A rheo-press forming method for powder metallurgy precision components

Abstract

The application provides a rheological pressing forming method of a powder metallurgy structure: a powder containing ceramic and metal is mixed with a thermoplastic adhesive to obtain a semi-solid hot material, the semi-solid hot material is crushed to obtain feed particles, the feed particles are preheated to 60-80 DEG C, meanwhile, a mold is preheated to 60-100 DEG C, then the feed particles are filled into the mold, the mold is pressurized to 30-60 MPa, and the temperature is raised to 5-50 DEG C higher than the softening point temperature of the organic binder, the mold is kept at the temperature and pressure for 15-60 min, the mold heating is stopped, the mold is cooled, the blank is solidified, and then the blank is demolded to obtain a precision blank. The application realizes near-net-shape forming of high-performance precision complex parts under low forming pressure, provides good flowability of the slurry of the feed under constant temperature conditions, has good adaptability to materials, the prepared precision structure can be widely applied to the fields of mechanism manufacturing, biological medicine, energy and environment in the powder metallurgy field, and has good application prospect.

Description

Technical Field

[0001] This invention belongs to the field of powder metallurgy and powder engineering technology, and specifically relates to a rheological pressing forming method for powder metallurgy structures. Background Technology

[0002] Precision forming technology is currently a hot topic in powder metallurgy research and development. Traditional pressing forming technology typically involves loading the mixed powder to be formed into a steel mold and then applying pressure in one or both directions on a press to densify and shape it. However, limited by powder filling, mold design, and powder pressure distribution, traditional pressing methods often present significant challenges for forming precision components with large aspect ratios and complex shapes. Currently, new technologies and processes are emerging for forming precision components with uniform cross-sections, such as warm pressing, injection molding, and cold isostatic pressing. These advancements have significantly reduced the forming difficulty of precision powder metallurgy components, making near-net-shape forming of such workpieces possible.

[0003] The Fraunhofer Institute for Advanced Materials and Manufacturing in Germany proposed Warm Forming Compaction (WFC) in 2001. This technology involves loading a mixture of powders with a certain degree of fluidity into a mold cavity, then pressing it at a specific temperature to form complex-shaped powder metallurgy parts directly by sintering without debinding. For example, patent CN109434093A discloses a method for preparing high-density powder metallurgy parts using WFC; patent CN1660527A provides a low-temperature warm forming method for iron-based and tungsten-based alloy workpieces, achieving near-net-shape forming of high-performance, high-density, complex-shaped parts at low cost and in a short process; and patent CN102941347B discloses a method for manufacturing rotary door lock wrenches using warm forming. However, this method requires axial pressures as high as 400–700 MPa to complete the forming of the blank and is limited to sintering materials such as tungsten, titanium, and steel. There are no reports on achieving precision forming under low pressure. Summary of the Invention

[0004] In order to solve the above-mentioned technical problems in the background art, the purpose of this invention is to provide a rheological pressing forming method for precision powder metallurgy construction, which has the characteristics of low forming pressure, low forming temperature, good feed flowability, and uniform filling. It is suitable for mass production of components with complex geometry, high aspect ratio, high performance, and high precision.

[0005] To achieve the above objectives, the present invention provides the following technical solution:

[0006] This invention discloses a rheological pressing method for precision powder metallurgy components. The method involves mixing ceramic and metal powders with a thermoplastic binder to obtain a semi-solid thermal material. The semi-solid thermal material is then crushed to obtain feed particles. These feed particles are preheated to 60–80°C, and the mold is simultaneously preheated to 60–100°C. The feed particles are then filled into the mold, pressurized to 30–60 MPa, and heated to 5–50°C above the softening point of the organic binder. The temperature and pressure are maintained for 15–60 minutes. Mold heating is then stopped, and the mold is allowed to cool. After the blank solidifies, it is demolded to obtain a precision blank. The ceramic and metal powders are a mixture of fine ceramic and metal phase powders.

[0007] This invention provides a novel rheological pressing method for precision powder metallurgy components. By preheating the feed particles and placing them directly into the mold cavity, the mold cavity is heated to above the softening point of the thermoplastic binder. Utilizing the high wetting properties of the interface between the binder and the powder, the binder flows under the action of capillary force, which drives the secondary distribution of powder and rearrangement of particles in the material. This achieves stable filling of complex shapes and fine structures, resulting in highly uniform and dense precision part blanks.

