CN110616359B - Self-lubricating stainless steel and preparation method thereof - Google Patents

Self-lubricating stainless steel and preparation method thereof Download PDF

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CN110616359B
CN110616359B CN201910885815.5A CN201910885815A CN110616359B CN 110616359 B CN110616359 B CN 110616359B CN 201910885815 A CN201910885815 A CN 201910885815A CN 110616359 B CN110616359 B CN 110616359B
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stainless steel
self
lubricating
pressure
hot
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CN110616359A (en
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陈强
解志文
高旭
郭锋
陈永君
邢志辉
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University of Science and Technology Liaoning USTL
No 59 Research Institute of China Ordnance Industry
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University of Science and Technology Liaoning USTL
No 59 Research Institute of China Ordnance Industry
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    • 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
    • B22F1/10—Metallic powder containing lubricating or binding agents; Metallic powder containing organic material
    • B22F1/105—Metallic powder containing lubricating or binding agents; Metallic powder containing organic material containing inorganic lubricating or binding agents, e.g. metal salts
    • 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
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/12—Both compacting and sintering
    • B22F3/14—Both compacting and sintering simultaneously
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/02—Making ferrous alloys by powder metallurgy
    • C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
    • C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%

Abstract

The invention discloses a self-lubricating stainless steel and a preparation method thereof, wherein the self-lubricating stainless steel is prepared by adopting stainless steel powder and a nano metal solid lubricating phase as raw materials through a hot-pressing sintering process, and the nano metal solid lubricating phase adopts molybdenum disulfide or tungsten disulfide. The preparation method comprises the following steps: mixing stainless steel powder and a nano metal solid lubricating phase according to a proportion; placing the mixture in a hot-pressing sintering furnace, heating to 1120-1160 ℃, starting pressurizing at 1030-1060 ℃, and pressurizing to 18-20 Mpa; keeping the temperature and the pressure for 55-65 min; naturally cooling to 580-620 ℃ after the heat preservation and pressure maintaining are finished, simultaneously keeping the pressure at 9-11Mpa, closing the pressure after the temperature is reduced to 580-620 ℃, continuously naturally cooling to below 90-110 ℃, and taking the prepared self-lubricating stainless steel out of the furnace. The self-lubricating stainless steel has the advantages of corrosion resistance and wear resistance, a wear-resistant coating does not need to be deposited on the surface of the stainless steel, a new thought is provided for the wear-resistant design of the stainless steel, and an important promotion effect is achieved on the engineering application of stainless steel parts.

Description

Self-lubricating stainless steel and preparation method thereof
Technical Field
The invention relates to a self-lubricating metal material, in particular to self-lubricating stainless steel and a preparation method thereof.
Background
The stainless steel material is one of important materials for manufacturing key equipment parts such as a mandrel, a bearing and the like, is widely applied to the fields of aerospace, ships, engineering machinery and the like, can work in an environment of-60-300 ℃, often faces a high-speed heavy-load friction working condition, and can cause early failure of the bearing due to the characteristics of the stainless steel material in an extreme environment. The austenitic stainless steel can meet the environmental requirements of aerospace field on high and low temperature, radiation, corrosion and the like due to non-magnetism, no phase change and high corrosion resistance, and the application of the austenitic stainless steel is more and more extensive. However, the austenitic stainless steel has low hardness and cannot meet the working requirement on wear resistance, and how to solve the problem of wear resistance is a key technical problem in the industrial application of the austenitic stainless steel at present.
At present, the wear resistance of the metal material is generally improved by increasing the hardness and reducing the friction coefficient, but for austenitic stainless steel: the wear resistance of the alloy cannot be improved even if heat treatment strengthening is adopted; although the friction coefficient can be reduced by coating lubricating oil on the contact surface of austenitic stainless steel, the defects of quick abrasion, short service time and the like exist under the conditions of high temperature, high pressure, corrosivity and the like; although the self-lubricating bearing bush manufactured by embedding the solid lubricant into the stainless steel substrate has the advantages of compact structure, firm combination, high temperature resistance, good pressure resistance and prolonged service life of a friction pair, the defects are complex manufacture, unstable friction coefficient, poor corrosion resistance and easy scratching of an exposed substrate layer and a friction surface; although the bearing bush made of the plastic and sintered copper powder self-lubricating wear-resistant composite material has the advantages of high mechanical strength, good heat resistance, self-lubricating property and the like, the stainless steel and the plastic have poor bonding property, and the creep property of the plastic can cause the stainless steel and the plastic to be easily peeled off, so that the service life of the stainless steel and the plastic is influenced.
