CN114231895A - High-performance low-temperature high-efficiency ionic composite permeation surface modification method for austenitic stainless steel - Google Patents
High-performance low-temperature high-efficiency ionic composite permeation surface modification method for austenitic stainless steel Download PDFInfo
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- 229910000963 austenitic stainless steel Inorganic materials 0.000 title claims abstract description 32
- 239000002131 composite material Substances 0.000 title claims abstract description 30
- 238000002715 modification method Methods 0.000 title claims abstract description 14
- 238000005121 nitriding Methods 0.000 claims abstract description 52
- 230000008595 infiltration Effects 0.000 claims abstract description 24
- 238000001764 infiltration Methods 0.000 claims abstract description 24
- 238000000034 method Methods 0.000 claims abstract description 24
- 238000004140 cleaning Methods 0.000 claims abstract description 19
- 238000005498 polishing Methods 0.000 claims abstract description 10
- 238000001035 drying Methods 0.000 claims abstract description 8
- 239000003960 organic solvent Substances 0.000 claims abstract description 5
- 238000005520 cutting process Methods 0.000 claims abstract description 3
- 238000012545 processing Methods 0.000 claims abstract 2
- 238000004458 analytical method Methods 0.000 claims description 26
- 230000008569 process Effects 0.000 claims description 12
- 239000001257 hydrogen Substances 0.000 claims description 10
- 229910052739 hydrogen Inorganic materials 0.000 claims description 10
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims description 7
- 238000002791 soaking Methods 0.000 claims description 7
- 238000004506 ultrasonic cleaning Methods 0.000 claims description 7
- 239000007789 gas Substances 0.000 claims description 5
- 238000011056 performance test Methods 0.000 claims description 2
- 238000005260 corrosion Methods 0.000 abstract description 27
- 230000007797 corrosion Effects 0.000 abstract description 24
- 239000002184 metal Substances 0.000 abstract description 6
- 229910052751 metal Inorganic materials 0.000 abstract description 6
- 230000000694 effects Effects 0.000 abstract description 5
- 230000018199 S phase Effects 0.000 abstract description 3
- 230000000536 complexating effect Effects 0.000 abstract description 3
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 abstract description 2
- 229910052804 chromium Inorganic materials 0.000 abstract description 2
- 239000011651 chromium Substances 0.000 abstract description 2
- 238000009792 diffusion process Methods 0.000 abstract description 2
- 238000004381 surface treatment Methods 0.000 abstract description 2
- 230000015572 biosynthetic process Effects 0.000 abstract 1
- 239000002244 precipitate Substances 0.000 abstract 1
- 239000006104 solid solution Substances 0.000 abstract 1
- 239000010935 stainless steel Substances 0.000 abstract 1
- 239000010963 304 stainless steel Substances 0.000 description 24
- 229910000589 SAE 304 stainless steel Inorganic materials 0.000 description 24
- 230000000052 comparative effect Effects 0.000 description 14
- 238000004544 sputter deposition Methods 0.000 description 14
- 238000010586 diagram Methods 0.000 description 7
- 230000003287 optical effect Effects 0.000 description 6
- 239000012535 impurity Substances 0.000 description 5
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 239000002905 metal composite material Substances 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 230000035515 penetration Effects 0.000 description 2
- 230000010287 polarization Effects 0.000 description 2
- 239000010936 titanium Substances 0.000 description 2
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 238000003889 chemical engineering Methods 0.000 description 1
- 238000001514 detection method Methods 0.000 description 1
- 238000005530 etching Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 239000003208 petroleum Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000005215 recombination Methods 0.000 description 1
- 230000035939 shock Effects 0.000 description 1
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- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C12/00—Solid state diffusion of at least one non-metal element other than silicon and at least one metal element or silicon into metallic material surfaces
- C23C12/02—Diffusion in one step
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- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
Abstract
The invention belongs to the technical field of metal surface treatment, and relates to a high-performance low-temperature high-efficiency ion composite infiltration surface modification method for austenitic stainless steel, which can precipitate CrN aiming at high-temperature ion nitriding, reduce solid-solution chromium and reduce the corrosion resistance of austenitic stainless steel; and the diffusion speed of active atoms at low temperature is low, so that the nitriding efficiency is low. The method comprises the steps of processing and cutting original austenitic stainless steel into samples; polishing a sample, ultrasonically cleaning the sample in an organic solvent, and drying the sample; and putting the sample into a vacuum nitriding furnace, and adding TC4 wires around the sample to perform ion complexing treatment. The low-temperature ion composite permeation surface modification method avoids the formation of CrN and keeps the excellent corrosion resistance of austenitic stainless steel; and forming S phase and Ti phase on the surface of austenitic stainless steel2N phase, the surface hardness of the austenitic stainless steel is greatly improved; and meanwhile, the effect of improving the ion nitriding efficiency is obviously achieved.
