CN114214567B - Ni 3 Al intermetallic compound precipitation-strengthened high-temperature bearing steel and preparation method thereof - Google Patents

Ni 3 Al intermetallic compound precipitation-strengthened high-temperature bearing steel and preparation method thereof Download PDF

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CN114214567B
CN114214567B CN202111555888.1A CN202111555888A CN114214567B CN 114214567 B CN114214567 B CN 114214567B CN 202111555888 A CN202111555888 A CN 202111555888A CN 114214567 B CN114214567 B CN 114214567B
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闫志杰
韩蔚然
高永亮
李猛
王睿
于志强
康燕
范婧
苗芳
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North University of China
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Abstract

Ni 3 Al intermetallic compound precipitation strengthened high-temperature bearing steel belongs to the technical field of steel smelting, and comprises the following chemical components in percentage by weight: 0.15-0.35% of C, 0.05-0.45% of Si, 0.15-0.45% of Mn, 4.0-8.0% of Cr, 4.0-8.0% of Ni, 1.2-4.8% of Al, 0.3-0.9% of Mo, 0.3-0.9% of V, 0.05-0.35% of M, less than or equal to 0.15% of P, less than or equal to 0.01% of S and the balance of Fe, wherein the alloy element Ni/Al is 1.7-3.3, and M is 1 or more of W, Zr, Nd, Co, Cu and B. Preparing dispersed fine Ni through vacuum smelting, vacuum electroslag remelting smelting, forging or rolling, heat treatment and other processes 3 Al intermetallic compound precipitation strengthened high-temperature bearing steel. The hardness of the bearing steel prepared by the invention is not lower than HRC 56 after tempering at 450-550 ℃, and the bearing steel is manufactured at high temperature and high speedThe material is ideal for long-life reliable bearing working under working conditions.

Description

Ni 3 Al intermetallic compound precipitation-strengthened high-temperature bearing steel and preparation method thereof
Technical Field
The invention relates to the technical field of steel smelting, in particular to high-temperature bearing steel and a preparation method thereof 3 Al intermetallic compound precipitation strengthened high temperature bearing steel.
Background
The high-temperature bearing steel has high tempering stability and dimensional stability, good high-temperature oxidation resistance, low thermal expansion and high creep strength, is widely applied to manufacturing bearings which work under high-temperature, high-speed and corrosion working conditions, such as jet engines, gas turbines, aerospace industries, and aerospace aircrafts, and the like, and the currently commonly used high-temperature bearing steel is second-generation high-temperature bearing steel represented by Cr4Mo4V, 13Cr4Mo4Ni4V, Cr4Mo4V, W18Cr4V, and the like.
With the development of aviation and aerospace technologies, the ultimate performance of equipment is continuously broken through and improved, and the importance of high-temperature bearings is more and more prominent, so that higher-performance bearing steel is required. At present, the third-generation high-temperature bearing is developed internationally, and the hardness of the bearing after tempering at 500-600 ℃ can still reach more than HRC 58. The component design and preparation process are key technical problems for researching and preparing the novel high-temperature bearing steel. From the invention patents disclosed in China at present, the high-temperature bearing steel is prepared by the following ways: (1) smelting and electroslag remelting under the protection of nitrogen or other inert gases, using nitrogen as an alloy element to replace part of carbon in high-carbon martensitic stainless steel, obviously refining carbide, more importantly, obtaining excellent comprehensive performance through precipitation strengthening of a nitrogen-containing phase in dispersion distribution (as a recently disclosed invention patent: CN 113528941A, CN 108277432A, CN 108441599B), and obtaining good effect, but adding nitrogen element in steel is difficult, the components are difficult to control, even a high-pressure nitrogen increasing technology is adopted to fix nitrogen, and special preparation equipment is needed; (2) the high-temperature bearing steel is prepared by adopting a powder metallurgy method, for example, the nitrogen-containing stainless steel (CN 101342591B) is prepared by utilizing nitrogen-containing stainless steel powder through powder metallurgy, and the carbide high-temperature bearing steel (CN 102952986A) is prepared by utilizing carbide high-temperature alloy powder, so that better performance is obtained, but the process is complex and the performance is unstable. By combining the above contents, the nitrogen-containing martensitic stainless bearing steel and carbide high-temperature bearing steel prepared by special equipment and special process have good performance, but the components are not easy to control, the cost is high, and the performance stability is not good.
