WO2016065498A1 - 一种高强度的变形锌基合金材料 - Google Patents

一种高强度的变形锌基合金材料 Download PDF

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WO2016065498A1
WO2016065498A1 PCT/CN2014/001014 CN2014001014W WO2016065498A1 WO 2016065498 A1 WO2016065498 A1 WO 2016065498A1 CN 2014001014 W CN2014001014 W CN 2014001014W WO 2016065498 A1 WO2016065498 A1 WO 2016065498A1
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zinc
alloy material
based alloy
weight
strength
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PCT/CN2014/001014
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French (fr)
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孙文声
王丽强
陈永力
吴一凤
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宁波博威合金材料股份有限公司
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C18/00—Alloys based on zinc
    • C22C18/02—Alloys based on zinc with copper as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C18/00—Alloys based on zinc
    • C22C18/04—Alloys based on zinc with aluminium as the next major constituent

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  • the invention relates to a zinc-based alloy material and an application field thereof, in particular to a high-strength deformed zinc-based alloy material, which can be applied to the electronics and electrical industries.
  • the traditional die-cast zinc alloy is mainly composed of Zn-Cu or Zn-Al binary alloy and Zn-Al-Cu system, but its strength is generally between 200 and 400 MPa, the hardness is generally between 60 and 100 HV, and the strength and hardness are low. And casting molding, can not meet the cutting requirements of the current machining industry.
  • the tensile strength of the sand casting product is between 276 and 317 MPa, and the tensile strength of the metal casting product is between 310 and 345 MPa, although the tensile strength of the pressure casting product is somewhat Improve, but can only reach about 404MPa.
  • American die-cast zinc alloy grade ZA-12 10.8 ⁇ 11.5% Al, 0.5 ⁇ 1.2% Cu, 0.020 ⁇ 0.030% Mg, Fe ⁇ 0.065%, Pb ⁇ 0.005%, Cd ⁇ 0.005%, Sn ⁇ 0.002%, the rest is Zn .
  • the alloy has a tensile strength of about 400 MPa, an elongation of 4 to 7%, and an HV of 95 to 115. Compared with traditional cast zinc alloy (sand casting, metal casting), this grade die-cast zinc alloy has achieved higher strength, but the tensile strength still cannot reach 450MPa or more, and it can not be machined, which greatly limits the replacement of copper alloy. Aspect of the application.
  • Deformed zinc alloy grade ZnAl10-2 9-11% Al, 1.5-2.5% Cu, 0.02-0.05% Mg, and the rest is Zn.
  • the tensile strength of the alloy in the extruded state is 343.4 to 451.3 MPa, the elongation is 15 to 20%, and the hardness is HV 95-100.
  • the alloy is also a deformed zinc alloy, the tensile strength is still much lower than 500 MPa.
  • Deformed zinc alloy grade ZnAl10-5 9-11% Al, 4.5-5.5% Cu, 0.02-0.05% Mg, and the rest is Zn.
  • the tensile strength of the alloy in the extruded state is 343.4 to 441.5 MPa, the elongation is 12 to 18%, and the hardness is HV 90 to 100. Although the alloy has an increased Cu content, the tensile strength is not improved as compared with ZnAl10-2.
  • the technical problem to be solved by the present invention is the ubiquitous strength against existing zinc-based alloy materials.
  • the problem of low and poor plasticity is to achieve uniformity and refinement of the zinc alloy structure by means of alloying, and to provide a high-strength deformed zinc-based alloy material having a strength of up to 500 MPa and good plasticity.
  • the technical solution adopted by the present invention to solve the above technical problem is: a high-strength deformed zinc-based alloy material, the weight percentage composition of the zinc-based alloy material includes: Cu: 5 to 15 wt%, Al: 7 to 20 wt%, Mg : 0.01 to 1.5 wt%, Cr: 0.01 to 2.0 wt%, the balance being Zn and unavoidable impurities.
  • the microstructure of the zinc-based alloy material contains a fine and uniformly distributed primary phase ⁇ , aluminum-rich Al-Zn- A fine eutectoid structure composed of Cu ternary and a zinc-rich Zn-Al-Cu ternary eutectic structure.
  • Al forms nascent alpha dendrites and eutectic ⁇ phases in the form of aluminum-rich ⁇ -Al solid solution.
  • a small amount of Al is dissolved in ⁇ -Zn solid solution, which mainly plays a strengthening role in the alloy.