In addition, the wear resistance of the stainless steel can be improved by depositing a coating on the surface of the stainless steel, for example, in a preparation method of a wear-resistant stainless steel composite plate disclosed in document CN109136873A, a layer of polymer organic material is compounded on the surface of a stainless steel plate substrate, so that the stainless steel plate has the advantages of high strength, self lubrication, wear resistance, impact resistance and light weight; for example, CN108950455A discloses a method for improving wear resistance and self-lubricity of austenitic stainless steel, which comprises performing plasma beam cladding on the surface of a steel plate with prepared powder of a working layer, priming with a metal bond compound composed of NiAl and TiC before cladding of the working layer to enhance the bonding strength between the working layer and the steel plate, and improve the hardness of the coating, and finally preparing the coating with excellent wear resistance and self-lubricating property by using a plasma coating method. Although the method of depositing the coating on the surface of the stainless steel can improve the wear resistance, the wear resistance of the coating is greatly reduced after the coating is damaged or abraded to a certain extent.
Disclosure of Invention
The invention aims to provide self-lubricating stainless steel with good integral wear resistance.
In order to achieve the above object, the present invention adopts the following technical solutions.
The self-lubricating stainless steel is characterized in that stainless steel powder and a nano metal solid lubricating phase are adopted as raw materials and are prepared by a hot-pressing sintering process.
Preferably, the nano metal solid lubricating phase adopts molybdenum disulfide (MoS)2) Or tungsten disulfide (WS)2)。
Preferably, the addition amount (mass ratio) of the nano metal solid lubricating phase is 10-14%, and the balance is stainless steel powder.
Preferably, the nano metal solid lubricating phase has the particle size of not more than 1.5 mu m and the purity of more than 98.5 percent.
Preferably, the stainless steel powder has a particle size of not more than 20 μm and an oxygen content of 500-600 ppm.
Further, under the normal temperature environment, the wear rate of the self-lubricating stainless steel is not more than
(1.58±0.11)×10-5mm3(N·m)-1(ii) a Preferably, the self-lubricating stainless steel has a wear rate of (1.58 + -0.11) × 10 in a normal temperature environment-5mm3(N·m)-1～(2.22±0.31)×10-5mm3(N·m)-1。
Further, the wear rate of the self-lubricating stainless steel is not more than (5.59 +/-0.11) multiplied by 10 under the high-temperature environment of about 300 DEG C-5mm3(N·m)-1(ii) a Preferably, the self-lubricating stainless steel has a wear rate of (5.87 + -0.26) × 10 in a high temperature environment of about 300 deg.C-5mm3(N·m)-1～(5.59±0.11)×10-5mm3(N·m)-1。
Further, under the normal temperature environment, the friction coefficient of the whole self-lubricating stainless steel is not more than 0.62; preferably, the friction coefficient of the whole self-lubricating stainless steel is 0.41 to 0.62 in a normal temperature environment.
Further, the friction coefficient of the whole self-lubricating stainless steel is not more than 0.42 under the high-temperature environment of about 300 ℃; preferably, the friction coefficient of the self-lubricating stainless steel is 0.41 to 0.42 in a high temperature environment of about 300 ℃.
Further, under the normal temperature environment, the Vickers hardness of the whole self-lubricating stainless steel is not less than 320 HV; preferably, the self-lubricating stainless steel has a Vickers hardness of 320 to 350HV in a normal temperature environment.
Further, under the normal temperature environment, the integral nano-hardness of the self-lubricating stainless steel is not less than 5.22 +/-0.135 GPa; preferably, the nano-hardness of the self-lubricating stainless steel is 5.22 + -0.135 GPa-5.67 + -0.165 GPa in the whole body in a normal temperature environment.
The second purpose of the invention is to provide a preparation method of the self-lubricating stainless steel.