[0008] In a preferred embodiment, the ceramic- and metal-containing powder is a mixed powder composed of fine ceramic phase powder and fine metal phase powder.

[0009] In a further preferred embodiment, the particle size of the ceramic phase fine powder and the metal phase fine powder is 0.05 to 1 μm.

[0010] In a further preferred embodiment, the ceramic phase fine powder and the metal phase fine powder are obtained by crushing and classifying ceramic phase powder and metal phase powder.

[0011] Through crushing and grading, raw material powder with uniform particle size and narrow particle size distribution is obtained.

[0012] In a further preferred embodiment, the crushing method is to use a turbine nano-grinding mill for nano-grinding, and the operating parameters during nano-grinding are: rotation speed of 580-1500 rpm, flow rate of 50-500 L / H, and zirconium bead filling ratio of 60-70%.

[0013] In a further preferred embodiment, the grading method is to use a jet-type air classifier for grading, and the working parameters during grading are: feed rate 50-100 kg / h, working pressure 1.5-20 MPa, and cyclone collector air pressure 1.5-20 kPa.

[0014] In a further preferred embodiment, the ceramic in the ceramic phase powder is selected from at least one of tungsten carbide, molybdenum carbide, titanium carbide, silicon carbide, titanium nitride, titanium boride, boron nitride, iron oxide, nickel oxide, aluminum oxide, magnesium oxide, zirconium oxide, nickel ferrite, manganese ferrite, cobalt ferrite, zinc ferrite, copper ferrite, chromium ferrite, and iron ferrite.

[0015] In a further preferred embodiment, the metal in the fine metal phase powder is selected from at least one of W, Mo, Zr, Ti, Co, Ni, Fe, Cu, Al, Zn, Sn, Ag, Au, and Pb.

[0016] In a further preferred embodiment, the volume ratio of the ceramic phase fine powder to the metal phase fine powder is 1-9:1-6; preferably 1-4:1-6.

[0017] In a preferred embodiment, the volume fraction of ceramic and metal powders in the semi-solid thermal material is 60% to 80%; more preferably 68% to 75%.

[0018] In a preferred embodiment, the thermoplastic adhesive comprises, by volume percentage, the following: 60-92 vol% filler adhesive, 5-30 vol% backbone adhesive, 0-8 vol% surfactant, and 0.5-5% plasticizer; the melt index of the filler adhesive is ≥80 g / min, and the melt index of the backbone adhesive is ≥35 g / min.

[0019] The semi-solid thermal material for precision components provided by this invention has high interfacial wettability between the organic binder and the raw material powder. The raw material powder has a high volume fraction, but the low binder content can maintain good blank strength. When heated above the softening point temperature of the organic binder, under certain pressure and capillary force, slow viscous migration will occur, driving secondary distribution / particle rearrangement of the powder in the material. During this stage, the porosity gradually decreases, resulting in a highly uniform and dense precision part blank, thus achieving the densification process.

[0020] In this invention, the volume fraction of the organic binder cannot be too high, because if the viscosity of the material is too low, the material will shear thinning and continuously flow out in the gap between the die and the mold, causing pressure relief and local powder separation, reducing the forming density and surface quality of the blank. Based on this, the binder content of the rheological pressing material can be further reduced compared to the injection molding process, thus improving the dimensional accuracy of the manufactured parts.

[0021] In a further preferred embodiment, the thermoplastic binder, by volume percentage, comprises: 65-85 vol% filler binder, 10-25 vol% backbone binder, 3-6 vol% surfactant, and 2-4% plasticizer. Using this preferred organic binder formulation, the resulting powder metallurgy rheological pressing material, after rheological pressing and sintering, yields products with optimal performance.

[0022] In a preferred embodiment, the filler binder is selected from at least one of paraffin wax, carnauba wax, microcrystalline wax, polyethylene wax, polyethylene glycol, polyoxymethylene, ethylene-vinyl acetate copolymer, ethylene-ethyl acrylate, and methylcellulose, preferably at least one of carnauba wax, polyoxymethylene, and polyethylene glycol, and more preferably polyoxymethylene.

[0023] The backbone binder is selected from at least one of polypropylene, high-density polyethylene, low-density polyethylene, polystyrene, and polymethyl methacrylate.

