WO2020038313A1 - 一种金属基碳纤维复合材料及陶瓷的制备方法 - Google Patents

一种金属基碳纤维复合材料及陶瓷的制备方法 Download PDF

Info

Publication number
WO2020038313A1
WO2020038313A1 PCT/CN2019/101302 CN2019101302W WO2020038313A1 WO 2020038313 A1 WO2020038313 A1 WO 2020038313A1 CN 2019101302 W CN2019101302 W CN 2019101302W WO 2020038313 A1 WO2020038313 A1 WO 2020038313A1
Authority
WO
WIPO (PCT)
Prior art keywords
carbon fiber
metal
composite material
fiber composite
based carbon
Prior art date
Application number
PCT/CN2019/101302
Other languages
English (en)
French (fr)
Inventor
靳普
陈宗良
Original Assignee
至玥腾风科技集团有限公司
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 至玥腾风科技集团有限公司 filed Critical 至玥腾风科技集团有限公司
Publication of WO2020038313A1 publication Critical patent/WO2020038313A1/zh

Links

Images

Classifications

    • D—TEXTILES; PAPER
    • D06—TREATMENT OF TEXTILES OR THE LIKE; LAUNDERING; FLEXIBLE MATERIALS NOT OTHERWISE PROVIDED FOR
    • D06M—TREATMENT, NOT PROVIDED FOR ELSEWHERE IN CLASS D06, OF FIBRES, THREADS, YARNS, FABRICS, FEATHERS OR FIBROUS GOODS MADE FROM SUCH MATERIALS
    • D06M11/00—Treating fibres, threads, yarns, fabrics or fibrous goods made from such materials, with inorganic substances or complexes thereof; Such treatment combined with mechanical treatment, e.g. mercerising
    • D06M11/83—Treating fibres, threads, yarns, fabrics or fibrous goods made from such materials, with inorganic substances or complexes thereof; Such treatment combined with mechanical treatment, e.g. mercerising with metals; with metal-generating compounds, e.g. metal carbonyls; Reduction of metal compounds on textiles
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C04B35/01—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics
    • C04B35/48—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on zirconium or hafnium oxides, zirconates, zircon or hafnates
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C47/00—Making alloys containing metallic or non-metallic fibres or filaments
    • C22C47/02—Pretreatment of the fibres or filaments
    • C22C47/04—Pretreatment of the fibres or filaments by coating, e.g. with a protective or activated covering
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C47/00—Making alloys containing metallic or non-metallic fibres or filaments
    • C22C47/08—Making alloys containing metallic or non-metallic fibres or filaments by contacting the fibres or filaments with molten metal, e.g. by infiltrating the fibres or filaments placed in a mould
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C49/00—Alloys containing metallic or non-metallic fibres or filaments
    • C22C49/14—Alloys containing metallic or non-metallic fibres or filaments characterised by the fibres or filaments
    • C—CHEMISTRY; METALLURGY
    • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
    • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
    • C25D3/00—Electroplating: Baths therefor
    • C25D3/02—Electroplating: Baths therefor from solutions
    • C25D3/12—Electroplating: Baths therefor from solutions of nickel or cobalt
    • C—CHEMISTRY; METALLURGY
    • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
    • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
    • C25D5/00—Electroplating characterised by the process; Pretreatment or after-treatment of workpieces
    • C25D5/54—Electroplating of non-metallic surfaces
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
    • C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
    • C04B2235/30—Constituents and secondary phases not being of a fibrous nature
    • C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
    • C04B2235/3224—Rare earth oxide or oxide forming salts thereof, e.g. scandium oxide
    • C04B2235/3225—Yttrium oxide or oxide-forming salts thereof
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
    • C04B2235/65—Aspects relating to heat treatments of ceramic bodies such as green ceramics or pre-sintered ceramics, e.g. burning, sintering or melting processes
    • C04B2235/656—Aspects relating to heat treatments of ceramic bodies such as green ceramics or pre-sintered ceramics, e.g. burning, sintering or melting processes characterised by specific heating conditions during heat treatment
    • C04B2235/6562—Heating rate
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
    • C04B2235/65—Aspects relating to heat treatments of ceramic bodies such as green ceramics or pre-sintered ceramics, e.g. burning, sintering or melting processes
    • C04B2235/656—Aspects relating to heat treatments of ceramic bodies such as green ceramics or pre-sintered ceramics, e.g. burning, sintering or melting processes characterised by specific heating conditions during heat treatment
    • C04B2235/6567—Treatment time
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
    • C04B2235/70—Aspects relating to sintered or melt-casted ceramic products
    • C04B2235/96—Properties of ceramic products, e.g. mechanical properties such as strength, toughness, wear resistance
    • D—TEXTILES; PAPER
    • D06—TREATMENT OF TEXTILES OR THE LIKE; LAUNDERING; FLEXIBLE MATERIALS NOT OTHERWISE PROVIDED FOR
    • D06M—TREATMENT, NOT PROVIDED FOR ELSEWHERE IN CLASS D06, OF FIBRES, THREADS, YARNS, FABRICS, FEATHERS OR FIBROUS GOODS MADE FROM SUCH MATERIALS
    • D06M2101/00—Chemical constitution of the fibres, threads, yarns, fabrics or fibrous goods made from such materials, to be treated
    • D06M2101/40—Fibres of carbon

