CN112680668B - Martensite precipitation hardening stainless steel and preparation method thereof - Google Patents
Martensite precipitation hardening stainless steel and preparation method thereof Download PDFInfo
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- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract description 30
- 239000010935 stainless steel Substances 0.000 title claims abstract description 26
- 229910000734 martensite Inorganic materials 0.000 title claims abstract description 22
- 238000004881 precipitation hardening Methods 0.000 title claims abstract description 15
- 238000002360 preparation method Methods 0.000 title claims abstract description 14
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 32
- 239000010959 steel Substances 0.000 claims abstract description 32
- 239000000126 substance Substances 0.000 claims abstract description 6
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 16
- 238000005242 forging Methods 0.000 claims description 16
- 238000001816 cooling Methods 0.000 claims description 13
- 239000000243 solution Substances 0.000 claims description 13
- 238000003723 Smelting Methods 0.000 claims description 12
- 230000032683 aging Effects 0.000 claims description 10
- 239000002245 particle Substances 0.000 claims description 10
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims description 9
- 239000011259 mixed solution Substances 0.000 claims description 9
- 230000006698 induction Effects 0.000 claims description 8
- 239000007788 liquid Substances 0.000 claims description 8
- 229910052757 nitrogen Inorganic materials 0.000 claims description 8
- 238000003756 stirring Methods 0.000 claims description 8
- 239000010425 asbestos Substances 0.000 claims description 7
- 229910052895 riebeckite Inorganic materials 0.000 claims description 7
- 238000010583 slow cooling Methods 0.000 claims description 7
- 238000001556 precipitation Methods 0.000 claims description 6
- 239000011248 coating agent Substances 0.000 claims description 4
- 238000000576 coating method Methods 0.000 claims description 4
- 239000002994 raw material Substances 0.000 claims description 4
- 239000004576 sand Substances 0.000 claims description 3
- 238000007599 discharging Methods 0.000 claims description 2
- 239000006104 solid solution Substances 0.000 claims description 2
- 230000007797 corrosion Effects 0.000 abstract description 11
- 238000005260 corrosion Methods 0.000 abstract description 11
- 229910045601 alloy Inorganic materials 0.000 abstract description 3
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- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- VEXZGXHMUGYJMC-UHFFFAOYSA-N Hydrochloric acid Chemical compound Cl VEXZGXHMUGYJMC-UHFFFAOYSA-N 0.000 description 2
- 229910052799 carbon Inorganic materials 0.000 description 2
- 238000000227 grinding Methods 0.000 description 2
- 238000010907 mechanical stirring Methods 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910000628 Ferrovanadium Inorganic materials 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 239000011651 chromium Substances 0.000 description 1
- UPHIPHFJVNKLMR-UHFFFAOYSA-N chromium iron Chemical compound [Cr].[Fe] UPHIPHFJVNKLMR-UHFFFAOYSA-N 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 150000002500 ions Chemical class 0.000 description 1
- 229910001337 iron nitride Inorganic materials 0.000 description 1
- PNXOJQQRXBVKEX-UHFFFAOYSA-N iron vanadium Chemical compound [V].[Fe] PNXOJQQRXBVKEX-UHFFFAOYSA-N 0.000 description 1
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- OXNIZHLAWKMVMX-UHFFFAOYSA-N picric acid Chemical compound OC1=C([N+]([O-])=O)C=C([N+]([O-])=O)C=C1[N+]([O-])=O OXNIZHLAWKMVMX-UHFFFAOYSA-N 0.000 description 1
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Abstract
The invention belongs to the technical field of metallurgy, and particularly relates to ultrahigh-strength high-hardness martensitic precipitation hardening stainless steel and a preparation method thereof. The martensite precipitation hardening stainless steel is 1Cr15Co14Mo5VN, and the steel comprises the following chemical components in percentage by mass: cr: 12.8 ‒ 15.2.15.2, Co: 11.0 ‒ 15.0.0, Mo: 4.0 ‒ 5.5.5, V: 0.2 ‒ 0.8.8, C: 0.13 ‒ 0.19, N: 0.02 ‒ 0.10.10, Ti: 0.02 ‒ 0.10.10, Nb: 0.02 ‒ 0.10, Ta: 0.02 ‒ 0.10, Hf: 0.02-0.10; mn: less than or equal to 0.20, P: less than or equal to 0.02, S: 0.01 or less, Si: less than or equal to 0.20 percent, less than or equal to 0.005 percent of O and the balance of Fe. The alloy prepared by the preparation method provided by the invention has the tensile strength of more than 2000MPa, the hardness HRC of more than 52, high strength, high hardness, higher toughness and good high-temperature corrosion resistance, and can be applied to parts such as bearing steel, gear steel, ball screw pair and the like which bear corrosion resistance at high temperature in the fields of aviation, aerospace, nuclear technology, ships and the like. The preparation method is simple, low in production cost and suitable for industrial production.