  • the alloy Strength and hardness increase, but plasticity decreases.
  • Appropriate Al content can also improve the fluidity of alloy casting, prevent oxidation, and improve the press workability.
  • the Al content is higher than 7%, the strength and hardness of the zinc alloy are improved, but the plasticity is greatly reduced, and the processing property is improved. It also deteriorates significantly and is prone to cracking during drawing or stamping.
  • the alloy of the invention adds 7-20% by weight of Al and 5-15% by weight of Cu, which is a deformed zinc-based alloy material with high aluminum and high copper, and the high aluminum and the high copper each play the role of strengthening the matrix, and the formed aluminum-rich
  • the fine eutectoid structure composed of Al-Zn-Cu ternary composition and the zinc-rich Zn-Al-Cu ternary eutectic structure also play an important role in the improvement of strength. It is found that these ternary structures enhance the strength.
  • the plasticity of the alloy also has a lifting effect, that is, the deformed zinc-based alloy material of the present invention can achieve a combination of high strength and high plasticity, which has not been found in the prior zinc alloy research.
  • the strengthening mechanism of the alloy of the present invention in addition to the solid solution strengthening effect of Al in Zn and the Al-Zn-Cu ternary eutectoid structure of aluminum-rich, zinc-rich Zn-Al-Cu ternary eutectic structure, ⁇
  • fine grain strengthening is also included, and fine grain strengthening also plays an important role in the strength and plasticity of the alloy of the present invention.
  • the ⁇ phase and the ternary structure show a small and uniform distribution, and the respective strengthening mechanisms are combined to make The material can achieve high strength and high plasticity.
  • the content of Al and Cu is not as high as possible.
  • the Al content exceeds 20% by weight
  • the Cu content exceeds 15% by weight
  • the strength of the material decreases, the processability deteriorates severely, and the desired properties cannot be achieved. Therefore, the Cu content is controlled to 5 to 15% by weight
  • the Al content is controlled at 7 to 20% by weight.
  • the invention studies the alloying mechanism of Al and Cu-based zinc alloys, and through the proper proportion matching of the two, and through other alloying elements, the high-strength, high-plasticity and easy-cutting deformed zinc alloy is studied.
  • Cu has little solid solubility in zinc-based alloy materials, a part of Cu is solid-solubilized in the matrix of zinc, and more mainly exists in the form of intermetallic compound CuZn5( ⁇ ) phase, and the content of the intermetallic compound
  • An increase in the copper content leads to an increase in strength while reducing its plasticity.
  • the alloy of the present invention plays a key role in improving strength and improving plasticity by achieving a uniformly distributed grain refining structure due to the occurrence of four-phase transformation in a zinc-based alloy containing high copper and high aluminum.
  • the coarseness and unevenness of the as-cast structure are eliminated, thereby realizing the refinement of the structure, which promotes the improvement of the mechanical properties and the processing property, so that the Cu content can be controlled to be high in the range of 5 to 15 wt%.
  • the perfect combination of strength and high plasticity is achieved.
  • a small amount of magnesium plays a role in purifying grain boundaries in zinc-aluminum-based alloys, preventing the risk of intergranular corrosion of zinc-aluminum elements due to electrochemical factors.
  • an appropriate amount of magnesium, zinc, aluminum and other elements are easy to form fine second phase particles. It creates a pinning effect on the dislocation motion during material loading, thereby increasing the strength of the material.
  • excessive magnesium causes severe embrittlement of the zinc-based alloy material, so the Mg content is controlled to be 0.01 to 1.5% by weight.
  • Chromium mainly forms intermetallic compounds with high melting point and fine distribution in the matrix. Improve the strength and hardness. However, the content of chromium is too low, the strengthening effect is not obvious; the chromium content is too high, which is easy to form inclusions and increase the cost of raw materials. Therefore, the present invention controls the content of chromium to be 0.01 to 2.0% by weight.
  • the primary phase ⁇ has an average particle size of less than 10 ⁇ m, and the primary phase ⁇ has a volume fraction of 30 to 90% in the microstructure of the zinc-based alloy material. It can be seen from the scanning electron micrograph that the grain size of the alloy is less than 10um, the ⁇ phase and the ternary structure show a fine and uniform distribution, and the proportion of the ⁇ phase accounts for 30-90%, so the comprehensive effect enables the material to achieve high strength and High plasticity.