Definitions

  • the invention relates to the field of composite material preparation, in particular to a metal-based carbon fiber composite material and a method for preparing ceramics.
  • Metal-based carbon fiber composites have broad application prospects in the fields of aerospace, biomaterials and civil industry due to their excellent properties such as high specific strength, high specific modulus and good toughness. Compared with metal materials, it has a high specific modulus. Amount and specific strength; Compared with ceramics, it has high toughness and impact resistance.
  • metal carbonization, carburization, and electrochemical corrosion occur when carbon fibers and metals are compounded.
  • ceramic materials are a class of inorganic non-metallic materials made from natural or synthetic compounds through shaping and high-temperature sintering. It has the advantages of high melting point, high hardness, high wear resistance, and oxidation resistance. It can be used as a structural material and a tool material. Since ceramics also have some special properties, it can also be used as a functional material. Ceramic material is the material with the best stiffness and the highest hardness among engineering materials, and its hardness is mostly above 1500HV. Ceramics have higher compressive strength, but lower tensile strength, poor plasticity and toughness.
  • Ceramic materials generally have a high melting point (mostly above 2000 ° C) and have excellent chemical stability at high temperatures; the thermal conductivity of ceramics is lower than that of metal materials, and ceramics are also good thermal insulation materials. At the same time, the linear expansion coefficient of ceramics is lower than that of metals. When temperature changes, ceramics have good dimensional stability. Ceramic materials are not easily oxidized at high temperatures, and have good corrosion resistance to acids, alkalis, and salts. In order to improve the abrasion resistance of the metal, a ceramic coating is applied on the metal substrate. However, due to the large physical and chemical properties of ceramic and metal, it is difficult to directly connect them, mainly because the thermal expansion coefficients of the two differ greatly. The joint is prone to generate large residual thermal stress.
  • the present invention provides a method for preparing a metal-based carbon fiber composite material and a ceramic, so as to improve the bonding strength of the carbon fiber and the metal matrix, and improve the hardness, compressive strength and heat resistance of the ceramic.
  • a first aspect of the present invention provides a method for preparing a metal-based carbon fiber composite material, including the following steps:
  • the shaped carbon fiber is heated to the melting point of the metal, and after the metal is melted and mixed, it is cooled to room temperature and discharged, and the metal-based carbon fiber composite material is prepared.
  • the metal-based carbon fiber composite material is a nickel-based carbon fiber composite material.
  • the step of placing carbon fibers in an electrolyte for electroplating is to place carbon fibers in an electroplating bath containing a nickel-containing electrolyte, wherein, in the nickel-containing electrolyte, the mass percentage of nickel Above 25%, the diameter of the carbon fiber is 0.1-0.3mm.
  • the step of shaping the electroplated carbon fiber includes:
  • Non-electroplated metal fiber is used to reinforce the shaped carbon fiber.
  • the electroplated carbon fiber is shaped by using a tool made of ceramic.
  • the ceramic is one or more combinations of alumina, zirconium carbide, and boron nitride.
  • the step of heating the shaped carbon fiber to the melting point of the metal and cooling the metal to room temperature after the metal is melted and mixed includes: after the metal is heated and melted, the surface of the electroplated carbon fiber and the non-electroplated carbon fiber have metal and metal After sticking together, after cooling to room temperature, the metal solidifies.
  • a second aspect of the present invention provides a method for preparing a ceramic using a metal-based carbon fiber composite material, including the following steps:
  • Ceramics are sintered on the surface of the metal-based carbon fiber composite material subjected to anodization.
  • the ceramic is yttria-stabilized zirconia.
  • the step of sintering ceramics on the surface of the metal-based carbon fiber composite material subjected to anodization includes: spraying yttria-stabilized zirconia powder on the surface of the metal-based carbon fiber composite material and performing hot isostatic Pressure sintering.
  • the step of hot isostatic sintering includes: increasing the temperature from room temperature 25 ° C to 1400-1800 ° C at a speed of 1-5 ° C / min at 1-3Mpa; Pressure, heat preservation time is 0.5-3 hours, heat preservation pressure is 3-6Mpa; after heat preservation and pressure preservation, under the pressure of 1-3Mpa, the temperature is reduced to room temperature 25 ° C at a speed of 3-7 ° C / min.
  • the present invention provides a method for preparing a metal-based carbon fiber composite material and a ceramic.
  • the method for preparing the metal-based carbon fiber composite material includes: electroplating carbon fibers into an electrolyte; sculpting the electroplated carbon fibers, A carbon fiber having a predetermined shape is obtained; the shaped carbon fiber is heated to a melting point of the metal, and is cooled to room temperature after the metal is melted and mixed, and then discharged to obtain the metal-based carbon fiber composite material.
  • the method for preparing the ceramic includes anodizing the surface of the metal-based carbon fiber composite material; sintering the ceramic on the surface of the metal-based carbon fiber composite material after the anodization.
  • the preparation method of metal-based carbon fiber composite material realizes the effective combination of metal nickel and carbon fiber.
  • the metal-based carbon fiber composite material prepared by the method of the present invention effectively fuses carbon fiber and metal substrate, forms an organic whole, and improves carbon fiber. Bonding strength with metal substrate;
  • the method for preparing ceramics using the metal-based carbon fiber composite material realizes the connection between the metal material and the ceramic.
  • the metal-based carbon fiber composite material has extremely high hardness and compressive strength, good heat resistance, and high temperature resistance. It can keep the shape and size unchanged, and can resist the erosion of high temperature jet.
  • FIG. 1 is a flowchart of a method for preparing a metal-based carbon fiber composite material according to the present invention
  • FIG. 2 is a flowchart of a method for preparing a metal-based carbon fiber composite ceramic according to the present invention
  • FIG. 3 is a flow chart of a method for preparing a Tesla turbine disk by using the metal-based carbon fiber composite ceramic preparation method of the present invention
  • FIG. 4 is a schematic structural diagram of a Tesla turbine disk prepared by using the metal-based carbon fiber composite ceramic preparation method of the present invention.
  • a method 100 for preparing a metal-based carbon fiber composite material, as shown in FIG. 1, includes the following steps:
  • Step 110 The carbon fiber is electroplated in an electrolyte
  • Step 120 Shape the carbon fibers after plating to obtain carbon fibers of a predetermined shape
  • Step 130 The shaped carbon fiber is heated to the melting point of the metal, and after the metal is melted and mixed, it is cooled to room temperature and discharged, and the metal-based carbon fiber composite material is obtained.
  • the metal-based carbon fiber composite material is a nickel-based carbon fiber composite material.
  • the step 110 includes electroplating the carbon fibers in a plating bath containing a nickel-containing electrolyte, wherein, in the nickel-containing electrolyte, the mass percentage of nickel is greater than 25%, and the diameter of the carbon fibers is 0.1-0.3 mm. , Preferably 0.2 mm.
  • the step 120 includes:
  • Shape the carbon fiber after plating use the tooling to shape the carbon fiber after plating, the meaning of the shape is to shape the carbon fiber into a predetermined shape.
  • the tooling material needs to be resistant to high temperatures, difficult to deform, and difficult to react with metals, and is preferably made of ceramics, which is one or more combinations of alumina, zirconium carbide, and boron nitride.
  • the method further comprises the step of using a non-plated metal carbon fiber to reinforce the shaped carbon fiber.
  • the step 130 includes: after the metal is melted (when the metal-based carbon fiber composite material is a nickel-based carbon fiber composite material, the heating temperature is greater than 1000 ° C), all carbon fiber surfaces have metal and the metal is stuck together, and cooled to After room temperature, the metal solidified.
  • the metal-based carbon fiber composite material prepared by the above method realizes the effective combination of metal nickel and carbon fiber, effectively fuses the carbon fiber and the metal substrate, forms an organic whole, and improves the bonding strength of the carbon fiber and the metal matrix.
  • a second aspect of the present invention provides a method 200 for preparing ceramics using a metal-based carbon fiber composite material. As shown in FIG. 2, the method includes the following steps:
  • Step 210 The carbon fiber is electroplated in an electrolyte
  • Step 220 Shape the electroplated carbon fibers to obtain carbon fibers of a predetermined shape
  • Step 230 heating the shaped carbon fiber to the melting point of the metal, cooling to room temperature after the metal is melted and mixed, and discharging, to obtain the metal-based carbon fiber composite material;
  • Step 240 Anodize the surface of the metal-based carbon fiber composite material.
  • the effect of the anodization can make the interface between the metal (nickel) and the high-temperature ceramics better, and form a transition surface.
  • An oxide layer is formed on the surface;
  • Step 250 Sinter a high-temperature-resistant ceramic on the surface of the metal-based carbon fiber composite material subjected to anodization to obtain the ceramic.
  • the metal-based carbon fiber composite material is a nickel-based carbon fiber composite material
  • the ceramic is yttria-stabilized zirconia YSZ.
  • the steps 210-230 are the same as the method for preparing the aforementioned metal-based carbon fiber composite material.
  • the step 250 includes: spraying yttria-stabilized zirconia powder on the surface of the metal-based carbon fiber composite material, and then performing hot isostatic sintering.
  • the specific process is: increasing the temperature from room temperature 25 ° C at a speed of 1-5 ° C / min (preferably 3 ° C / min) to 1400-1800 ° C (preferably 1600 ° C) at 1-3Mpa;
  • the holding time is 0.5-3 hours (preferably 1 hour) and the holding pressure is 3-6Mpa.
  • the temperature is reduced at a speed of 3-7 ° C / minute (preferably 5 ° C / minute) under the pressure of 1-3Mpa.
  • heating or cooling rate If the heating or cooling rate is too fast, it will cause the components to shrink and phase change unevenly, resulting in a large amount of internal stress, which will cause the ceramic to crack; if the insulation pressure and time are not enough, it will also cause the components to shrink and phase change unevenly, resulting A large amount of internal stress causes the ceramic to crack.
  • the method for preparing ceramics by using the metal-based carbon fiber composite material realizes the connection between the metal material and the ceramic.
  • the metal-based carbon fiber composite material has extremely high hardness and compressive strength, good heat resistance, and can be used at high temperatures. Keeping the shape and size unchanged, it can resist the erosion of high-temperature jets.
  • a third aspect of the present invention provides a method 300 for manufacturing a Tesla turbine disk.
  • the Tesla turbine disk is provided with positioning holes 410 and exhaust holes 420.
  • the rotating shaft passes through the positioning holes 410 of the same structure of the Tesla turbine disk 400 and has the same features as the several structures.
  • the Sierra turbine disk 400 is fixedly connected.
  • the exhaust hole 420 is disposed near the positioning block 410. Further preferably, there are several, preferably three, exhaust holes 420, which are all distributed on the surface of the Tesla turbine disk 400.
  • the method 300 for manufacturing a Tesla turbine disk includes the following steps:
  • Step 310 Place the carbon fibers in a nickel-containing electrolyte for electroplating
  • Step 320 Wound the electroplated carbon fiber on a mandrel to form a disc-shaped carbon fiber; the mandrel needs to be resistant to high temperatures, difficult to deform, and difficult to react with metals, and is preferably made of ceramics to make the mandrel.
  • the ceramic is one or more combinations of alumina, zirconium carbide and boron nitride;
  • Step 330 The disc-shaped carbon fiber and the mandrel are heated together to the melting point of nickel, the metallic nickel is melted and adhered, and then cooled to room temperature to obtain a nickel-based carbon fiber composite material of the Tesla turbine disc;
  • Step 340 Remove the mandrel and machine an exhaust hole on the nickel-based carbon fiber composite material of the Tesla turbine disc by machining.
  • the exhaust hole is disposed near the positioning hole of the turbine disc, and the exhaust There may be several holes, preferably three, evenly distributed on the surface of the turbine disk;
  • Step 350 Anodize the surface of the nickel-based carbon fiber composite material of the Tesla turbine disk
  • Step 360 Sinter ceramics on the surface of the nickel-based carbon fiber composite material of the Tesla turbine disc that has been anodized to obtain a ceramic material of the Tesla turbine disc.
  • the ceramic is yttria-stabilized zirconia YSZ;
  • Step 370 Polish using a diamond abrasive to obtain the Tesla turbine disk.
  • the Tesla turbine disk made by the above-mentioned method for manufacturing a Tesla turbine disk has extremely high hardness and compressive strength, good heat resistance, can maintain the shape and size unchanged at high temperatures, and can resist the erosion of high-temperature jets. When the disc size is large, it is not easy to deform, which realizes the universal application of Tesla turbine discs.
  • carbon fibers are put into a nickel-containing electrolyte for electroplating; the electrolyte contains 500 g / L of nickel sulfate; 70 g / L of nickel chloride; 40 g / L of boric acid; and 0.1 g / L of sodium lauryl sulfate.
  • the nickel sulfate is a main salt
  • boric acid is a buffering agent
  • nickel chloride is an anti-passivation agent
  • sodium lauryl sulfate is a dispersant.
  • Experimental conditions pH value is 3 ⁇ 4; temperature is 25 °C; plating time is 1 ⁇ 12min; current density is 0.1 ⁇ 0.5A / dm2.
  • the diameter of the carbon fiber was 0.2 mm. After electroplating, nickel-based carbon fibers were obtained.
  • the electroplated nickel-based carbon fiber is wound on a mandrel to form a disc-shaped carbon fiber; the mandrel is selected from alumina, zirconium carbide, or boron nitride.
  • the disc-shaped carbon fiber and the mandrel are heated together to a temperature above the melting point of nickel, and the heating temperature is 1500 ° C, and the temperature is maintained for 10-45 minutes, preferably 30 minutes. After the metal nickel is melted and adhered, it is cooled to room temperature to obtain the Tesla turbine Plate of nickel-based carbon fiber composite material.
  • the mandrel is removed, and three uniformly distributed exhaust holes are machined on the nickel-based carbon fiber composite material of the Tesla turbine disk.
  • Anodizing is performed on the surface of the nickel-based carbon fiber composite material of the Tesla turbine disk.
  • the specific process is: anodizing the nickel-based carbon fiber composite material in an external magnetic field, and the strength of the external magnetic field is 20-60mT.
  • the cathode and electrolyte are ammonium salts, the concentration of the electrolyte is 1-15%, the temperature of the electrolyte is 0-50 ° C, the applied current density is 0.5-10mA / cm2, and the residence time of the nickel-based carbon fiber composite material in the electrolyte It is 1-2 minutes; then it is taken out for washing and drying to obtain an anodized nickel-based carbon fiber composite material.
  • hot isostatic pressing is performed for sintering.
  • the specific process is: at 1-3Mpa, the temperature is increased from room temperature 25 ° C to 1600 ° C at a rate of 3 ° C / min. After maintaining the temperature for 1 hour, the temperature is 3-6Mpa, and under the pressure of 1-3Mpa, Cool down to 25 °C at room temperature at a rate of 5 °C / min;
  • the nickel-based carbon fiber composite material is polished by using a diamond polishing liquid to prepare the Tesla turbine disk.
  • the nickel-based carbon fiber composite material obtained through the above method has a tensile strength of 4 to 7 Gpa and a tensile modulus of 400 to 700 Gpa.
  • the present invention provides a method for preparing a metal-based carbon fiber composite material and a ceramic.
  • the method for preparing the metal-based carbon fiber composite material includes: electroplating carbon fibers into an electrolyte; sculpting the electroplated carbon fibers, A carbon fiber having a predetermined shape is obtained; the shaped carbon fiber is heated to a melting point of the metal, and is cooled to room temperature after the metal is melted and mixed, and then discharged to obtain the metal-based carbon fiber composite material.
  • the method for preparing the ceramic includes anodizing the surface of the metal-based carbon fiber composite material; sintering the ceramic on the surface of the metal-based carbon fiber composite material after the anodization.
  • the metal-based carbon fiber composite material prepared by the method has higher bonding strength between carbon fiber and metal matrix, and the ceramic material has higher hardness, compressive strength and heat resistance.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Organic Chemistry (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Ceramic Engineering (AREA)
  • Manufacturing & Machinery (AREA)
  • Mechanical Engineering (AREA)
  • Electrochemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Structural Engineering (AREA)
  • Inorganic Chemistry (AREA)
  • Textile Engineering (AREA)
  • Composite Materials (AREA)
  • Manufacture Of Alloys Or Alloy Compounds (AREA)
  • Turbine Rotor Nozzle Sealing (AREA)
  • Chemical Or Physical Treatment Of Fibers (AREA)
  • Powder Metallurgy (AREA)