[0024] The surfactant is selected from at least one of stearic acid, zinc stearate, glycerol, castor oil, and peanut oil;

[0025] The plasticizer is selected from at least one of dibutyl phthalate, dioctyl phthalate, isooctyl β-(3,5-di-tert-butyl-4-hydroxyphenyl)propionate, pentaerythritol 4-[β-(3,5-di-tert-butyl-4-hydroxyphenyl)propionate], 4,4'-methylenebis(2,6-di-tert-butylphenol), and n-octadecyl 3-(3,5-di-tert-butyl-4-hydroxyphenyl)propionate.

[0026] In this invention, high-density polyethylene refers to polyethylene with a density of 0.94-0.97 g / cm³. 3 Low-density polyethylene (LDPE) refers to polyethylene with a density of 0.91-0.93 g / cm³. 3 Polyethylene.

[0027] In a preferred embodiment, the mixing temperature is 120–200°C, and the mixing time is 30–60 minutes. The mixing of this invention is carried out in a roll-type medium-temperature internal mixer.

[0028] In a preferred embodiment, the heating temperature during crushing is 60–150°C, and the screw speed is 400–600 r / min. The crushing is carried out in a screw extrusion hot-cutting granulator.

[0029] In a preferred embodiment, the particle size of the feed particles is -10 mesh to +200 mesh. Controlling the particle size within this range optimizes the filling performance.

[0030] In actual operation, after the feed pellets are filled into a heatable mold with a heating sleeve, a four-column hydraulic press is used for pressure pressing.

[0031] In the preferred embodiment, precision components are obtained by degreasing and sintering a precision blank.

[0032] Principles and advantages

[0033] This invention provides a novel powder metallurgy rheological pressing method for precision components. The rheological pressing method involves placing powder metallurgy rheological pressing material into a mold cavity and, under specific temperature and pressure, utilizing the high wetting properties of the interface between the binder and the powder, achieving slow densification of the material under capillary force to obtain a highly uniform and dense precision part blank. Combined with subsequent debinding and sintering densification, the final product is obtained.

[0034] A key characteristic of rheological pressing is the gradual densification process of the material in the mold cavity. The material, composed of binder and powder, is initially loose and porous in the mold cavity. Under pressure, the binder between the powders begins to soften, causing flow and rearranging the powder particles in the material. During this stage, the porosity gradually decreases, accompanied by a secondary redistribution of the binder to some extent.

[0035] Compared to powder injection molding, extrusion molding, and other powder plasticizing molding methods, powder metallurgy rheological pressing can significantly reduce the binder content in the molding material. It directly places specific materials into the mold cavity and, under specific temperature and pressure, utilizes the high wetting properties of the interface between the binder and the powder to achieve slow densification of the material under capillary force, obtaining a highly uniform and dense precision part blank. Combined with subsequent debinding and sintering densification, the final product is obtained. Based on this, powder metallurgy rheological manufacturing technology has the following four advantages in manufacturing precision parts: 1) It eliminates the flow channel design of materials in the traditional plasticizing process, reducing the binder content of the material. If further combined with powder particle gradation, the solid volume fraction of the powder can reach 60-80 vol%. 2) The relatively low binder content reduces the difficulty of debinding the formed blank and reduces the linear shrinkage rate of the formed blank, which is conducive to improving the dimensional control accuracy of precision products. 3) It can realize the rheological pressing of products with complex shapes. The secondary distribution of binder in the material can reduce the forming stress in various parts of the formed blank, and obtain blanks with uniform density distribution. 4) Since the formed blank has a relatively high density (low binder content), the requirements for powder particle size are not high. Coarse powder can be selected instead of highly active fine powder for subsequent sintering densification, reducing raw material costs.

[0036] The advantages of this invention are as follows:

[0037] (1) This invention realizes near-net-shape forming of high-performance precision complex parts under low forming pressure. The process is simple, practical and applicable. The precision parts prepared can be widely used in the fields of powder metallurgy, such as mechanical manufacturing, biomedicine, energy and environment, and have good application prospects.

[0038] (2) The present invention provides a slurry with good fluidity under constant temperature conditions, which can achieve stable filling of complex shapes and fine structures.

[0039] (3) The present invention has good adaptability to materials. It does not require special spherical powder. Ordinary metal, ceramic and composite powders can be used after spheroidization pretreatment. Attached Figure Description

[0040] Figure 1 This is a schematic diagram of the mold structure in Embodiment 1 of the present invention.

