WO2018107829A1 - 含N的无Be无Ni高硬Zr基块体非晶合金及制备方法 - Google Patents

含N的无Be无Ni高硬Zr基块体非晶合金及制备方法 Download PDF

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WO2018107829A1
WO2018107829A1 PCT/CN2017/101423 CN2017101423W WO2018107829A1 WO 2018107829 A1 WO2018107829 A1 WO 2018107829A1 CN 2017101423 W CN2017101423 W CN 2017101423W WO 2018107829 A1 WO2018107829 A1 WO 2018107829A1
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bulk amorphous
amorphous alloy
alloy
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吕昭平
曹迪
吴渊
王辉
刘雄军
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北京科技大学
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    • 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
    • C22C1/11—Making amorphous alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C45/00—Amorphous alloys
    • C22C45/10—Amorphous alloys with molybdenum, tungsten, niobium, tantalum, titanium, or zirconium or Hf as the major constituent

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  • the invention belongs to a bulk amorphous alloy, in particular to an N-containing non-Be high-hardness Zr-based bulk amorphous alloy.
  • Amorphous alloys are metal materials that have emerged in recent years as a new generation of structural and functional applications. Unlike the long-range ordered arrangement of atoms in traditional metal materials, the atoms of amorphous alloys are randomly arranged, have no long-range order, and have no grain boundaries, which also makes amorphous alloys have unique mechanical properties. And broad application prospects.
  • Zr-based bulk amorphous alloys have attracted much attention due to their excellent amorphous forming ability.
  • Zr-Ti-Cu-Ni-Be, Zr-Ti-Cu-Ni-Al and Zr-Cu-Ni-Al and other Zr amorphous alloys can be prepared by copper die casting to prepare centimeter-scale amorphous alloys.
  • Zr-based amorphous alloys also have excellent mechanical properties.
  • the Zr-based bulk amorphous alloy system with high amorphous forming ability in order to improve the amorphous forming ability, Be or Ni is often indispensable in the alloy system.
  • the Zr-based bulk amorphous alloy containing Be and Ni may precipitate Be and Ni elements in the ionic form in the living environment, and the element diffuses and penetrates into the biological tissue, and the Be ion induces the biological tissue.
  • Ni ions are easy to induce allergic reactions in organisms, and the above-mentioned ions eluted may also cause necrosis of surrounding biological tissues and even induce cancer. Therefore, it is of great significance to develop a Zr-based amorphous alloy system containing no Be or Ni.
  • the hardness of the metal material is closely related to the wear resistance of the material.
  • the hardness of Zr-based amorphous alloys currently developed is much lower than that of common Fe-based and Co-based amorphous alloys.
  • the hardening of Zr-based amorphous materials improves the friction and wear properties during service and is one of the important issues that must be solved in industrial applications.
  • the development of a new high-hardness Zr-based amorphous alloy containing Be and Ni with strong amorphous forming ability has important engineering for broadening the application of bulk amorphous alloys in precision wear-resistant castings and biomedical applications. significance.
  • the invention develops a non-Be-free Ni high-hardness Zr-based bulk amorphous alloy containing N, which has strong glass forming ability and high Vickers hardness.
  • the purpose is to not only remove the Be and Ni elements which have toxic side effects on the human body, but also have good biocompatibility, and at the same time, through the microalloying of N, the alloy has strong amorphous forming ability and high hardness.
  • Hf 14 Al 12 Fe 8 Nb 1 N 0.1 alloy can form bulk amorphous with a critical dimension of not less than 2 mm and a Vickers hardness of not less than 561 Hv.
  • the alloy can form bulk amorphous with a critical dimension of not less than 4 mm and a Vickers hardness of not less than 575 Hv.