Description
Technical Field
The invention belongs to the technical field of metallurgy, and particularly relates to ultrahigh-strength high-hardness martensitic precipitation hardening stainless steel and a preparation method thereof.
Background
Stainless steel accounts for a large proportion of materials for mechanical parts or electronic equipment, the requirement for a new high-quality and high-performance stainless steel material is extremely urgent in the transformation and upgrading process of the mechanical part or electronic equipment industry, and the mainstream mechanical part or electronic equipment factory also puts forward the requirement for developing the high-quality stainless steel for the mechanical parts or the electronic equipment. Stainless steel materials for mechanical parts or electronic devices mainly include austenitic stainless steels 304L, 316L, 317L, martensitic stainless steels 20Cr13, 30Cr13, 60Cr13 with high carbon content, and the like. Taking the double-joint rongeur made of martensitic stainless steel 3Cr13Mo as an example, the hardness of the double-joint rongeur can reach more than HRC50, the high strength and hardness can avoid the deformation of instruments in the operation process, but the toughness and the corrosion resistance of the material are far lower than those of austenitic stainless steel such as 304, the precipitation of ions caused by insufficient corrosion resistance causes pollution risk to human tissues, the fracture and breakage risk of the rongeur caused by insufficient toughness easily causes harm in the operation. Martensitic stainless steels have high hardness and high wear resistance, but have low corrosion resistance and poor toughness.
The martensite precipitation hardening stainless steel has high strength, high hardness, high toughness and good high-temperature corrosion resistance, and is applied to bearing steel, gear steel, ball screw pair and other parts which bear corrosion resistance at high temperature in the fields of aviation, aerospace, nuclear technology, ships and warships and the like. The steel adopts the superimposed strengthening modes of low-carbon martensite phase transformation strengthening, aging strengthening, secondary precipitation hardening and the like, so that the steel has the comprehensive properties of high strength, high hardness and excellent performance. Patent CN106119736A discloses a preparation method of 1Cr14Co13Mo5 of maraging stainless steel, wherein the tensile strength reaches 1900MPa, and the hardness reaches HRC 50.
In the face of the development of high speed and high precision of components under the high-temperature corrosion-resistant condition, the ultrahigh strength, ultrahigh hardness and good toughness are required to be met under the high-temperature and corrosion-resistant conditions. Therefore, the strength, the hardness and the toughness of the martensitic precipitation hardening stainless steel are comprehensively improved, and the method has important theoretical significance and application value.
Disclosure of Invention
In view of the problems in the prior art, the invention aims to provide the martensite precipitation hardening stainless steel with ultrahigh strength, high hardness and good toughness and the preparation method thereof, and the alloy prepared by the preparation method provided by the invention has the tensile strength of more than 2000MPa and the hardness HRC of more than 52.
In order to achieve the purpose, the invention adopts the following technical scheme.
The martensitic precipitation hardening stainless steel is 1Cr15Co14Mo5VN, and the chemical components of the steel in percentage by mass are as follows: cr: 12.8-15.2, Co: 11.0-15.0, Mo: 4.0-5.5, V: 0.2-0.8, C: 0.13-0.19, N: 0.02-0.10, Ti: 0.02-0.10, Nb: 0.02-0.10, Ta: 0.02-0.10, Hf: 0.02-0.10; mn: less than or equal to 0.20, P: less than or equal to 0.02, S: 0.01 or less, Si: less than or equal to 0.20 percent, less than or equal to 0.005 percent of O and the balance of Fe.
Preferably, the martensite precipitation hardening stainless steel comprises the following chemical components in percentage by mass: cr: 13.0-15.0, Co: 13-14, Mo: 4.0-5.5, V: 0.3-0.6, C: 0.13-0.19, Ti: 0.02-0.10, Nb: 0.02-0.10, Ta: 0.02-0.10, Hf: 0.02-0.10; mn: 0.20 or less, N: 0.03 to 0.08, P: less than or equal to 0.02, S: 0.01 or less, Si: less than or equal to 0.20 percent, less than or equal to 0.005 percent of O and the balance of Fe.
