设定 770°C， 在炉内石墨粘土坩埚中加入工业纯 铝 2920g， Al-13 %TiB2中间合金 400g。 (1) The furnace temperature of the electric resistance furnace is set at 770 °C, and industrial pure is added to the graphite clay crucible in the furnace. Aluminum 2920 g, Al-13 % TiB 2 master alloy 400 g.
(2 ) 上述合金熔化后加入 694g纯 Si。  (2) After the above alloy was melted, 694 g of pure Si was added.
(3 )纯 Si完全熔化， 对合金熔体在 760°C精炼， 精炼后于 750°C浇入 金属模中。  (3) Pure Si is completely melted, refined on the alloy melt at 760 ° C, refined and poured into a metal mold at 750 ° C.
合金试样金相分析显示 （见图 1 )， 合金中共晶 Si为针片状， 初晶 Si 为 35~45微米颗粒状。  The metallographic analysis of the alloy sample shows (see Fig. 1) that the eutectic Si in the alloy is needle-like, and the primary Si is 35 to 45 micron particles.
实施例 3  Example 3
一种细化过共晶铝硅合金中初晶硅的方法， 在坩埚电阻炉中熔配 Al-20%Si-2%TiB2-0.05%Sr过共晶铝硅合金 3600g。 A method for refining primary silicon in a hypereutectic Al-Si alloy, wherein 3600 g of Al-20%Si-2%TiB 2 -0.05% Sr hypereutectic Al-Si alloy is melted in a tantalum resistance furnace.
( 1 ) 坩埚电阻炉炉温设定 760°C， 在炉内石墨粘土坩埚中加入工业纯 铝 2500g， Al-20%TiB2中间合金 360g。 (1) The furnace temperature of the electric resistance furnace is set at 760 °C, and 2500 g of industrial pure aluminum and 360 g of Al-20% TiB 2 intermediate alloy are added to the graphite clay crucible in the furnace.
(2 ) 上述合金熔化后加入 734g纯 Si。  (2) After the above alloy was melted, 734 g of pure Si was added.
(3 ) 纯 Si完全熔化， 对合金熔体在 760°C精炼， 精炼后加入 Al-10Sr 中间合金 18g。  (3) Pure Si is completely melted, and the alloy melt is refined at 760 ° C. After refining, 18 g of Al-10Sr master alloy is added.
(4) Al-10Sr 中间合金完全熔化后， 对熔体进行搅拌并于 740°C浇入 金属模中。  (4) After the Al-10Sr master alloy was completely melted, the melt was stirred and poured into a metal mold at 740 °C.
合金试样金相分析显示（见图 2)， 合金中共晶 Si为点状或细小的纤维 状， 初晶 Si为 25~35微米颗粒状。  The metallographic analysis of the alloy sample shows (see Fig. 2) that the eutectic Si in the alloy is in the form of dots or fine fibers, and the primary Si is 25 to 35 μm.
实施例 4  Example 4
一种细化过共晶铝硅合金中初晶硅的方法， 在坩埚电阻炉中熔配 1-17%8 4.5%01-0.6%^¾-0.06%81"-1.3%丁182过共晶铝硅合金 4300g。 A method for refining primary silicon in a hypereutectic Al-Si alloy, which is melted in a 坩埚 resistance furnace with 1-17%8 4.5%01-0.6%^3⁄4-0.06%81"-1.3% Ding 18 2 Crystalline aluminum silicon alloy 4300g.
( 1 ) 坩埚电阻炉炉温设定 770°C， 在炉内石墨粘土坩埚中加入工业纯 铝 2120g， Α1-5Ή中间合金 775g， A1-4B中间合金 430g。 (1) The furnace temperature of the electric resistance furnace is set at 770 °C, and industrial pure is added to the graphite clay crucible in the furnace. Aluminum 2120g, Α1-5Ή intermediate alloy 775g, A1-4B intermediate alloy 430g.
(2 ) 上述合金熔化后加入 730g纯 Si， 212g纯 Cu。  (2) After the above alloy was melted, 730 g of pure Si and 212 g of pure Cu were added.
(3 ) 纯 Si完全熔化， 对合金熔体在 760°C精炼。  (3) Pure Si is completely melted and refined on the alloy melt at 760 °C.