  • Another object of the present invention is to provide a method for preparing the above alloy, which specifically comprises the following steps:
  • Step 1 The metal raw material having a purity of 99.0 wt% to 99.99 wt% is converted into a mass according to the atomic percentage of the above expression, wherein the N element is added as a powder or a bulk nitride;
  • Step 2 The surface of the raw material in the step 1 is removed, and the raw materials are washed with industrial ethanol and weighed according to the respective required qualities;
  • Step 3 The raw materials processed in the step 2 are stacked in a non-consumable vacuum electric arc furnace or a cold heading suspension furnace in the order of the melting point, wherein the nitride is placed in the middle of the metal raw material for melting. After the mother alloy is sufficiently smelted uniformly, the alloy is suction-cast into water-cooled copper molds of different sizes using a vacuum suction casting apparatus to obtain an amorphous alloy material.
  • the beneficial effects of the invention are:
  • the alloy does not contain Be and Ni elements harmful to living organisms, and is excellent in biocompatibility.
  • the alloy has a strong amorphous forming ability, and the amorphous alloy prepared by the copper mold suction casting method has a critical dimension of not less than 2 mm, and can satisfy the dimensional requirements of the processing field of the amorphous alloy.
  • the alloy is microalloyed by the N element, and the hardness of the alloy is improved, and the Vickers hardness is higher than 540 Hv, so that the amorphous friction property is more excellent.
  • Figure 1 is an XRD pattern of a Zr-Cu-Ti-X-N bulk amorphous alloy prepared in Example 1 of the present invention and a corresponding size alloy containing no N.
  • Figure 2 is a comparison of Vickers hardness of a Zr-Cu-Ti-X-N bulk amorphous alloy prepared in Example 1 of the present invention and a Zr-Cu-Ti-X alloy containing no N.
  • Fig. 3 is an XRD chart of a Zr-Hf-Cu-Fe-Al-Z-N bulk amorphous alloy prepared in Example 2 of the present invention.
  • Figure 4 is a comparison of Vickers hardness of Zr-Hf-Cu-Fe-Al-ZN bulk amorphous alloy prepared by Example 2 of the present invention and Zr-Hf-Cu-Fe-Al-Z amorphous alloy containing no N Figure.
  • Example 1 Preparation and properties of Zr-Cu-Ti-X-N bulk amorphous alloy
  • the Zr-Cu-Ti-XN bulk amorphous alloy composition was designed, and in order to reflect the influence of N microalloying on the amorphous, the inventors also prepared nitrogen-free Zr-Cu-Ti- under the same conditions.
  • Zr-Cu-Ti-X is only used as a reference alloy, but is not within the scope of this patent, and is hereby described.
  • the alloy composition was designed as shown in Table 1, and the components were replaced by N-I, N-II, N-III and N-IV.
  • the XRD patterns of the 3 mm N-I and N-II alloys and the 4 mm N-III and N-IV alloys all exhibited typical diffuse scattering amorphous peaks, and all four alloys were amorphous in this size.
  • the XRD pattern of the alloy containing no N corresponding to N-I to N-IV is shown in Fig. 2. It can be clearly observed that at the same size, the sharp crystal phase diffraction peak in the X-ray pattern of the alloy containing no N indicates that the N-alloy microalloying promotes the amorphous forming ability of the alloy system.
  • Example 2 Preparation and properties of Zr-Hf-Cu-Fe-Al-Z-N bulk amorphous alloy
  • the Zr-Hf-Cu-Fe-Al-ZN bulk amorphous alloy composition was designed, and in order to reflect the influence of N microalloying on the amorphous, the inventors also prepared nitrogen-free Zr- under the same conditions.
  • Zr-Hf-Cu-Fe-Al-Z is only used as a reference alloy, but is not within the scope of this patent, and is hereby described.
  • the alloy composition designed is shown in Table 2, and the components are replaced by N-1 to N-12.
  • Figure 3 shows the XRD pattern of a 4 mm sample of N-1, N-3, N-4 alloy. There is only a typical diffuse scattering peak in the XRD pattern, indicating that the 4mm alloy is amorphous, indicating that the alloy is Has a strong amorphous forming ability.