Ni 3 The Al intermetallic compound has high melting point (1395 ℃), has good wear resistance, is a strengthening phase of the nickel-based superalloy, and ensures that the nickel-based superalloy obtains excellent high-temperature creep resistance strength. The invention utilizes Ni 3 The performance characteristics of Al intermetallic compound, nano-sized Ni distributed by self-generated dispersion 3 The precipitation strengthening of the Al phase prepares a high-temperature bearing steel with excellent comprehensive performance.
Disclosure of Invention
The invention aims to provide a method for designing and preparing Ni 3 A method for strengthening high-temperature bearing steel by Al intermetallic compound precipitation. The steel has high strength, high-temperature hardness and tempering stability, the tensile strength is higher than 2100MPa, and with the increase of the tempering temperature, Ni 3 The precipitation strengthening of the Al phase reaches the hardness peak value at 450-550 ℃, the hardness is not lower than HRC 56, and the Al phase is an ideal material for manufacturing long-life reliable bearings working under high-temperature and high-speed working conditions.
To realize Ni 3 Precipitation strengthening of Al intermetallic compounds, the inventionObviously, the designed bearing steel is smelted and electroslag remelting is carried out in a vacuum environment by reasonably designing the Ni/Al value of the components of the bearing steel and other component design technologies of alloy elements for improving hardenability and hardness, and the nano-Ni is prepared from the smelted bearing steel ingot through the processes of forging or rolling, heat treatment and the like 3 Al intermetallic compound is dispersed in the novel high-temperature bearing steel of the matrix.
The steel comprises the following chemical components in percentage by weight: 0.15 to 0.35 percent of C, 0.05 to 0.45 percent of Si, 0.15 to 0.45 percent of Mn, 4.0 to 8.0 percent of Cr, 4.0 to 8.0 percent of Ni, 1.2 to 4.8 percent of Al, 0.3 to 0.9 percent of Mo, 0.3 to 0.9 percent of V, 0.05 to 0.35 percent of M, less than or equal to 0.15 percent of P, less than or equal to 0.01 percent of S, and the balance of Fe; wherein the alloy element Ni/Al is 1.7-3.3, and M is 1 or more of W, Zr, Nd, Co, Cu and B.
The steel of the invention has the following functions and proportions of elements:
carbon (C): the high-hardness steel is one of key elements for obtaining sufficient hardenability and ensuring high hardness of high-temperature bearing steel. With the increase of the carbon content, the hardness of the bearing steel after quenching is improved, but the plasticity and the toughness are obviously reduced. The steel of the present invention is strengthened by solid solution of carbon and Ni 3 Good high-temperature strength, hardness and wear resistance are obtained under the combined action of precipitation strengthening of Al intermetallic compounds, wherein Ni 3 The contribution rate of Al precipitation strengthening is about 60-80%. The carbon content of Cr4Mo4V high-temperature bearing steel is referred to, and the carbon content is preferably controlled to be 0.15-0.35% in order to ensure that the steel has enough toughness.
Silicon (Si): the element ensures that the high-temperature bearing steel obtains enough elasticity, the addition of silicon is favorable for inhibiting the precipitation of cementite in the low-temperature tempering process of the bearing steel, and the excessive silicon causes the deterioration of the plastic deformation capability and the cutting performance of the bearing steel and is preferably controlled to be below 0.45 percent.
Manganese (Mn): the manganese is an alloy element for improving the hardenability of the bearing steel, and excessively high manganese can be segregated at a grain boundary, so that the residual austenite is difficult to control, and the manganese is unfavorable for the high-temperature performance of the bearing steel and is preferably controlled to be below 0.45%.
Chromium (Cr): is to improve the hardenability of bearing steel and form M 23 C 6 The carbide strengthening phase is an important element of the bearing steel, and is a key element of the bearing steel with high hardness and certain corrosion resistance. Too high chromium is easy to form net-shaped and massive carbides, is not beneficial to the obdurability of the bearing steel, and is generally controlled to be about 4.0 percent. The carbon content of the steel is low, the chromium content is properly improved and controlled to be 4.0-8.0%.