(4) 精炼后的熔体在 720°C加入 27g纯 Mg， 29g Al-10Sr中间合金。 (5) Al-10Sr中间合金完全熔化后， 熔体升至 740°C， 对熔体进行搅拌 后浇入金属模中。  (4) The refined melt was charged with 27 g of pure Mg and 29 g of Al-10Sr master alloy at 720 °C. (5) After the Al-10Sr master alloy is completely melted, the melt is raised to 740 ° C, and the melt is stirred and poured into a metal mold.
合金试样金相分析显示， 合金中共晶 Si 为点状或细小的纤维状， 初晶 Si为 35~45微米的颗粒状。  The metallographic analysis of the alloy sample showed that the eutectic Si in the alloy was in the form of dots or fine fibers, and the primary Si was in the form of particles of 35 to 45 μm.
实施例 5  Example 5
一种细化过共晶铝硅合金中初晶硅的方法， 在坩埚电阻炉中熔配 1-19%8 1%^¾-0.6%01-0.4%^[11-0.06%81"-2%丁182过共晶铝硅合金 4000g。 A method for refining primary silicon in a hypereutectic Al-Si alloy, which is melted in a 坩埚 resistance furnace by 1-19%, 8 1%^3⁄4-0.6%, 01-0.4%^[11-0.06%81"-2 % Ding 18 2 hypereutectic Al-Si alloy 4000g.
( 1 ) 坩埚电阻炉炉温设定 760°C， 在炉内石墨粘土坩埚中加入工业纯 铝 2350g， Α1-15Ή中间合金 373g， A1-10B中间合金 267g。  (1) The furnace temperature of the electric resistance furnace is set at 760 °C, and 2350 g of industrial pure aluminum, 373 g of Α1-15Ή intermediate alloy and 267 g of A1-10B intermediate alloy are added to the graphite clay crucible in the furnace.
(2 )上述合金熔化后加入 775g纯 Si, 25g纯 Cu和 160g Al-10Mn中间 合金。  (2) After melting the above alloy, 775 g of pure Si, 25 g of pure Cu and 160 g of Al-10Mn intermediate alloy were added.
(3 ) 纯 Si完全熔化， 对合金熔体在 760°C精炼。  (3) Pure Si is completely melted and refined on the alloy melt at 760 °C.
(4) 精炼后的熔体在 720°C加入 42g纯 Mg， 27g Al-10Sr中间合金。 (4) The refined melt was charged with 42 g of pure Mg and 27 g of Al-10Sr master alloy at 720 °C.
(5) 纯 Mg、 Al-10Sr中间合金完全熔化后， 熔体升至 750°C， 对熔体 进行搅拌后浇入金属模中。 (5) After the pure Mg and Al-10Sr master alloys are completely melted, the melt is raised to 750 ° C, and the melt is stirred and poured into a metal mold.
合金试样金相分析显示， 合金中共晶 Si 为点状或细小的纤维状， 初晶 Si为 35~45微米的颗粒状。 一种细化过共晶铝硅合金中初晶硅的方法， 在坩埚电阻炉中熔配Metallographic analysis of the alloy sample showed that the eutectic Si in the alloy was in the form of dots or fine fibers, and the primary Si was in the form of particles of 35 to 45 μm. Method for refining primary silicon in hypereutectic aluminum-silicon alloy, melting in tantalum resistance furnace
Al-22%Si-2.3%Ni-l%Mg-0.9%Cu-0.06%Sr-2.4%TiB2过共晶铝硅合金 3600g。 Al-22% Si-2.3% Ni-1% Mg-0.9% Cu-0.06% Sr-2.4% TiB 2 hypereutectic aluminum silicon alloy 3600 g.
( 1 ) 坩埚电阻炉炉温设定 760°C， 在炉内石墨粘土坩埚中加入工业纯 铝 1200g， Α1-15Ή中间合金 408g， A1-10B中间合金 280g Al-lONi中间合 金 828g。  (1) The furnace temperature of the electric resistance furnace is set at 760 °C, and 1200 g of industrial pure aluminum, 408 g of Α1-15Ή intermediate alloy, 280 g of A1-10B intermediate alloy 280 g of Al-lONi intermediate alloy are added to the graphite clay crucible in the furnace.
(2 ) 上述合金熔化后加入 808g纯 Si和 34g纯 Cu。  (2) After the above alloy was melted, 808 g of pure Si and 34 g of pure Cu were added.
(3 ) 纯 Si完全熔化， 对合金熔体在 760°C精炼。  (3) Pure Si is completely melted and refined on the alloy melt at 760 °C.