Abstract

一种含N的无Be无Ni高塑性Zr基块体非晶合金，该合金原子百分比表达式为：ZraCubAcBdXeZfNg，其中，A为Hf和Ti中的一种；B为IIIA族元素；X为除Ni之外的VIII族或稀土元素中至少一种；Z为IB族和VB族元素中的至少一种，其中，a+b+c+d+e+f+g＝100％，25≤a≤65，15≤b≤65，5≤c≤15，0≤d≤15，0≤e≤15，0≤f≤10且0.05≤g≤0.5。该合金不含金属元素Be和Ni，提高Zr基合金的生物相容性；具有强非晶形成能力，采用铜模吸铸法可制备出Zr基块体非晶合金临界尺寸不小于2mm；和不含氮的非晶合金相比，该合金体系的维氏硬度不小于540Hv。

Description

含N的无Be无Ni高硬Zr基块体非晶合金及制备方法 技术领域
本发明属于块体非晶合金，具体涉及一种含N的无Be无Ni高硬度Zr基块体非晶合金。
技术背景
非晶态合金(金属玻璃)是近年来出现的有望作为新一代结构和功能应用的金属材料。和传统金属材料中原子具有长程有序的排列不同，非晶态合金的原子是无规排列的，不具有长程有序性，也不存在晶界，这也使得非晶合金有着独特的力学性能和广阔的应用前景。
目前，研究者已在Zr基、Pd基、La基、Mg基、Fe基、Ni基等十余种合金体系中获得了块体非晶材料。与其他体系的合金相比，Zr基块体非晶合金因其优异的非晶形成能力而备受关注。近期开发的Zr-Ti-Cu-Ni-Be、Zr-Ti-Cu-Ni-Al和Zr-Cu-Ni-Al等Zr非晶合金均可通过铜模铸造制备厘米级非晶合金。另外，Zr基非晶合金还具有优异的力学性能。1)低模量，Zr基非晶合金的杨氏模量和普通的Al合金弹性模量近似，远远低于相对应的Zr基晶体合金；2)弹性极限高，非晶合金的弹性极限为2.0％左右，远远大于普通的晶体合金材料，这也使得非晶合金具有极高的弹性比功，Zr基非晶合金的弹性比功可达19.0MJ/m2， 是弹性最好的弹簧钢弹性比功(2.24MJ/m2)的8倍；3)断裂韧性高，Zr-Ti-Cu-Ni-Be非晶合金的断裂韧性达到了60MPm1/2，随着合金成分的不断优化，Zr基非晶合金的断裂韧性又进一步的提高，如Zr-Cu-Al-Ti非晶合金的断裂韧性已经超过了100MPm1/2。
然而，在非晶形成能力强的Zr基块体非晶合金体系中，为提高非晶形成能力，Be或Ni在该合金体系中常不可或缺。但含Be和Ni的Zr基块体非晶合金在生物体内时可能以离子形式向生物体环境中析出Be和Ni元素，同时该元素向生物组织扩散和渗透，而Be离子会引发生物组织的毒性作用，Ni离子容易诱导生物体的过敏反应，溶出的上述离子还可能导致周围生物组织的坏死，甚至诱发癌症。因此开发不含Be或Ni的Zr基非晶合金体系具有重要意义。此外，金属材料硬度与材料的耐摩性能密切相关。目前开发的Zr基非晶合金的硬度远远低于常见的Fe基和Co基非晶合金。Zr基非晶的硬化，提高服役期间的摩擦磨损性能，也是其工业应用中必须解决的重要课题之一。综上所述，开发具有强非晶形成能力的不含Be和Ni的新型高硬度Zr基非晶合金，对于拓宽块体非晶合金在精密耐磨铸件和生物医学领域的应用具有重要的工程意义。