A self-lubricating stainless steel preparation method adopts a hot-pressing sintering method to prepare self-lubricating stainless steel, argon protection is adopted in the hot-pressing process, and the steps comprise: mixing stainless steel powder and a nano metal solid lubricating phase according to a proportion to obtain a mixture; placing the mixture in a hot-pressing sintering furnace, heating to 1120-1160 ℃, starting pressurizing at 1030-1060 ℃, and pressurizing to 18-20 Mpa; keeping the temperature and the pressure for 55-65 min; naturally cooling to 580-620 ℃ after the heat preservation and pressure maintaining are finished, simultaneously keeping the pressure at 9-11Mpa, closing the pressure after the temperature is reduced to 580-620 ℃, continuously naturally cooling to below 90-110 ℃, and taking the prepared self-lubricating stainless steel out of the furnace.
Preferably, the self-lubricating stainless steel is prepared by a hot-pressing sintering method, argon is adopted for protection in the hot-pressing process, and the steps comprise: mixing stainless steel powder and a nano metal solid lubricating phase according to a proportion to obtain a mixture; placing the mixture in a hot-pressing sintering furnace, heating to 1150 ℃, starting pressurizing at 1050 ℃, and pressurizing to 20 Mpa; keeping the temperature and the pressure for 60 min; and naturally cooling to 600 ℃ after the heat preservation and pressure preservation are finished, keeping the pressure at 10Mpa, closing the pressure after the temperature is reduced to below 600 ℃, continuously naturally cooling to below 100 ℃, and taking the prepared self-lubricating stainless steel out of the furnace.
Further, the time for heating from room temperature to 1150 deg.C is controlled to 80-100min, and the time for pressurizing to 20MPa is controlled to 18-23 min.
The self-lubricating stainless steel has excellent integral mechanical property, especially excellent wear resistance, and the wear rate is (1.58 +/-0.11) multiplied by 10 under the normal temperature environment-5mm3(N·m)-1～(2.22±0.31)×10-5mm3(N·m)-1(ii) a Under the high-temperature environment of about 300 ℃, the wear rate is (5.87 +/-0.26) multiplied by 10-5mm3(N·m)-1～(5.59±0.11)×10-5mm3(N·m)-1(ii) a The integral Vickers hardness of the self-lubricating stainless steel can reach 320-350 HV, and is 1.6-1.75 times that of common stainless steel (the Vickers hardness of the common stainless steel is calculated according to a larger value of 200 HV).
The self-lubricating stainless steel has the advantages of corrosion resistance and wear resistance, and a wear-resistant coating does not need to be deposited on the surface of the stainless steel, so that a new thought is provided for the wear-resistant design of the stainless steel, and an important promotion effect is achieved on the engineering application of stainless steel parts; the self-lubricating stainless steel has simple preparation steps, is economical and practical, and can be used for industrial production.
Drawings
FIG. 1 is a Vickers hardness of a self-lubricating stainless steel of example 1;
FIG. 2 is a load-displacement curve of the self-lubricating stainless steel of example 1;
FIG. 3 is the nano-hardness of the self-lubricating stainless steel of example 1;
FIG. 4 shows friction curves (room temperature, 5N), (a) S0, (b) S1, (c) S2, and (d) S3 of the self-lubricating stainless steel of example 1;
FIG. 5 shows the wear scar shapes (normal temperature, 5N), (a) S0, (b) S1, (c) S2, and (d) S3 of the self-lubricating stainless steel of example 1;
FIG. 6 shows the wear scar profiles (ambient temperature, 5N), (a) S0, (b) S1, (c) S2, (d) S3 of the self-lubricating stainless steel of example 1;
FIG. 7 shows the wear rates (normal temperature, 5N) of the self-lubricating stainless steel of example 1;
FIG. 8 is the friction curve (300 ℃ C.) of the self-lubricating stainless steel of example 1, (a) S0, (b) S1, (c) S2, (d) S3;
FIG. 9 shows the wear scar morphology (300 ℃ C.) of the self-lubricating stainless steel of example 1, (a) S0, (b) S1, (c) S2, (d) S3;
FIG. 10 shows the wear scar profiles (300 ℃ C.) of the self-lubricating stainless steel of example 1, (a) S0, (b) S1, (c) S2, (d) S3;
FIG. 11 is a graph of the wear rate (300 ℃ C.) of the self-lubricating stainless steel of example 1.