Nickel (Ni): is an effective element for improving the toughness of the common bearing steel. In the steel of the invention, nickel not only improves the toughness of the bearing steel, but also plays a more important role in separating out Ni dispersed in a matrix in the heat treatment process by matching with aluminum 3 An Al intermetallic compound. In order to ensure sufficient Ni precipitation 3 The content of nickel in the Al strengthening phase is controlled to be 4.0-8.0%.
Aluminum (Al): in general bearing steel, aluminum is not added as a main alloying element, and the aluminum remaining in the steel is derived from deoxidation and raw materials. In the steel of the invention, Ni which is dispersed and distributed is separated out in the tempering process in cooperation with nickel 3 An Al intermetallic compound. Our experiments show that the Ni/Al content is controlled to be 1.7-3.3, so the aluminum content is controlled to be 1.2-4.8%.
Molybdenum (Mo): the hardenability, the tempering stability and the size stability of the bearing steel can be improved, the crystal grains are refined, and the high-temperature bearing steel plays an important role. The steel contains high chromium and the price of molybdenum is high, so that the content of molybdenum is low and is controlled to be 0.3-0.9%.
Vanadium (V): is high hardness carbide VC, V 4 C 3 The forming elements of (a) can greatly improve the hardness and wear resistance of the steel. Fine and dispersedly distributed vanadium carbide is separated out in the tempering process, the secondary hardening of the bearing steel is improved, the grain growth at high temperature is hindered, and the high-temperature performance of the steel is obviously improved. The excessively high vanadium content reduces the grinding processability of the bearing steel, and simultaneously the vanadium price is very high, so that the vanadium content is controlled to be 0.3-0.9%.
Trace elements M (W, Zr, Nd, Co, Cu, B): the method is used for further improving the hardenability of the high-temperature bearing steel, improving the hardness of the bearing steel, refining crystal grains, improving the corrosion resistance and the like.
Phosphorus (P): the steel is a harmful element in bearing steel, is derived from raw materials, is segregated to a crystal boundary in the process of solidification of molten steel, deteriorates the toughness of the bearing steel, has the content as low as possible in the bearing steel, and is difficult to dephosphorize in the smelting process. In order to ensure the properties of the steel of the present invention, and in view of the economical efficiency of production, phosphorus is controlled to be 0.15% or less.
Sulfur (S): is a harmful element in bearing steel, is derived from raw materials, and forms flaky low-melting-point MnS with manganese in the process of molten steel solidification, thereby causing hot brittleness of the steel, reducing the plastic deformation capacity of the steel and ensuring that the content is as low as possible. In order to ensure the performance of the steel, the sulfur is controlled below 0.01 percent by combining with the actual production process.
The invention provides Ni 3 The Al intermetallic compound precipitation-strengthened high-temperature bearing steel is prepared according to the following process steps: vacuum smelting → vacuum electroslag remelting → forging or rolling → spheroidizing annealing → quenching → tempering.
Wherein:
smelting in a vacuum induction furnace: the raw materials for proportioning are pure metal or master alloy, scrap steel with definite components, carburant for adjusting carbon content, additional materials required in the smelting process and the like; placing the prepared furnace burden in a vacuum induction furnace as compactly as possible, and then electrifying to melt, wherein the whole smelting process is carried out in a vacuum environment; preserving heat for 10min after the alloy is completely melted, sampling samples to test components and adjust the components, ensuring the content of all alloy elements to be in the component requirement range, and then casting the alloy elements into a mother cast ingot in a vacuum chamber;
vacuum electroslag remelting smelting: the electroslag remelting of the mother ingot is carried out in vacuum, and the electroslag remelting smelting slag system comprises the following components in percentage by weight: 50-70% CaF 2 、10～35％CaO、10～35％Al 2 O 3 1-5% of MgO; the filling coefficient, the slag layer thickness, the working voltage, the current density and other electric slag remelting process parameters are adjusted according to the ingot casting diameter needing remelting and actual electric slag remelting equipment;
forging or rolling: the initial forging or rolling temperature of the electroslag ingot is 1150-1200 ℃, the final forging or rolling temperature is 950-980 ℃, the total deformation amount of the bearing steel is not less than 6, and the bearing steel is air-cooled to room temperature after being deformed;
spheroidizing annealing: carrying out spheroidizing annealing on the forged or rolled bearing steel, firstly heating to 760-820 ℃ and preserving heat for a certain time, then cooling to 680-740 ℃ at a speed of 10-20 ℃/h in a furnace and preserving heat for a certain time at the temperature, finally cooling to 450-550 ℃ at a speed of 10-20 ℃/h in a furnace, then discharging from the furnace and air cooling to room temperature, wherein the preserving heat time in the furnace in the annealing process is determined according to the size of a bearing steel billet;
quenching: heating the spheroidized annealed bearing steel to 950-1150 ℃, preserving heat for a certain time, quenching to room temperature to obtain a martensite matrix, wherein the quenching heat preservation time is determined according to the size of a bearing steel billet;
tempering: heating the quenched bearing steel to 450-550 ℃, preserving heat for a certain time, air-cooling to room temperature, and precipitating fine Ni dispersedly distributed on the matrix 3 The tempering and heat preservation time of the Al intermetallic compound is determined according to the size of the bearing steel billet.