(4) 精炼后的熔体在 720°C加入 40g纯 Mg， 24g Al-10Sr中间合金。 (4) The refined melt was charged with 40 g of pure Mg and 24 g of Al-10Sr master alloy at 720 °C.
(5) 纯 Mg、 Al-10Sr中间合金完全熔化后， 熔体升至 750°C， 对熔体 进行搅拌后浇入金属模中。 (5) After the pure Mg and Al-10Sr master alloys are completely melted, the melt is raised to 750 ° C, and the melt is stirred and poured into a metal mold.
合金试样金相分析显示， 合金中共晶 Si为点状或细小的纤维状， 初晶 Si为 35~45微米的颗粒状。  Metallographic analysis of the alloy sample showed that the eutectic Si in the alloy was in the form of dots or fine fibers, and the primary Si was in the form of particles of 35 to 45 μm.
实施例 7  Example 7
一种细化过共晶铝硅合金中初晶硅的方法， 在感应电炉中熔配 Al-30%Si-4.5%TiB2过共晶铝硅合金 1600g。 A method for refining primary silicon in a hypereutectic Al-Si alloy, in which 1600 g of Al-30% Si-4.5% TiB 2 hypereutectic Al-Si alloy is melted in an induction furnace.
( 1 ) 感应炉中熔化 1050g纯铝锭，  (1) melting 1050g of pure aluminum ingot in the induction furnace,
(2 )铝熔体温度达到 790 °C时，将充分混合后的 280g氟钛酸钾（K2TiF6) 和 280g氟硼酸钾 （KBF4) 压入熔体中使之与熔体充分反应。 (2) When the aluminum melt temperature reaches 790 °C, 280 g of potassium fluorotitanate (K 2 TiF 6 ) and 280 g of potassium fluoroborate (KBF 4 ) are thoroughly mixed into the melt to fully react with the melt. .
(3 ) 上述混合物与铝熔体反应完成后， 加入 490g纯 Si。。  (3) After the reaction of the above mixture with the aluminum melt was completed, 490 g of pure Si was added. .
(4) 合金熔体精炼后于 860°C浇入石墨模中。  (4) The alloy melt is refined and poured into a graphite mold at 860 °C.
合金试样金相分析显示， 合金中共晶 Si为针片状， 合金中初晶 Si为 45-55微米的颗粒状。 一种细化过共晶铝硅合金中初晶硅的方法， 在感应电炉中熔配 Al-30%Si-0.06%Sr-4.5%TiB2过共晶铝硅合金 1700g。 The metallographic analysis of the alloy sample showed that the eutectic Si in the alloy was needle-like, and the primary Si in the alloy was 45-55 micron particles. A method for refining primary silicon in a hypereutectic Al-Si alloy, wherein 1700 g of Al-30% Si-0.06% Sr-4.5% TiB 2 hypereutectic Al-Si alloy is melted in an induction furnace.
( 1 ) 感应炉中熔化 llOOg纯铝锭，  (1) Melting llOOg pure aluminum ingot in induction furnace,
(2 )铝熔体温度达到 790 °C时，将充分混合后的 300g氟钛酸钾 (K2TiF6) 和 300g氟硼酸钾 （KBF4) 压入熔体中使之与熔体充分反应。 (2) When the aluminum melt temperature reaches 790 °C, 300 g of potassium fluorotitanate (K 2 TiF 6 ) and 300 g of potassium fluoroborate (KBF 4 ) are thoroughly mixed and pressed into the melt to fully react with the melt. .
(3 ) 上述混合物与铝熔体反应完成后， 加入 520g纯 Si。  (3) After the reaction of the above mixture with the aluminum melt was completed, 520 g of pure Si was added.
(4) 纯 Si完全熔化后加入 11 g A1- 1 OSr中间合金。  (4) 11 g of A1- 1 OSr master alloy was added after pure Si was completely melted.
(5) 合金熔体精炼后于 850°C浇入石墨模中。  (5) The alloy melt is refined and poured into a graphite mold at 850 °C.
合金试样金相分析显示， 合金中共晶 Si为点状或细小的纤维状， 合金中初 晶 Si为 40~50微米的颗粒状。 The metallographic analysis of the alloy sample shows that the eutectic Si in the alloy is in the form of dots or fine fibers, and the primary Si in the alloy is in the form of particles of 40 to 50 μm.