[0041] Figure 2 This is a schematic diagram of a powder metallurgy precision gear component blank according to Embodiment 1 of the present invention.

[0042] Figure 3 This is a schematic diagram of a powder metallurgy component with a hole and equal cross-section, according to Embodiment 2 of the present invention.

[0043] Figure 4 This is a schematic diagram of a powder metallurgy stepped component with a large aspect ratio, as described in Embodiment 3 of the present invention. Detailed Implementation

[0044] The preferred embodiments of the present invention will now be described in detail with reference to the accompanying drawings, so that the advantages and features of the present invention can be more easily understood by those skilled in the art, thereby providing a clearer and more explicit definition of the scope of protection of the present invention. The embodiments of the present invention include:

[0045] Example 1

[0046] A rheological pressing method for powder metallurgy precision gear components. The specific implementation steps are as follows:

[0047] Step S1: TiN, TiC ceramic phase powder and Co are separated using nano-grinding and airflow classification techniques.

[0048] The metallic phase powder was crushed and classified to obtain raw material powder with an average particle size of 0.8μm; the working parameters of the turbine nano-sand mill were: rotation speed 800rpm, flow rate 60L / H, zirconium bead loading ratio 60%; the working parameters of the jet air classifier were: feed speed 60kg / h, working pressure 10MPa, cyclone collector air pressure 15KPa.

[0049] Step S2: After thoroughly mixing TiN, TiC, and Co powders at a volume ratio of 1:1:0.6, add 30% thermoplastic binder by volume and mix thoroughly to obtain a semi-solid thermal material. The binder contains polyethylene glycol: polymethyl methacrylate: glycerol: zinc diphthalate at a volume ratio of 75%: 20%: 3%: 2%. The mixing temperature is 150℃ and the mixing time is 45 minutes.

[0050] Step S3: The semi-solid hot material obtained in step S2 is quickly transferred to a screw extrusion hot cutting granulator for crushing. The working parameters are: heating temperature 100℃, screw speed 400r / min; after passing through a -20 mesh +100 mesh sieve, metal ceramic feed pellets are obtained.

[0051] Step S4: Preheat the feed pellets obtained in step S3 to 80°C; use a heatable mold and preheat the mold to 100°C, the mold structure is as follows. Figure 1 As shown;

[0052] Step S5: Fill the mold cavity with the preheated feed powder, pressurize to 40MPa and maintain the pressure for 12min to form the blank, while continuously heating the mold to 150℃ (softening point is 130℃).

[0053] Step S6: Stop heating the mold, wait for the mold to cool and the blank to solidify, then demold to obtain a precision construct; the construct is as follows Figure 2 As shown. The precision gear blank obtained after demolding is as follows. Figure 2 As shown, the accuracy is better than ±0.1mm / 100mm, the porosity is less than 3%, and the crushing strength is 54MPa.

[0054] The precision gear blank was then sintered using the following parameters: flowing nitrogen atmosphere, sintering temperature of 1400℃, and sintering time of 180 min. The resulting precision gear component exhibited a dimensional accuracy better than ±0.5 mm / 100 mm, a relative density of 97.0%, and a Vickers hardness of 1400 N / mm². 2 The crushing strength is 42 MPa.

[0055] Example 2

[0056] A rheological pressing method for forming powder metallurgy components with perforated cross-sections. The specific implementation steps are as follows:

[0057] Step S1: SiC ceramic phase powder and Zr metallic phase powder are crushed and classified using nano-grinding and air classifying technologies to obtain raw material powder with an average particle size of 0.8 μm. The operating parameters of the turbine nano-sand mill are: rotation speed 800 rpm, flow rate 60 L / H, zirconium bead loading ratio 60%. The operating parameters of the jet air classifier are: feed rate 60 kg / h, working pressure 10 MPa, and cyclone collector air pressure 15 kPa.

[0058] Step S2: After thoroughly mixing SiC and Zr powders at a volume ratio of 4:1, add 25% thermoplastic binder by volume to obtain a semi-solid thermal material. The binder contains polyoxymethylene:polypropylene:zinc stearate:zinc diphthalate by volume ratio of 85%:10%:3%:2%. The mixing temperature is 180℃ and the mixing time is 60min.

[0059] Step S3: The semi-solid hot material obtained in step S2 is quickly transferred to a screw extrusion hot cutting granulator for crushing. The working parameters are heating temperature 130℃ and screw speed 500r / min. After passing through a -20 mesh +100 mesh sieve, metal ceramic feed pellets are obtained.