发明内容
本发明开发出一种含N的无Be无Ni高硬度Zr基块体非晶合金，具有强玻璃形成能力和高维氏硬度。目的在于不仅去除对人体具有毒副作用的Be和Ni元素，生物相容性好，同时通过N的微合金化，使得合金具有强非晶形成能力和高硬度。
该合金的原子百分比表达式为ZraCubAcBdXeZfNg，其中A为Hf和Ti中的一种；B为IIIA族元素，包括但不限于Al和Ga；X为除Ni之外的VIII族或稀土元素中至少一种，包括但不限于Fe、Co或Y；Z为IB族和VB族元素中的至少一种，包括但不限于Nb和Ag；各组分25≤a≤65，15≤b≤65，5≤c≤15，0≤d≤15，0≤e≤15，0≤f≤10，0.05≤g≤0.5，且a+b+c+d+e+f+g＝100％，；采用电弧熔炼铜模吸铸的方法制备。
当A为Hf，B为Al，X为Fe，Z为Nb，a＝40.9，b＝26，c＝14，d＝12，e＝8，f＝1且g＝0.1时，Zr40.9Cu26Hf14Al12Fe8Nb1N0.1合金能够形成大块非晶的临界尺寸不小于2mm，维氏硬度不低于561Hv。
进一步，该合金的原子百分比表达式为ZraCubAcXeNg，其中，其中A为Hf和Ti中的一种；X为除Ni之外的VIII族中至少一种，包括但不限于Fe和Co；a+b+c+e+g＝100％，28≤a≤35，55≤b≤65，8≤c≤12，0≤e≤5且0.05≤g≤0.5。
当A为Ti，X为Fe，a＝30，b＝58.9，c＝10，e＝1且g＝0.1时， Zr30Cu58.9Ti10Fe1N0.1合金能够形成大块非晶的临界尺寸不小于4mm，维氏硬度不低于551Hv，和不含N的非晶合金相比，非晶形成能力和硬度同时提高。
进一步，该合金的原子百分比表达式为ZraCubAcBdXeNg，其中A为Hf和Ti中的一种；B为IIIA族元素，包括但不限于Al和Ga；X为除Ni之外的VIII族或稀土元素中至少一种，包括但不限于Fe、Co或Y；a+b+c+d+e+g＝100％，35≤a≤65，15≤b≤30，5≤c≤15，6≤d≤15，0≤e≤15且0.05≤g≤0.5。
当A为Hf，B为Al，X为Fe，a＝41.9，b＝26，c＝14，d＝12，e＝8且g＝0.1时，Zr41.9Cu26Hf14Al12Fe8N0.1合金能够形成大块非晶的临界尺寸不小于4mm，维氏硬度不低于575Hv。
本发明的另一目的是提供上述合金的制备方法，具体包括以下步骤：
步骤1.以纯度为99.0wt％-99.99wt％的金属原料按照上述表达式的原子百分比换算成质量，其中N元素以粉体或块体氮化物的方式加入；
步骤2.将步骤1中的原料表面氧化皮去除，并使用工业乙醇清洗原料，并按各自所需质量称取；
步骤3.将步骤2处理后的原料按熔点高低顺序堆放在非自耗真空电弧炉或冷坩埚悬浮炉里其中氮化物放置在金属原料的中间，进行熔炼。待母合金充分熔炼均匀后，使用真空吸铸设备，将合金吸铸到不同尺寸的水冷铜模中，获得非晶合金材料。本发明的有益效果在于：
(1)该合金系不含有对生物体有害的Be和Ni元素，生物相容性优异。