The preparation method of the martensite precipitation hardening stainless steel specifically comprises the following steps.
Step 1, putting the raw materials into a vacuum induction furnace for smelting, adding high-melting-point carbide at the later stage of smelting, and uniformly dispersing and distributing the high-melting-point carbide through electromagnetic stirring or physical stirring.
Step 2, open forging the obtained steel ingot at 1100-1200 ℃, wherein the finish forging temperature is 850-950 ℃; keeping the temperature of the forge piece at 850-900 ℃ for 2h, cooling the forge piece to 500 ℃, discharging the forge piece, and covering asbestos or burying sand for slow cooling.
And 3, carrying out solution treatment on the forged piece at 1000-1150 ℃ for 1-2 h, and then carrying out oil cooling.
And 4, carrying out cryogenic treatment.
And 5, aging treatment is carried out twice at 450-600 ℃, and the heat preservation is carried out for 2-3 h each time.
Further, the carbide in the step 1 is one or more of TiC, NbC, TaC and HfC.
Furthermore, the addition amount of the carbide in the step 1 is 0.02-0.10% of the total mass of the raw materials, and the grain diameter of the carbide is 0.5-5 μm.
Preferably, the solution treatment temperature in the step 3 is 1050-1100 ℃, and the solution treatment time is 1-1.5 h.
Preferably, the oil-cooled cooling rate in step 3 is cooled to room temperature within 2 min.
In the step 4, the subzero treatment is carried out on the mixed solution of liquid nitrogen and alcohol at the temperature of minus 80 ℃ to minus 140 ℃, so that the stainless steel is cooled to the temperature of minus 80 ℃ to minus 130 ℃ within 5min, and the temperature is kept for 0.5 to 1 h.
Preferably, the aging treatment temperature in the step 5 is 500-550 ℃.
Compared with the prior art, the invention has the following beneficial effects.
The preparation method provided by the invention introduces the dispersed and distributed high-melting-point carbide in the later stage of smelting, can refine austenite grains of an as-cast sample, and can continuously refine the structure in the forging and heat treatment processes; 2, the deep cooling treatment and the aging annealing process are matched to refine the structure, reduce the size of precipitated phases, improve the number of the precipitated phases and comprehensively improve the strength, the hardness and the toughness.
The 1Cr15Co14Mo5VN prepared by the preparation method provided by the invention has the tensile strength of more than 2000MPa, the hardness HRC of more than 52, high strength, high hardness and high toughness, and good high-temperature corrosion resistance, and can be applied to parts such as bearing steel, gear steel, ball screw pair and the like which bear corrosion resistance at high temperature in the fields of aviation, aerospace, nuclear technology, ships and the like. The preparation method is simple, low in production cost and suitable for industrial production.
Drawings
FIG. 1 shows the microstructure morphology of the solution cryogenic treatment after forging of component A in the first embodiment of the present invention.
FIG. 2 shows the metallographic structure of component B after solution cryogenic treatment +540 ℃ aging twice in the first embodiment of the present invention.
FIG. 3 is a graph showing the effect of different solid solution temperatures of component C on the tensile strength of a sample in example two of the present invention.
FIG. 4 is a graph showing the effect of different cryogenic temperatures of component D on the tensile strength of a sample in the third example of the present invention.
FIG. 5 shows the effect of different aging temperatures of component G on the hardness of the test specimens in the fourth example of the present invention.
FIG. 6 shows the impact of different aging temperatures of component H on the impact toughness of test specimens in example five of the present invention.
FIG. 7 shows the effect of different aging temperatures of component I on the fracture toughness of the test specimens in the sixth example of the invention.
Detailed Description
The present invention will be described in further detail with reference to the following specific embodiments and the accompanying drawings. It should be understood that the specific embodiments described herein are merely illustrative of the invention and are not intended to limit the invention. The following examples are only for illustrating the technical idea and features of the present invention, and are intended to enable those skilled in the art to understand the contents of the present invention and implement the present invention, and not to limit the protection scope of the present invention. All equivalent changes and modifications made according to the spirit of the present invention should be covered within the protection scope of the present invention.