In the figure: s0 is smelted 316L stainless steel, S1 is hot-pressed 316L/molybdenum disulfide-6% stainless steel, S2 is hot-pressed 316L/molybdenum disulfide-12% stainless steel, and S3 is hot-pressed 316L/molybdenum disulfide-18% stainless steel.
Detailed Description
The present invention will be further described with reference to the accompanying drawings and specific embodiments, but the following embodiments are only used for understanding the principle of the present invention and the core idea thereof, and do not limit the scope of the present invention. It should be noted that modifications to the invention as described herein, which do not depart from the principles of the invention, are intended to be within the scope of the claims which follow.
Example 1: a self-lubricating stainless steel is prepared by taking stainless steel powder and a nano metal solid lubricating phase as raw materials and carrying out a hot-pressing sintering process, wherein the stainless steel powder adopts 316L stainless steel powder with the granularity of less than 20 mu m, and the oxygen content is 500-600 ppm; the nano metal solid lubricating phase adopts molybdenum disulfide with the granularity of less than 1.5 mu m, the purity is more than 98.5 percent, and the mass percentage of the molybdenum disulfide is 12 percent.
Example 2: a self-lubricating stainless steel is prepared by taking stainless steel powder and a nano metal solid lubricating phase as raw materials and carrying out a hot-pressing sintering process, wherein the stainless steel powder adopts 316L stainless steel powder with the granularity of less than 20 mu m, and the oxygen content is 500-600 ppm; the nano metal solid lubricating phase adopts molybdenum disulfide with the granularity of less than 1.5 mu m, the purity is more than 98.5 percent, and the mass percentage of the molybdenum disulfide is 6 percent.
Example 3: a self-lubricating stainless steel is prepared by taking stainless steel powder and a nano metal solid lubricating phase as raw materials and carrying out a hot-pressing sintering process, wherein the stainless steel powder adopts 316L stainless steel powder with the granularity of less than 20 mu m, and the oxygen content is 500-600 ppm; the nano metal solid lubricating phase adopts molybdenum disulfide with the granularity of less than 1.5 mu m, the purity is more than 98.5 percent, and the mass proportion of the molybdenum disulfide is 18 percent.
Comparative example: 316L stainless steel formed by smelting is adopted.
In the preparation methods of the self-lubricating stainless steel in the embodiments 1 to 3, the self-lubricating stainless steel is prepared by a hot-pressing sintering method, and the hot-pressing process adopts argon protection, and comprises the following steps: mixing stainless steel powder and a nano metal solid lubricating phase according to a corresponding proportion to obtain a mixture; placing the mixture in a hot-pressing sintering furnace, heating to 1150 deg.C, heating from room temperature to 1150 deg.C for 90min, pressurizing at 1050 deg.C to 20Mpa, and pressurizing to 20Mpa for 20 min; keeping the temperature and the pressure for 60 min; and naturally cooling to 600 ℃ after the heat preservation and pressure preservation are finished, simultaneously keeping the pressure at 10Mpa, closing the pressure after the temperature is reduced to below 600 ℃, continuously naturally cooling to below 100 ℃, taking out the prepared self-lubricating stainless steel from the furnace, and keeping the temperature reduction process for about 5-7 hours.
Performance detection
The self-lubricating steels of examples 1, 2 and 3 and the general stainless steels of the comparative examples were subjected to vickers hardness, load-displacement curve, nano-hardness, normal temperature and high temperature (300 ℃) friction curve, wear scar profile, and wear rate tests, and the results are shown in fig. 1 to 11. Wherein, the hardness adopts HV-1000 type microhardness instrument to polish the surface of the sample, 15 test points are taken at the flat part of the surface of the sample to be measured and the average value is calculated to obtain the final result. The loading force was 10N and the dwell time was 12 s. The nano hardness is measured by a nano indenter (G200-2), and the surface hardness of the material is automatically recorded and calculated by adopting a continuous automatic loading mode. 20 points were measured for each sample and averaged. In the friction and wear experiment, the normal-temperature friction and wear performance of the surface of the material is measured by means of an MS-T300 friction and wear testing machine. Paired grinding ballsBy using Si3N4Ceramic ball, hardness 1600Gpa, diameter 6mm, experimental parameters: the load is 3N, the rotating speed is 300rap/min, the testing radius is 5mm, and the testing time is 60 min. The high-temperature experiment part adopts a HT-1000 type high-temperature friction wear tester. Using Si for grinding balls3N4Ceramic balls with a hardness of 1600GPa and a diameter of 6.34 mm. The normal temperature part adopts 5N load, the rotating speed is 300rap/min, the testing radius is 4mm, and the testing time is 30 min. The high-temperature experiment part adopts 5N load, the rotating speed is 300rap/min, the testing radius is 4mm, and the testing time is 30 min. After the normal temperature/high temperature friction and wear experiment, an Alpha-step instrument is used for measuring a two-dimensional profile curve of a grinding crack, so that the width and depth data of the grinding crack of the sample are obtained, and the wear loss is calculated. And observing the appearance and characteristics of the frictional wear surface by adopting a Ginshi VHX-5000 digital microscope.