  • the volume fraction of the primary phase ⁇ in the microstructure of the zinc-based alloy material is 60 to 80%.
  • the above deformed zinc-based alloy material may further include X: 0.001 to 0.7% by weight, and the X is at least one of Mn, Zr, Ti, Ni, V, RE, and Si.
  • the content of Mn is 0.001 to 0.1% by weight
  • the content of Zr is 0.001 to 0.1% by weight
  • the content of Ti is 0.001 to 0.1% by weight
  • the content of Ni is 0.001 to 0.1% by weight.
  • the content of V is 0.001 to 0.1% by weight
  • the content of RE is 0.001 to 0.1% by weight
  • the content of Si is 0.001 to 0.05% by weight.
  • Mn, Zr, Ti, Ni, V, RE, and Si are present in the matrix of zinc in the form of a small amount of an intermetallic compound phase, respectively, and serve to strengthen.
  • the addition of Mn to the zinc alloy can refine the zinc alloy structure and improve the overall mechanical properties. Experiments have shown that adding an appropriate amount of Mn to the zinc alloy can improve the strength and hardness of the alloy without affecting the elongation.
  • Mn forms a high melting point zinc-manganese compound ( ⁇ phase) on the zinc grain boundary, which increases the diffusion activation energy at the grain boundary and reduces the diffusion rate of the atom, thereby increasing the tensile strength of the alloy.
  • the final addition amount of Mn in the zinc alloy is 0.001 to 0.1% by weight by a large number of alloying tests.
  • Zirconium has the effect of refining grains and preventing segregation, and the rare earth metal has the functions of refining crystal grains and removing oxygen.
  • the content and total amount of Mn, Zr, Ti, Ni, V, RE, and Si are less than 0.001% by weight, the strengthening effect is not obtained, and if it exceeds 0.7% by weight, the plastic working property of the alloy is obtained.
  • the content of Mn, Zr, Ti, Ni, V, and RE is controlled to be 0.001 to 0.1% by weight, and the content of Si is controlled to be 0.001 to 0.05% by weight, respectively.
  • the above deformed zinc-based alloy material has a tensile strength ⁇ 500 MPa and an elongation ⁇ 10%.
  • the above-mentioned deformed zinc-based alloy materials are used in power plugs, communication connectors, and electronic and electrical products.
  • the production process of the alloy of the present invention mainly includes casting, extrusion, drawing and annealing.
  • the casting can be carried out by vertical semi-continuous casting or hot-top casting, or by a horizontal continuous casting process or a hard-die casting process. Since the melting point of the zinc-based alloy is relatively low, the heating method can be various, and a reverberatory furnace, a power frequency furnace, an induction heating furnace, a resistance furnace, and the like can be used.
  • the extrusion uses a horizontal forward or reverse extruder. According to the actual situation, after different annealing treatments, the broaching machine or the combined drawing machine is used to make the final products of various sizes.
  • the invention has the advantages that the high-strength deformed zinc-based alloy material obtained by the invention has fine microstructure and is based on the fact that the conventional cast zinc alloy and the deformed zinc alloy cannot achieve high strength and high plasticity.
  • the above, the elongation is above 10%
  • the electrical conductivity is above 26% IACS, and has good machinability.
  • it has significant improvement, and can be used as a traditional copper alloy, especially An alternative to traditional lead brass for use in power plugs, electrical and electronic products, and communications connectors.
  • Example 1 is a scanning electron micrograph of a high-strength deformed zinc-based alloy of Example 1 in which a copper-rich phase is uniformly distributed;
  • Example 2 is a scanning electron micrograph of a fine structure of a zinc-rich region of the alloy of Example 2;
  • Figure 3 is a result of energy spectrum analysis at A in Figure 2;
  • Example 4 is a scanning electron micrograph of a fine alloy structure of an aluminum-rich region of the alloy of Example 3;
  • Figure 5 is a result of energy spectrum analysis at B in Figure 4.
  • Figure 6 is a scanning electron micrograph of the morphology of the primary phase of the alloy of Example 4.
  • Fig. 7 is a result of energy spectrum analysis at C in Fig. 6.
  • the master alloy was smelted by induction melting or gas heating. Then, the casting billet with diameter of 170 mm was made by continuous casting or die casting, and the temperature was 180-380 °C. It is extruded into a bar of 13 mm in diameter and finally processed into a finished product of ⁇ 12 mm by cold drawing.