(2)该合金系具有强非晶形成能力，通过铜模吸铸的方法制备的非晶合金，其临界尺寸不小于2mm，可以满足非晶合金的加工领域的尺寸要求。
(3)该合金通过N元素的微合金化，提高了合金的硬度，其维氏硬度均高于540Hv，使得非晶的摩擦性能更加优异。
附图说明
图1本发明实例1制备的Zr-Cu-Ti-X-N系大块非晶合金与不含N的对应尺寸合金的XRD图。
图2本发明实例1制备的Zr-Cu-Ti-X-N系大块非晶合金与不含N的Zr-Cu-Ti-X合金维氏硬度的对比。
图3本发明实例2制备的Zr-Hf-Cu-Fe-Al-Z-N系大块非晶合金的XRD图。
图4本发明实例2制备的Zr-Hf-Cu-Fe-Al-Z-N系大块非晶合金与不含N的的Zr-Hf-Cu-Fe-Al-Z系非晶合金维氏硬度对比图。
具体实施方式
下面通过具体实施例对本发明的技术方案做进一步说明。
下面结合具体实施例子对本发明的技术方案做进一步的说明。
实施例1：Zr-Cu-Ti-X-N系大块非晶合金的制备及其性能
设计Zr-Cu-Ti-X-N系大块非晶合金成分，同时为了反映N微合金化对该非晶的影响，本发明人还在同样条件下制备了不含氮的Zr-Cu-Ti-X合金。Zr-Cu-Ti-X仅作为参考合金，但是不在本专利要求范围内，特此说明。所设计的合金成分见表1，成分以N-I，N-II，N-III和N-IV代替。
如图1所示，3mm N-I和N-II合金以及4mm N-III和N-IV合金的XRD图谱均表现出典型的漫散射非晶峰，四个合金在该尺寸下均为非晶相。而与之对应，与N-I～N-IV对应不含N的合金XRD图谱如图2所示。可以明显观察到，在相同的尺寸下，不含N的合金XRD图谱中尖锐的晶体相衍射峰，表明N元素微合金化对该合金系的非晶形成能力有促进作用。
由图5可以明显的观察到N元素的添加显著增强了非晶的维氏硬 度，含N的非晶合金维氏硬度均大于540Hv，相关的硬度数据参见表1。
表1：本发明的一种含N的无Be无Ni高硬度Zr基大块非晶合金的合金组成、力学性能和热力学参数：
Figure PCTCN2017101423-appb-000001
实施例2：Zr-Hf-Cu-Fe-Al-Z-N系大块非晶合金的制备及其性能
设计Zr-Hf-Cu-Fe-Al-Z-N系大块非晶合金成分，同时为了反映N微合金化对该非晶的影响，本发明人还在同样条件下制备了不含氮的Zr-Hf-Cu-Fe-Al-Z合金。Zr-Hf-Cu-Fe-Al-Z仅作为参考合金，但是不在本专利要求范围内，特此说明。所设计的合金成分见表2，成分以N-1～N-12代替。
图3所示为N-1，N-3，N-4合金4mm试样XRD图谱。XRD图谱中只有非晶典型的漫散射峰，表明4mm的合金均为非晶相，说明该合金系具 有强非晶形成能力。
由图4可以明显的观察到N元素的添加显著增强了非晶的维氏硬度，维氏硬度均大于560Hv，相关的硬度数据参见表2。
表2：本发明的一种含N的无Be无Ni高硬度Zr基大块非晶合金的合金组成、力学性能和热力学参数：
Figure PCTCN2017101423-appb-000002
Figure PCTCN2017101423-appb-000003