As can be seen from fig. 1: the hardness of the self-lubricating stainless steel shows a slight rising trend along with the increase of the addition amount of the molybdenum disulfide, the Vickers hardness of common 316 stainless steel is about 245HV, the Vickers hardness of sample S1 is about 320HV, the Vickers hardness of sample S2 is 325HV, and the Vickers hardness of sample S3 reaches 350 HV.
As can be seen from fig. 2: within the indentation displacement depth range of 2000nm, the pressure load required by the sample S0 is about 310mN, the indentation load required by the sample S1 is about 350mN, the indentation load required by the sample S2 is about 350mN, and the indentation load required by the sample S3 is about 390mN, which shows that the nano mechanical property of the self-lubricating stainless steel is further improved along with the increase of the addition amount of the molybdenum disulfide.
As can be seen from fig. 3: the nano hardness of the sample S0 is about 4.42 +/-0.143 GPa, the nano hardness of the sample S1 is about 5.24 +/-0.285 GPa, the nano hardness of the sample S2 is about 5.22 +/-0.135 GPa, and the nano hardness of the sample S3 is about 5.67 +/-0.165 GPa.
As can be seen from fig. 4: the friction process of the sample S0 is not stable and has high noise, the friction coefficient is about 0.65, the friction coefficient of the sample S1 gradually tends to a stable value of 0.61 along with the increase of the friction stroke, the sample S2 shows the lowest friction coefficient of about 0.41 along with the increase of the content of molybdenum disulfide in the material, the friction process is stable and has low noise, the friction performance of the material is obviously improved along with the increase of the doping amount of molybdenum disulfide, the friction process of the sample S2 is stable and has low noise, the doping amount of molybdenum disulfide is further increased, the friction performance of the material is reduced, and the friction coefficient of the sample S3 is increased to about 0.62.
As can be seen from fig. 5: sample S0 exhibits severe wear characteristics with a rough wear scar surface and adhered abrasive dust in large amounts, representing typical adhesive wear failure, with significant improvement in the frictional wear characteristics of the material by doping with molybdenum disulfide, reduced surface frictional damage, reduced adhered abrasive dust on the wear scar surface and increased smoothness of the surface of sample S1. The smoothness of the surface of the grinding mark of the sample S2 is improved and the adhered abrasive dust is reduced along with the increase of the content of the doped molybdenum disulfide, and the adhered abrasive dust on the surface of the grinding mark of the sample S3 is less along with the further increase of the content of the doped molybdenum disulfide, so that the anti-friction and anti-wear capability is different from that of the sample S0. Obviously, the molybdenum disulfide is doped to improve the anti-friction and anti-wear characteristics of the composite material, and the adhesion and wear degree of the material is relieved to different degrees as the content of the molybdenum disulfide is increased.
As can be seen from fig. 6: the sample S0 has severe grinding trace profile fluctuation, which reaches 11.2 μm at the most, and confirms that the material friction process and the friction pair have severe abrasion. After the molybdenum disulfide is doped, the fluctuation of the profile of the grinding mark of the material is reduced, the fluctuation of the profile of the grinding mark of the sample S1 is reduced, the maximum depth of the sample S1 is about 8.2 mu m, the content of the doped molybdenum disulfide is increased, the surface of the profile of the grinding mark of the sample S2 is smooth and flat, the wear resistance is very excellent, the maximum depth of the profile of the grinding mark is about 4.0 mu m, the content of the doped molybdenum disulfide material is further increased, the profile of the grinding mark of the sample S3 is smoother, the fluctuation is reduced remarkably, the maximum depth of the grinding mark is about 3.7 mu m, and obviously, the molybdenum disulfide remarkably improves the.