Abstract

一种金属基碳纤维复合材料及陶瓷的制备方法，所述金属基碳纤维复合材料的制备方法包括：将碳纤维放入电解液中电镀；对电镀后的碳纤维造型，得到预定形状的碳纤维；将造型后的碳纤维加热至金属熔点，待金属熔化混合后冷却至室温，出料，即制得所述金属基碳纤维复合材料。所述陶瓷的制备方法包括将所述金属基碳纤维复合材料表面进行阳极氧化；在经过阳极氧化的所述金属基碳纤维复合材料表面烧结陶瓷。所述方法制得的金属基碳纤维复合材料具有较高的碳纤维与金属基体的结合强度，陶瓷材料具有较高的硬度、抗压强度和耐热性。

Description

一种金属基碳纤维复合材料及陶瓷的制备方法 技术领域
本发明涉及复合材料制备领域，具体涉及一种金属基碳纤维复合材料及陶瓷的制备方法。
背景技术
金属基碳纤维复合材料因具有高比强度、高比模量和韧性好等优良性能，在航空航天，生物材料和民用工业领域具有广阔的应用前景，与金属材料相比，它具有高的比模量和比强度；与陶瓷相比，具有高的韧性和耐冲击性能。但由于碳纤维表面惰性大、表面能低，缺乏有化学活性的化学键，反应活性低，与基体的结合力差，表面存在较多的缺陷，直接影响了复合材料的力学性能，限制了碳纤维高性能的发挥。复合材料制造过程中，碳纤维与金属复合时会发生金属碳化、渗碳及电化学腐蚀现象。现有技术中对碳纤维金属化方法做了很多有效的尝试和探索，但现有的方法都存在一定的缺陷，金属化后的碳纤维的质量参差不齐，普适性补强，因此寻求一种最大限度地提高碳纤维与基体间的界面结合强度的制备方法是非常必要的。
此外，陶瓷材料是用天然或合成化合物经过成形和高温烧结制成的一类无机非金属材料。它具有高熔点、高硬度、高耐磨性、耐氧化等优点，可用作结构材料、刀具材料，由于陶瓷还具有某些特殊的性能，又可作为功能材料。陶瓷材料是工程材料中刚度最好、硬度最高的材料，其硬度大多在1500HV以上。陶瓷的抗压强度较高，但抗拉强度较低，塑性和韧性很差。陶瓷材料一般具有高的熔点(大多在2000℃以上)，且在高温下具有极好的化学稳定性；陶瓷的导热性低于金属材料，陶瓷还是良好的隔热材料。同时陶瓷的线 膨胀系数比金属低，当温度发生变化时，陶瓷具有良好的尺寸稳定性。陶瓷材料在高温下不易氧化，并对酸、碱、盐具有良好的抗腐蚀能力。为了提高金属的耐磨性，会在金属基体上涂覆一层陶瓷涂层，但是由于陶瓷与金属的理化性质差异较大，很难直接连接，主要因为两者的热膨胀系数差异较大，在连接处易产生很大的残余热应力。
发明内容
为解决上述问题，本发明提供了一种金属基碳纤维复合材料及陶瓷的制备方法，以提高碳纤维与金属基体的结合强度、以及提高陶瓷的硬度、抗压强度和耐热性。
具体由下列技术方案实现：
本发明的第一方面提供了一种金属基碳纤维复合材料的制备方法，包括如下步骤：
将碳纤维放入电解液中电镀；
对电镀后的碳纤维造型，得到预定形状的碳纤维；
将造型后的碳纤维加热至金属熔点，待金属熔化混合后冷却至室温，出料，即制得所述金属基碳纤维复合材料。
在一些具体实施例中，所述金属基碳纤维复合材料为镍基碳纤维复合材料。
在一些具体实施例中，所述将碳纤维放入电解液中电镀的步骤为将碳纤维放入装有含镍电解液的电镀池中电镀，其中，所述含镍电解液中，镍的质量百分比大于25％，碳纤维的直径为0.1-0.3mm。
在一些具体实施例中，所述对电镀后的碳纤维造型的步骤包括：
对经过电镀后的碳纤维造型；
使用非电镀金属的碳纤维对所述造型后的碳纤维加固。
在一些具体实施例中，采用工装对电镀后的碳纤维造型，所述工装由陶 瓷制成。
在一些具体实施例中，所述陶瓷为氧化铝、碳化锆和氮化硼的一种或多种组合。
在一些具体实施例中，将造型后的碳纤维加热至金属熔点，待金属熔化混合后冷却至室温的步骤包括：加热金属熔化后，电镀金属的碳纤维和非电镀金属的碳纤维表面均有金属且金属粘连在一起，冷却至室温后，金属凝固。
本发明的第二方面提供了一种使用金属基碳纤维复合材料制备陶瓷的方法，包括如下步骤：
使用如前所述的金属基碳纤维复合材料的制备方法制备金属基碳纤维复合材料；
在所述金属基碳纤维复合材料表面进行阳极氧化；
在经过阳极氧化的所述金属基碳纤维复合材料表面烧结陶瓷。
在一些具体实施例中，所述陶瓷为氧化钇稳定氧化锆。
在一些具体实施例中，所述在经过阳极氧化的所述金属基碳纤维复合材料表面烧结陶瓷的步骤包括：将氧化钇稳定氧化锆粉末喷洒至所述金属基碳纤维复合材料表面后进行热等静压烧结。
在一些具体实施例中，所述热等静压烧结的步骤包括：在1-3Mpa下，将温度从室温25℃开始以1-5℃/分钟的速度上升至1400-1800℃；然后保温保压，保温时间为0.5-3小时、保温压力为3-6Mpa；保温保压后，在1-3Mpa的压力下，以3-7℃/分钟的速度降温到室温25℃。