The invention has the beneficial effects that the Ni provided by the invention is utilized 3 Al intermetallic compound precipitation strengthened high-temperature bearing steel and preparation method thereof, and can design and prepare nano-scale fine Ni 3 The novel high-temperature bearing steel with Al phase dispersed in a martensite matrix has good tempering stability, the hardness after tempering at 450-550 ℃ is not lower than HRC 56, and the application potential is huge under the extreme working conditions of high temperature, high speed and the like.
Drawings
FIG. 1 is a metallographic photograph of a bearing steel of example 1 after quenching at 1150 ℃ and tempering at 550 ℃;
FIG. 2 is a metallographic photograph of bearing steel of example 2 after quenching at 1100 ℃ and tempering at 530 ℃;
FIG. 3 is a photograph of a bearing steel of example 1 after quenching at 1150 ℃ and tempering at 550 ℃;
FIG. 4 is a transmission photograph of the bearing steel of example 1 after quenching at 1150 ℃ and tempering at 550 ℃.
Detailed Description
Any feature disclosed in this specification may be replaced by alternative features serving equivalent or similar purposes, unless expressly stated otherwise. Unless expressly stated otherwise, each feature is only an example of a generic series of equivalent or similar features. The description is only for the purpose of facilitating understanding of the present invention and should not be construed as specifically limiting the present invention.
The present invention will be further described with reference to the following embodiments and drawings, and the components of the high temperature bearing steel of each example are shown in table 1.
TABLE 1 composition (wt%, balance Fe) of high-temperature bearing steel for each example
Figure BDA0003419063620000061
Figure BDA0003419063620000071
Example 1
The high-temperature bearing steel of the present invention was prepared by compounding according to the composition design of the high-temperature bearing steel provided in table 1. The specific preparation process comprises the following steps:
step 1, vacuum smelting: placing the prepared furnace burden into a 100kg vacuum induction furnace for smelting, and casting the qualified furnace burden into a cylindrical ingot with the diameter of 180mm and the weight of 100 kg;
step 2, vacuum electroslag remelting: taking a cylindrical ingot with the diameter of 180mm as a consumable electrode, smelting in a vacuum electroslag remelting furnace, and aiming at further refining to reduce non-metallic inclusions to prepare the cylindrical electroslag ingot with the diameter of 200 mm; the electroslag remelting slag system comprises the following components in percentage by weight: 60% CaF 2 、 15％CaO、20％Al 2 O 3 、5％MgO；
Step 3, forging: heating the electroslag ingot to 1250 ℃, preserving heat for 8 hours, and then starting forging and cogging, wherein the initial forging temperature is 1200 ℃, and the final forging temperature is not lower than 980 ℃. In the forging process, the first upsetting length is reduced by 50%; then drawing out for the first time, and restoring the length to the original length; the deformation of the second upsetting is the same as that of the first upsetting; after the second drawing, a bar with the diameter of 100mm is finally formed, air cooling is carried out to the room temperature, and the deformation in the whole forging process is 6;
step 4, spheroidizing annealing: firstly, heating a forging bar to 820 ℃ and preserving heat for 4h, then cooling the bar to 740 ℃ at a rate of 20 ℃/h in a furnace and preserving heat for 2h at the temperature, finally cooling the bar to 550 ℃ at a rate of 10 ℃/h in the furnace, discharging the bar out of the furnace and air cooling the bar to room temperature;
step 5, quenching: heating the spheroidizing annealed bar to 1150 ℃ and preserving heat for 1h, and then carrying out oil cooling;
step 6, tempering: and heating the quenched bar to 550 ℃, preserving the heat for 4 hours, and then cooling the bar to room temperature in air.
