[go: up one dir, main page]

WO2022193487A1 - 一种高强韧耐热铝合金电枢材料及其制备方法 - Google Patents

一种高强韧耐热铝合金电枢材料及其制备方法 Download PDF

Info

Publication number
WO2022193487A1
WO2022193487A1 PCT/CN2021/105093 CN2021105093W WO2022193487A1 WO 2022193487 A1 WO2022193487 A1 WO 2022193487A1 CN 2021105093 W CN2021105093 W CN 2021105093W WO 2022193487 A1 WO2022193487 A1 WO 2022193487A1
Authority
WO
WIPO (PCT)
Prior art keywords
strength
alloy
heat
toughness
aluminum alloy
Prior art date
Legal status (The legal status 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 status listed.)
Ceased
Application number
PCT/CN2021/105093
Other languages
English (en)
French (fr)
Inventor
高海燕
吕海洋
彭朋
王宇飞
王朦朦
吴贇
张驰
王俊
孙宝德
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Shanghai Jiao Tong University
Original Assignee
Shanghai Jiao Tong University
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 Shanghai Jiao Tong University filed Critical Shanghai Jiao Tong University
Publication of WO2022193487A1 publication Critical patent/WO2022193487A1/zh
Priority to US18/467,734 priority Critical patent/US12123077B2/en
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

Links

Images

Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
    • B33Y80/00—Products made by additive manufacturing
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B22F1/06—Metallic powder characterised by the shape of the particles
    • B22F1/065—Spherical particles
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
    • B22F10/20—Direct sintering or melting
    • B22F10/28—Powder bed fusion, e.g. selective laser melting [SLM] or electron beam melting [EBM]
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
    • B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
    • B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
    • B33Y10/00—Processes of additive manufacturing
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
    • B33Y40/00—Auxiliary operations or equipment, e.g. for material handling
    • B33Y40/10—Pre-treatment
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
    • B33Y70/00—Materials specially adapted for additive manufacturing
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/026—Alloys based on aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/0408—Light metal alloys
    • C22C1/0416—Aluminium-based alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
    • B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
    • B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
    • B22F2009/0824—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid with a specific atomising fluid
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
    • B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
    • B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
    • B22F2009/0836—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid with electric or magnetic field or induction
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2304/00—Physical aspects of the powder
    • B22F2304/10—Micron size particles, i.e. above 1 micrometer up to 500 micrometer
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10—Processes characterised by the sequence of their steps