Description
Technical Field
The invention belongs to the technical field of metal surface treatment, and particularly relates to a high-performance low-temperature high-efficiency ionic composite infiltration surface modification method for austenitic stainless steel.
Background
The austenitic stainless steel is widely applied to industries such as petroleum, chemical engineering, oceans, pharmacy, food and the like due to good corrosion resistance, but because the surface hardness is lower and the wear resistance is poorer, wear-resistant mechanical parts manufactured by the austenitic stainless steel usually fail due to early surface wear and are difficult to meet the use requirements, so the popularization and the application of the austenitic stainless steel are greatly limited.
The ion nitriding technology is a nitriding process which is widely applied in the current production, can obviously improve the surface hardness, the wear resistance, the fatigue resistance and the corrosion resistance of materials, and has the advantages of uniform infiltration layer, simple working procedure, small deformation of workpieces, no pollution and the like. However, in the prior art of the ion nitriding of austenitic stainless steel, when high-temperature ion nitriding (more than 450 ℃) is adopted, the nitriding efficiency is high, but the corrosion resistance of austenitic stainless steel is greatly influenced; the method for solving the problems comprises laser shock, pre-oxidation, metal composite infiltration and the like, and has higher promotion on the organization and the performance of an infiltrated layer, wherein the existing metal composite infiltration technology has higher use temperature, and has great influence on the corrosion resistance of the austenitic stainless steel. Therefore, how to adopt the method of low-temperature nitriding and low-temperature metal composite infiltration can achieve higher hardness and thicker effective hardened layer under the conditions of ensuring corrosion resistance and not influencing nitriding efficiency, and the invention aims to solve the problem.
Disclosure of Invention
The technical problem to be solved by the invention is as follows: based on the problems of high-temperature and low-temperature ion nitriding of austenitic stainless steel, the invention provides a high-performance low-temperature high-efficiency ion composite nitriding surface modification method of austenitic stainless steel.
The technical scheme adopted by the invention for solving the technical problems is as follows: a high-performance low-temperature high-efficiency ionic composite infiltration surface modification method for austenitic stainless steel comprises the following steps:
(1) the austenitic stainless steel in the original state is processed and cut into test pieces. 304 stainless steel is selected as the original state austenitic stainless steel, and the original state austenitic stainless steel is processed into a sample with the size of 10mm multiplied by 5mm by adopting wire cutting.
(2) And polishing the sample, and then ultrasonically cleaning and drying the sample in an organic solvent. The polishing treatment comprises the following steps: the sample is respectively polished by using 600# -2000 # SiC abrasive paper to a mirror surface, and the ultrasonic cleaning process in the organic solvent comprises the following steps: and soaking the sample in absolute ethyl alcohol, and ultrasonically cleaning for 10 min.
(3) And (3) putting the dried sample into a vacuum nitriding furnace, and adding TC4 wires around the surface of the sample to perform low-temperature ion composite infiltration treatment.