According to the invention, metallographic samples under various heat treatment systems are ground and polished, then corroded by adopting a mixed solution of picric acid, hydrochloric acid and alcohol, and the grain structure is observed by using an Axio Scope A1 metallographic optical microscope.
In the mechanical property test, the tensile sample is a GB/T228-2002 standard sample, the length of a gauge length of the tensile sample is 25mm, and the diameter of the tensile sample is 5 mm. The hardness of the martensite precipitation hardening stainless steel after heat treatment is tested by a Rockwell hardness tester, the sample is subjected to coarse grinding and fine grinding, the upper surface and the lower surface are parallel, the roughness is higher than 0.8, at least three points are measured on each sample, and the average value is taken.
The first embodiment.
The steel ingot is prepared by selecting intermediate alloys such as pure Fe, electrolytic Co, Mo, high-purity ferrovanadium, chromium iron nitride and the like, setting steel components according to the table 1, and smelting a 25kg steel ingot by adopting an ultrahigh vacuum induction furnace. 0.02% of NbC with the size of 0.5-2 μm and 0.10% of HfC particles with the size of 0.5-2 μm are added in the smelting process, and are uniformly dispersed and distributed by mechanical stirring. The steel ingot is forged into a bar with the diameter of 50mm at the beginning and the end forging temperature of 1150 ℃ and the temperature of 900 ℃, the forged piece is preserved for 2h at the temperature of 900 ℃ after being forged, then the asbestos is coated and slowly cooled, the forged piece is preserved for 1h after being treated for solution at the temperature of 1100 ℃, then the forged piece is preserved for 1h in a mixed solution of liquid nitrogen and alcohol (minus 130 ℃), then the forged piece is preserved for 2h at the temperature of 540 ℃, the steps are carried out twice continuously, and the final tensile property is shown in table 2.
Table 1. table of chemical compositions of the examples stainless steels.
| Composition (I) | Cr | Co | Mo | C | V | N | O | Mn | S | P | Fe |
| A | 13.39 | 12.91 | 4.85 | 0.135 | 0.55 | 0.03 | 0.002 | 0.05 | 0.014 | 0.010 | Balance of |
| B | 13.55 | 13.14 | 4.15 | 0.159 | 0.47 | 0.05 | 0.004 | 0.15 | 0.005 | 0.014 | Balance of |
| C | 13.86 | 13.59 | 4.64 | 0.146 | 0.63 | 0.04 | 0.005 | 0.10 | 0.013 | 0.015 | Balance of |
| D | 14.17 | 13.88 | 5.19 | 0.175 | 0.39 | 0.03 | 0.003 | 0.12 | 0.007 | 0.018 | Balance of |
| E | 14.69 | 13.97 | 5.36 | 0.190 | 0.52 | 0.05 | 0.002 | 0.08 | 0.005 | 0.017 | Balance of |
| F | 14.91 | 14.05 | 4.98 | 0.184 | 0.67 | 0.06 | 0.001 | 0.04 | 0.006 | 0.019 | Balance of |
| G | 14.28 | 13.75 | 4.83 | 0.169 | 0.59 | 0.05 | 0.002 | 0.09 | 0.004 | 0.012 | Balance of |
| H | 13.89 | 13.51 | 4.93 | 0.151 | 0.48 | 0.04 | 0.004 | 0.06 | 0.008 | 0.011 | Balance of |
| I | 14.01 | 13.57 | 5.05 | 0.180 | 0.51 | 0.03 | 0.005 | 0.07 | 0.009 | 0.013 | Balance of |
TABLE 2 tensile properties, hardness, grain size, fracture toughness and impact toughness for example one.
Example two.
The steel composition was set as in table 1 and 25kg steel ingots were melted in an ultra-high vacuum induction furnace. 0.02 percent of 0.5-2 mu m TiC, 0.02 percent of 0.5-2 mu m TaC particles and 0.04 percent of 1-5 mu m HfC particles are added in the smelting process, and the mixture is uniformly dispersed and distributed by utilizing electromagnetic stirring. The steel ingot is forged into a bar with the diameter of 50mm at the temperature of 1200 ℃ for open forging and the finish forging temperature of 950 ℃, the forged piece is subjected to heat preservation at 900 ℃ for 2h and then is subjected to asbestos coating and slow cooling, the forged piece is subjected to solution treatment at 1050 ℃ for 1h and then is subjected to oil cooling, then the temperature of the forged piece is preserved for 1h in a mixed solution of liquid nitrogen and alcohol (-80 ℃), the temperature of the forged piece is preserved for 2h at 550 ℃, the steps are carried out twice continuously, and the final tensile property is shown in table 3.