  • the room temperature tensile test is carried out in accordance with GB/T228.1-2010 Metallic Material Tensile Test Part 1: Room Temperature Test Method on the electronic universal performance test machine.
  • the sample adopts a circular section proportional sample with a proportional coefficient of 12 mm.
  • the stretching speed is 5 mm/min.
  • composition and performance test results of the examples, comparative examples are shown in Table 1.
  • the tensile strength of the alloy material of the present invention is 515 to 580 MPa
  • the HV hardness is 120 to 161
  • the elongation is 10.1 to 19.8%
  • the volume fraction of the ⁇ phase is 68 to 90%.

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Abstract

高强度的变形锌基合金材料，包括：Cu：5～15wt％，Al：7～20wt％，Mg：0.01～1.5wt％，Cr：0.01～2.0wt％，余量为Zn和不可避免的杂质，该锌基合金材料的微观组织含有细小而均匀分布的初生相ε、富铝的Al-Zn-Cu三元组成的细小共析组织和富锌的Zn-Al-Cu三元共晶组织。该合金材料的抗拉强度在500MPa以上、HV硬度在120以上、延伸率在10％以上、导电率在26％IACS以上，同时具有良好的机加工性能，可应用于电源插头、电子电气产品和通讯连接器等行业中。

Description

一种高强度的变形锌基合金材料 技术领域
本发明涉及锌基合金材料及其应用领域，具体涉及一种高强度的变形锌基合金材料，该合金材料可应用于电子、电气行业。
背景技术
一直以来，人们对锌基合金的研究与开发多集中在铸造领域，对变形锌合金特别是高强度的变形锌合金研究甚少，但包括铸造锌合金在内的锌合金普遍存在强度偏低的问题，不能满足当前电子、电气等领域对高强度(500MPa以上)的需求，且塑性较差，机加工性能难以满足要求。
传统的压铸锌合金以Zn-Cu或者Zn-Al二元合金以及Zn-Al-Cu系为主，但其强度普遍在200～400MPa、硬度普遍在60～100HV，存在强度和硬度偏低的问题，且采用铸造成型，不能满足当前机加工行业的切削加工要求。以ZA-12铸造锌合金为例，其砂型铸造产品的抗拉强度在276～317MPa之间，金属型铸造产品的抗拉强度在310～345MPa之间，压力铸造产品的抗拉强度虽有所提高，但也只能达到404MPa左右。
美国压铸锌合金牌号ZA-12：10.8～11.5％Al，0.5～1.2％Cu，0.020～0.030％Mg，Fe≤0.065％，Pb≤0.005％，Cd≤0.005％，Sn≤0.002％，其余为Zn。该合金的抗拉强度在400MPa左右，延伸率4～7％，HV：95～115。该牌号压铸锌合金与传统铸造锌合金(砂型铸造、金属铸造)相比，已经实现较高的强度，但抗拉强度仍然无法达到450MPa以上，且不能采用机加工，大大限制了在替代铜合金方面的应用。
美国压铸锌合金牌号ZA-27：25～28％Al，2.0～2.5％Cu，0.012～0.020％Mg，Fe≤0.072％，Pb≤0.005％，Cd≤0.005％，Sn≤0.002％，其余为Zn。该合金的抗 拉强度为420MPa左右，延伸率在1～3％，HV：105～125。随着Al和Cu含量的提高，通过压铸方法生产的变形锌合金在提高抗拉强度方面并没有多大的提高。
近年来业内对变形锌合金也有所研发，通过适当的成分调整、挤压或者拉拔工艺改进，以满足机加工性能要求，但各种类型的变形锌合金仍然存在强度较低(一般＜450MPa)的问题，例如挤压态的变形锌合金ZnAl10-5的抗拉强度仅为343.4～441.5MPa，不能满足对高强度领域合金的需求，限制了锌合金对传统铜合金的替代。