Claims (10)

  1. 一种含N的无Be无Ni高硬度Zr基块体非晶合金，其特征在于，该Zr基块体非晶合金的原子百分比表达式为ZraCubAcBdXeZfNg，其中，A为Hf或Ti；B为IIIA族元素；X为除Ni之外的VIII族或稀土元素中至少一种；Z为IB族和VB族元素中的至少一种，；a+b+c+d+e+f+g＝100％，25≤a≤65at％，15≤b≤65at％，5≤c≤15at％，0≤d≤15at％，0≤e≤15at％，0≤f≤10at％、0.05≤g≤0.5at％。
  2. 根据权利要求1所述的Zr基块体非晶合金，其特征在于，该Zr基块体非晶合金的原子百分比表达式为ZraCubAcBdXeZfNg，其中A为Hf和Ti中的一种；B为IIIA族元素；X为除Ni之外的VIII族或稀土元素中至少一种；Z为IB族和VB族元素中的至少一种；a+b+c+d+e+f+g＝100％，35≤a≤65at％，15≤b≤30at％，5≤c≤15at％，6≤d≤15，0≤e≤15at％，0≤f≤2at％且0.05≤g≤0.5at％。
  3. 根据权利要求1所述的Zr基块体非晶合金，其特征在于，该Zr基块体非晶合金的原子百分比表达式为ZraCubAcXeNg，其中，其中A为Hf和Ti中的一种；X为除Ni之外的VIII族中至少一种；a+b+c+e+g＝100％，28≤a≤35at％，55≤b≤65at％，8≤c≤12at％，0≤e≤5at％且0.05≤g≤0.5at％。
  4. 根据权利要求1所述的Zr基块体非晶合金，其特征在于，该Zr 基块体非晶合金的原子百分比表达式为ZraCubAcBdXeNg，其中A为Hf和Ti中的一种；B为IIIA族元素；X为除Ni之外的VIII族或稀土元素中至少一种；a+b+c+d+e+g＝100％，35≤a≤65at％，15≤b≤30at％，5≤c≤15at％，6≤d≤15at％，0≤e≤15at％且0.05≤g≤0.5at％。
  5. 根据权利要求1所述的Zr基块体非晶合金，其特征在于，该Zr基块体非晶合金：A为Hf，B为Al，X为Fe，Z为Nb，a＝40.9，b＝26，c＝14，d＝12，e＝8，f＝1且g＝0.1，Zr40.9Cu26Hf14Al12Fe8Nb1N0.1合金能够形成大块非晶的临界尺寸不小于2mm，维氏硬度不小于561Hv。
  6. 根据权利要求3所述的Zr基块体非晶合金，其特征在于，该Zr基块体非晶合金：A为Ti，X为Fe，a＝30，b＝58.9，c＝10，e＝1，g＝0.1，Zr30Cu58.9Ti10Fe1N0.1合金能够形成大块非晶的临界尺寸不小于4mm，维氏硬度不小于551Hv。
  7. 根据权利要求4所述的Zr基块体非晶合金，其特征在于，该Zr基块体非晶合金：A为Hf，B为Al，X为Fe，a＝41.9，b＝26，c＝14，d＝12，e＝8且g＝0.1，Zr41.9Cu26Hf14Al12Fe8N0.1合金能够形成大块非晶的临界尺寸不小于4mm，维氏硬度不小于561Hv。
  8. 一种制备如权利要求1-7任意一项所述的Zr基块体非晶合金的方法，其特征在于，具体包括以下步骤：
    步骤1.以纯度为99.0wt％-99.99wt％的金属原料按照表达式的原子百分比换算成质量，其中N元素以粉体或块体氮化物的方式加入；
    步骤2.将步骤1中的原料表面氧化皮去除，并使用工业乙醇清洗原料，并按各自所需质量称取；
    步骤3.将步骤2处理后的金属原料先按熔点高低顺序依次堆放在非自耗真空电弧炉或冷坩埚悬浮炉里，然后将其中氮化物放置在金属原料的中间，确认无误后进行熔炼再引弧熔炼。待母合金充分熔炼均匀后，使用真空吸铸设备，最后将合金吸铸到不同尺寸的水冷铜模中，获得Zr基块体非晶合。
  9. 根据权利要求8所述的方法，其特征在于，所述Zr基块体非晶合的临界尺寸不小于2mm；维氏硬度高于540Hv。
  10. 一种如权利要求8所述的制备方法制备的Zr基块体非晶合金应用于小型精密耐磨铸件和生物材料领域。
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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN113981335A (zh) * 2021-10-29 2022-01-28 盘星新型合金材料(常州)有限公司 微量元素改性无Be块体非晶合金及其制备方法、应用
CN117626141A (zh) * 2024-01-26 2024-03-01 乌镇实验室 一种具有良好非晶形成能力和超高比强度的钛基非晶合金及其制备方法