The adding mode is that 200 mg-400 mg TC4 wires are added around the surface of each gram of sample; subsequently, vacuumizing is carried out, hydrogen is introduced for sputtering cleaning, the furnace pressure is kept at 300Pa, and the sputtering cleaning time is 30min (the sputtering cleaning condition is that the gas pressure in the furnace is 300Pa, and the hydrogen flow is 500 ml/min); and introducing nitrogen after sputtering and cleaning, wherein the flow ratio of the nitrogen to the hydrogen is 1:3, the total flow of the nitrogen-hydrogen mixed gas is 700ml/min, and the working pressure is 470 Pa; the ion composite infiltration temperature is 400-450 ℃, and the nitriding time is 4-8 h.
Wherein the sample size is specified as 10X 5(mm), which can be scaled up. If the TC4 wire is less than 200mg/g, the addition of the TC4 has no influence on the sample and does not have the effect of metal infiltration. Above 400mg/g, the effective hardened layer thickness does not increase.
After low-temperature ion composite penetration treatment, surface performance test analysis is carried out, and the specific method comprises the following steps:
1) observing the microscopic structure of the section by adopting an optical metallographic microscope;
2) performing hardness test analysis by using a Vickers microhardness tester, and measuring the thickness of an effective hardening layer;
3) performing phase analysis by using an X-ray diffractometer;
4) and (4) carrying out corrosion resistance analysis by adopting an electrochemical workstation.
The invention has the beneficial effects that:
(1) the method selects the TC4 titanium wire as a metal infiltration material, combines ion nitriding, simultaneously performs low-temperature ion nitriding and metal infiltration, and obviously improves the hardness on the premise that the corrosion resistance of the raw material is not changed or even slightly improved after the two materials are cooperated, thereby achieving the effect that the corrosion resistance, the hardness and the like are simultaneously considered, and the corrosion resistance of the austenitic stainless steel is not reduced;
(2) after low-temperature nitriding and low-temperature metal infiltration treatment, S phase and trace high-hardness strengthening phase Ti are generated on the surface of the infiltrated layer2N, the surface hardness of the austenitic stainless steel is remarkably improved;
(3) can still have high nitriding efficiency at low temperature.
The invention provides a simple, convenient and efficient high-performance surface modification method for austenitic stainless steel.
The invention is further described below with reference to the accompanying drawings.
Drawings
FIG. 1 is a microstructure diagram of a carburized layer of 304 stainless steel after a conventional low-temperature ion nitriding treatment at 420 ℃/4h (i.e., comparative example 1);
FIG. 2 is a microstructure diagram of a carburized layer of 304 stainless steel after a conventional high temperature ion nitriding treatment at 520 ℃/4h (i.e., comparative example 2);
FIG. 3 is a microstructure diagram of a carburized layer of 304 stainless steel after 520 ℃/4h of high temperature ion complexing carburization (i.e., comparative example 3);
FIG. 4 is a microstructure diagram of a infiltrated layer of 304 stainless steel after 420 deg.C/4 h of low temperature ion-complexing infiltration (i.e., example 1);
FIG. 5 is a microstructure diagram of a infiltrated layer of 304 stainless steel after 420 deg.C/4 h of low temperature ion complexing infiltration (i.e., example 2);
FIG. 6 is a potentiodynamic polarization plot of 304 stainless steel under different process conditions (corresponding to comparative examples 2, 3, examples 1, 2);
FIG. 7 is a cross-sectional microhardness plot of 304 stainless steel under different process conditions (corresponding to comparative examples 1, 2, 3, examples 1, 2);
fig. 8 is a phase analysis diagram of 304 stainless steel under different processes (corresponding to comparative examples 1 and 3, examples 1 and 2).
Detailed Description
The invention will now be further illustrated by reference to specific examples, which are intended to be illustrative of the invention and are not intended to be a further limitation of the invention.
Example 1
(1) 304 stainless steel was machined and cut into specimens having dimensions of 10mm by 5 mm.
(2) And sequentially and respectively polishing the test samples to a mirror surface by using 600# to 2000# SiC abrasive paper, soaking the test samples in absolute ethyl alcohol for ultrasonic cleaning for 10min, thereby removing oil stains and other impurities on the surface and drying the test samples for later use.
