WO2018209970A1 - 一种锆基非晶合金及其制备方法 - Google Patents

一种锆基非晶合金及其制备方法 Download PDF

Info

Publication number
WO2018209970A1
WO2018209970A1 PCT/CN2018/000148 CN2018000148W WO2018209970A1 WO 2018209970 A1 WO2018209970 A1 WO 2018209970A1 CN 2018000148 W CN2018000148 W CN 2018000148W WO 2018209970 A1 WO2018209970 A1 WO 2018209970A1
Authority
WO
WIPO (PCT)
Prior art keywords
amorphous alloy
based amorphous
alloy
amorphous
preparing
Prior art date
Application number
PCT/CN2018/000148
Other languages
English (en)
French (fr)
Inventor
李毅
王寅霄
蔡红传
仇金九
Original Assignee
中国科学院金属研究所
江苏海金非晶科技有限公司
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 中国科学院金属研究所, 江苏海金非晶科技有限公司 filed Critical 中国科学院金属研究所
Priority to US16/500,083 priority Critical patent/US11655529B2/en
Publication of WO2018209970A1 publication Critical patent/WO2018209970A1/zh

Links

Images

Classifications

    • 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
    • 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

Definitions

  • the invention relates to a Zr-based amorphous alloy with high amorphous forming ability and excellent mechanical properties and a preparation method thereof.
  • amorphous alloys Since the discovery of amorphous alloys, after decades of research and exploration, many amorphous alloy systems such as Zr-based, Cu-based, Fe-based, Ti-based, and rare-earth based have been developed. Among them, Zr-based amorphous alloys have high strength, high elasticity, excellent corrosion resistance and good forming ability, and it is believed that Zr-based amorphous alloys should have great application prospects due to the existence of these excellent properties.
  • Zr-based bulk amorphous alloys are considered to be a new material in the 21st century.
  • the applicable range is currently complex parts made of traditional metal materials such as steel, titanium and aluminum with a weight below 100g.
  • Traditional parts made of metal materials such as steel, aluminum alloy, and magnesium alloy often require many processing steps. Although the raw material cost is low, the processing cost is very high.
  • Zr-based amorphous alloys also have the characteristics of small shrinkage during solidification, high surface smoothness, and good mold filling ability.
  • Zr-based amorphous alloys can be formed in one step by die-casting process, directly obtaining components with complicated shapes and precise dimensions, which greatly reduces processing steps and costs, which is also the advantage of Zr-based amorphous alloys in industrial applications.
  • this advantage is offset by the shortcomings of Zr-based bulk amorphous alloys in the industrial high-oxygen and high-impurity environment, such as a large decrease in amorphous forming ability, a large reduction in mechanical properties, and a low yield.
  • the requirements for industrialization are extremely slow. Therefore, solving the problems encountered in the industrialization process of Zr-based bulk amorphous alloys has become a prerequisite for the wide application of Zr-based bulk amorphous alloys in the future.
  • the method for solving the excessive oxygen content of Zr-based bulk amorphous alloy under industrial production conditions is usually to add rare earth elements to the alloy, and to use rare earth elements as "oxygen scavengers" to neutralize the oxygen in the alloy, so that The ability to form amorphous is maintained.
  • this method causes the oxide to precipitate and be trapped in the alloy, thereby destroying the mechanical properties of the alloy. Therefore, the invention of a Zr-based amorphous alloy containing no rare earth elements and having excellent amorphous forming ability and mechanical properties at a high oxygen content is the only way to promote its large-scale application in the future.