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN106702292B (zh) * 2016-12-12 2020-01-07 北京科技大学 含N的无Be无Ni高硬Zr基块体非晶合金及制备方法
CN109355602B (zh) * 2018-11-15 2020-12-29 北京科技大学 具有高玻璃形成能力无镍无铍锆基非晶合金及制备和应用
WO2020223162A1 (en) * 2019-04-30 2020-11-05 Oregon State University Cu-based bulk metallic glasses in the cu-zr-hf-al and related systems
CN114959696B (zh) * 2022-04-29 2023-06-23 清华大学 硬质涂层及其制备方法和应用

Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN102146550A (zh) * 2010-02-05 2011-08-10 中国科学院金属研究所 易于通过熔体铜模浇铸形成非晶态结构的不含镍的锆合金
US20130032252A1 (en) * 2011-08-04 2013-02-07 Institute Of Metal Research Chinese Academy Of Science Amorphous nickel-free zirconium alloy
CN103556085A (zh) * 2013-10-30 2014-02-05 北京科技大学 Zr-Al-Cu-Fe-Nb块体非晶合金及制备方法
CN103774065A (zh) * 2012-10-19 2014-05-07 华为技术有限公司 一种锆基非晶合金
CN104264082A (zh) * 2014-09-28 2015-01-07 南京工程学院 一种氮元素掺杂强韧化金属玻璃复合材料及其制备方法
CN106702292A (zh) * 2016-12-12 2017-05-24 北京科技大学 含N的无Be无Ni高硬Zr基块体非晶合金及制备方法
CN106756647A (zh) * 2016-12-12 2017-05-31 北京科技大学 一种无铍无镍的高塑性锆基块体非晶合金及其制备方法

Family Cites Families (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2005350720A (ja) * 2004-06-10 2005-12-22 Ykk Corp 疲労強度に優れた非晶質合金
CN103911564B (zh) * 2012-12-31 2016-07-27 比亚迪股份有限公司 锆基非晶合金及其制备方法
CN104498844B (zh) * 2014-11-18 2017-03-15 北京科技大学 一种大尺寸trip非晶复合材料及其制备方法
CN105420642B (zh) * 2015-11-25 2017-08-25 北京科技大学 一种氮氧合金化的钛基非晶合金及其制备方法

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN102146550A (zh) * 2010-02-05 2011-08-10 中国科学院金属研究所 易于通过熔体铜模浇铸形成非晶态结构的不含镍的锆合金
US20130032252A1 (en) * 2011-08-04 2013-02-07 Institute Of Metal Research Chinese Academy Of Science Amorphous nickel-free zirconium alloy
CN103774065A (zh) * 2012-10-19 2014-05-07 华为技术有限公司 一种锆基非晶合金
CN103556085A (zh) * 2013-10-30 2014-02-05 北京科技大学 Zr-Al-Cu-Fe-Nb块体非晶合金及制备方法
CN104264082A (zh) * 2014-09-28 2015-01-07 南京工程学院 一种氮元素掺杂强韧化金属玻璃复合材料及其制备方法
CN106702292A (zh) * 2016-12-12 2017-05-24 北京科技大学 含N的无Be无Ni高硬Zr基块体非晶合金及制备方法
CN106756647A (zh) * 2016-12-12 2017-05-31 北京科技大学 一种无铍无镍的高塑性锆基块体非晶合金及其制备方法

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN113981335A (zh) * 2021-10-29 2022-01-28 盘星新型合金材料(常州)有限公司 微量元素改性无Be块体非晶合金及其制备方法、应用
CN113981335B (zh) * 2021-10-29 2022-09-23 盘星新型合金材料(常州)有限公司 微量元素改性无Be块体非晶合金及其制备方法、应用
CN117626141A (zh) * 2024-01-26 2024-03-01 乌镇实验室 一种具有良好非晶形成能力和超高比强度的钛基非晶合金及其制备方法
CN117626141B (zh) * 2024-01-26 2024-04-26 乌镇实验室 一种具有良好非晶形成能力和超高比强度的钛基非晶合金及其制备方法

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