(3) Putting the sample into a vacuum nitriding furnace, and adding TC4 wires around the surface of the sample, wherein the method specifically comprises the following steps: 200mg is added around the surface of each gram of sample, and sputtering cleaning is carried out for 30 min.
(4) After the sputtering cleaning is finished, low-temperature ion nitriding is carried out under the given process parameter of 420 ℃/4 h. The model of the vacuum nitriding furnace is LDMC-8CL, the nitrogen-hydrogen flow ratio is 1:3, and the total flow of nitrogen-hydrogen mixed gas is 700 ml/min;
(5) and taking out the sample after the ion composite infiltration treatment, and observing the section microstructure by adopting an optical metallographic microscope, wherein the infiltrated layer microstructure is shown in figure 4.
(6) Hardness analysis was performed using a Vickers microhardness tester model HXD-1000TMC, and effective hardened layer thickness analysis was performed using original.
(7) Phase analysis was performed using an X-ray diffractometer model D/max-2500.
(8) Corrosion resistance analysis was performed using the CS350 electrochemical workstation.
Example 2
(1) 304 stainless steel was machined and cut into specimens having dimensions of 10mm by 5 mm.
(2) And sequentially and respectively polishing the test samples to a mirror surface by using 600# to 2000# SiC abrasive paper, soaking the test samples in absolute ethyl alcohol for ultrasonic cleaning for 10min, thereby removing oil stains and other impurities on the surface and drying the test samples for later use.
(3) Putting the sample into a vacuum nitriding furnace, and adding TC4 wires around the surface of the sample, wherein the method specifically comprises the following steps: 250mg is added around the surface of each gram of sample, and the sample is firstly subjected to sputtering cleaning for 30 min.
(4) After the sputtering cleaning is finished, low-temperature ion nitriding is carried out under the given process parameter of 420 ℃/4 h. The model of the vacuum nitriding furnace is LDMC-8CL, the nitrogen-hydrogen flow ratio is 1:3, and the total flow of nitrogen-hydrogen mixed gas is 700 ml/min;
(5) and taking out the sample after the ion composite infiltration treatment, and observing the section microstructure by adopting an optical metallographic microscope, wherein the infiltrated layer microstructure is shown in a figure 5.
(6) Hardness analysis was performed using a Vickers microhardness tester model HXD-1000TMC, and effective hardened layer depth analysis was performed using original.
(7) Phase analysis was performed using an X-ray diffractometer model D/max-2500.
(8) Corrosion resistance analysis was performed using the CS350 electrochemical workstation.
Comparative example 1
(1) 304 stainless steel was machined and cut into specimens having dimensions of 10mm by 5 mm.
(2) And sequentially and respectively polishing the test samples to a mirror surface by using 600# to 2000# SiC abrasive paper, soaking the test samples in absolute ethyl alcohol for ultrasonic cleaning for 10min, thereby removing oil stains and other impurities on the surface and drying the test samples for later use.
(3) The sample is put into a vacuum nitriding furnace and is firstly subjected to sputtering cleaning for 30 min.
(4) After the sputtering cleaning is finished, ion nitriding is carried out under the given process parameter of 420 ℃/4 h.
(5) And taking out the sample subjected to the ion nitriding treatment, observing the section microstructure by using an optical metallographic microscope, wherein the permeated layer microstructure is shown in figure 1.
(6) Hardness analysis was performed using a Vickers microhardness tester model HXD-1000TMC, and effective hardened layer depth analysis was performed using original.
(7) Phase analysis was performed using an X-ray diffractometer model D/max-2500.
Comparative example 2
(1) 304 stainless steel was machined and cut into specimens having dimensions of 10mm by 5 mm.
(2) And sequentially and respectively polishing the test samples to a mirror surface by using 600# to 2000# SiC abrasive paper, soaking the test samples in absolute ethyl alcohol for ultrasonic cleaning for 10min, thereby removing oil stains and other impurities on the surface and drying the test samples for later use.
(3) The sample is put into a vacuum nitriding furnace and is firstly subjected to sputtering cleaning for 30 min.