综上所述，本发明提供了一种金属基碳纤维复合材料及陶瓷的制备方法，所述金属基碳纤维复合材料的制备方法包括：将碳纤维放入电解液中电镀；对电镀后的碳纤维造型，得到预定形状的碳纤维；将造型后的碳纤维加热至金属熔点，待金属熔化混合后冷却至室温，出料，即制得所述金属基碳纤维复 合材料。所述陶瓷的制备方法包括将所述金属基碳纤维复合材料表面进行阳极氧化；在经过阳极氧化的所述金属基碳纤维复合材料表面烧结陶瓷。
(三)有益效果
本发明的上述技术方案具有如下有益的技术效果：
1、金属基碳纤维复合材料的制备方法，实现了金属镍和碳纤维的有效结合，通过本发明方法制得的金属基碳纤维复合材料，使碳纤维与金属基材发生有效融合，形成有机整体，提高碳纤维与金属基体的结合强度；
2、使用所述金属基碳纤维复合材料制备陶瓷的方法，实现了在金属材料与陶瓷的连接，该金属基碳纤维复合材料制备陶瓷具有极高的硬度和抗压强度，耐热性好，在高温下可以保持形状尺寸不变，能够抵御高温射流的侵蚀。
附图说明
图1是本发明金属基碳纤维复合材料制备的方法流程图；
图2是本发明金属基碳纤维复合材料陶瓷制备的方法流程图；
图3是使用本发明金属基碳纤维复合材料陶瓷制备方法制备特斯拉涡轮盘的方法流程图；
图4是使用本发明金属基碳纤维复合材料陶瓷制备方法制备的特斯拉涡轮盘的结构示意图。
具体实施方式
为使本发明的目的、技术方案和优点更加清楚明了，下面结合具体实施方式并参照附图，对本发明进一步详细说明。应该理解，这些描述只是示例性的，而并非要限制本发明的范围。此外，在以下说明中，省略了对公知结构和技术的描述，以避免不必要地混淆本发明的概念。
一种金属基碳纤维复合材料的制备方法100，如图1所示，包括如下步骤：
步骤110、将碳纤维放入电解液中电镀；
步骤120、对电镀后的碳纤维造型，得到预定形状的碳纤维；
步骤130、将造型后的碳纤维加热至金属熔点，待金属熔化混合后冷却至室温，出料，即制得所述金属基碳纤维复合材料。
所述金属基碳纤维复合材料为镍基碳纤维复合材料。
具体的，所述步骤110包括将碳纤维放入装有含镍电解液的电镀池中电镀，其中，所述含镍电解液中，镍的质量百分比大于25％，碳纤维的直径为0.1-0.3mm，优选0.2mm。
具体的，所述步骤120包括：
对经过电镀后的碳纤维造型；采用工装对电镀后的碳纤维造型，造型的含义为将碳纤维塑造成预定的形状。所述工装材料需耐高温、不易变形、很难与金属发生反应，优选由陶瓷制成，所述陶瓷为氧化铝、碳化锆和氮化硼的一种或多种组合。
优选地，还可包括使用非电镀金属的碳纤维对所述造型后的碳纤维加固的步骤。
具体的，所述步骤130包括：加热金属熔化后(所述金属基碳纤维复合材料为镍基碳纤维复合材料时，加热温度大于1000℃)，所有碳纤维表面均有金属且金属粘连在一起，冷却至室温后，金属凝固。
由上述方法制得的金属基碳纤维复合材料，实现了金属镍和碳纤维的有效结合，使碳纤维与金属基材发生有效融合，形成有机整体，提高了碳纤维与金属基体的结合强度。
本发明的第二方面提供了一种使用金属基碳纤维复合材料制备陶瓷的方法200，如图2所示，包括如下步骤：
步骤210、将碳纤维放入电解液中电镀；
步骤220、对电镀后的碳纤维造型，得到预定形状的碳纤维；
步骤230、将造型后的碳纤维加热至金属熔点，待金属熔化混合后冷却至室温，出料，得到所述金属基碳纤维复合材料；
步骤240、在所述金属基碳纤维复合材料表面进行阳极氧化，阳极氧化所起的作用可以让金属(镍)和高温陶瓷的相接面融合更好，形成一个过渡面，在金属(镍)的表面形成氧化层；
步骤250、在经过阳极氧化的所述金属基碳纤维复合材料表面烧结耐高温陶瓷，得到所述陶瓷。
具体的，所述金属基碳纤维复合材料为镍基碳纤维复合材料，所述陶瓷为氧化钇稳定氧化锆YSZ。所述步骤210-230与前述金属基碳纤维复合材料的制备方法相同。
所述步骤250包括：将氧化钇稳定氧化锆粉末喷洒至所述金属基碳纤维复合材料表面后进行热等静压烧结。具体过程为：在1-3Mpa下，将温度从室温25℃开始以1-5℃/分钟(优选3℃/分钟)的速度上升至1400-1800℃(优选1600℃)；然后保温保压，保温时间为0.5-3小时(优选1小时)、保温压力为3-6Mpa；保温保压后，在1-3Mpa的压力下，以3-7℃/分钟(优选5℃/分钟)的速度降温到室温25℃。如果升温或降温速度过快，会导致各组分收缩及相变不均匀，产生大量内应力，导致陶瓷开裂；如果保温压力和时长不足，同样会导致各组分收缩及相变不均匀，产生大量内应力，导致陶瓷开裂。
使用所述金属基碳纤维复合材料制备陶瓷的方法，实现了在金属材料与陶瓷的连接，该金属基碳纤维复合材料制备陶瓷具有极高的硬度和抗压强度，耐热性好，在高温下可以保持形状尺寸不变，能够抵御高温射流的侵蚀。