Definitions

  • the invention relates to the field of heat-resistant aluminum alloy materials, in particular to a high-strength and toughness heat-resistant aluminum alloy armature material and a preparation method thereof.
  • the electromagnetic railgun is a new concept kinetic energy weapon that uses electromagnetic energy to drive a current-carrying armature to slide to ultra-high speed and propel projectiles to launch. Compared with conventional artillery, it has the advantages of high initial velocity, high power, high safety, strong controllability, simple operation, and high cost-effectiveness ratio. It has great strategic and tactical application value in future wars. With the gradual development of the electromagnetic railgun towards actual combat application, its service life has become one of the technical difficulties that is difficult to break through. In the process of launching the armature of the electromagnetic railgun, the sliding electrical contact between the armature and the rail is very bad, and complex mechanical, thermal, electrical effects and strong side impact will be generated between the armature rail interface. Performance has become the key technology of electromagnetic railguns.
  • the material of electromagnetic railgun armature is usually aluminum alloy with lower density.
  • aluminum alloy materials have the following main problems that are difficult to solve: 1. There are a large number of precipitation phases with poor thermal stability in the existing alloy structure. These phases will gradually grow at high temperatures and lose their precipitation strengthening effect. Traditional methods It is difficult to control the microstructure to suppress the large number of these precipitates; 2. It is difficult to take into account the casting properties, mechanical properties and electrical conductivity of the alloys processed by conventional means; 3. It is difficult to take into account the room temperature properties and high temperature properties of the alloys. These aluminum alloy materials are still not sufficient for ultra-high-speed sliding on the pivot rail of the electromagnetic railgun.
  • the selection of armature materials should be considered from the following aspects: in order to minimize the mass of the armature, the density of the armature material should be lower to improve the launch efficiency; the armature material can withstand high temperature and has a relatively low density. High energy absorption rate to increase the critical temperature of contact point transfer to prevent arcing and softening; high electrical conductivity to reduce the generation of ohmic heat and ensure good heat dissipation.
  • the armature material has the following characteristics: during the launching process, the armature is in the current loop, and a large current flows through the armature, accompanied by heating and melting; corrosion and other phenomena, further planing of the armature rail material will occur; the armature, as the main force-bearing component in the launching process, forms the electromagnetic railgun projectile together with the warhead, bullet rest and other components, and the mass of the armature should be as small as possible to avoid Improves the warhead's terminal damage capability.
  • the purpose of the present invention is to provide a high-strength, toughness and heat-resistant aluminum alloy armature material and a preparation method thereof.
  • a first aspect of the present invention provides a method for preparing a high-strength, toughness and heat-resistant aluminum alloy armature material, comprising: performing according to the following steps:
  • the aluminum ingot is heated and melted into molten aluminum, and the temperature is 760 °C ⁇ 780 °C;
  • the spherical alloy powder is formed by selective laser melting and solidification, so as to produce nano-scale Al 11 Ce 3 , Al 3 (Y, Zr) and/or Al 3 RE distributed in the aluminum matrix in the form of a network framework structure
  • the material of the intermetallic compound is obtained, that is, the high-strength and toughness heat-resistant aluminum alloy armature material is obtained.
  • the following elements by mass percentage are added to the molten aluminum: Ce is 8.00%-10.00%, Y is 7.50%-9.50%, Zr is 0.65%-1.00%, Mg is 1.50% ⁇ 2.50%, RE is 0.15% ⁇ 0.50%, Fe is 0.15% ⁇ 0.20%, Mn is 0.05% ⁇ 0.10%, Si is 0.10% ⁇ 0.25%, RE is one of Yb, Er, La, Sc or Mixing of various elements, the content of other impurities is less than 0.1%.
  • the following elements by mass percentage are added to the molten aluminum, wherein the RE is a mixture of one or more of Yb, Er, La or Sc.
  • the spherical alloy powder is melted and solidified by selective laser melting, wherein the following process parameters are adopted: the laser power is 260W ⁇ 350W, the scanning layer thickness is 10 ⁇ m ⁇ 30 ⁇ m, and the input energy density is 50J/mm 3 ⁇ 90J/mm 3 .
  • the laser power is 260W ⁇ 350W
  • the scanning layer thickness is 10 ⁇ m ⁇ 30 ⁇ m
  • the input energy density is 50J/mm 3 ⁇ 90J/mm 3 .
  • nanoscale intermetallic compounds such as Al 11 Ce 3 , Al 3 (Y, Zr) and/or Al 3 RE, which have a network frame structure and have good thermal stability.
  • the obtained alloy ingot is processed into spherical alloy powder, wherein the alloy ingot is processed into spherical alloy powder by plasma rotating electrode atomization or gas atomization, and during the processing Gas protection was carried out by passing through argon or helium.
  • the alloy ingot is processed into spherical alloy powder by plasma rotating electrode atomization or gas atomization, wherein,
  • the working speed of the atomization of the plasma rotating electrode is 40000rpm ⁇ 50000rpm;
  • the working air pressure of the gas atomization is 6MPa-10MPa.
  • the obtained alloy ingot is processed into spherical alloy powder, wherein the spherical powder has a particle size distribution of 15 ⁇ m to 65 ⁇ m, an average particle size of 45 ⁇ m to 55 ⁇ m, and the spherical powder has a sphericity greater than 95%.
  • a high-strength and toughness heat-resistant aluminum alloy armature material is provided, which is prepared by the above-mentioned preparation method of the high-strength and toughness heat-resistant aluminum alloy armature material.
  • the density of the high-strength and heat-resistant rare earth aluminum alloy material is greater than 99%, and the density is 2.75g/cm 3 to 2.90g/cm 3 .
  • the room temperature yield strength of the high-strength and toughness heat-resistant aluminum alloy armature material is 270MPa-350MPa, the tensile strength is 400MPa-450MPa, and the elongation is 10%-12%;
  • the high-strength heat-resistant rare-earth aluminum alloy material is above 400° C., the yield strength is 160MPa-200MPa, the tensile strength is 220MPa-280MPa, and the elongation is greater than 15%.
  • the present invention has at least one of the following beneficial effects:
  • the above-mentioned method of the present invention uses the selective laser melting process to process and form, and its cooling rate is extremely fast, thereby forming nano-scale intermetallic compounds such as Al 11 Ce 3 , Al 3 (Y, Zr) and/or Al 3 RE, which are in the form of a network.
  • the skeleton structure, evenly distributed in the aluminum matrix has good thermal stability, so that the material has the characteristics of low density, high strength and toughness, excellent electrical conductivity, wear resistance, ablation resistance and high temperature resistance, which solves the problem of softening of the armature material during operation. , ablation, etc.
  • a laser is used as the energy source, and the metal powder is completely melted by the laser in the process of processing, and the metal powder is directly formed without a binder.
  • the formed parts have high precision and excellent mechanical properties.
  • the above method of the present invention can directly obtain solid parts of any complex shape according to the three-dimensional model of the part, using metal powder without any fixtures and molds, and realizes the new concept of "net shape” material processing; it is especially suitable for manufacturing complex inner cavities.
  • the structural parts shorten the post-processing time and steps and improve the processing efficiency.
  • the high-strength, toughness and heat-resistant aluminum alloy material prepared by the above method of the present invention has great development prospects in the fields of weight-sensitive application, national defense and military industry and aerospace.
  • FIG. 1 is a microstructure diagram of a high-strength, toughness, heat-resistant aluminum alloy armature material of a preferred embodiment of the present invention
  • FIG. 2 is a tensile fracture topography diagram of a high-strength, tough, heat-resistant aluminum alloy armature material according to a preferred embodiment of the present invention.
  • the present embodiment provides a method for preparing a high-strength, toughness and heat-resistant aluminum alloy armature material, comprising: performing according to the following steps:
  • the aluminum ingot is heated and melted into molten aluminum in an induction furnace at a temperature of 770°C.