Claims

WO 2014/019400 权 利 要 求 书 PCT/CN2013/076255 WO 2014/019400 Claims PCT/CN2013/076255
1、 一种细化过共晶铝硅合金中初晶硅的方法， 其特征在于： 过共晶铝硅合 金在常规熔铸时， 利用 TiB2颗粒相细化过共晶铝硅合金中初晶硅相。 1. A method for refining the primary crystal silicon in the hypereutectic aluminum-silicon alloy, which is characterized by: during conventional melting and casting of the hypereutectic aluminum-silicon alloy, the TiB 2 particle phase is used to refine the primary crystal in the hypereutectic aluminum-silicon alloy. silicon phase.
2、 根据权利要求 1的细化过共晶铝硅合金中初晶硅的方法， 其特征是： 过 共晶铝硅合金的显微组织特征为， 被细化的初晶硅相中存在 1162颗粒相。 2. The method for refining primary silicon in a hypereutectic aluminum-silicon alloy according to claim 1, characterized in that: the microstructural characteristics of the hypereutectic aluminum-silicon alloy are that there are 116 in the refined primary silicon phase 2 granular phase.
3、 根据权利要求 1的细化过共晶铝硅合金中初晶硅的方法， 其特征是： 在 含硅量为 15~30% (质量分数） 的过共晶铝硅合金中， 细化初晶硅相所需的 TiB2颗粒相含量为 0.5~4.5% (质量分数）。 3. The method for refining primary silicon in a hypereutectic aluminum-silicon alloy according to claim 1, characterized in that: in a hypereutectic aluminum-silicon alloy with a silicon content of 15 to 30% (mass fraction), refining The TiB 2 particle phase content required for the primary silicon phase is 0.5~4.5% (mass fraction).
4、 根据权利要求 3的细化过共晶铝硅合金中初晶硅的方法， 在熔铸过共晶 铝硅合金时， 0.5~4.5%的丁162颗粒相由合金熔体中加入的氟硼酸钾（KBF4) 和氟钛酸钾 （K2TiF6) 合成。 4. According to the method for refining primary silicon in a hypereutectic aluminum-silicon alloy according to claim 3, when the hypereutectic aluminum-silicon alloy is cast, 0.5~4.5% of the D162 particle phase is obtained by adding fluorine to the alloy melt. Potassium borate (KBF 4 ) and potassium fluotitanate (K 2 TiF 6 ) are synthesized.
5、 根据权利要求 3的细化过共晶铝硅合金中初晶硅的方法， 在熔铸过共晶 铝硅合金时， 0.5~4.5%的 TiB2颗粒相由合金熔体中加入 Al-Ti中间合金和 A1-B中间合金合成。 其中 Al-Ti中间合金中含有质量分数为 5~15%的 Ti、 A1-B中间合金中含有质量分数为 1~10%的 B。 5. The method for refining primary silicon in a hypereutectic aluminum-silicon alloy according to claim 3, when the hypereutectic aluminum-silicon alloy is cast, 0.5~4.5% of the TiB 2 particle phase is added to the alloy melt by Al-Ti Master alloy and A1-B master alloy are synthesized. The Al-Ti master alloy contains Ti with a mass fraction of 5 to 15%, and the A1-B master alloy contains B with a mass fraction of 1 to 10%.
6、 根据权利要求 3的细化过共晶铝硅合金中初晶硅的方法， 在熔铸过共晶 铝硅合金时， 0.5~4.5%的 TiB2颗粒相由合金熔体中加入 A1- 丁162中间合金 形成， Al- TiB2中间合金中含有质量分数为 4~20% 的 TiB2。 6. According to the method for refining primary silicon in a hypereutectic aluminum-silicon alloy according to claim 3, when the hypereutectic aluminum-silicon alloy is cast, 0.5~4.5% of the TiB 2 particle phase is added to the alloy melt. 16 2 master alloy is formed, and the Al-TiB 2 master alloy contains TiB 2 with a mass fraction of 4 to 20%.
PCT/CN2013/076255 2012-08-02 2013-05-27 Method for refining primary silicon of hypereutectic al-si alloy WO2014019400A1 (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CN201210272948.3 2012-08-02
CN201210272948.3A CN102787248B (en) 2012-08-02 2012-08-02 Method for refining primary silicon of hypereutectic Al-Si alloy

Publications (1)

Publication Number Publication Date
WO2014019400A1 true WO2014019400A1 (en) 2014-02-06

Family

ID=47152832

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/CN2013/076255 WO2014019400A1 (en) 2012-08-02 2013-05-27 Method for refining primary silicon of hypereutectic al-si alloy

Country Status (2)