Example 2
The high-temperature bearing steel of the present invention was prepared by compounding according to the composition design of the high-temperature bearing steel provided in table 1. The specific preparation process comprises the following steps:
step 1, vacuum smelting: placing the prepared furnace burden into a 100kg vacuum induction furnace for smelting, and casting the qualified furnace burden into a cylindrical ingot with the diameter of 180mm and the weight of 100 kg;
step 2, vacuum electroslag remelting: taking a cylindrical ingot with the diameter of 180mm as a consumable electrode, smelting in a vacuum electroslag remelting furnace, and aiming at further refining to reduce non-metallic inclusions to prepare the cylindrical electroslag ingot with the diameter of 200 mm; the electroslag remelting slag system comprises the following components in percentage by weight: 50% CaF 2 、 35％CaO、10％Al 2 O 3 、5％MgO；
Step 3, forging: heating the electroslag ingot to 1230 ℃, keeping the temperature for 8 hours, then starting forging and cogging, wherein the initial forging temperature is 1180 ℃, and the final forging temperature is not lower than 970 ℃. In the forging process, the first upsetting length is reduced by 50%; then drawing out for the first time, and restoring the length to the original length; the deformation of the second upsetting is the same as that of the first upsetting; after the second drawing, a bar with the diameter of 100mm is finally formed, air cooling is carried out to the room temperature, and the deformation in the whole forging process is 6;
step 4, spheroidizing annealing: firstly, heating a forging bar to 800 ℃ and preserving heat for 4h, then cooling to 720 ℃ in a furnace at a speed of 10 ℃/h and preserving heat for 2h at the temperature, finally cooling to 530 ℃ in a furnace at a speed of 20 ℃/h, discharging and air cooling to room temperature;
step 5, quenching: heating the spheroidizing annealed bar to 1100 ℃, preserving heat for 1h, and then carrying out oil cooling;
step 6, tempering: and heating the quenched bar to 530 ℃ and preserving heat for 4 hours, and then air-cooling to room temperature.
Example 3
The high-temperature bearing steel of the present invention was prepared by compounding according to the composition design of the high-temperature bearing steel provided in table 1. The specific preparation process comprises the following steps:
step 1, vacuum smelting: placing the prepared furnace burden into a 100kg vacuum induction furnace for smelting, and casting the qualified furnace burden into a cylindrical ingot with the diameter of 180mm and the weight of 100 kg;
step 2, vacuum electroslag remelting: taking a cylindrical ingot with the diameter of 180mm as a consumable electrode, smelting in a vacuum electroslag remelting furnace, and aiming at further refining, reducing non-metallic inclusions and preparing a cylindrical electroslag ingot with the diameter of 200 mm; the electroslag remelting slag system comprises the following components in percentage by weight: 70% CaF 2 、 10％CaO、19％Al 2 O 3 、1％MgO；
Step 3, rolling: heating the electroslag ingot to 1220 ℃, keeping the temperature for 8 hours, and then starting rolling, wherein the starting rolling temperature is 1180 ℃, and the final rolling temperature is not lower than 960 ℃. Rolling the steel bar into a bar with the diameter of 50mm after 8-pass rolling deformation;
step 4, spheroidizing annealing: firstly, heating a forging bar to 780 ℃ and preserving heat for 4h, then cooling the bar to 720 ℃ in a furnace at the speed of 15 ℃/h and preserving heat for 2h at the temperature, finally cooling the bar to 480 ℃ in the furnace at the speed of 15 ℃/h, discharging the bar out of the furnace and air cooling the bar to room temperature;
step 5, quenching: heating the spheroidizing annealed bar to 980 ℃ and preserving heat for 1h, and then carrying out oil cooling;
step 6, tempering: and heating the quenched bar to 480 ℃ and preserving the heat for 4 hours, and then cooling the bar to room temperature in air.