  • the selective laser melting forming method adopts the following process parameters: the laser power is 350W, the scanning layer thickness is 30 ⁇ m, and the input energy density is 70.4J/mm 3 , the spherical alloy powder is rapidly melted and solidified to obtain a high-strength, toughness and heat-resistant aluminum alloy armature material, and nano-scale Al 11 Ce 3 and Al 3 (Y, Zr) intermetallic compounds are formed in the aluminum matrix, with good thermal stability. Its microstructure is shown in Figure 1.
  • the white intermetallic compounds have a network-like skeleton structure and are uniformly distributed in the aluminum matrix, which shows that the formed structure is dense and defect-free.
  • the density of the high-strength and toughness heat-resistant aluminum alloy armature material is greater than 99.8%, and the density is 2.79 g/cm 3 .
  • the yield strength at room temperature is 284MPa
  • the tensile strength is 400MPa
  • the elongation is 10.2%.
  • the tensile fracture morphology is shown in Figure 2, and the small tensile dimples can be seen in Figure 2, which can indicate that the material is ductile fracture, and the strong-plastic matching is good.
  • the alloy has a yield strength of 170 MPa, a tensile strength of 230 MPa, and an elongation of 15.6%.
  • the present embodiment provides a method for preparing a high-strength, toughness and heat-resistant aluminum alloy armature material, comprising: performing according to the following steps:
  • the aluminum ingot is heated and melted into molten aluminum in an induction furnace at a temperature of 780°C.
  • the selective laser melting forming method adopts the following process parameters: the laser power is 330W, the scanning layer thickness is 20 ⁇ m, and the input energy density is 64.4J/mm 3 , the spherical alloy powder is rapidly melted and solidified to obtain a high-strength, toughness and heat-resistant aluminum alloy armature material, and nano-scale Al 3 (Y, Zr) and Al 11 Ce 3 intermetallic compounds are formed in the aluminum matrix, which is a network skeleton structure , good thermal stability.
  • the density of the high-strength and toughness heat-resistant aluminum alloy armature material is greater than 99.6%, and the density is 2.83 g/cm 3 .
  • the yield strength at room temperature is 284MPa
  • the tensile strength is 400MPa
  • the elongation is 10.2%.
  • the alloy has a yield strength of 173 MPa, a tensile strength of 245 MPa, and an elongation of 16%.
  • the present embodiment provides a method for preparing a high-strength, toughness and heat-resistant aluminum alloy armature material, comprising: performing according to the following steps:
  • the aluminum ingot is heated and melted into molten aluminum in an induction furnace at a temperature of 760°C.
  • S3 adopt the gas atomization method, pass argon gas for gas protection, the working pressure is 8MPa, and process the alloy ingot into spherical alloy powder; degree greater than 96%.
  • the selective laser melting forming method adopts the following process parameters: the laser power is 330W, the scanning layer thickness is 30 ⁇ m, and the input energy density is 70.4J/mm 3 , the spherical alloy powder is rapidly melted and solidified to obtain a high-strength, toughness and heat-resistant aluminum alloy armature material, and nano-scale Al 3 (Y, Zr) and Al 11 Ce 3 intermetallic compounds are formed in the aluminum matrix, which is a network skeleton structure , good thermal stability.
  • the density of the high-strength and toughness heat-resistant aluminum alloy armature material is greater than 99.5%, and the density is 2.85 g/cm 3 .
  • the yield strength at room temperature is 279MPa
  • the tensile strength is 422MPa
  • the elongation is 10%.
  • the alloy has a yield strength of 185 MPa, a tensile strength of 270 MPa, and an elongation of 17%.
  • the present embodiment provides a method for preparing a high-strength, toughness and heat-resistant aluminum alloy armature material, comprising: performing according to the following steps:
  • the aluminum ingot is heated and melted into molten aluminum in an induction furnace at a temperature of 770°C.
  • S3 adopt the gas atomization method, pass argon gas for gas protection, the working pressure is 8MPa, and process the alloy ingot into spherical alloy powder; degree greater than 98%.
  • the selective laser melting forming method adopts the following process parameters: the laser power is 330W, the scanning layer thickness is 20 ⁇ m, and the input energy density is 54.3J/mm 3 , the spherical alloy powder is rapidly melted and solidified to obtain a high-strength, toughness and heat-resistant aluminum alloy armature material, and nano-scale Al 3 (Y, Zr), Al 3 Sc, Al 11 Ce 3 intermetallic compounds are formed in the aluminum matrix. Reticular skeleton structure, good thermal stability.
  • the density of the high-strength and toughness heat-resistant aluminum alloy armature material is greater than 99.8 percent, and the density is 2.88 g/cm 3 .
  • the yield strength at room temperature is 350MPa
  • the tensile strength is 450MPa
  • the elongation is 11.2%.
  • the alloy has a yield strength of 190 MPa, a tensile strength of 275 MPa, and an elongation of 16.5%.
  • the present embodiment provides a method for preparing a high-strength and toughness heat-resistant aluminum alloy armature material, comprising: performing according to the following steps:
  • the aluminum ingot is heated and melted into molten aluminum in an induction furnace at a temperature of 760°C.
  • the spherical alloy powder is rapidly melted and solidified by the selective laser melting forming method; wherein, the selective laser melting forming method adopts the following process parameters: the laser power is 300W, the scanning layer thickness is 30 ⁇ m, and the input energy density is 69.8J/mm 3 , the spherical alloy powder is rapidly melted and solidified to obtain a high-strength, toughness and heat-resistant aluminum alloy armature material, and nano-scale Al 3 (Y, Zr), Al 3 Yb, Al 3 Sc, Al 11 Ce 3 metals are formed in the aluminum matrix It is a reticular skeleton structure and has good thermal stability.
  • the selective laser melting forming method adopts the following process parameters: the laser power is 300W, the scanning layer thickness is 30 ⁇ m, and the input energy density is 69.8J/mm 3 , the spherical alloy powder is rapidly melted and solidified to obtain a high-strength, toughness and heat-resistant aluminum alloy armature material, and nano
  • the density of the high-strength and toughness heat-resistant aluminum alloy armature material is greater than 99.8%, and the density is 2.79 g/cm 3 .
  • the yield strength at room temperature is 287MPa
  • the tensile strength is 445MPa
  • the elongation is 11%.
  • the alloy has a yield strength of 190 MPa, a tensile strength of 270 MPa, and an elongation of 16%.
  • the present embodiment provides a method for preparing a high-strength, toughness and heat-resistant aluminum alloy armature material, comprising: performing according to the following steps:
  • the aluminum ingot is heated and melted into molten aluminum in an induction furnace at a temperature of 780°C.
  • S3 adopt the gas atomization method, pass argon gas for gas protection, the working pressure is 10MPa, and process the alloy ingot into spherical alloy powder; degree greater than 97%.
  • the spherical alloy powder is rapidly melted and solidified by the selective laser melting forming method; wherein, the selective laser melting forming method adopts the following process parameters: the laser power is 260W, the scanning layer thickness is 30 ⁇ m, and the input energy density is 89.5J/mm 3 , the spherical alloy powder is rapidly melted and solidified to obtain a high-strength, toughness and heat-resistant aluminum alloy armature material, and nano-scale Al 3 (Y, Zr), Al 3 Yb, Al 3 Sc, Al 3 La, Al 11 are formed in the matrix. Ce 3 intermetallic compound, with a network skeleton structure, good thermal stability.
  • the density of the high-strength and toughness heat-resistant aluminum alloy armature material is greater than 99.8%, and the density is 2.84 g/cm 3 .
  • the yield strength at room temperature is 289MPa
  • the tensile strength is 402MPa
  • the elongation is 12%.
  • the alloy has a yield strength of 180MPa, a tensile strength of 275MPa, and an elongation of 18%.
  • the cooling speed of the selective laser melting process is extremely fast, forming nano-scale Al 11 Ce 3 , Al 3 (Y, Zr) and/or Al 3 RE and other intermetallic compounds, which have a network skeleton structure and good thermal stability, coat the aluminum matrix or form a substructure in the matrix, so that the material has high strength and toughness, excellent electrical conductivity, wear resistance and burning resistance. It has the characteristics of corrosion and high temperature resistance, and solves the problems of softening and ablation of the armature material during operation.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Manufacturing & Machinery (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Plasma & Fusion (AREA)
  • Physics & Mathematics (AREA)
  • Nanotechnology (AREA)
  • Manufacture Of Metal Powder And Suspensions Thereof (AREA)
  • Powder Metallurgy (AREA)
  • Conductive Materials (AREA)