本发明的第三方面提供了一种特斯拉涡轮盘的制造方法300。所述特斯拉涡轮盘如图4所示，设置有定位孔410和排气孔420，转轴穿过若干结构相同的特斯拉涡轮盘400的定位孔410并与所述若干结构相同的特斯拉涡轮盘400固定连接。
优选的，所述排气孔420设置在靠近定位块410处。进一步优选，所述排气孔420有若干个，优选3个，均布于特斯拉涡轮盘400表面。
所述特斯拉涡轮盘的制造方法300，如图3所示，包括如下步骤：
步骤310、将碳纤维放置在含镍电解液中电镀；
步骤320、将电镀后的碳纤维缠绕在芯轴上形成盘状碳纤维；所述芯轴需耐高温、不易变形、很难与金属发生反应，优选由陶瓷制成，制成所述芯轴的所述陶瓷为氧化铝、碳化锆和氮化硼的一种或多种组合；
步骤330、将盘状碳纤维和芯轴一起加热到镍的熔点，使金属镍融化并粘连后冷却至室温，制得所述特斯拉涡轮盘的镍基碳纤维复合材料；
步骤340、拆除芯轴，通过机加工的方式在所述特斯拉涡轮盘的镍基碳纤维复合材料上加工排气孔，所述排气孔设置在靠近涡轮盘定位孔处，所述排气孔可以设置有若干个，优选3个，均布于涡轮盘表面；
步骤350、在所述特斯拉涡轮盘的镍基碳纤维复合材料表面进行阳极氧化；
步骤360、在经过阳极氧化的所述特斯拉涡轮盘的镍基碳纤维复合材料表面烧结陶瓷，得到特斯拉涡轮盘的陶瓷材料；所述陶瓷为氧化钇稳定氧化锆YSZ；
步骤370、使用金刚石研磨液抛光，制得所述特斯拉涡轮盘。
由上述特斯拉涡轮盘的制造方法制得的特斯拉涡轮盘具有极高的硬度和抗压强度，耐热性好，在高温下可以保持形状尺寸不变，能够抵御高温射流的侵蚀，圆盘尺寸大时不易变形，实现了特斯拉涡轮盘的普及应用。
下面通过具体的实施例对本发明进行进一步地说明。
实施例1：
使用镍基碳纤维复合材料陶瓷制备特斯拉涡轮盘的制备方法：
首先，将碳纤维放入含镍电解液中进行电镀；所述电解液中含硫酸镍500g/L；氯化镍70g/L；硼酸40g/L；十二烷基硫酸钠0.1g/L。其中所述硫酸镍为主盐，硼酸为缓冲剂，氯化镍为防钝化剂，十二烷基硫酸钠为分散剂。实验条件：pH值为3～4；温度为25℃；电镀时间为1～12min；电流密度为0.1～0.5A/dm2。碳纤维的直径为0.2mm。电镀后得到镍基碳纤维。
将电镀后的镍基碳纤维缠绕在芯轴上形成盘状碳纤维；所述芯轴选自氧化铝、碳化锆或氮化硼。
将盘状碳纤维和芯轴一起加热到镍的熔点以上，加热温度为1500℃，保持10-45分钟，优选30分钟，使金属镍融化并粘连后冷却至室温，制得所述特斯拉涡轮盘的镍基碳纤维复合材料。
拆除芯轴，通过机加工的方式在所述特斯拉涡轮盘的镍基碳纤维复合材料上加工3个均匀分布的排气孔。
在所述特斯拉涡轮盘的镍基碳纤维复合材料表面进行阳极氧化，具体过程为：将镍基碳纤维复合材料在外加磁场中进行阳极氧化处理，外加磁场的强度为20-60mT，以石墨为阴极，电解质为铵盐，电解液的浓度为1-15％，电解液的温度为0-50℃，施加的电流密度为0.5-10mA/cm2，镍基碳纤维复合材料在电解液中停留的时间为1-2分钟；然后取出进行清洗干燥得到表面经过阳极氧化的镍基碳纤维复合材料。
将YSZ粉末喷洒至所述镍基碳纤维复合材料表面后进行热等静压烧结。具体过程为：在1-3Mpa下，将温度从室温25℃开始以3℃/分钟的速度上升至1600℃，在保持保温1小时、保温压力3-6Mpa后，在1-3Mpa的压力下，以5℃/分钟的速度降温到室温25℃；
使用金刚石研磨液对所述镍基碳纤维复合材料进行抛光，制得所述特斯拉涡轮盘。
经过上述方法制得的镍基碳纤维复合材料具有的拉伸强度为4～7Gpa,拉伸模量为400～700Gpa。
综上所述，本发明提供了一种金属基碳纤维复合材料及陶瓷的制备方法，所述金属基碳纤维复合材料的制备方法包括：将碳纤维放入电解液中电镀；对电镀后的碳纤维造型，得到预定形状的碳纤维；将造型后的碳纤维加热至金属熔点，待金属熔化混合后冷却至室温，出料，即制得所述金属基碳纤维复合材料。所述陶瓷的制备方法包括将所述金属基碳纤维复合材料表面进行阳极氧化；在经过阳极氧化的所述金属基碳纤维复合材料表面烧结陶瓷。所述方法制得的金属基碳纤维复合材料具有较高的碳纤维与金属基体的结合强 度，陶瓷材料具有较高的硬度、抗压强度和耐热性。
应当理解的是，本发明的上述具体实施方式仅仅用于示例性说明或解释本发明的原理，而不构成对本发明的限制。因此，在不偏离本发明的精神和范围的情况下所做的任何修改、等同替换、改进等，均应包含在本发明的保护范围之内。此外，本发明所附权利要求旨在涵盖落入所附权利要求范围和边界、或者这种范围和边界的等同形式内的全部变化和修改例。