  • the invention aims at the problem that the existing Zr-based amorphous alloy has poor amorphous forming ability at high oxygen content, and provides a Zr-based amorphous alloy suitable for high oxygen content and a preparation method thereof.
  • the invention provides a Zr-based amorphous alloy, the composition of which is: (Zr a Hf b Cu c Ni d Al e ) 100-x O x , a, b, c, d, e, x are atomic percentage Where: 49 ⁇ a ⁇ 55, 0.05 ⁇ b ⁇ 1, 31 ⁇ c ⁇ 38, 3 ⁇ d ⁇ 5, 7 ⁇ e ⁇ 10.5, 0.05 ⁇ x ⁇ 0.5.
  • the Zr-based amorphous alloy has an amorphous content of 40%-95% when it is cast into a rod-shaped sample having a diameter of 12-16 mm and a length of 60 mm, and its strength reaches 1800 MPa or more, and the fracture toughness is higher than that. 90KPam 1/2 .
  • the invention provides a Zr-based amorphous alloy, the composition of which is: (Zr a Hf b Cu c Ni d Al e ) 100-x O x , a, b, c, d, e, x are atomic percentage
  • the preferred alloy composition range is: 52.5 ⁇ a ⁇ 54, 0.3 ⁇ b ⁇ 0.6, 33 ⁇ c ⁇ 35.5, 3.2 ⁇ d ⁇ 4, 8 ⁇ e ⁇ 10, 0.05 ⁇ x ⁇ 0.2.
  • the Zr-based amorphous alloy has an amorphous content of more than 80% when cast into a rod-like sample having a diameter of 12 mm and a length of 60 mm, based on the volume of the alloy.
  • the invention provides a Zr-based amorphous alloy, the composition of which is: (Zr a Hf b Cu c Ni d Al e ) 100-x O x , a, b, c, d, e, x are atomic percentage
  • the preferred alloy composition range is: 50.5 ⁇ a ⁇ 52, 0.4 ⁇ b ⁇ 0.8, 36 ⁇ c ⁇ 37.5, 3 ⁇ d ⁇ 4.5, 8 ⁇ e ⁇ 10, 0.05 ⁇ x ⁇ 0.3.
  • the Zr-based amorphous alloy has an amorphous content of more than 80% when cast into a rod-shaped sample having a diameter of 16 mm and a length of 60 mm, based on the volume of the alloy.
  • the invention also provides a preparation method of the above Zr-based amorphous alloy, which comprises three stages of charging, smelting, casting and cooling forming under vacuum or under an inert gas atmosphere: the raw materials are in accordance with the above atomic percentage After the weighing, the smelting process is carried out in a vacuum state or a protective atmosphere of an inert gas, and the raw material is slowly heated by induction heating to gradually form a molten pool, and finally the raw materials are all melted. After a certain holding time, the melt is inverted and cast into a mold for cooling.
  • the method for preparing a Zr-based amorphous alloy according to the present invention is characterized in that the invention can adopt industrial grade raw materials, and the purity requirement thereof is not high, so that the raw material cost of the alloy is greatly reduced: the purity of the raw material is >97%, and the oxygen thereof The content requirement is not higher than 2 at.%.
  • the present invention does not require a high melting atmosphere, and may be selected as a vacuum environment or an inert gas protective atmosphere. If a vacuum environment is selected, the smelting vacuum is maintained at 0.5-500 Pa. If an inert gas is used for protection, argon gas should be selected. Protect.
  • the invention adopts the method of induction melting to heat and smelt the raw materials
  • the crucible may be selected from one of quartz crucible, graphite crucible, calcium oxide crucible and mullite, and the power is slowly increased during the melting and the melting temperature is controlled, and the maximum temperature should be 1400. -1600 ° C, the holding time should be no less than 180 seconds at the highest temperature.