Abstract

本发明提供一种高强韧耐热铝合金电枢材料及其制备方法，包括：将铝锭加热熔化成铝液；向铝液中添加以下质量百分含量的元素：Ce为6～12％、Y为5～9.5％、Zr为0.5～3％、Mg为0.1～2.5％、RE为0.15～2.5％、Fe为0.15～0.25％、Mn为0.05～0.15％、Si为0.1～0.5％；形成合金液，浇铸成合金铸锭；将合金铸锭加工成球形合金粉末；将球形合金粉末利用选区激光熔化凝固成形，以制成在铝基体中呈网状骨架结构分布的纳米尺度的Al 11Ce 3、Al 3(Y,Zr)和/或Al 3RE金属间化合物的材料。本发明的材料具有密度低、耐高温、能量吸收率高及导电性优良等特点，室温和高温力学性能优异。

Description

一种高强韧耐热铝合金电枢材料及其制备方法 技术领域
本发明涉及耐热铝合金材料领域，具体地，涉及一种高强韧耐热铝合金电枢材料及其制备方法。
背景技术
电磁轨道炮是一种利用电磁能驱动带电流的电枢滑动至超高速并推动弹丸发射的新概念动能武器。与常规火炮相比具有初速高、威力大、安全性高、可控性强、操纵简单、效费比高等优点，在未来战争中具有极大的战略和战术应用价值。随着电磁轨道炮逐步向实战应用方向发展，其服役寿命成了难以突破的技术难点之一。在电磁轨道炮发射电枢的过程中，电枢和轨道的滑动电接触状况十分恶劣，枢轨界面间会产生复杂的机械、热力、电气作用及强大的侧冲击力，因此提高电枢材料综合性能成为了电磁轨道炮的关键技术。
目前，电磁轨道炮电枢材料通常采用密度较低的铝合金。然而，铝合金材料存在以下几个主要问题难以解决：1、现有合金组织中存在大量热稳定性较差的析出相，这些相在高温下会逐渐长大并失去其析出强化效果，传统手段很难调控组织以抑制这些析出相的大量出现；2、常规手段加工成型的合金的铸造性能和力学性能以及导电性能难以兼顾；3、合金的室温性能和高温性能难以兼顾。这些铝合金材料仍不能满足在电磁轨道炮枢轨上超高速滑动。另外，在不明显降低热导率和电导率的前提下，材料的耐磨损、抗高温烧蚀性能还不能满足电磁轨道炮实战化需求。因此，研究高强韧、导电性优良、耐磨耐烧蚀及耐高温的新型电枢材料成为了未来的发展方向，是从根本上解决电磁轨道炮不同发射条件下电枢材料失效问题最可靠的途径。
结合电磁轨道炮电枢温升机理，电枢材料的选择应从以下几个方面考虑：为使电枢质量最小，电枢材料密度要较低，以提高发射效率；电枢材料能耐高温，有较高的能量吸收率，以提高接触点转移的临界温度，防止产生电弧和软化；具有高导电性，以减少欧姆热的产生，保证散热良好。电枢材料有如下特点：在发射过程中电枢处于电流回路 中，大电流从电枢中流过，并伴随着升温及融化等现象；枢轨界面在接触状态不良时，会出现转捩、烧蚀等现象，进一步会发生枢轨材料的刨削现象；电枢作为发射过程中的主要受力部件，与战斗部、弹托等部件共同组成电磁轨道炮弹丸，电枢质量应该尽量小，以提高战斗部的终点毁伤能力。目前报道的铝合金导体材料，无论是从强度还是耐热性上都无法很好地满足电磁轨道炮电枢材料的使用要求，有待进一步提高综合性能和高温稳定性。
发明内容
针对现有技术中的缺陷，本发明的目的是提供一种高强韧耐热铝合金电枢材料及其制备方法。
本发明第一个方面，提供一种高强韧耐热铝合金电枢材料的制备方法，包括：按照以下步骤执行：
S1，在气氛保护下，将铝锭加热熔化成铝液，温度为760℃～780℃；
S2，向所述铝液中添加以下质量百分含量的元素：Ce为6.00％～12.00％、Y为5.00％～9.50％、Zr为0.50％～3.00％、Mg为0.10％～2.50％、RE为0.15％～2.50％、Fe为0.15％～0.25％、Mn为0.05％～0.15％、Si为0.10％～0.50％，其他杂质含量小于0.1％；调整各元素比例，除气除渣，使之达到预设成分，形成合金液，之后将形成的所述合金液浇铸成合金铸锭；
S3，将得到的所述合金铸锭加工成球形合金粉末；
S4，将所述球形合金粉末利用选区激光熔化凝固成形，以制成在铝基体中呈网状骨架结构分布的纳米尺度的Al 11Ce 3、Al 3(Y,Zr)和/或Al 3RE的金属间化合物的材料，即得到所述高强韧耐热铝合金电枢材料。
优选地，所述S2，向所述铝液中添加以下质量百分含量的元素：Ce为8.00％～10.00％、Y为7.50％～9.50％、Zr为0.65％～1.00％、Mg为1.50％～2.50％、RE为0.15％～0.50％、Fe为0.15％～0.20％、Mn为0.05％～0.10％、Si为0.10％～0.25％，RE为Yb、Er、La、Sc中的一种或多种元素的混合，其他杂质含量小于0.1％。
优选地，所述S2，向所述铝液中添加以下质量百分含量的元素，其中，所述RE为Yb、Er、La或Sc的一种或多种混合。
优选地，所述S4，将所述球形合金粉末利用选区激光熔化凝固成形，其中，采用以下工艺参数：激光功率为260W～350W，扫描层厚为10μm～30μm，输入能量密度为 50J/mm 3～90J/mm 3。在上述工艺参数内，有利于形成纳米尺度的Al 11Ce 3、Al 3(Y,Zr)和/或Al 3RE等金属间化合物，呈网状骨架结构，热稳定性好。
优选地，所述S3，将得到的所述合金铸锭加工成球形合金粉末，其中，将所述合金铸锭利用等离子旋转电极雾化或气体雾化加工成球形合金粉末，并在加工过程中通入氩气或氦气进行气体保护。
优选地，所述S3，将所述合金铸锭利用等离子旋转电极雾化或气体雾化加工成球形合金粉末，其中，
所述等离子旋转电极雾化的工作转速为40000rpm～50000rpm；
所述气体雾化的工作气压为6MPa～10MPa。
优选地，所述S3，将得到的所述合金铸锭加工成球形合金粉末，其中，所述球形粉末粒径分布为15μm～65μm，平均粒径为45μm～55μm，所述球形粉末球形度大于95％。
本发明第二个方面，提供一种高强韧耐热铝合金电枢材料，由上述的高强韧耐热铝合金电枢材料的制备方法制备得到。