As can be seen from fig. 7: the wear rate of sample S0 was about (2.99. + -. 0.13). times.10-5mm3(N·m)-1As the doped molybdenum disulfide content increases, the wear rate of the material decreases, and the wear rate of sample S1 decreases to (2.54 + -0.24) × 10-5mm3(N·m)-1Sample S2 showed the lowest wear rate of about (1.58 + -0.11). times.10 when doped molybdenum disulfide was present at 12%-5mm3(N·m)-1Further increasing the doped molybdenum disulfide content, the abrasion of sample S3The ratio was increased to (2.22. + -. 0.31). times.10-5mm3(N·m)-1. According to the data characterization results of a friction curve, the appearance of a grinding trace, the wear rate and the like, the content of molybdenum disulfide has an important influence on the friction performance of the material, and when the content of doped molybdenum disulfide is 12%, the material has better friction and wear resistance.
As can be seen from fig. 8: the friction coefficient of the sample S0 is about 0.42 under the high-temperature environment of 300 ℃, the high-temperature friction coefficient of the composite material is slightly reduced along with the increase of the content of the doped molybdenum disulfide, the high-temperature friction coefficient of the sample S1 is reduced to about 0.41, the high-temperature friction coefficient of the sample S2 is maintained at about 0.42 along with the increase of the content of the doped molybdenum disulfide in the material, the doping amount of the molybdenum disulfide is further increased, the friction coefficient of the sample S3 is slightly increased, the value of the friction coefficient is about 0.51, and obviously, the fluctuation interval of the friction coefficient of the composite material under the high-temperature environment is small and is not obviously distinguished.
As can be seen from fig. 9: under the high-temperature friction environment of 300 ℃, the quantity of adhered abrasive dust on the surface of the grinding scar of the sample S0 is reduced, and the abrasion appearance is different from the adhered abrasion characteristic at normal temperature, which indicates that the abrasion form is changed. In addition, the wear appearance of the doped molybdenum disulfide composite material also changes obviously, a small amount of abrasive dust adheres to the surfaces of the wear scars of the samples S1 and S2, and in contrast, the surfaces of the wear scars of the sample S2 are smooth and smooth, and the surface of the wear scars is less in adhering abrasive dust. The appearance of the high-temperature grinding trace at 300 ℃ proves that the differentiation trend of the friction and wear characteristics of the material under the high-temperature environment is gradually weakened.
As can be seen from fig. 10: the sample S0 has severe grinding trace profile fluctuation, which reaches 14.8 μm at the most, and confirms that the material friction process and the friction pair have severe abrasion. After the molybdenum disulfide is doped, the fluctuation of the profile of the grinding mark of the material is reduced, the fluctuation of the profile of the grinding mark of the sample S1 is reduced, the maximum depth of the sample S1 is about 13.6 mu m, the content of the doped molybdenum disulfide is increased, the surface of the profile of the grinding mark of the sample S2 is smooth and flat, the wear resistance is very excellent, the maximum depth of the profile of the grinding mark is about 10.4 mu m, the content of the doped molybdenum disulfide material is further increased, the profile of the grinding mark of the sample S3 is smoother, the fluctuation is reduced remarkably, and the maximum depth of the grinding mark is about 16.1 mu m.
As can be seen from fig. 11: the wear rate of sample S0 was about (6.22+ 0.29). times.10-5mm3(N·m)-1As the doped molybdenum disulfide content increases, the wear rate of the material decreases, and the wear rate of sample S1 decreases to (5.87 + -0.26) × 10-5mm3(N·m)-1Sample S2 showed the lowest wear rate of about (5.59. + -. 0.11). times.10 when doped molybdenum disulfide was present at 12% level-5mm3(N·m)-1Further increasing the doped molybdenum disulfide content, the wear rate of sample S3 increased to (7.57. + -. 0.12). times.10-5mm3(N·m)-1. According to the data characterization results of a friction curve, the appearance of a grinding trace, the wear rate and the like, the added molybdenum disulfide is continuously increased to generate an important influence on the friction performance of the material, so that the material has better friction and wear resistance when the content of the doped molybdenum disulfide is 12% at 300 ℃.