  • the melt is poured into the mold by means of flip casting, and the casting temperature should be greater than 1100 ° C.
  • the mold can be made of steel mold, copper mold and the like, and the mold can be cooled by water cooling.
  • the Zr-based amorphous alloy provided by the invention contains Hf element, and compared with the addition of the rare earth element, the micro-addition of the Hf element improves the amorphous forming ability of the alloy, and the amorphous alloy with a larger critical dimension is more easily obtained. At the same time, the addition of Hf maintains the mechanical properties of the alloy without increasing the brittleness of the alloy due to the addition of rare earth elements.
  • the Zr-based amorphous alloy provided by the present invention adds oxygen as an element to the alloy system, and it is actually proved that the oxygen content is too low, which is not entirely advantageous for the improvement of the mechanical properties of the amorphous alloy, and the present invention passes By appropriately increasing the oxygen content, the most preferable range of the oxygen content is obtained, and the mechanical properties of the amorphous alloy are improved.
  • Figure 1 is an amorphous alloy XRD diffraction pattern of Example 1.
  • Figure 2 is a thermodynamic parameter of the amorphous alloy described in Example 1.
  • Figure 3 is a graph showing the mechanical properties of the amorphous alloy described in Example 1.
  • Figure 4 is an amorphous alloy XRD diffraction pattern of Example 2.
  • Figure 5 is a thermodynamic parameter of the amorphous alloy described in Example 2.
  • Figure 6 shows the mechanical properties of the amorphous alloy described in Example 2.
  • the raw materials used in the following examples were >97% pure, ⁇ 2 at.% oxygen, and >97% argon.
  • the raw material was placed in a graphite crucible, vacuumed to 5 Pa, smelted under an argon atmosphere, the power was slowly increased, the melting temperature was controlled to rise to 1400 ° C, the holding time was 300 s, and then the power was slowly reduced and the temperature was lowered to 1200 ° C.
  • Casting into a copper mold a rod-shaped sample having a size of ⁇ 12 ⁇ 60 mm was obtained, and its amorphous content was 95% by volume. It was analyzed by an XRD diffractometer whether it was amorphous, and its structure was confirmed to be an amorphous structure as shown in Fig. 1.
  • the thermodynamic parameters were measured by DSC, as shown in Fig.
  • the raw material was placed in a quartz crucible, vacuumed to 0.5 Pa, smelted under an argon atmosphere, the power was slowly increased, the melting temperature was controlled to rise to 1500 ° C, the holding time was 240 s, and then the power was slowly reduced and the temperature was lowered to 1150 ° C.
  • Casting into a copper mold a rod-shaped sample having a size of ⁇ 16 ⁇ 60 mm was obtained, and its amorphous content was 99% by volume. It was analyzed whether it was amorphous by an XRD diffractometer, and its structure was confirmed to be an amorphous structure as shown in Fig. 4.
  • the thermodynamic parameters were measured by DSC, as shown in Fig.
  • the 2mm bar had a compressive strength of 1890 MPa, a Vickers hardness of 550, and a fracture toughness of 93 KPam 1/2 .
  • the raw material was placed in a graphite crucible, vacuumed to 0.5 Pa, smelted under an argon atmosphere, the power was slowly increased, the melting temperature was controlled to rise to 1400 ° C, the holding time was 180 s, and then the power was slowly reduced and the temperature was lowered to 1200 ° C.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacture And Refinement Of Metals (AREA)
  • Continuous Casting (AREA)