[0060] Step S4: Preheat the feed pellets obtained in step S3 to 70°C; use a heatable mold and preheat the mold to 80°C. The mold structure is as follows: Figure 1 As shown;

[0061] Step S5: Fill the mold cavity with the preheated feed powder, pressurize to 40MPa and maintain the pressure for 12min to form the blank, while continuously heating the mold to 150℃ (softening point is 140℃).

[0062] Step S6: Stop mold heating, wait for the mold to cool and the blank to solidify, then demold to obtain a precision-built part; the built part is as follows: Figure 3 As shown, the final precision gear component blank has a dimensional accuracy better than ±0.5mm / 100mm, a porosity of less than 3%, and a crushing strength of 42MPa.

[0063] Then, the powder metallurgy components with holes and other cross-sections were sintered at a temperature of 1800℃ for 1 hour, ultimately obtaining precision gear components with a dimensional accuracy better than ±0.2mm / 100mm and a relative density of 96.0%.

[0064] Example 3

[0065] A rheological pressing method for forming high aspect ratio stepped components using powder metallurgy. The specific implementation steps are as follows:

[0066] Step S1: WC ceramic phase powder and Fe metal phase powder are crushed and classified using nano-grinding and air classifying technologies to obtain raw material powder with an average particle size of 0.8 μm. The operating parameters of the turbine nano-sand mill are: rotation speed 800 rpm, flow rate 60 L / H, zirconium bead loading ratio 60%. The operating parameters of the jet air classifier are: feed rate 60 kg / h, working pressure 10 MPa, and cyclone collector air pressure 15 kPa.

[0067] Step S2: After thoroughly mixing WC and Fe powders at a volume ratio of 1:6, add 25% thermoplastic binder by volume to obtain a semi-solid thermal material. The binder contains carnauba wax, high-density polyethylene, polypropylene, and stearic acid in a mass ratio of 65%:25%:6%:4%. The mixing temperature is 160℃ and the mixing time is 45min.

[0068] Step S3: The semi-solid hot material obtained in step S2 is quickly transferred to a screw extrusion hot cutting granulator for crushing. The working parameters are heating temperature 120℃ and screw speed 600r / min. After passing through a -20 mesh +100 mesh sieve, metal ceramic feed pellets are obtained.

[0069] Step S4: Preheat the feed pellets obtained in step S3 to 75°C; use a heatable mold and preheat the mold to 75°C, the mold structure is as follows. Figure 1 As shown;

[0070] Step S5: Fill the mold cavity with the preheated feed powder, pressurize to 40MPa and maintain the pressure for 12min to form the blank, while continuously heating the mold to 150℃ (30℃ above the softening point).

[0071] Step S6: Stop heating the mold, wait for the mold to cool and the blank to solidify, then demold to obtain a precision construct; the construct is as follows Figure 4 As shown. The final precision gear component blank has a dimensional accuracy better than ±0.5mm / 100mm, a porosity of less than 5%, and a crushing strength of 61MPa.

[0072] The powder metallurgical stepped component with a large aspect ratio was then sintered at 1380℃ for 2 hours, ultimately yielding a precision gear component with a dimensional accuracy better than ±0.5mm / 100mm, a relative density of 99.0%, and a Vickers hardness of 1500N / mm². 2 .

[0073] Comparative Example 1

[0074] The other conditions are the same as in Example 1, except that the proportion of the adhesive is not within the preferred range. By volume, the ratio of polyethylene glycol: polymethyl methacrylate: glycerol: zinc phthalate is 75%: 20%: 4.8%: 0.2%.

[0075] The resulting precision gears have an accuracy of less than ±0.8 mm / 100 mm. After sintering, the dimensional accuracy of the parts is less than ±1.5 mm / 100 mm, and the relative density reaches 95.0%.

[0076] Comparative Example 2

[0077] The other conditions were the same as in Example 1, except that the mold heating temperature in step S5 was 100°C (below the softening temperature), and the resulting billet porosity was greater than 40% and the crushing strength was less than 5 MPa.

[0078] The above description is merely an embodiment of the present invention and does not limit the patent scope of the present invention. Any equivalent structural or procedural transformations made based on the content of the present invention's specification and drawings, or direct or indirect applications in other related technical fields, are similarly included within the patent protection scope of the present invention.