Claims (10)

  1. 一种金属基碳纤维复合材料的制备方法，其特征在于，包括如下步骤：
    将碳纤维放入电解液中电镀；
    对电镀后的碳纤维造型，得到预定形状的碳纤维；
    将造型后的碳纤维加热至金属熔点，待金属熔化混合后冷却至室温，出料，即制得所述金属基碳纤维复合材料。
  2. 根据权利要求1所述的金属基碳纤维复合材料的制备方法，其特征在于，所述金属基碳纤维复合材料为镍基碳纤维复合材料。
  3. 根据权利要求2所述的金属基碳纤维复合材料的制备方法，其特征在于，所述将碳纤维放入电解液中电镀的步骤为将碳纤维放入装有含镍电解液的电镀池中电镀，其中，所述含镍电解液中，镍的质量百分比大于25％，碳纤维的直径为0.1-0.3mm。
  4. 根据权利要求1-3任一项所述的金属基碳纤维复合材料的制备方法，其特征在于，所述对电镀后的碳纤维造型的步骤包括：
    对电镀后的碳纤维造型；
    使用非电镀金属的碳纤维对所述造型后的碳纤维加固。
  5. 根据权利要求4所述的金属基碳纤维复合材料的制备方法，其特征在于，采用工装对电镀后的碳纤维造型，所述工装由陶瓷制成。
  6. 根据权利要求5所述的金属基碳纤维复合材料的制备方法，其特征在于，所述陶瓷为氧化铝、碳化锆和氮化硼的一种或多种组合。
  7. 根据权利要求4所述的金属基碳纤维复合材料的制备方法，其特征在于，将造型后的碳纤维加热至金属熔点，待金属熔化混合后冷却至室温的步骤包括：加热金属熔化后，电镀金属的碳纤维和非电镀金属的碳纤维表面均有金属且金属粘连在一起，冷却至室温后，金属凝固。
  8. 一种使用金属基碳纤维复合材料制备陶瓷的方法，其特征在于，包括如下步骤：
    使用如权利要求1-7任一项所述的金属基碳纤维复合材料的制备方法制备金属基碳纤维复合材料；
    在所述金属基碳纤维复合材料表面进行阳极氧化；
    在经过阳极氧化的所述金属基碳纤维复合材料表面烧结陶瓷。
  9. 根据权利要求8所述的使用金属基碳纤维复合材料制备陶瓷的方法，其特征在于，所述陶瓷为氧化钇稳定氧化锆。
  10. 根据权利要求9所述的使用金属基碳纤维复合材料制备陶瓷的方法，其特征在于，所述在经过阳极氧化的所述金属基碳纤维复合材料表面烧结陶瓷的步骤包括：将氧化钇稳定氧化锆粉末喷洒至所述金属基碳纤维复合材料表面后进行热等静压烧结。
PCT/CN2019/101302 2018-08-22 2019-08-19 一种金属基碳纤维复合材料及陶瓷的制备方法 WO2020038313A1 (zh)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CN201810959186.1A CN109267332B (zh) 2018-08-22 2018-08-22 一种金属基碳纤维复合材料及陶瓷的制备方法
CN201810959186.1 2018-08-22