Abstract

一种Zr基非晶合金及其制备方法，该合金的组成为：(Zr aHf bCu cNi dAl e) 100-xO x，a、b、c、d、e、x为原子百分比，其中：49≤a≤55，0.05≤b≤1，31≤c≤38，3≤d≤5，7≤e≤10.5，0.05≤x≤0.5。以合金体积为准，该Zr基非晶合金在浇铸成为直径为12-16mm、长度为60mm的棒状样品，非晶含量为40％-95％，其强度达到1800MPa以上，断裂韧性高于90KPam 1/2。

Description

一种锆基非晶合金及其制备方法 技术领域
本发明涉及一种具有较高非晶形成能力及优良机械性能的Zr基非晶合金及其制备方法。
背景技术
自非晶合金发现以来，经过几十年的研究探索，目前已经发展出了如Zr基、Cu基、Fe基、Ti基、稀土基等诸多非晶合金体系。其中Zr基非晶合金拥有高强度、高弹性、优良的耐腐蚀性以及良好的成型能力等特点，并被认为由于这些优异性能的存在，Zr基非晶合金应该有着巨大的应用前景。
Zr基大块非晶合金被认为是一种21世纪的新材料，其可应用的范围是目前重量在100g以下由钢、钛、铝等传统金属材料所制造的复杂零件。传统的钢铁、铝合金、镁合金等金属材料制成的复杂零件往往需要许多加工步骤，虽然原料成本较低，但加工成本非常高昂。然而Zr基非晶合金除了具有高强度、高弹性等一系列优异的机械性能外，还具有凝固过程中收缩率小、表面光洁程度极高、充模能力好等特点。这些特点使得Zr基非晶合金可以通过压铸工艺一步成型，直接获得形状复杂并且尺寸精确的零部件，大幅度减少了加工步骤及成本，这也是Zr基非晶合金在工业应用中的优势所在。但是这种优势却被Zr基大块非晶合金在工业高氧、高杂质的环境下其非晶形成能力大幅度下降、机械性能大打折扣、良品率低的缺点所抵消，使其无法满足市场的要求，产业化的速度极为缓慢。因此解决在Zr基大块非晶合金产业化过程中遇到的问题成为未来Zr基大块非晶合金广泛应用的前提条件。
在以往，解决Zr基大块非晶合金在工业生产条件下氧含量过高的方法通常是向合金中添加稀土元素，利用稀土元素作为“除氧剂”，中和合金中的氧，使得 其非晶形成能力得以保持。然而这种方法会使氧化物析出并夹杂在合金中，进而破坏合金的力学性能。因此发明不含稀土元素并且在高氧含量下具有优良的非晶形成能力及机械性能的Zr基非晶合金是未来推动其大规模应用的唯一途径。
发明内容
本发明针对现有Zr基非晶合金在高氧含量下非晶形成能力较差的问题，提供了一种适用于高氧含量的Zr基非晶合金及其制备方法。
本发明提供了一种Zr基非晶合金，该合金的组成为：(Zr aHf bCu cNi dAl e) 100-xO x，a、b、c、d、e、x为原子百分比，其中：49≤a≤55，0.05≤b≤1，31≤c≤38，3≤d≤5，7≤e≤10.5，0.05≤x≤0.5。以合金体积为准，该Zr基非晶合金在浇铸成为直径为12-16mm、长度为60mm的棒状样品时，其非晶含量为40％-95％，其强度达到1800MPa以上，断裂韧性高于90KPam 1/2。
本发明提供了一种Zr基非晶合金，该合金的组成为：(Zr aHf bCu cNi dAl e) 100-xO x，a、b、c、d、e、x为原子百分比，优选的合金成分组成范围为：52.5≤a≤54，0.3≤b≤0.6，33≤c≤35.5，3.2≤d≤4，8≤e≤10，0.05≤x≤0.2。以合金体积为准，该Zr基非晶合金在浇铸成为直径为12mm、长度为60mm的棒状样品时，其非晶含量大于80％。
本发明提供了一种Zr基非晶合金，该合金的组成为：(Zr aHf bCu cNi dAl e) 100-xO x，a、b、c、d、e、x为原子百分比，优选的合金成分组成范围为：50.5≤a≤52，0.4≤b≤0.8，36≤c≤37.5，3≤d≥4.5，8≤e≤10，0.05≤x≤0.3。以合金体积为准，该Zr基非晶合金在浇铸成为直径为16mm、长度为60mm的棒状样品时，其非晶含量大于80％。