TABLE 3 tensile properties, hardness, grain size, fracture toughness and impact toughness for example two.
Example three.
The steel composition was set as in table 1 and 25kg steel ingots were melted in an ultra-high vacuum induction furnace. 0.05 percent of NbC with the size of 0.5-5 mu m and 0.08 percent of TaC particles with the size of 0.5-2 mu m are added in the smelting process, and are uniformly dispersed and distributed by utilizing electromagnetic stirring. The steel ingot is forged into a bar with the diameter of 50mm at the beginning forging temperature of 1100 ℃ and the finish forging temperature of 850 ℃, the forged piece is subjected to heat preservation at 850 ℃ for 2h and then sand burying and slow cooling, the forged piece is subjected to solution treatment at 1080 ℃ for 1.0h and then oil cooling, then the temperature of the forged piece is preserved for 0.5h in a mixed solution of liquid nitrogen and alcohol (-80 ℃), and then the temperature is preserved for 3h at 500 ℃ for two times. The final tensile properties and hardness are shown in Table 4.
TABLE 4 tensile properties, hardness, grain size, fracture toughness and impact toughness for example three.
Example four.
The steel composition was set as in table 1 and 25kg steel ingots were melted in an ultra-high vacuum induction furnace. 0.10 percent of NbC with the size of 0.5-5 mu m and 0.02 percent of HfC particles with the size of 0.5-2 mu m are added in the smelting process, and the mixture is uniformly dispersed and distributed by utilizing electromagnetic stirring. The steel ingot is forged into a bar with the diameter of 50mm at the temperature of 1180 ℃ in a beginning forging mode and the finish forging temperature of 900 ℃, the forged piece is subjected to heat preservation at 900 ℃ for 2 hours after being subjected to asbestos coating and slow cooling, the forged piece is subjected to solution treatment at 1100 ℃ for 1.5 hours and then subjected to oil cooling, the temperature of the forged piece is preserved for 0.5 hour in a liquid nitrogen and alcohol mixed solution (-130 ℃), and then the temperature of the forged piece is preserved for 2 hours at 540 ℃, and the steps are carried out twice continuously. The final tensile properties and hardness are shown in Table 5.
TABLE 5 tensile properties, hardness, grain size, fracture toughness and impact toughness for example four.
Example five.
The steel composition was set as in table 1 and 25kg steel ingots were melted in an ultra-high vacuum induction furnace. 0.10 percent of NbC particles with the size of 0.5-5 mu m are added in the smelting process, and the NbC particles are uniformly dispersed and distributed by mechanical stirring. The steel ingot is forged into a bar with the diameter of 80mm at the temperature of 1150 ℃ and the finish forging temperature of 850 ℃, the forged piece is subjected to heat preservation at 950 ℃ for 2h and then is coated with asbestos for slow cooling, the forged piece is subjected to solution treatment at 1100 ℃ for 2h and then is subjected to oil cooling, and then is subjected to heat preservation in a mixed solution of liquid nitrogen and alcohol (-130 ℃) for 2h and then is subjected to heat preservation at 540 ℃ for 2h twice continuously. The final tensile properties and hardness are shown in Table 6.
TABLE 6 tensile properties, hardness, grain size, fracture toughness and impact toughness for example four.
Example six.
The steel composition was set as in table 1 and 25kg steel ingots were melted in an ultra-high vacuum induction furnace. 0.10 percent of TaC particles with the size of 0.5-5 mu m and 0.05 percent of HfC particles with the size of 0.5-5 mu m are added in the smelting process, and are uniformly dispersed and distributed by utilizing electromagnetic stirring. The steel ingot is forged into a bar with the diameter of 60mm at the temperature of 1180 ℃ in a beginning forging mode and the finish forging temperature of 880 ℃, the forged piece is subjected to heat preservation at 980 ℃ for 1h and then is subjected to asbestos coating and slow cooling, the forged piece is subjected to solution treatment at 1180 ℃ for 1h and then is subjected to oil cooling, then the temperature of the forged piece is preserved for 1.5h in a mixed solution of liquid nitrogen and alcohol (-110 ℃), and then the temperature of the forged piece is preserved for 2h at 550 ℃ for two times. The final tensile properties and hardness are shown in Table 7.