(4) After the sputtering cleaning is finished, ion nitriding is carried out under the given process parameter of 520 ℃/4 h.
(5) And taking out the sample subjected to the ion nitriding treatment, observing the section microstructure by using an optical metallographic microscope, wherein the permeated layer microstructure is shown in figure 2.
(6) Hardness analysis was performed using a Vickers microhardness tester model HXD-1000TMC, and effective hardened layer depth analysis was performed using original.
(7) Corrosion resistance analysis was performed using the CS350 electrochemical workstation.
Comparative example 3
(1) 304 stainless steel was machined and cut into specimens having dimensions of 10mm by 5 mm.
(2) And sequentially and respectively polishing the test samples to a mirror surface by using 600# to 2000# SiC abrasive paper, soaking the test samples in absolute ethyl alcohol for ultrasonic cleaning for 10min, thereby removing oil stains and other impurities on the surface and drying the test samples for later use.
(3) Putting the sample into a vacuum nitriding furnace, and adding TC4 wires around the surface of the sample, wherein the method specifically comprises the following steps: 250mg is added around the surface of each gram of sample, and the sample is firstly subjected to sputtering cleaning for 30 min.
(4) After the sputtering cleaning is finished, ion nitriding is carried out under the given process parameter of 520 ℃/4 h.
(5) And taking out the sample after the ion composite infiltration treatment, and observing the section microstructure by adopting an optical metallographic microscope, wherein the infiltrated layer microstructure is shown in figure 3.
(6) Hardness analysis was performed using a Vickers microhardness tester model HXD-1000TMC, and effective hardened layer depth analysis was performed using original.
(7) Phase analysis was performed using an X-ray diffractometer model D/max-2500.
(8) Corrosion resistance analysis was performed using the CS350 electrochemical workstation.
FIG. 6 is a potentiodynamic polarization curve diagram of examples 1 and 2 and comparative examples 2 and 3, and it can be seen that 304 stainless steel treated by high-temperature conventional ion nitriding has a greatly reduced self-corrosion potential compared with a matrix under the same time condition; compared with the high-temperature ion composite infiltration treatment, the self-corrosion potential of the 304 stainless steel subjected to the low-temperature ion composite infiltration treatment is greatly improved; and adding TC under the same temperature and time condition4304 stainless steel with no addition of TC4The self-corrosion potential is improved. Therefore, under the same conditions, the high-temperature ion nitriding has greatly reduced corrosion resistance compared with the low-temperature ion nitriding; hardly influences the corrosion resistance of the 304 stainless steel under the condition of low temperature, and adds TC under the condition of the same temperature and time4Compared with the treatment without addition, the ion composite infiltration treatment improves the corrosion resistance. .
FIG. 7 is a cross-sectional microhardness analysis chart of examples 1 and 2 and comparative examples 1, 2 and 3, and in combination with Table 1, it can be seen that the conventional high temperature ion nitriding surface hardness and the effective hardened layer thickness are both improved, but the self-etching potential is greatly reduced; under the condition of the same temperature and time, the surface hardness of the 304 stainless steel after low-temperature ion composite infiltration treatment is greatly improved to the maximum extent by 224HV0.025Is lifted to 1251HV0.025The improvement is 5.6 times; meanwhile, as can be seen from the figure, after the low-temperature ion composite penetration treatment is carried out on the 304 stainless steel, the surface hardness is improved by nearly 200HV compared with that of the conventional ion nitriding treatment0.025And the thickness of the effective hardening layer can be increased to about 53 μm from 24 μm of the conventional ion nitriding at most, which is increased by more than 2 times. Therefore, the high-temperature ion nitriding can improve the surface hardness and the effective hardened layer depth of the 304 stainless steel, but the corrosion resistance is greatly reduced; the low-temperature ion composite nitriding treatment has better nitriding effect than the conventional ion nitriding, and can greatly improve the surface hardness of 304 stainless steel and obviously improve the thickness of an effective hardening layer on the premise of not reducing the corrosion resistance.