本发明还提供了上述Zr基非晶合金的制备方法，此方法包括在真空状态或 者在惰性气体保护氛围下所进行的装料、熔炼、浇铸并冷却成型等三个阶段：原料按照上述原子百分比进行称取后进行熔炼，熔炼过程应在真空状态或惰性气体的保护气氛下进行，利用感应加热的方式将原料缓慢加热，逐步形成熔池，最终将原料全部融化。在经过一定的保温时间后，将熔体翻转浇铸进入模具进行冷却。
本发明所述的Zr基非晶合金制备方法，其特征在于本发明可以采用工业级原材料，对其纯度要求不高，使得合金的原料成本大幅度降低：原料纯度＞97％即可，其氧含量要求为不高于2at.％。此外，本发明对熔炼气氛要求不高，可选择为真空环境或者惰性气体保护气氛，如选择真空环境，其熔炼真空度保持在0.5-500帕，若采用惰性气体进行保护，则应选用氩气进行保护。本发明采用感应熔炼的方式对原材料进行加热熔炼，坩埚可选用石英坩埚、石墨坩埚、氧化钙坩埚、莫来石坩埚中的一种，熔炼期间缓慢提高功率并控制熔炼温度，最高温度应达到1400-1600℃，在最高温度下保温时间应不少于180秒。最后通过翻转浇铸的方式将熔体浇入模具中冷却，浇铸温度应大于1100℃，模具可选用钢模、铜模等材料制成，模具可通过水冷方式降温。
本发明所提供的Zr基非晶合金中含有Hf元素，与添加稀土元素相比较，Hf元素的微量添加使得合金的非晶形成能力得到了提高，更容易获得较大临界尺寸的非晶合金，同时Hf的添加使得合金的机械性能得以保持，不会因为由于添加稀土元素而导致合金脆性增加。于此同时，本发明提供的Zr基非晶合金是将氧作为一种元素添加到合金体系中，实际证明氧含量过低并不完全有利于非晶合金的机械性能的提高，而本发明通过适当提高氧的含量，获得了氧含量的最优选范围，提高了非晶合金的机械性能。
附图说明
图1实施例1所述非晶合金XRD衍射图。
图2实施例1所述非晶合金热力学参数。
图3实施例1所述非晶合金力学性能。
图4实施例2所述非晶合金XRD衍射图。
图5实施例2所述非晶合金热力学参数。
图6实施例2所述非晶合金力学性能。
具体实施方式
以下通过实施例详细描述本发明，以下描述的具体实施例仅用于进一步解释本发明，并不用于限制本发明。
以下实施例中所用原料纯度＞97％，氧含量＜2at.％，氩气纯度＞97％。
实施例1
成分：(Zr 54Hf 0.5Cu 32.9Ni 3.6Al 9) 99.95O 0.05
将原料放入石墨坩埚中后抽真空至5帕，在氩气保护气氛下进行熔炼，缓慢提升功率，控制熔炼温度升至1400℃，保温时间300s，之后缓慢降低功率并降低温度至1200℃后浇铸进入铜模，获得尺寸为Φ12×60mm的棒状样品，其非晶含量占体积百分数为95％。利用XRD衍射仪分析其是否为非晶，由图1可证明其结构为非晶结构。利用DSC测量其热力学参数，如图2所示，其T g为687K，T x为763K。利用力学性能试验机检测其力学性能，如图3所示，其2mm棒材压缩强度达到1941MPa，维氏硬度达到544，断裂韧性达到90KPam 1/2。
实施例2
成分：(Zr 50.5Hf 0.5Cu 36.45Ni 4.05Al 8.5) 99.9O 0.1
将原料放入石英坩埚中后抽真空至0.5帕，在氩气保护气氛下进行熔炼，缓 慢提升功率，控制熔炼温度升至1500℃，保温时间240s，之后缓慢降低功率并降低温度至1150℃后浇铸进入铜模，获得尺寸为Φ16×60mm的棒状样品，其非晶含量占体积百分数为99％。利用XRD衍射仪分析其是否为非晶，由图4可证明其结构为非晶结构。利用DSC测量其热力学参数，如图5所示，其T g为690K，T x为767K。利用力学性能试验机检测其力学性能，如图6所示，其2mm棒材压缩强度达到1890MPa，维氏硬度达到550，断裂韧性达到93KPam 1/2。