Claims

1. A rheoforming method for powder metallurgical precision components, characterized by: The ceramic and metal containing powder is mixed with a thermoplastic binder to obtain a semi-solid hot material, the semi-solid hot material is broken to obtain feedstock particles, the feedstock particles are preheated to 60-80℃, at the same time the mold is preheated to 60-100℃, then the feedstock particles are filled into the mold, pressurized to 30-60MPa, and heated to 5-50℃ above the softening point temperature of the thermoplastic binder, and kept for 15-60min, stop heating the mold, and after the mold cools down, the blank is solidified and demolded to obtain a precision blank; the ceramic and metal containing powder is a mixed powder composed of ceramic phase fine powder and metal phase fine powder; The volume fraction of the ceramic and metal containing powder in the semi-solid hot material is 68-75%; The thermoplastic binder is composed of the following components in terms of volume percentage: 65-85 vol% of filling binder, 10-25 vol% of backbone binder, 3-6 vol% of surfactant, 2-4% of plasticizer, the melting index of the filling binder is ≥80g / min, and the melting index of the backbone binder is ≥35g / min; The particle size of the feedstock particles is-10 mesh to +200 mesh.

2. The rheological pressing forming method of the powder metallurgy precision component according to claim 1, characterized in that: The particle size of the ceramic phase fine powder and the metal phase fine powder is 0.05-1μm; The ceramic phase fine powder and the metal phase fine powder are obtained by crushing and grading the ceramic phase powder and the metal phase powder.

3. The rheological pressing forming method of the powder metallurgy precision component according to claim 2, characterized in that: The crushing method is nanometer grinding by using a turbine type nanometer sand mill, and the working parameters during nanometer grinding are: rotation speed of 580-1500rpm, flow rate of 50-500L / H, and zirconium bead filling ratio of 60-70%; The grading method is grading by using a jet airflow classifier, and the working parameters during grading are: feeding speed of 50-100kg / h, working pressure of 1.5-20MPa, and cyclone collector air pressure of 1.5-20Kpa.

4. The method of claim 2, wherein the powder metallurgical precision component is formed by a rheoforming process. The ceramic in the ceramic phase fine powder is at least one selected from tungsten carbide, molybdenum carbide, titanium carbide, silicon carbide, titanium nitride, titanium boride, boron nitride, iron oxide, nickel oxide, aluminum oxide, magnesium oxide, zirconium oxide, nickel ferrite, manganese ferrite, cobalt ferrite, zinc ferrite, copper ferrite, chromium ferrite, and iron ferrite; The metal in the metal phase fine powder is at least one selected from W, Mo, Zr, Ti, Co, Ni, Fe, Cu, Al, Zn, Sn, Ag, Au, and Pb; The volume ratio of the ceramic phase fine powder to the metal phase fine powder is 1-9:1-6.

5. The rheological pressing forming method of the powder metallurgy precision component according to claim 1, characterized in that: The filling binder is at least one selected from paraffin wax, Brazil palm wax, microcrystalline wax, polyethylene wax, polyethylene glycol, polyformaldehyde, ethylene-vinyl acetate copolymer, ethylene-ethyl acrylate, and methyl cellulose, The backbone binder is at least one selected from polypropylene, high density polyethylene, low density polyethylene, polystyrene, and polymethyl methacrylate, The surfactant is selected from at least one of stearic acid, zinc stearate, glycerol, castor oil, and peanut oil; The plasticizer is selected from at least one of dibutyl phthalate, dioctyl phthalate, isooctyl β-(3,5-di-tert-butyl-4-hydroxyphenyl)propionate, pentaerythritol 4-[β-(3,5-di-tert-butyl-4-hydroxyphenyl)propionate], 4,4'-methylenebis(2,6-di-tert-butylphenol), and n-octadecyl 3-(3,5-di-tert-butyl-4-hydroxyphenyl)propionate.

6. The method for rheological pressing of precision powder metallurgy components according to claim 1, characterized in that: The mixing temperature is 120~200℃, and the mixing time is 30~60min.

7. The method for rheological pressing of precision powder metallurgy components according to claim 1, characterized in that: The heating temperature during crushing is 60~150℃, and the screw speed is 400~600r / min.

8. The method for rheological pressing of precision powder metallurgy components according to claim 1, characterized in that: Precision components are obtained by degreasing and sintering a precision blank.

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