变形锌合金牌号ZnAl10-2：9～11％Al，1.5～2.5％Cu，0.02～0.05％Mg，其余为Zn。该合金挤压态的抗拉强度为343.4～451.3MPa，延伸率15～20％，硬度HV95-100。该合金虽然也为变形锌合金，但抗拉强度仍然远低于500MPa。
变形锌合金牌号ZnAl10-5：9～11％Al，4.5～5.5％Cu，0.02～0.05％Mg，其余为Zn。该合金挤压态的抗拉强度为343.4～441.5MPa，延伸率12～18％，硬度HV90～100。该合金虽然对Cu含量进行了提高，但抗拉强度与ZnAl10-2相比并没有提高。
随着对家用电器环保性能要求的不断提高，对于材料中的铅、镉等有害元素也提出了更高的要求，而这些元素并不是锌合金的必加元素，因此锌合金具有环保优势。我国锌资源储量居世界第1位，而铜资源相对比较匮乏，因此开展高性能变形锌合金材料的研发，替代部分铜合金材料，对于节约我国紧缺的铜资源、综合高效利用锌资源，缓解我国铜资源越来越严重的瓶颈问题，迫在眉睫。
发明内容
本发明所要解决的技术问题是，针对现有的锌基合金材料普遍存在的强度 低、塑性差的问题，通过合金化的手段，实现锌合金组织的均匀与细化，提供一种强度高达500MPa以上、具有良好的塑性的高强度的变形锌基合金材料。
本发明解决上述技术问题所采用的技术方案为：一种高强度的变形锌基合金材料，该锌基合金材料的重量百分比组成包括：Cu：5～15wt％，Al：7～20wt％，Mg：0.01～1.5wt％，Cr：0.01～2.0wt％，余量为Zn和不可避免的杂质，该锌基合金材料的微观组织含有细小而均匀分布的初生相ε、富铝的Al-Zn-Cu三元组成的细小共析组织和富锌的Zn-Al-Cu三元共晶组织。
Al以富含铝的α-Al固溶体形式形成初生α枝晶和共晶α相，少量Al固溶于η-Zn固溶体中，在合金中主要起强化作用，随着Al含量的提高，合金的强度、硬度提高，但塑性降低。适当的Al含量还可以改善合金铸造的流动性，防止氧化，并且改善压力加工性能，但当Al含量高于7％时，锌合金的强度和硬度虽然有所提高，但塑性大幅下降，加工性能也明显恶化，在拉拔或者冲压加工时容易开裂。本发明合金添加7～20wt％的Al、5～15wt％的Cu，是一种高铝高铜的变形锌基合金材料，高铝和高铜各自起到强化基体的作用，形成的富铝的Al-Zn-Cu三元组成的细小共析组织和富锌的Zn-Al-Cu三元共晶组织也对强度的提升起到了重要的作用，实验发现，这些三元组织在提升强度的同时，对合金的塑性同样具有提升作用，也就是说，本发明变形锌基合金材料能够实现高强度和高塑性的结合，这在以往的锌合金研究中还没有发现。
在本发明合金的强化机理，除了Al在Zn中起到的固溶强化作用和富铝的Al-Zn-Cu三元共析组织、富锌的Zn-Al-Cu三元共晶组织、ε相等的第二相强化作用外，还包括细晶强化，细晶强化对本发明合金的强度和塑性提高也具有重要的作用。ε相和三元组织呈现细小和均匀分布，各自强化机理综合作用，使 得材料能够实现高的强度和高的塑性。
但Al和Cu的含量并非越高越好，本发明人通过对不同Al、Cu含量的铸造锌合金和变形锌合金相比发现，提高两者元素的含量，强度并没有明显提高，甚至反而下降。当Al含量超过20wt％时，Cu含量超过15wt％时，材料的强度反而出现下降，加工性能严重恶化，不能够实现所需性能，因此将Cu含量控制在5～15wt％，将Al含量控制在7～20wt％。本发明通过研究Al、Cu基锌合金的合金化机理，通过两者适当的比例搭配，并通过其他合金化元素，研究出高强度、高塑性、易切削的变形锌合金。
Cu在锌基合金材料中有很少的固溶度，一部分Cu固溶于锌的基体中，而更多的主要以金属间化合物CuZn5(ε)相的形式存在，该金属间化合物的含量随铜含量的增加而提高，会导致强度的提高，同时降低其塑性。本发明的合金通过实现均匀分布的晶粒细化的组织，这对于提高强度，改善塑性起到关键性的作用，这是由于在含有高铜、高铝的锌基合金中四相转变的发生，消除了铸态组织的粗大和不均匀现象，从而实现组织的细化，这对于改善机械性能和加工性能起到促进作用，因此将Cu含量控制在5～15wt％的范围内时能够实现高强度和高塑性的完美结合。
少量的镁在锌铝基的合金中起到净化晶界，阻止锌铝元素由于电化学因素发生晶间腐蚀的危险，此外适量的镁和锌、铝等元素都容易形成细小的第二相颗粒，对材料加载过程中的位错运动产生钉扎作用，从而提高材料的强度。而过量的镁却使锌基合金材料发生严重的脆化，因此将Mg含量控制在0.01～1.5wt％。