实施例3
成分：(Zr 52.7Hf 0.3Cu 34.2Ni 3.8Al 9) 99.7O 0.3
将原料放入石墨坩埚中后抽真空至15帕，在真空气氛下进行熔炼，缓慢提升功率，控制熔炼温度升至1600℃，保温时间240s，之后缓慢降低功率并降低温度至1100℃后浇铸进入铜模，获得尺寸为Φ12×60mm的棒状样品，其非晶含量占体积百分数为90％。
实施例4
成分：(Zr 50.6Hf 0.4Cu 35.1Ni 3.9Al 10) 99.8O 0.2
将原料放入石墨坩埚中后抽真空至0.5帕，在氩气保护气氛下进行熔炼，缓慢提升功率，控制熔炼温度升至1400℃，保温时间180s，之后缓慢降低功率并降低温度至1200℃后浇铸进入铜模，获得尺寸为Φ16×60mm的棒状样品，其非晶含量占体积百分数为90％。
实施例5
成分：(Zr 53.7Hf 0.3Cu 34.2Ni 3.8Al 8) 99.9O 0.1
将原料放入氧化钙坩埚中后抽真空至10帕，在氩气保护气氛下进行熔炼，缓慢提升功率，控制熔炼温度升至1500℃，保温时间240s，之后缓慢降低功率并降低温度至1150℃后浇铸进入铜模，获得尺寸为Φ12×60mm的棒状样品，其 非晶含量占体积百分数为80％。
实施例6
成分：(Zr 54.1Hf 0.9Cu 31.5Ni 3.5Al 10) 99.85O 0.15
将原料放入氧化钙坩埚中后抽真空至10帕，在氩气保护气氛下进行熔炼，缓慢提升功率，控制熔炼温度升至1500℃，保温时间240s，之后缓慢降低功率并降低温度至1150℃后浇铸进入铜模，获得尺寸为Φ12×60mm的棒状样品，其非晶含量占体积百分数为70％。
实施例7
成分：(Zr 54.9Hf 0.1Cu 34.2Ni 3.8Al 7) 99.7O 0.3
将原料放入氧化钙坩埚中后抽真空至50帕，在氩气保护气氛下进行熔炼，缓慢提升功率，控制熔炼温度升至1600℃，保温时间240s，之后缓慢降低功率并降低温度至1200℃后浇铸进入铜模，获得尺寸为Φ12×60mm的棒状样品，其非晶含量占体积百分数为70％。
实施例8
成分：(Zr 50.2Hf 0.8Cu 37.8Ni 4.2Al 7) 99.9O 0.1
将原料放入氧化钙坩埚中后抽真空至5帕，在氩气保护气氛下进行熔炼，缓慢提升功率，控制熔炼温度升至1400℃，保温时间300s，之后缓慢降低功率并降低温度至1200℃后浇铸进入铜模，获得尺寸为Φ16×60mm的棒状样品，其非晶含量占体积百分数为50％。
实施例9
成分：(Zr 49.3Hf 0.7Cu 37.8Ni 4.2Al 8) 99.5O 0.5
将原料放入氧化钙坩埚中后抽真空至10帕，在氩气保护气氛下进行熔炼，缓慢提升功率，控制熔炼温度升至1600℃，保温时间180s，之后缓慢降低功率 并降低温度至1150℃后浇铸进入铜模，获得尺寸为Φ16×60mm的棒状样品，其非晶含量占体积百分数为40％。
实施例10
成分：(Zr 49.4Hf 0.6Cu 35.55Ni 3.95Al 10.5) 99.6O 0.4
将原料放入氧化钙坩埚中后抽真空至1帕，在氩气保护气氛下进行熔炼，缓慢提升功率，控制熔炼温度升至1500℃，保温时间180s，之后缓慢降低功率并降低温度至1100℃后浇铸进入铜模，获得尺寸为Φ16×60mm的棒状样品，其非晶含量占体积百分数为50％。
上述实施例只为说明本发明的技术构思及特点，其目的在于让熟悉此项技术的人士能够了解本发明的内容并据以实施，并不能以此限制本发明的保护范围。凡根据本发明精神实质所作的等效变化或修饰，都应涵盖在本发明的保护范围之内。