Example 4
The high-temperature bearing steel of the present invention was prepared by compounding according to the composition design of the high-temperature bearing steel provided in table 1. The specific preparation process comprises the following steps:
step 1, vacuum smelting: placing the prepared furnace burden into a 100kg vacuum induction furnace for smelting, and casting the qualified furnace burden into a cylindrical ingot with the diameter of 180mm and the weight of 100 kg;
step 2, vacuum electroslag remelting: taking a cylindrical ingot with the diameter of 180mm as a consumable electrode, smelting in a vacuum electroslag remelting furnace, and aiming at further refining to reduce non-metallic inclusions to prepare the cylindrical electroslag ingot with the diameter of 200 mm; the electroslag remelting slag system comprises the following components in percentage by weight: 55% CaF 2 、 20％CaO、22％Al 2 O 3 、3％MgO；
Step 3, rolling: heating the electroslag ingot to 1200 ℃, keeping the temperature for 8 hours, and then starting rolling, wherein the starting rolling temperature is 1150 ℃, and the final rolling temperature is not lower than 950 ℃. Rolling the mixture into a bar with the diameter of 50mm after 8-pass rolling deformation;
step 4, spheroidizing annealing: firstly, heating a forging bar to 760 ℃ and preserving heat for 4h, then cooling to 720 ℃ with a furnace at a speed of 20 ℃/h and preserving heat for 2h at the temperature, finally cooling to 450 ℃ with the furnace at a speed of 20 ℃/h, discharging and air cooling to room temperature;
step 5, quenching: heating the spheroidizing annealed bar to 950 ℃ and preserving heat for 1h, and then carrying out oil cooling;
step 6, tempering: and heating the quenched bar to 450 ℃, preserving the heat for 4 hours, and then cooling the bar to room temperature in air.
FIG. 1 is a metallographic photograph of a high-temperature bearing steel of example 1 after being quenched at 1150 ℃ and tempered at 550 ℃, FIG. 2 is a metallographic photograph of a high-temperature bearing steel of example 2 after being quenched at 1100 ℃ and tempered at 530 ℃, and FIG. 3 is a scanning electron micrograph of a bearing steel of example 1 after being quenched at 1150 ℃ and tempered at 550 ℃, and it can be seen that the structure of the bearing steel after heat treatment is a martensite matrix + carbide, and Ni 3 The Al intermetallic compound has a small size and can be observed only in a transmission electron micrograph. FIG. 4 is a transmission electron micrograph of the bearing steel of example 1 after 1150 ℃ quenching and 550 ℃ tempering, which shows that the nano-sized black Ni is dispersed and distributed 3 An Al intermetallic compound. Through detection, the hardness of the bearing steel prepared in the examples 1-4 is HRC 56, HRC 58 and HRC 60 respectively, and the hardness of the bearing steel after quenching and tempering is not lower than HRC 56 in all the examples, which shows that the steel has good high-temperature hardness and is an ideal high-temperature bearing steel material.
The above-mentioned embodiments only express several embodiments of the present invention, and the description thereof is more specific and detailed, but not construed as limiting the scope of the present invention. It should be noted that, for a person skilled in the art, several variations and modifications can be made without departing from the inventive concept, which falls within the scope of the present invention. Therefore, the protection scope of the present patent shall be subject to the appended claims.