优选地，所述高强耐热稀土铝合金材料的致密度大于99％，密度为2.75g/cm 3～2.90g/cm 3。
优选地，所述高强韧耐热铝合金电枢材料的室温屈服强度为270MPa～350MPa，抗拉强度为400MPa～450MPa，延伸率为10％～12％；
所述高强耐热稀土铝合金材料在400℃以上，屈服强度为160MPa～200MPa，抗拉强度为220MPa～280MPa，延伸率大于15％。
与现有技术相比，本发明具有如下至少一种的有益效果：
本发明上述方法，利用选区激光熔化过程加工成形，其冷却速度极快，从而形成纳米尺度的Al 11Ce 3、Al 3(Y,Zr)和/或Al 3RE等金属间化合物，呈网状骨架结构，均匀分布于铝基体中，热稳定性好，使制成的材料具有密度低、高强韧、导电性优良、耐磨耐烧蚀及耐高温等特点，解决了电枢材料工作时软化、烧蚀等问题。
本发明上述方法，选用激光作为能量源，加工的过程中用激光使金属粉体完全熔化，不需要黏结剂而直接成形，成形后零件的精度高，力学性能优良。
本发明上述方法，可根据零件三维模型，利用金属粉末而无需任何工装夹具和模具，直接获得任意复杂形状的实体零件，实现“净成形”的材料加工新理念；特别适用于制造具有复杂内腔结构的零件，缩短了后处理时间和步骤，提高了加工效率。
本发明上述方法，制备的高强韧耐热铝合金材料，在重量敏感应用领域、国防军工 和航空航天领域具有很大发展前景。
附图说明
通过阅读参照以下附图对非限制性实施例所作的详细描述，本发明的其它特征、目的和优点将会变得更明显：
图1是本发明一优选实施例的高强韧耐热铝合金电枢材料的显微组织图；
图2是本发明一优选实施例的高强韧耐热铝合金电枢材料的拉伸断口形貌图。
具体实施方式
下面结合具体实施例对本发明进行详细说明。以下实施例将有助于本领域的技术人员进一步理解本发明，但不以任何形式限制本发明。应当指出的是，对本领域的普通技术人员来说，在不脱离本发明构思的前提下，还可以做出若干变形和改进。这些都属于本发明的保护范围。
实施例1
本实施例提供一种高强韧耐热铝合金电枢材料的制备方法，包括：按照以下步骤执行：
S1，在高纯氩气的保护下，将铝锭在感应电炉中加热熔化成铝液，温度为770℃。
S2，向铝液中添加以下质量百分含量的元素：Ce为12.00％、Y为5.00％、Zr为0.50％、Mg为0.60％、La为0.15％、Fe为0.15％、Mn为0.05％、Si为0.10％，其他杂质含量小于0.1％；调整各元素比例，除气除渣，使之达到预设成分，形成合金液，之后将形成的合金液浇铸成合金铸锭。
S3，采用等离子旋转电极雾化法，通入氩气进行气体保护，工作转速为40000rpm，将合金铸锭加工成球形合金粉末；球形粉末粒径分布为20μm～63μm，平均粒径为45.2μm，粉末球形度大于98％。
S4，利用选区激光熔化成形法，将球形合金粉末快速熔化凝固成形；其中，选区激光熔化成形法采用以下工艺参数：激光功率为350W，扫描层厚为30μm，输入能量密度为70.4J/mm 3，将球形合金粉末快速熔化凝固成形，得到高强韧耐热铝合金电枢材料，在铝基体中形成纳米尺度的Al 11Ce 3、Al 3(Y,Zr)金属间化合物，热稳定性好，其显微组织图如图1所示，由图1中可见白色金属间化合物呈网状骨架结构，均匀分布于铝基体中，可说明成形的组织致密、无缺陷。高强韧耐热铝合金电枢材料的致密度大于99.8％， 密度为2.79g/cm 3。经测试，其室温屈服强度为284MPa，抗拉强度为400MPa，延伸率为10.2％。拉伸断口形貌如图2所示，由图2中可见细小的拉伸韧窝，可说明材料呈韧性断裂，强塑性匹配良好。在400℃时，合金屈服强度为170MPa，抗拉强度为230MPa，延伸率为15.6％。
实施例2
本实施例提供一种高强韧耐热铝合金电枢材料的制备方法，包括：按照以下步骤执行：
S1，在高纯氩气的保护下，将铝锭在感应电炉中加热熔化成铝液，温度为780℃。
S2，向铝液中添加以下质量百分含量的元素：Ce为6.00％、Y为9.50％、Zr为0.50％、Mg为0.10％、Yb为0.20％、Fe为0.25％、Mn为0.10％、Si为0.10％，其他杂质含量小于0.1％；调整各元素比例，除气除渣，使之达到预设成分，形成合金液，之后将形成的合金液浇铸成合金铸锭。
S3，采用等离子旋转电极雾化法，通入氩气进行气体保护，工作转速为45000rpm，将合金铸锭加工成球形合金粉末；球形粉末粒径分布为15μm～60μm，平均粒径为48.3μm，粉末球形度大于98％。
S4，利用选区激光熔化成形法，将球形合金粉末快速熔化凝固成形；其中，选区激光熔化成形法采用以下工艺参数：激光功率为330W，扫描层厚为20μm，输入能量密度为64.4J/mm 3，将球形合金粉末快速熔化凝固成形，得到高强韧耐热铝合金电枢材料，在铝基体中形成纳米尺度的Al 3(Y,Zr)、Al 11Ce 3金属间化合物，呈网状骨架结构，热稳定性好。高强韧耐热铝合金电枢材料的致密度大于99.6％，密度为2.83g/cm 3。经测试，其室温屈服强度为284MPa，抗拉强度为400MPa，延伸率为10.2％。在400℃时，合金屈服强度为173MPa，抗拉强度为245MPa，延伸率为16％。
实施例3
本实施例提供一种高强韧耐热铝合金电枢材料的制备方法，包括：按照以下步骤执行：
S1,在高纯氩气的保护下，将铝锭在感应电炉中加热熔化成铝液，温度为760℃。
S2，向铝液中添加以下质量百分含量的元素：Ce为8.00％、Y为7.50％、Zr为1.00％、Mg为1.50％、Er为0.50％、Fe为0.15％、Mn为0.05％、Si为0.10％，其他杂质含量小于0.1％；调整各元素比例，除气除渣，使之达到预设成分，形成合金液，之后将形成的合金液浇铸成合金铸锭；
S3，采用气体雾化法，通入氩气进行气体保护，工作气压为8MPa，将合金铸锭加工成球形合金粉末；球形粉末粒径分布为15μm～53μm，平均粒径为50.6μm，粉末球形度大于96％。