Claims (8)

  1. 一种Zr基非晶合金，其特征在于，按照原子百分比计，该Zr基非晶合金成分组成范围为：(Zr aHf bCu cNi dAl e) 100-xO x，其中：49≤a≤55，0.05≤b≤1，31≤c≤38，3≤d≤5，7≤e≤10.5，0.05≤x≤0.5。
  2. 按照权利要求1所述Zr基非晶合金，其特征在于，按照原子百分比计，合金成分组成范围为：(Zr aHf bCu cNi dAl e) 100-xO x，其中：52.5≤a≤54，0.3≤b≤0.6，33≤c≤35.5，3.2≤d≤4，8≤e≤10，0.05≤x≤0.2。
  3. 按照权利要求1所述Zr基非晶合金，其特征在于，按照原子百分比计，合金成分组成范围为：(Zr aHf bCu cNi dAl e) 100-xO x，其中：50.5≤a≤52，0.4≤b≤0.8，36≤c≤37.5，3≤d≤4.5，8≤e≤10，0.05≤x≤0.3。
  4. 一种权利要求1所述Zr基非晶合金的制备方法，其特征在于：采用感应熔炼的方式对原材料进行加热熔炼，熔炼期间缓慢提高功率并控制熔炼温度，熔炼温度应达到1400-1600℃，在最高温度下保温时间不少于180秒，通过翻转浇铸的方式将熔体浇入模具中冷却，浇铸温度高于1100℃。
  5. 按照权利要求4所述Zr基非晶合金的制备方法，其特征在于：制备非晶合金的原料纯度＞97％，氧含量要求为不高于2at％。
  6. 按照权利要求4所述Zr基非晶合金的制备方法，其特征在于：熔炼过程中采用的坩埚为石英坩埚、石墨坩埚、氧化钙坩埚、莫来石坩埚中的一种。
  7. 按照权利要求4所述Zr基非晶合金的制备方法，其特征在于：在真空条件下熔炼合金，所需真空度为0.5-500帕。
  8. 按照权利要求4所述Zr基非晶合金的制备方法，其特征在于：熔炼保护气体为惰性气体氩气。
PCT/CN2018/000148 2017-05-18 2018-04-20 一种锆基非晶合金及其制备方法 WO2018209970A1 (zh)

Priority Applications (1)

Application Number Priority Date Filing Date Title
US16/500,083 US11655529B2 (en) 2017-05-18 2018-04-20 Zr-based amorphous alloy and manufacturing method thereof

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CN201710351253.7A CN107236913B (zh) 2017-05-18 2017-05-18 一种锆基非晶合金及其制备方法
CN201710351253.7 2017-05-18

Publications (1)

Publication Number Publication Date
WO2018209970A1 true WO2018209970A1 (zh) 2018-11-22

Family

ID=59984508

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/CN2018/000148 WO2018209970A1 (zh) 2017-05-18 2018-04-20 一种锆基非晶合金及其制备方法

Country Status (3)

Country Link
US (1) US11655529B2 (zh)
CN (1) CN107236913B (zh)
WO (1) WO2018209970A1 (zh)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN114032478A (zh) * 2021-11-11 2022-02-11 盘星新型合金材料(常州)有限公司 具有塑性的Zr基非晶合金及其制备方法

Families Citing this family (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN107236913B (zh) * 2017-05-18 2019-04-26 中国科学院金属研究所 一种锆基非晶合金及其制备方法
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
CN115807199B (zh) * 2022-11-24 2023-12-22 新疆大学 一种同时提高块体非晶合金复合材料屈服强度和塑性的方法

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH05117822A (ja) * 1991-10-22 1993-05-14 Takeshi Masumoto 繊維強化金属複合材料
JP2001316784A (ja) * 2000-05-09 2001-11-16 Toshiba Corp バルク状非晶質合金、バルク状非晶質合金の製造方法、および高強度部材
CN101906598A (zh) * 2009-06-08 2010-12-08 比亚迪股份有限公司 一种锆基非晶合金及其制备方法
CN105132837A (zh) * 2015-08-27 2015-12-09 常州世竟液态金属有限公司 一种低成本块体非晶合金
CN106282851A (zh) * 2015-06-10 2017-01-04 中国科学院金属研究所 一种低成本锆基非晶合金及其制备方法
CN107236913A (zh) * 2017-05-18 2017-10-10 中国科学院金属研究所 一种锆基非晶合金及其制备方法