铬在合金中主要形成熔点高而且细小分布于基体中的金属间化合物，起到 提高强度和硬度的作用。但铬的含量过低，强化效果不明显；铬含量过高，易形成夹杂并提高原料成本。因此，本发明将铬的含量控制在0.01～2.0wt％。
所述的初生相ε的平均颗粒尺寸小于10微米，所述的初生相ε在该锌基合金材料的微观组织中的体积分数为30～90％。从扫描电镜照片可以看出，合金晶粒度小于10um，ε相和三元组织呈现细小和均匀分布，且ε相的比例占到30～90％，因此综合作用使得材料能够实现高的强度和高的塑性。
所述的初生相ε在该锌基合金材料的微观组织中的体积分数为60～80％。
上述变形锌基合金材料还可包括X：0.001～0.7wt％，所述的X为Mn、Zr、Ti、Ni、V、RE和Si中的至少一种。
所述的Mn的含量为0.001～0.1wt％，Zr的含量为0.001～0.1wt％，所述的Ti的含量为0.001～0.1wt％，所述的Ni的含量为0.001～0.1wt％，所述的V的含量为0.001～0.1wt％，所述的RE的含量为0.001～0.1wt％，所述的Si的含量为0.001～0.05wt％。
Mn、Zr、Ti、Ni、V、RE、Si分别以少量的金属间化合物相形式存在于锌的基体中，起到强化的作用。在锌合金中加入Mn可以细化锌合金组织，提高综合力学性能。实验表明，在锌合金中加入适量的Mn，可以在不影响延伸率的情况下，改善合金的强度和硬度。此外，Mn会在锌的基体晶界上生成高熔点的锌锰化合物(ξ相)，能够增大晶界上的扩散激活能，降低原子的扩散速度，从而提高合金的抗拉强度。通过大量的合金化试验，最终确定的Mn在锌合金中的合适添加量为0.001～0.1wt％。锆具有细化晶粒和防止偏析的作用，稀土金属具有细化晶粒和除氧的作用。Mn、Zr、Ti、Ni、V、RE、Si的含量及总量若不足0.001wt％，则起不到强化作用，反之若超过0.7wt％，则会使合金的塑性加工性 能显著下降，导致加工出现困难，因此本发明合金中，将Mn、Zr、Ti、Ni、V、RE的含量分别控制在为0.001～0.1wt％，Si的含量控制在0.001～0.05wt％。
上述变形锌基合金材料的抗拉强度≥500MPa，延伸率≥10％。
上述变形锌基合金材料在电源插头、通讯连接器和电子电气产品中的应用。
本发明合金的生产流程主要包括熔铸、挤压、拉伸和退火。熔铸可以采用垂直的半连续铸造或热顶铸造，也可以采用水平连续铸造工艺或硬模浇铸工艺。由于锌基合金的熔点比较低，因此其加热方式可以多种多样，反射炉、工频炉、感应加热炉、电阻炉等都可以采用。挤压采用卧式的正向或反向挤压机。根据实际情况，采取不同的退火处理后，采用拉床或联合拉拔机制成各种尺寸的最终产品。
与现有技术相比，本发明的优点在于：基于传统铸造锌合金和变形锌合金无法实现高强度、高塑性的现状，本发明获得的高强度的变形锌基合金材料的微观组织含有细小而均匀分布的初生相ε、富铝的Al-Zn-Cu三元组成的细小共析组织和富锌的Zn-Al-Cu三元共晶组织，其抗拉强度在500MPa以上、HV硬度在120以上、延伸率在10％以上、导电率在26％IACS以上，同时具有良好的机加工性能，与现有铸造锌合金和变形锌合金相比，具有显著的提高，可作为传统铜合金尤其是传统铅黄铜的替代品，应用于电源插头、电子电气产品和通讯连接器等行业中。
附图说明
图1为富铜相均匀分布的实施例1高强度变形锌基合金扫描电镜照片；
图2为实施例2合金的富锌区域的细小组织的扫描电镜照片；
图3为图2中A处的能谱分析结果；
图4为实施例3合金的富铝区域的细小合金组织的扫描电镜照片；
图5为图4中B处的能谱分析结果；
图6为实施例4合金的初生相的形貌的扫描电镜照片；
图7为图6中C处的能谱分析结果。
具体实施方式
以下结合附图实施例对本发明作进一步详细描述。
选取了25个实施例合金和2个对比例合金，采用感应熔炼或燃气加热熔炼母合金，然后采用连续铸造或硬模铸造的方法制成直径170mm的铸坯，在180～380℃温度下热挤压成直径13mm的棒材，最后经过冷拉加工制成Φ12mm的成品。
室温拉伸试验按照《GB/T228.1-2010金属材料拉伸试验第1部分：室温试验方法》在电子万能力学性能试验机上进行，试样采用比例系数为12mm的圆截面比例试样，拉伸速度为5mm/min。
实施例、对比例的成分及性能测试结果见表1。
从表1可见，本发明合金材料实施例的抗拉强度为515～580MPa，HV硬度为120～161，延伸率为10.1～19.8％，ε相的体积分数为68～90％。