S4，利用选区激光熔化成形法，将球形合金粉末快速熔化凝固成形；其中，选区激光熔化成形法采用以下工艺参数：激光功率为330W，扫描层厚为30μm，输入能量密度为70.4J/mm 3，将球形合金粉末快速熔化凝固成形，得到高强韧耐热铝合金电枢材料，在铝基体中形成纳米尺度的Al 3(Y,Zr)、Al 11Ce 3金属间化合物，呈网状骨架结构，热稳定性好。高强韧耐热铝合金电枢材料的致密度大于99.5％，密度为2.85g/cm 3。经测试，其室温屈服强度为279MPa，抗拉强度为422MPa，延伸率为10％。在400℃时，合金屈服强度为185MPa，抗拉强度为270MPa，延伸率为17％。
实施例4
本实施例提供一种高强韧耐热铝合金电枢材料的制备方法，包括：按照以下步骤执行：
S1，在高纯氩气的保护下，将铝锭在感应电炉中加热熔化成铝液，温度为770℃。
S2，向铝液中添加以下质量百分含量的元素：Ce为6.00％、Y为9.50％、Zr为3.00％、Mg为0.60％、Sc为0.15％、Fe为0.20％、Mn为0.05％、Si为0.10％，其他杂质含量小于0.1％；调整各元素比例，除气除渣，使之达到预设成分，形成合金液，之后将形成的合金液浇铸成合金铸锭。
S3，采用气体雾化法，通入氩气进行气体保护，工作气压为8MPa，将合金铸锭加工成球形合金粉末；球形粉末粒径分布为16μm～60μm，平均粒径为53.1μm，粉末球形度大于98％。
S4，利用选区激光熔化成形法，将球形合金粉末快速熔化凝固成形；其中，选区激光熔化成形法采用以下工艺参数：激光功率为330W，扫描层厚为20μm，输入能量密度为54.3J/mm 3，将球形合金粉末快速熔化凝固成形，得到高强韧耐热铝合金电枢材料，在铝基体中形成纳米尺度的Al 3(Y,Zr)、Al 3Sc、Al 11Ce 3金属间化合物，呈网状骨架结构，热稳定性好。高强韧耐热铝合金电枢材料的致密度大于99.8％，密度为2.88g/cm 3。经测试，其室温屈服强度为350MPa，抗拉强度为450MPa，延伸率为11.2％。在400℃时，合金屈服强度为190MPa，抗拉强度为275MPa，延伸率为16.5％。
实施例5
本实施例提供一种高强韧耐热铝合金电枢材料的制备方法，包括：按照以下步骤执 行：
S1，在高纯氩气的保护下，将铝锭在感应电炉中加热熔化成铝液，温度为760℃。
S2，向铝液中添加以下质量百分含量的元素：Ce为6.00％、Y为5.00％、Zr为3.00％、Mg为2.50％、Yb为0.25％、Sc为0.25％、Fe为0.15％、Mn为0.05％、Si为0.10％，其他杂质含量小于0.1％；调整各元素比例，除气除渣，使之达到预设成分，形成合金液，将形成的合金液浇铸成合金铸锭。
S3，采用等离子旋转电极雾化法，通入氩气进行气体保护，工作转速为50000rpm，将合金铸锭加工成球形合金粉末；球形粉末粒径分布为15μm～63μm，平均粒径为40.5μm，粉末球形度大于99％。
S4，利用选区激光熔化成形法，将球形合金粉末快速熔化凝固成形；其中，选区激光熔化成形法采用以下工艺参数：激光功率为300W，扫描层厚为30μm，输入能量密度为69.8J/mm 3，将球形合金粉末快速熔化凝固成形，得到高强韧耐热铝合金电枢材料，在铝基体中形成纳米尺度的Al 3(Y,Zr)、Al 3Yb、Al 3Sc、Al 11Ce 3金属间化合物，呈网状骨架结构，热稳定性好。高强韧耐热铝合金电枢材料的致密度大于99.8％，密度为2.79g/cm 3。经测试，其室温屈服强度为287MPa，抗拉强度为445MPa，延伸率为11％。在400℃时，合金屈服强度为190MPa，抗拉强度为270MPa，延伸率为16％。
实施例6
本实施例提供一种高强韧耐热铝合金电枢材料的制备方法，包括：按照以下步骤执行：
S1，在高纯氩气的保护下，将铝锭在感应电炉中加热熔化成铝液，温度为780℃。
S2，向铝液中添加以下质量百分含量的元素：Ce为10.00％、Y为8.00％、Zr为0.50％、Mg为1.50％、La为0.50％、Yb为0.25％、Sc为0.25％、Fe为0.15％、Mn为0.05％、Si为0.10％，其他杂质含量小于0.1％；调整各元素比例，除气除渣，使之达到预设成分，形成合金液，之后将形成的合金液浇铸成合金铸锭。
S3，采用气体雾化法，通入氩气进行气体保护，工作气压为10MPa，将合金铸锭加工成球形合金粉末；球形粉末粒径分布为15μm～53μm，平均粒径为46.6μm，粉末球形度大于97％。
S4，利用选区激光熔化成形法，将球形合金粉末快速熔化凝固成形；其中，选区激光熔化成形法采用以下工艺参数：激光功率为260W，扫描层厚为30μm，输入能量密度为89.5J/mm 3，将球形合金粉末快速熔化凝固成形，得到高强韧耐热铝合金电枢材料， 在基体中形成纳米尺度的Al 3(Y,Zr)、Al 3Yb、Al 3Sc、Al 3La、Al 11Ce 3金属间化合物，呈网状骨架结构，热稳定性好。高强韧耐热铝合金电枢材料的致密度大于99.8％，密度为2.84g/cm 3。经测试，其室温屈服强度为289MPa，抗拉强度为402MPa，延伸率为12％。在400℃时，合金屈服强度为180MPa，抗拉强度为275MPa，延伸率为18％。
上述实施例，通过对制备工艺的改进和合金成分调控，以提高耐热铝合金强度和高温稳定性，选区激光熔化过程冷却速度极快，形成纳米尺度的Al 11Ce 3、Al 3(Y,Zr)和/或Al 3RE等金属间化合物，呈网状骨架结构，热稳定性好，包覆铝基体或者在基体中形成亚结构，使材料具有高强韧、导电性优良、耐磨耐烧蚀及耐高温等特点，解决电枢材料工作时软化、烧蚀等问题。
以上对本发明的具体实施例进行了描述。需要理解的是，本发明并不局限于上述特定实施方式，本领域技术人员可以在权利要求的范围内做出各种变形或修改，这并不影响本发明的实质。