FIG. 8 is a phase analysis chart of examples 1 and 2 and comparative examples 1 and 3, and it can be seen that in comparative example 3 after the high temperature ion-recombination, a large amount of CrN phase is formed, the chromium content of 304 stainless steel is reduced, the corrosion resistance is reduced, and the corrosion resistance is basically unchanged without CrN precipitation due to the low temperature ion-nitriding, which is consistent with the corrosion resistance comparison in FIG. 6; compared with the traditional ion nitriding treatment, the two examples after the low-temperature ion composite nitriding treatment have the advantages that S phase and high-hardness strengthening phase Ti are formed on the surface of the diffusion layer2N, has the effect of surface double strengthening, further confirming the reliability of the hardness change in fig. 6.
Table 1 shows the detection data of the modified surfaces of examples 1 and 2 and comparative examples 1 and 3, and it can be seen from table 1 that the surface hardness of 304 stainless steel can be greatly improved and the effective hardened layer thickness can be significantly increased without reducing the corrosion resistance in the low temperature ion composite cementation process compared with the conventional ion nitriding and high temperature ion composite cementation.
TABLE 1
In light of the foregoing description of the preferred embodiment of the present invention, many modifications and variations will be apparent to those skilled in the art without departing from the spirit and scope of the invention. The technical scope of the present invention is not limited to the content of the specification, and must be determined according to the scope of the claims.
Claims (6)
1. A high-performance low-temperature high-efficiency ionic composite permeation surface modification method for austenitic stainless steel is characterized by comprising the following steps: the method comprises the following process steps:
(1) processing and cutting original state austenitic stainless steel into samples;
(2) polishing a sample, then ultrasonically cleaning the sample in an organic solvent and drying the sample;
(3) putting the dried sample into a vacuum nitriding furnace, adding TC4 wires on the surface of the sample, and performing low-temperature ion composite infiltration treatment at the temperature of 400-450 ℃;
(4) and taking out the sample after the composite infiltration treatment, and carrying out surface performance test analysis.
2. The austenitic stainless steel high-performance low-temperature high-efficiency ion composite cementation surface modification method according to claim 1, characterized in that: the original state austenitic stainless steel in the step (1) is 304 austenitic stainless steel.
3. The austenitic stainless steel high-performance low-temperature high-efficiency ion composite cementation surface modification method according to claim 1, characterized in that: the polishing treatment in the step (2) is as follows: the sample is polished by using 600# -2000 # SiC abrasive paper to a mirror surface, and the ultrasonic cleaning process in an organic solvent comprises the following steps: and soaking the sample in absolute ethyl alcohol, and ultrasonically cleaning for 10 min.
4. The austenitic stainless steel high-performance low-temperature high-efficiency ion composite cementation surface modification method according to claim 1, characterized in that: the model of the vacuum nitriding furnace in the step (3) is LDMC-8CL, and the ultimate vacuum degree is 6.7 Pa; the working current is 3A; the working voltage is 650-700V; the nitrogen-hydrogen ratio is 1:3, and the total flow of the nitrogen-hydrogen mixed gas is 700 ml/min; the working air pressure is 470 Pa.
5. The austenitic stainless steel high-performance low-temperature high-efficiency ion composite cementation surface modification method according to claim 1, characterized in that: the specific method in the step (3) is as follows: the addition amount of the TC4 yarn is 200 mg-400 mg added in each gram of sample.
6. The austenitic stainless steel high-performance low-temperature high-efficiency ion composite cementation surface modification method according to claim 1, characterized in that: the nitriding time in the step (3) is 4-8 h.
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| CN115074633A (en) * | 2022-07-05 | 2022-09-20 | 太原理工大学 | Method for inhibiting precipitation phase of super austenitic stainless steel |
| CN116219443A (en) * | 2022-12-29 | 2023-06-06 | 北京卫星制造厂有限公司 | Cooperative control method for high hardness and low brittleness of ultra-high strength stainless steel surface layer |
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| CN115074633B (en) * | 2022-07-05 | 2023-05-09 | 太原理工大学 | Method for inhibiting precipitation phase of super austenitic stainless steel |
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