Claims (4)

1. Ni 3 The Al intermetallic compound precipitation-strengthened high-temperature bearing steel is characterized by comprising the following chemical components in percentage by weight: 0.15 to 0.35 percent of C, 0.32 to 0.45 percent of Si, 0.35 to 0.45 percent of Mn, 4.0 to 8.0 percent of Cr, 4.0 to 8.0 percent of Ni, 1.2 to 4.8 percent of Al, 0.3 to 0.9 percent of Mo, 0.3 to 0.9 percent of V, 0.05 to 0.35 percent of M, less than or equal to 0.15 percent of P, less than or equal to 0.01 percent of S, and the balance of Fe; the alloy element Ni/Al is 1.7-3.3; m is composed of 1 or more elements of W, Zr, Nd, Co, Cu and B;
the preparation method of the high-temperature bearing steel comprises the following steps:
(1) smelting in a vacuum induction furnace: the prepared furnace burden is tightly placed in a vacuum induction furnace, then the furnace burden is electrified and melted, the whole smelting process is carried out in a vacuum environment, and a sample is poured into a cast ingot in a vacuum chamber after testing components are qualified;
(2) vacuum electroslag remelting smelting: carrying out electroslag remelting smelting on the mother ingot under vacuum to prepare an electroslag ingot;
(3) forging or rolling: the initial forging or rolling temperature of the electroslag ingot is 1150-1200 ℃, the final forging or rolling temperature is 950-980 ℃, the total deformation of the bearing steel is not less than 6, and the bearing steel is air-cooled to room temperature after being deformed;
(4) spheroidizing annealing: carrying out spheroidizing annealing on the forged or rolled bearing steel, firstly heating to 760-820 ℃ and preserving heat for a certain time, then carrying out furnace cooling to 680-740 ℃ at a speed of 10-20 ℃/h and preserving heat for a certain time at the temperature, finally carrying out furnace cooling to 450-550 ℃ at a speed of 10-20 ℃/h and then discharging and air cooling to room temperature;
(5) quenching: heating the spheroidized annealed bearing steel to 950-1150 ℃, preserving heat for a certain time, and quenching to room temperature;
(6) tempering: heating the quenched bearing steel to 450-550 ℃, preserving heat for a certain time, air-cooling to room temperature, and precipitating fine Ni dispersedly distributed on the matrix 3 An Al intermetallic compound.
2. A method for producing a high temperature bearing steel according to claim 1, comprising the steps of:
(1) smelting in a vacuum induction furnace: placing the prepared furnace burden in a vacuum induction furnace tightly, then electrifying and melting, carrying out the whole smelting process in a vacuum environment, and pouring a qualified sample into a vacuum chamber to form an ingot after the tested components are qualified;
(2) vacuum electroslag remelting smelting: carrying out electroslag remelting smelting on the mother ingot under vacuum to prepare an electroslag ingot;
(3) forging or rolling: the initial forging or rolling temperature of the electroslag ingot is 1150-1200 ℃, the final forging or rolling temperature is 950-980 ℃, the total deformation amount of the bearing steel is not less than 6, and the bearing steel is air-cooled to room temperature after being deformed;
(4) spheroidizing annealing: carrying out spheroidizing annealing on the forged or rolled bearing steel, firstly heating to 760-820 ℃ and preserving heat for a certain time, then carrying out furnace cooling to 680-740 ℃ at a speed of 10-20 ℃/h and preserving heat for a certain time at the temperature, finally carrying out furnace cooling to 450-550 ℃ at a speed of 10-20 ℃/h and then discharging and air cooling to room temperature;
(5) quenching: heating the spheroidized annealed bearing steel to 950-1150 ℃, preserving heat for a certain time, and quenching to room temperature;
(6) tempering: heating the quenched bearing steel to 450-550 ℃, preserving heat for a certain time, air-cooling to room temperature, and precipitating fine Ni dispersedly distributed on the matrix 3 An Al intermetallic compound.
3. The method for preparing high-temperature bearing steel according to claim 2, wherein the electroslag remelting slag system comprises the following components in percentage by weight: 50-70% CaF 2 、10～35％CaO、10～35％Al 2 O 3 、1～5％MgO。
4. The method for preparing high temperature bearing steel according to claim 2, wherein in the forging or rolling, the electroslag ingot is heated to a temperature higher than the forging or rolling start temperature, and the temperature is kept for 6-8 h.
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JP2008121031A (en) * 2006-10-17 2008-05-29 Kobe Steel Ltd Cold work die steel and die
US20110085930A1 (en) * 2007-01-12 2011-04-14 Isaac Valls Cold work tool steel with outstanding weldability
CN109642299A (en) * 2016-06-01 2019-04-16 奥瓦科瑞典股份公司 Precipitation hardening steel and its manufacture
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Publication number Priority date Publication date Assignee Title
JP2008121031A (en) * 2006-10-17 2008-05-29 Kobe Steel Ltd Cold work die steel and die
US20110085930A1 (en) * 2007-01-12 2011-04-14 Isaac Valls Cold work tool steel with outstanding weldability
US20200140979A1 (en) * 2015-12-24 2020-05-07 Rovalma, S.A. Long durability high performance steel for structural, machine and tooling applications
CN109642299A (en) * 2016-06-01 2019-04-16 奥瓦科瑞典股份公司 Precipitation hardening steel and its manufacture

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