经检测，各实施例的导电率均在26％IACS以上。
Figure PCTCN2014001014-appb-000001
Figure PCTCN2014001014-appb-000002

Claims (7)

  1. 一种高强度的变形锌基合金材料，其特征在于，该锌基合金材料的重量百分比组成包括：Cu：5～15wt％，Al：7～20wt％，Mg：0.01～1.5wt％，Cr：0.01～2.0wt％，余量为Zn和不可避免的杂质，该锌基合金材料的微观组织含有细小而均匀分布的初生相ε、富铝的Al-Zn-Cu三元组成的细小共析组织和富锌的Zn-Al-Cu三元共晶组织。
  2. 根据权利要求1所述的一种高强度的变形锌基合金材料，其特征在于所述的初生相ε的平均颗粒尺寸小于10微米，所述的初生相ε在该锌基合金材料的微观组织中的体积分数为30～90％。
  3. 根据权利要求2所述的一种高强度的变形锌基合金材料，其特征在于所述的初生相ε在该锌基合金材料的微观组织中的体积分数为60～80％。
  4. 根据权利要求1-3中任一项所述的一种高强度的变形锌基合金材料，其特征在于还包括X：0.001～0.7wt％，所述的X为Mn、Zr、Ti、Ni、V、RE和Si中的至少一种。
  5. 根据权利要求4所述的一种高强度的变形锌基合金材料，其特征在于所述的Mn的含量为0.001～0.1wt％，Zr的含量为0.001～0.1wt％，所述的Ti的含量为0.001～0.1wt％，所述的Ni的含量为0.001～0.1wt％，所述的V的含量为0.001～0.1wt％，所述的RE的含量为0.001～0.1wt％，所述的Si的含量为0.001～0.05wt％。
  6. 根据权利要求1-3中任一项所述的一种高强度的变形锌基合金材料，其特征在于该锌基合金材料的抗拉强度≥500MPa，延伸率≥10％。
  7. 权利要求1-3中任一项所述的一种高强度的变形锌基合金材料在电源插头、通讯连接器和电子电气产品中的应用。
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Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0291492A1 (fr) * 1987-05-13 1988-11-17 CENTRE DE RECHERCHES METALLURGIQUES CENTRUM VOOR RESEARCH IN DE METALLURGIE Association sans but lucratif Alliage à base de zinc résistant à chaud
JPH01230742A (ja) * 1988-03-10 1989-09-14 Sekisui Chem Co Ltd 亜鉛基合金
US20110014084A1 (en) * 2009-07-20 2011-01-20 Eastern Alloys, Inc. High strength, creep resistant zinc alloy

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CN104073685B (zh) * 2014-06-17 2016-08-17 宁波博威合金材料股份有限公司 一种高强度抗蠕变低铜合金材料及其应用

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0291492A1 (fr) * 1987-05-13 1988-11-17 CENTRE DE RECHERCHES METALLURGIQUES CENTRUM VOOR RESEARCH IN DE METALLURGIE Association sans but lucratif Alliage à base de zinc résistant à chaud
JPH01230742A (ja) * 1988-03-10 1989-09-14 Sekisui Chem Co Ltd 亜鉛基合金
US20110014084A1 (en) * 2009-07-20 2011-01-20 Eastern Alloys, Inc. High strength, creep resistant zinc alloy

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