TABLE 7 tensile properties, hardness, grain size, fracture toughness and impact toughness for example four.
Claims (6)
1. The martensitic precipitation hardening stainless steel is characterized by being 1Cr15Co14Mo5VN, and comprising the following chemical components in percentage by mass: cr: 12.8 ‒ 15.2.15.2, Co: 11.0 ‒ 15.0.0, Mo: 4.0 ‒ 5.5.5, V: 0.2 ‒ 0.8.8, C: 0.13 ‒ 0.19, N: 0.02 ‒ 0.10.10, Ti: 0.02 ‒ 0.10.10, Nb: 0.02 ‒ 0.10, Ta: 0.02 ‒ 0.10, Hf: 0.02-0.10; mn: less than or equal to 0.20, P: less than or equal to 0.02, S: 0.01 or less, Si: less than or equal to 0.20 percent, less than or equal to 0.005 percent of O and the balance of Fe;
the preparation method of the martensite precipitation hardening stainless steel specifically comprises the following steps:
step 1, putting the raw materials into a vacuum induction furnace for smelting, adding high-melting-point carbide at the later stage of smelting, and uniformly dispersing and distributing the carbide through electromagnetic stirring or physical stirring, wherein the addition amount of the carbide is 0.02 percent ‒ 0.10.10 percent of the total mass of the raw materials, and the particle size of the carbide is 0.5-5 mu m;
step 2, open forging the obtained steel ingot at 1100-1200 ℃, wherein the finish forging temperature is 850-950 ℃; keeping the temperature of the forge piece at 850-900 ℃ for 2h, cooling the forge piece to 500 ℃, discharging the forge piece, and coating asbestos or burying sand for slow cooling;
step 3, performing solid solution treatment on the forged piece at the temperature of 1000-1150 ℃ for 1-2 h, and performing oil cooling;
step 4, carrying out cryogenic treatment: carrying out cryogenic treatment on the mixed solution of liquid nitrogen and alcohol at the temperature of between 80 ℃ below zero and 140 ℃ below zero, cooling the stainless steel to the temperature of between ‒ 80 ℃ and ‒ 130 ℃ within 5min, and keeping the temperature for 0.5 ‒ 1 h;
and 5, aging treatment is carried out twice at 450-600 ℃, and the temperature is kept for 2-3 h each time.
2. The martensitic precipitation hardened stainless steel according to claim 1, wherein said steel comprises the following chemical components in percentage by mass: cr: 13.0 ‒ 15.0.0, Co: 13 ‒ 14, Mo: 4.0 ‒ 5.5.5, V: 0.3-0.6, C: 0.13 ‒ 0.19, Ti: 0.02 ‒ 0.10.10, Nb: 0.02 ‒ 0.10, Ta: 0.02 ‒ 0.10, Hf: 0.02-0.10; mn: 0.20 or less, N: 0.03 to 0.08, P: less than or equal to 0.02, S: 0.01 or less, Si: less than or equal to 0.20 percent, less than or equal to 0.005 percent of O and the balance of Fe.
3. The martensitic precipitation hardened stainless steel of claim 1, wherein the carbide in step 1 is one or more of TiC, NbC, TaC, and HfC in combination.
4. The martensitic precipitation hardened stainless steel according to claim 1, wherein the solution treatment temperature in step 3 is 1050 ℃ to 1100 ℃ and the solution treatment time is 1h to 1.5 h.
5. The martensitic precipitation hardened stainless steel according to claim 1, wherein said oil-cooled cooling rate in step 3 is cooled to room temperature within 2 min.
6. The martensitic precipitation hardened stainless steel of claim 1, wherein said aging temperature in step 5 is in the range of 500 ℃ to 550 ℃.
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| CN106119736B (en) * | 2016-05-26 | 2018-07-27 | 中国科学院金属研究所 | A kind of martensite aged stainless steel |
| CN106086631B (en) * | 2016-08-23 | 2018-05-01 | 钢铁研究总院 | High nitrogen martensite stainless bearing steel of high-hardness, wearable and preparation method thereof |
| CN110358983A (en) * | 2019-07-04 | 2019-10-22 | 中国科学院金属研究所 | A kind of precipitation hardening of martensitic stainless steel and preparation method thereof |
| CN111519113B (en) * | 2020-05-21 | 2021-10-29 | 北京科技大学 | High-strength stainless steel powder for electronic products and preparation process |
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