Country Link
CN (1) CN102787248B (en)
WO (1) WO2014019400A1 (en)

Families Citing this family (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN104384482B (en) * 2014-10-29 2016-05-04 青岛科技大学 A kind of method of primary silicon in refinement transcocrystallized Al-Si alloy
CN105401012B (en) * 2015-09-21 2017-06-16 辽宁工业大学 A kind of preparation method for being granulated hypereutectic Al Si alloys
CN106884113B (en) * 2017-03-28 2018-09-25 泉州宝顿机械技术开发有限公司 A kind of high-strength aluminum alloy and its casting method
CN108251668A (en) * 2018-04-17 2018-07-06 青岛科技大学 A kind of new application of silica
CN110273087A (en) * 2019-06-25 2019-09-24 昆明理工大学 Regulate and control the method for hypereutectic aluminum-silicon alloy casting overall performance
CN112410591B (en) * 2020-10-30 2022-03-04 滨州渤海活塞有限公司 Super-long-effect double-modification method for hypereutectic aluminum-silicon alloy

Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5217546A (en) * 1988-02-10 1993-06-08 Comalco Aluminum Limited Cast aluminium alloys and method

Family Cites Families (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101058855A (en) * 2007-05-31 2007-10-24 中国铝业股份有限公司 Microstructure thinning process for hypereutectic aluminum alloy

Patent Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5217546A (en) * 1988-02-10 1993-06-08 Comalco Aluminum Limited Cast aluminium alloys and method

Also Published As

Publication number Publication date
CN102787248A (en) 2012-11-21
CN102787248B (en) 2014-06-04

Similar Documents

Publication Publication Date Title
Qin et al. Effect of phosphorus on microstructure and growth manner of primary Mg2Si crystal in Mg2Si/Al composite
WO2014019400A1 (en) Method for refining primary silicon of hypereutectic al-si alloy
CN103361524B (en) Composite modification method for hypereutectic aluminum-silicon alloy
US8695684B2 (en) Method for preparing aluminum—zirconium—titanium—carbon intermediate alloy
CN101775530B (en) Hypereutectic al-si alloy piston material
CN110157935B (en) Al-V-B refiner for casting aluminum-silicon alloy, preparation method and application thereof
CN109136674B (en) Graphene rare earth scandium synergistically enhanced Al-Si-Mg cast aluminum alloy and preparation method thereof
CN112048629A (en) Preparation method of Al-Ti-Nb-B refiner for casting aluminum-silicon alloy
CN108251675B (en) Al-Ti-Nb-B refiner for casting aluminum-silicon alloy and preparation method and application thereof
US9937554B2 (en) Grain refiner for magnesium and magnesium alloys and method for producing the same
CN102952975A (en) High performance casting hypoeutectic Al-Si-Cu-Mg alloy
CN103451486A (en) Al-30Si aluminum alloy containing Sr, B, Ti and Zr and preparation process thereof
EP2487273B1 (en) Aluminum-zirconium-titanium-carbon crystal grain refiner for magnesium and magnesium alloys and preparation method thereof
CN115044809A (en) Cast aluminum-silicon alloy and preparation method thereof, and aluminum-silicon alloy for aviation or automobile castings
CN113549790B (en) High-performance Al-Ti-V-B alloy refiner and preparation method and application thereof
CN114438374A (en) Al-V-Ti-B grain refiner and preparation and application method thereof
CN101838759A (en) 4032 alloy alterant and use method thereof
CN107326228B (en) A kind of composite inoculating transcocrystallized Al-Si alloy and preparation method thereof
WO2023241681A1 (en) Aluminum alloy additive, and preparation method therefor and use thereof
Zhao et al. Preparation of Al–Ti–C–Sr master alloys and their refining efficiency on A356 alloy
CN103451487A (en) Magnesium-containing Al-30Si aluminum alloy and preparation technique thereof
CN102690964B (en) Alterant for hypereutectic aluminum-silicon alloy primary silicon and preparation method thereof
JP2012062501A (en) METHOD OF MANUFACTURING HYPEREUTECTIC Al-Si ALLOY, AND HYPEREUTECTIC Al-Si ALLOY
CN112662909B (en) Carbide nanoparticle modified die-casting aluminum alloy and preparation method thereof
CN108251668A (en) A kind of new application of silica

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 13826276

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: DE

122 Ep: pct application non-entry in european phase

Ref document number: 13826276

Country of ref document: EP

Kind code of ref document: A1