Claims (10)

  1. 一种高强韧耐热铝合金电枢材料的制备方法，其特征在于，包括：按照以下步骤执行：
    S1，在气氛保护下，将铝锭加热熔化成铝液，温度为760℃～780℃；
    S2，向所述铝液中添加以下质量百分含量的元素：Ce为6.00％～12.00％、Y为5.00％～9.50％、Zr为0.50％～3.00％、Mg为0.10％～2.50％、RE为0.15％～2.50％、Fe为0.15％～0.25％、Mn为0.05％～0.15％、Si为0.10％～0.50％，其他杂质含量小于0.1％；调整各元素比例，除气除渣，使之达到预设成分，形成合金液，之后将形成的所述合金液浇铸成合金铸锭；
    S3，将得到的所述合金铸锭加工成球形合金粉末；
    S4，将所述球形合金粉末利用选区激光熔化凝固成形，以制成在铝基体中呈网状骨架结构分布的纳米尺度的Al 11Ce 3、Al 3(Y,Zr)和/或Al 3RE的金属间化合物的材料，即得到所述高强韧耐热铝合金电枢材料。
  2. 根据权利要求1所述的高强韧耐热铝合金电枢材料的制备方法，其特征在于，所述S2，向所述铝液中添加以下质量百分含量的元素：Ce为8.00％～10.00％、Y为7.50％～9.50％、Zr为0.65％～1.00％、Mg为1.50％～2.50％、RE为0.15％～0.50％、Fe为0.15％～0.20％、Mn为0.05％～0.10％、Si为0.10％～0.25％，RE为Yb、Er、La、Sc中的一种或多种元素的混合，其他杂质含量小于0.1％。
  3. 根据权利要求1或2任一项所述的高强韧耐热铝合金电枢材料的制备方法，其特征在于，所述S2，向所述铝液中添加以下质量百分含量的元素，其中，所述RE为Yb、Er、La或Sc的一种或多种混合。
  4. 根据权利要求1或2任一项所述的高强韧耐热铝合金电枢材料的制备方法，其特征在于，所述S4，将所述球形合金粉末利用选区激光熔化凝固成形，其中，采用以下工艺参数：激光功率为260W～350W，扫描层厚为10μm～30μm，输入能量密度为50J/mm 3～90J/mm 3。
  5. 根据权利要求1或2任一项所述的高强韧耐热铝合金电枢材料的制备方法，其特征在于，所述S3，将得到的所述合金铸锭加工成球形合金粉末，其中，将所述合金铸锭利用等离子旋转电极雾化或气体雾化加工成球形合金粉末，并在加工过程中通入氩气或氦气进行气体保护。
  6. 根据权利要求5所述的高强韧耐热铝合金电枢材料的制备方法，其特征在于，所述S3，将所述合金铸锭利用等离子旋转电极雾化或气体雾化加工成球形合金粉末，其中，所述等离子旋转电极雾化的工作转速为40000rpm～50000rpm；
    所述气体雾化的工作气压为6MPa～10MPa。
  7. 根据权利要求5所述的高强韧耐热铝合金电枢材料的制备方法，其特征在于，所述S3，将得到的所述合金铸锭加工成球形合金粉末，其中，所述球形粉末粒径分布为15μm～65μm，平均粒径为45μm～55μm，所述球形粉末球形度大于95％。
  8. 一种高强韧耐热铝合金电枢材料，其特征在于，由权利要求1-7任一项所述的高强韧耐热铝合金电枢材料的制备方法制备得到。
  9. 根据权利要求8所述的高强韧耐热铝合金电枢材料，其特征在于，所述高强耐热稀土铝合金材料的致密度大于99％，密度为2.75g/cm 3～2.90g/cm 3。
  10. 根据权利要求7所述的高强韧耐热铝合金电枢材料，其特征在于，
    -所述高强韧耐热铝合金电枢材料的室温屈服强度为270MPa～350MPa，抗拉强度为400MPa～450MPa，延伸率为10％～12％；
    -所述高强耐热稀土铝合金材料在400℃以上，屈服强度为160MPa～200MPa，抗拉强度为220MPa～280MPa，延伸率大于15％。
PCT/CN2021/105093 2021-03-15 2021-07-08 一种高强韧耐热铝合金电枢材料及其制备方法 Ceased WO2022193487A1 (zh)

Priority Applications (1)

Application Number Priority Date Filing Date Title
US18/467,734 US12123077B2 (en) 2021-03-15 2023-09-15 High-toughness heat-resistant aluminum alloy armature material and preparation method thereof

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CN202110278614.6 2021-03-15
CN202110278614.6A CN113136505B (zh) 2021-03-15 2021-03-15 一种高强韧耐热铝合金电枢材料及其制备方法

Related Child Applications (1)

Application Number Title Priority Date Filing Date
US18/467,734 Continuation US12123077B2 (en) 2021-03-15 2023-09-15 High-toughness heat-resistant aluminum alloy armature material and preparation method thereof

Publications (1)

Publication Number Publication Date
WO2022193487A1 true WO2022193487A1 (zh) 2022-09-22

Family

ID=76811118

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/CN2021/105093 Ceased WO2022193487A1 (zh) 2021-03-15 2021-07-08 一种高强韧耐热铝合金电枢材料及其制备方法

Country Status (3)

Country Link
US (1) US12123077B2 (zh)
CN (1) CN113136505B (zh)
WO (1) WO2022193487A1 (zh)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN116140645A (zh) * 2023-02-28 2023-05-23 华中科技大学 一种激光选区熔注难熔金属以增强电枢抗烧蚀性能的方法
CN117165817A (zh) * 2023-09-20 2023-12-05 大连亚明汽车部件股份有限公司 一种可钎焊的高导热系数高压铸造铝合金

Families Citing this family (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN112831694B (zh) 2020-12-30 2022-12-20 上海交通大学 一种适用于增材制造的稀土铝合金粉末及其制备方法
CN115852207A (zh) * 2022-10-25 2023-03-28 安徽中科春谷激光产业技术研究院有限公司 用于大功率汽车发动机的增材制造耐热铝合金材料及其制备方法
CN115747579B (zh) * 2022-10-25 2024-02-02 安徽中科春谷激光产业技术研究院有限公司 一种高强韧增材制造铝合金材料及其制备方法
CN115821123B (zh) * 2022-12-16 2024-08-09 上海交通大学 石墨烯增强纳米双连续耐磨铝基复合材料导体及制备方法
CN116411206A (zh) * 2023-04-18 2023-07-11 上海交通大学 一种铝合金电枢材料及其制备方法和应用
CN117107121B (zh) * 2023-08-25 2025-12-19 中南大学 一种稀土改性增材制造高熵铝基合金粉末、其制备方法、应用及铝基合金
CN117230349A (zh) * 2023-10-23 2023-12-15 安徽中体新材料科技有限公司 一种选区激光熔化高强韧铝铈锰钙耐热铝合金及其制备方法
CN117532012A (zh) * 2023-11-23 2024-02-09 北京工业大学 一种金属3D打印的Al-Ce-Mg铝合金及其制备方法
CN118996211A (zh) * 2024-10-24 2024-11-22 帅翼驰(上海)新材料科技有限公司 一种免热处理高强韧挤压型材铝合金及制备方法

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN108559875A (zh) * 2017-12-28 2018-09-21 上海交通大学 一种用于发动机活塞的高强耐热铝合金材料及其制备方法
CN110052615A (zh) * 2018-08-10 2019-07-26 南方科技大学 一种选区激光熔化制备高强铝合金的方法
CN110484783A (zh) * 2019-09-06 2019-11-22 上海交通大学 一种铝-稀土合金粉末及其制备方法和应用
CN111496244A (zh) * 2020-04-27 2020-08-07 中南大学 一种增材制造高强铝合金粉及其制备方法和应用
CN112795818A (zh) * 2020-12-30 2021-05-14 上海交通大学 一种激光增材制造高强耐热稀土铝合金及其制备方法