Family Cites Families (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN102527982B (zh) * 2011-12-15 2015-05-13 比亚迪股份有限公司 非晶合金压铸设备及非晶合金压铸工艺
US9334553B2 (en) * 2012-03-29 2016-05-10 Washington State University Zirconium based bulk metallic glasses
CN104498845B (zh) * 2014-11-24 2017-01-25 中国科学院金属研究所 一种锆基非晶合金及其制备方法
CN104651756B (zh) * 2015-02-15 2016-11-23 中国科学院金属研究所 (ZrM)-(CuN)-Ni-Al-(Re)非晶合金、制备方法及应用
CN106567015B (zh) * 2016-11-21 2019-02-26 中国科学院金属研究所 一种CuZr基块状非晶合金及其制备方法和应用

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH05117822A (ja) * 1991-10-22 1993-05-14 Takeshi Masumoto 繊維強化金属複合材料
JP2001316784A (ja) * 2000-05-09 2001-11-16 Toshiba Corp バルク状非晶質合金、バルク状非晶質合金の製造方法、および高強度部材
CN101906598A (zh) * 2009-06-08 2010-12-08 比亚迪股份有限公司 一种锆基非晶合金及其制备方法
CN106282851A (zh) * 2015-06-10 2017-01-04 中国科学院金属研究所 一种低成本锆基非晶合金及其制备方法
CN105132837A (zh) * 2015-08-27 2015-12-09 常州世竟液态金属有限公司 一种低成本块体非晶合金
CN107236913A (zh) * 2017-05-18 2017-10-10 中国科学院金属研究所 一种锆基非晶合金及其制备方法

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN114032478A (zh) * 2021-11-11 2022-02-11 盘星新型合金材料(常州)有限公司 具有塑性的Zr基非晶合金及其制备方法

Also Published As

Publication number Publication date
US20210102280A1 (en) 2021-04-08
US11655529B2 (en) 2023-05-23
CN107236913A (zh) 2017-10-10
CN107236913B (zh) 2019-04-26

Similar Documents

Publication Publication Date Title
WO2018209970A1 (zh) 一种锆基非晶合金及其制备方法
CN103122431B (zh) 一种长周期结构相增强的镁锂合金的制备方法
EP3065148B1 (en) Magnetic phase-transformation material
CN102154596A (zh) 一种锆基非晶合金及其制备方法
CN103741080B (zh) （Ti-Zr-Nb-Cu-Be）-O系非晶复合材料及其制备方法
CN107287535A (zh) 一种大塑性高强度锆基块体非晶合金及制备方法
US20050121117A1 (en) Alloy and method of producing the same
CN101956148A (zh) 一种双重复合高强韧块体非晶合金及其制备方法
CN105506517B (zh) (Ti‑Zr‑Nb‑Cu‑Be)‑N系非晶复合材料及其制备方法
JP2020531683A (ja) バルク金属ガラスの製造のための銅に基づく合金
CN113528986B (zh) 一种超高韧性大尺寸锆基非晶合金及其制备方法和应用
CN113403555B (zh) 通过热变形工艺改善硅化物增强难熔高熵合金性能的方法
CN107058913B (zh) 一种高锆含量的锆基非晶合金及其制备方法
CN100494437C (zh) 大块金属玻璃复合材料中树枝晶球化的方法
CN106957986A (zh) 一种高塑性磁致伸缩材料及其制备方法
CN115354244B (zh) 一种纳米相强化型亚共晶高熵合金及其制备方法
CN114657437B (zh) 一种具有优异热改性的Co-Cr-Fe-Ni-V-B共晶高熵合金及其制备方法
CN104498845A (zh) 一种锆基非晶合金及其制备方法
CN102477519A (zh) 一种低氧含量块体金属玻璃的制备方法
CN113322422A (zh) 一种混杂相增强锆基非晶复合材料及其制备方法
CN114032478A (zh) 具有塑性的Zr基非晶合金及其制备方法
CN102776453B (zh) 球晶增韧的非晶基复合材料的制备方法
CN104419879A (zh) 一种具有抗氧化性能且宽过冷液相区的锆基非晶合金
KR950003051B1 (ko) 니켈기 초내열 단조합금
CN107829050B (zh) 一种含铝的铜基块体非晶合金及其制备工艺

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: 18802878

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: 18802878

Country of ref document: EP

Kind code of ref document: A1