Finally, it is noted that the above preferred embodiment is only used to illustrate the technical solution of the present invention and not to limit the same, in fact, the types of stainless steel in the present invention include, but are not limited to, 316L stainless steel, 304 stainless steel, 321 stainless steel, 310 stainless steel, and the added nano-metal solid lubricating phase may also be tungsten disulfide; the parameters of the invention are also not limited to the values disclosed in the examples, provided in fact that the process parameters satisfy the following: adding 10-14% of molybdenum disulfide, adopting inert gas for protection in the hot pressing process, raising the temperature from room temperature to 80-100min to 1120-.

Claims (10)

1. A self-lubricating stainless steel characterized by: the lubricant is prepared by adopting stainless steel powder and a nano metal solid lubricating phase as raw materials and performing a hot-pressing sintering process; the particle size of the nano metal solid lubricating phase is not more than 1.5 mu m, and the purity is more than 98.5%; the self-lubricating stainless steel is prepared by adopting a hot-pressing sintering method, argon is adopted for protection in the hot-pressing process, and the steps comprise: mixing stainless steel powder and a nano metal solid lubricating phase according to a proportion to obtain a mixture; placing the mixture in a hot-pressing sintering furnace, heating to 1120-1160 ℃, starting pressurizing at 1030-1060 ℃, and pressurizing to 18-20 Mpa; keeping the temperature and the pressure for 55-65 min; naturally cooling to 580-620 ℃ after the heat preservation and pressure maintaining are finished, simultaneously keeping the pressure at 9-11Mpa, closing the pressure after the temperature is reduced to 580-620 ℃, continuously naturally cooling to below 90-110 ℃, and taking the prepared self-lubricating stainless steel out of the furnace; the nano metal solid lubricating phase adopts molybdenum disulfide; the mass percentage of the addition amount of the nano metal solid lubricating phase is 10-14%, and the balance is stainless steel powder.
2. Self-lubricating stainless steel according to claim 1, characterized in that: the stainless steel powder has a particle size of not more than 20 μm and an oxygen content of 500-600 ppm.
3. Self-lubricating stainless steel according to any of claims 1-2, characterized in that: under the normal temperature environment, the wear rate of the self-lubricating stainless steel is (1.58 +/-0.11) multiplied by 10-5mm3(N·m)-1。
4. Self-lubricating stainless steel according to any of claims 1-2, characterized in that: the wear rate of the self-lubricating stainless steel is (5.59 +/-0.11) multiplied by 10 under the high-temperature environment of about 300 DEG C-5mm3 (N·m)-1。
5. Self-lubricating stainless steel according to any of claims 1-2, characterized in that: and under the normal temperature environment, the friction coefficient of the whole self-lubricating stainless steel is 0.41.
6. Self-lubricating stainless steel according to any of claims 1-2, characterized in that: the friction coefficient of the whole self-lubricating stainless steel is 0.42 under the high-temperature environment of about 300 ℃.
7. Self-lubricating stainless steel according to any of claims 1-2, characterized in that: under normal temperature environment, the Vickers hardness of the whole self-lubricating stainless steel is 325 HV.
8. Self-lubricating stainless steel according to any of claims 1-2, characterized in that: under the normal temperature environment, the integral nano-hardness of the self-lubricating stainless steel is 5.22 +/-0.135 GPa.
9. The method for preparing self-lubricating stainless steel according to any one of claims 1 to 8, wherein the self-lubricating stainless steel is prepared by a hot-pressing sintering method, argon gas is adopted for protection in the hot-pressing process, and the steps comprise: mixing stainless steel powder and a nano metal solid lubricating phase according to a proportion to obtain a mixture; placing the mixture in a hot-pressing sintering furnace, heating to 1150 ℃, starting pressurizing at 1050 ℃, and pressurizing to 20 Mpa; keeping the temperature and the pressure for 60 min; and naturally cooling to 600 ℃ after the heat preservation and pressure preservation are finished, keeping the pressure at 10Mpa, closing the pressure after the temperature is reduced to below 600 ℃, continuously naturally cooling to below 100 ℃, and taking the prepared self-lubricating stainless steel out of the furnace.
10. The method of claim 9, wherein the heating time from room temperature to 1150 ℃ is controlled to 80-100min, and the pressurizing time to 20MPa is controlled to 18-23 min.
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