Family Cites Families (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20080050268A1 (en) 2006-08-28 2008-02-28 Alfred Frank Daech Aluminum/lithium/x materials
RU2463365C2 (ru) 2010-09-27 2012-10-10 Открытое Акционерное Общество "Корпорация Всмпо-Ависма" СПОСОБ ПОЛУЧЕНИЯ СЛИТКА ПСЕВДО β-ТИТАНОВОГО СПЛАВА, СОДЕРЖАЩЕГО (4,0-6,0)% Аl, (4,5-6,0)% Мo, (4,5-6,0)% V, (2,0-3,6)% Cr, (0,2-0,5)% Fe, (0,1-2,0)% Zr
DE102013012259B3 (de) * 2013-07-24 2014-10-09 Airbus Defence and Space GmbH Aluminium-Werkstoff mit verbesserter Ausscheidungshärtung, Verfahren zu dessen Herstellung und Verwendung des Aluminium-Werkstoffes
CA3043850C (en) 2016-11-24 2021-03-30 Obshchestvo S Ogranichennoy Otvetstvennost'yu "Obedinennaya Kompaniya Rusal Inzhenerno-Tekhnologicheskiy Tsentr" Method of aluminium alloys production
JP2020503433A (ja) * 2016-12-21 2020-01-30 アーコニック インコーポレイテッドＡｒｃｏｎｉｃ Ｉｎｃ． 微細共晶型組織を有するアルミニウム合金製品、およびその製造方法
CN108220693B (zh) * 2017-12-28 2019-11-29 上海交通大学 一种大稀土含量的高强高导耐热铝合金导线及其制备方法
CN108559874B (zh) * 2017-12-28 2020-06-30 上海交通大学 一种高强高导的耐热铝合金导线及其制备方法
CN108356259A (zh) * 2018-01-31 2018-08-03 上海交通大学 一种纳米铝基复合材料粉末及其制备方法
US20220126367A1 (en) * 2019-02-15 2022-04-28 C-Tec Constellium Technology Center Process for manufacturing an aluminum alloy part
CN110343912A (zh) * 2019-07-18 2019-10-18 上海交通大学 一种稀土耐热铝合金导线材料及制备方法

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN108559875A (zh) * 2017-12-28 2018-09-21 上海交通大学 一种用于发动机活塞的高强耐热铝合金材料及其制备方法
CN110052615A (zh) * 2018-08-10 2019-07-26 南方科技大学 一种选区激光熔化制备高强铝合金的方法
CN110484783A (zh) * 2019-09-06 2019-11-22 上海交通大学 一种铝-稀土合金粉末及其制备方法和应用
CN111496244A (zh) * 2020-04-27 2020-08-07 中南大学 一种增材制造高强铝合金粉及其制备方法和应用
CN112795818A (zh) * 2020-12-30 2021-05-14 上海交通大学 一种激光增材制造高强耐热稀土铝合金及其制备方法

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN116140645A (zh) * 2023-02-28 2023-05-23 华中科技大学 一种激光选区熔注难熔金属以增强电枢抗烧蚀性能的方法
CN117165817A (zh) * 2023-09-20 2023-12-05 大连亚明汽车部件股份有限公司 一种可钎焊的高导热系数高压铸造铝合金

Also Published As

Publication number Publication date
US20240191324A1 (en) 2024-06-13
US12123077B2 (en) 2024-10-22
CN113136505A (zh) 2021-07-20
CN113136505B (zh) 2022-04-26

Similar Documents

Publication Publication Date Title
CN113136505B (zh) 一种高强韧耐热铝合金电枢材料及其制备方法
CN112553500B (zh) 一种同时提高Cu-Cr-Nb合金强度和导电率的方法
CN108486433B (zh) 选区激光熔化技术用Al-Mg-Sc-Zr系铝合金组合物及成型件制备方法
CN112935252B (zh) 一种基于激光选区熔化技术制备高强韧共晶高熵合金的方法
CN110218897A (zh) 一种航空发动机燃烧室内衬用耐高温Cu-Cr-Nb-Ce合金的制备方法
CN111593234A (zh) 一种激光增材制造用铝合金材料
CN113684403A (zh) 一种用于3d打印的高强铝合金粉及其制备方法
CN109811164B (zh) 一种增材制造铝合金的制备方法
CN108486431A (zh) 选区激光熔化技术用Al-Si-Mg系铝合金组合物及成型件制备方法
CN115323230B (zh) 一种铝铜铈系耐热铝合金及其制备方法
CN103949640A (zh) 一种电子束快速成形技术制备Nb-Si基超高温合金的方法
CN109957684B (zh) 一种汽车零部件用高强耐热铝合金材料的制备方法
CN116555625B (zh) 一种多尺度多相共格析出强化Cu-Ni-Al-Co-Cr-Ti耐高温铜合金及其制备方法
CN112371986B (zh) 一种高硅铝合金电子封装材料的制备方法
CN115821123B (zh) 石墨烯增强纳米双连续耐磨铝基复合材料导体及制备方法
CN115976391A (zh) 一种耐高温多主元金属间化合物及其制备方法
CN114592148B (zh) 一种增材制造用高强韧Al-Mg2Si-Zn合金及其制备方法和应用
CN118406943A (zh) 一种镁锂基复合材料丝材的制备及其电弧增材制造方法
CN108486402B (zh) 一种TiN颗粒增强镍基复合材料及其制备方法
CN118773489A (zh) 一种耐热高强铝合金及其制备方法
CN117532012A (zh) 一种金属3D打印的Al-Ce-Mg铝合金及其制备方法
CN116607037A (zh) 一种高强高导Cu-Y2O3-Ag复合材料的制备方法
CN1289702C (zh) 氮化硼/铝基复合材料制备工艺
CN115635098A (zh) 一种提高SLM成型Al-Cu-Mg合金力学性能的热处理方法
CN116815009A (zh) 一种多组元复杂共格析出强化Cu-Ni-Al-Cr-Ti耐高温铜合金及其制备方法

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: 21931069

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: 21931069

Country of ref document: EP

Kind code of ref document: A1

122 Ep: pct application non-entry in european phase

Ref document number: 21931069

Country of ref document: EP

Kind code of ref document: A1

32PN Ep: public notification in the ep bulletin as address of the adressee cannot be established

Free format text: NOTING OF LOSS OF RIGHTS PURSUANT TO RULE 112(1) EPC (EPO FORM 1205A DATED 28/02/2024)

122 Ep: pct application non-entry in european phase

Ref document number: 21931069

Country of ref document: EP

Kind code of ref document: A1