Publications (1)

Publication Number Publication Date
WO2020038313A1 true WO2020038313A1 (zh) 2020-02-27

Family

ID=65154003

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/CN2019/101302 WO2020038313A1 (zh) 2018-08-22 2019-08-19 一种金属基碳纤维复合材料及陶瓷的制备方法

Country Status (2)

Country Link
CN (1) CN109267332B (zh)
WO (1) WO2020038313A1 (zh)

Families Citing this family (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109267332B (zh) * 2018-08-22 2021-01-08 至玥腾风科技投资集团有限公司 一种金属基碳纤维复合材料及陶瓷的制备方法
CN111022185A (zh) * 2019-12-25 2020-04-17 迅玲腾风汽车动力科技(北京)有限公司 一种具有压盖的涡轮及转子系统

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101067192A (zh) * 2007-04-10 2007-11-07 中北大学 碳纤维增强镍基复合材料及其制备方法
CN101798665A (zh) * 2010-03-26 2010-08-11 东北大学 一种铝基泡沫材料的制备方法
CN102500245A (zh) * 2011-12-01 2012-06-20 西北有色金属研究院 一种金属基陶瓷复合滤膜的制备方法
CN109267332A (zh) * 2018-08-22 2019-01-25 至玥腾风科技投资集团有限公司 一种金属基碳纤维复合材料及陶瓷的制备方法

Family Cites Families (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH06128494A (ja) * 1992-10-16 1994-05-10 Toshiba Chem Corp 導電性樹脂組成物の製造方法
CN108193148B (zh) * 2017-12-27 2019-12-24 西安理工大学 一种碳纤维增强金属基复合材料的制备方法

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101067192A (zh) * 2007-04-10 2007-11-07 中北大学 碳纤维增强镍基复合材料及其制备方法
CN101798665A (zh) * 2010-03-26 2010-08-11 东北大学 一种铝基泡沫材料的制备方法
CN102500245A (zh) * 2011-12-01 2012-06-20 西北有色金属研究院 一种金属基陶瓷复合滤膜的制备方法
CN109267332A (zh) * 2018-08-22 2019-01-25 至玥腾风科技投资集团有限公司 一种金属基碳纤维复合材料及陶瓷的制备方法

Also Published As

Publication number Publication date
CN109267332B (zh) 2021-01-08
CN109267332A (zh) 2019-01-25

Similar Documents

Publication Publication Date Title
US4197902A (en) Molds for continuous casting of metals
WO2020038313A1 (zh) 一种金属基碳纤维复合材料及陶瓷的制备方法
CN108838504B (zh) 一种用于扩散连接碳化硅陶瓷的复合中间层及其连接工艺
US12110808B2 (en) Titanium alloy blade tip with high adhesion strength and wear-resistant protective coating and preparation method thereof
Zhang et al. Microstructure, microhardness and corrosion resistance of laser cladding Al 2 O 3@ Ni composite coating on 304 stainless steel
WO2020038318A1 (zh) 一种特斯拉涡轮盘的制备方法和特斯拉涡轮盘
CN102383115B (zh) 一种渗透镀制备功能梯度复合涂层的方法
CN112048752A (zh) 一种cBN/Ni-Mo钛合金叶片叶尖防护涂层的制备方法和应用
JP4554330B2 (ja) 高耐久性を有する断熱スタンパ構造
CN203197384U (zh) 带磨料线锯
CN110396703A (zh) 整体式金刚石套料钻的制备方法
Huang et al. Grinding performance of electroplated diamond tools strengthened with Cr-C deposit using D-150 diamond particles
CN101723599A (zh) 一种用于玻璃模具表面的复合镀层及其电镀方法
US11267102B2 (en) Aluminum diamond cutting tool
CN107487054B (zh) 多层复合膜、其制备方法以及作为纤维增强复合材料的连接材料的应用
CN112899733A (zh) 一种致密氮氧化铬阻氢渗透涂层及其制备方法
CN102864453B (zh) 激光熔覆原位合成硼化物陶瓷涂层及其制备方法
Wang et al. Preparing porous diamond composites via electrophoretic deposition of diamond particles on foam nickel substrate
CN106244885B (zh) 一种多层结构氧化铝自润滑复合陶瓷及其制备方法
CN114214684A (zh) 精密零件表面的金属-陶瓷梯度复合镀层及其制备方法
CN111286768B (zh) 一种镍钴锰镧合金镀液及其制备方法和应用
CN111074274A (zh) 一种结晶器铜板表面长寿命梯度复合涂层及其制备方法
CN114250496A (zh) 一种力学性能稳定的复合金属材料
CN115572974B (zh) 复合涂层及其制备方法
CN112226805A (zh) 一种电沉积钴基复合镀层的制备方法

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: 19852014

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: DE

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 1205 DATED 01/07/2021)

122 Ep: pct application non-entry in european phase

Ref document number: 19852014

Country of ref document: EP

Kind code of ref document: A1