WO2024093461A1 - 一种经济性高寿命大功率风电偏航轴承圈用钢、轴承圈及生产工艺 - Google Patents

一种经济性高寿命大功率风电偏航轴承圈用钢、轴承圈及生产工艺 Download PDF

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WO2024093461A1
WO2024093461A1 PCT/CN2023/114602 CN2023114602W WO2024093461A1 WO 2024093461 A1 WO2024093461 A1 WO 2024093461A1 CN 2023114602 W CN2023114602 W CN 2023114602W WO 2024093461 A1 WO2024093461 A1 WO 2024093461A1
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bearing ring
tempering
steel
quenching
life
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PCT/CN2023/114602
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English (en)
French (fr)
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杨志强
汪开忠
胡芳忠
王自敏
陈世杰
吴林
陈恩鑫
庄振
杨少朋
金国忠
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马鞍山钢铁股份有限公司
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Publication of WO2024093461A1 publication Critical patent/WO2024093461A1/zh

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/40—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rings; for bearing races
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
    • Y02E10/00—Energy generation through renewable energy sources
    • Y02E10/70—Wind energy
    • Y02E10/72—Wind turbines with rotation axis in wind direction
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/20—Recycling

Definitions

  • the present invention belongs to the field of alloy steel, and more specifically, relates to an economical, high-life, high-power wind power yaw bearing ring steel, a bearing ring and a production process.
  • Patent CN 104726783A points out a steel for wind turbine yaw and pitch bearing rings and its preparation method, which is designed with high Ni (1.30-1.70%) composition, and after heat treatment, the tensile strength at 12.5mm below the bearing ring is ⁇ 1200MPa, and the -20°C V-type impact energy is ⁇ 32J, which meets the performance requirements of 5MW wind turbine yaw bearing rings.
  • the patent increases the material cost by adding a large amount of precious metal Ni, and the economy is insufficient.
  • the material has not been tested and evaluated for the fatigue performance and corrosion resistance of marine wind turbine bearings, and the application support of the material is insufficient.
  • Patent CN 104178695A discloses the use of medium carbon boron microalloy steel to manufacture wind turbine bearing rings. After heat treatment, the tensile strength of the bearing rings is ⁇ 1090MPa, and the -20°C V-type impact energy is ⁇ 29J. The overall strength and toughness of the material of this invention is not high. The heat treatment quenching and insulation time is 50-130min. The thickness of the produced bearing rings is relatively thin, which cannot meet the needs of thick-walled performance of high-power wind turbine bearing rings. It has not tested and evaluated the fatigue performance of marine wind turbine bearings, and the application support of the material is insufficient. In addition, the patent will increase the material cost by adding a large amount of precious metal Ni, and the economy is insufficient.
  • the present invention provides an economical, high-life, high-power wind turbine yaw bearing ring steel, a bearing ring and a production process.
  • the produced bearing ring maintains relatively high low-temperature toughness in the Ni-free system.
  • the present invention discloses an economical, high-life, high-power wind power yaw bearing ring steel, which contains, by weight percentage: C 0.47% to 0.57%, Si 0.10% to 0.30%, Mn 0.70% to 0.90%, Cr 1.30% to 1.50%, Mo 0.30% to 0.50%, Cu 0.030% to 0.050%, V 0.035% to 0.075%, Nb 0.010% to 0.030%, Cu 0.030% to 0.050%, Al 0.015% to 0.025%, P ⁇ 0.015%, S ⁇ 0.010%, O ⁇ 0.0040%, N ⁇ 0.0080%, and the rest is Fe and other inevitable impurities.
  • the chemical composition ratio should meet the following requirements:
  • Heat treatment process parameters should meet the following requirements:
  • the invention provides a heat treatment method for the steel, and the obtained steel has excellent toughness and contact fatigue performance, and is suitable for manufacturing yaw bearings for high-power wind power (shaft ring wall thickness ⁇ 240mm).
  • the invention also discloses a process for producing bearing rings using the steel.
  • C is the cheapest strengthening element in steel. Every increase of 0.1% of solid solution C can increase the strength by about 450MPa. C forms precipitation phase with alloy elements in steel, which plays a precipitation strengthening role. C can significantly improve hardenability and obtain martensite structure in the center of thick wall periodic ring. However, as its content increases, plasticity and toughness decrease, so the C content is controlled at 0.47% to 0.57%.
  • Si is an effective solid solution strengthening element in steel, which improves the strength and hardness of steel. Si can play a deoxidizing role during steelmaking and is a commonly used deoxidizer. However, Si is easy to segregate at austenite grain boundaries, reduce grain boundary bonding strength, and cause brittleness. In addition, Si is easy to cause element segregation in steel. Therefore, the Si content is controlled at 0.10% to 0.30%.
  • Mn can play a role in solid solution strengthening, and its solid solution strengthening ability is weaker than that of Si.
  • Mn is an austenite stabilizing element that can significantly improve the hardenability of steel and reduce the decarburization of steel. Mn combined with S can prevent hot brittleness caused by S. However, excessive Mn will reduce the plasticity of steel. Therefore, the Mn content is controlled at 0.70% to 0.90%.
  • Cr is a carbide-forming element. Cr can improve the hardenability and strength of steel, but it is easy to cause temper brittleness. Cr can improve the oxidation resistance and corrosion resistance of steel, but too high Cr content will increase crack sensitivity. The Cr content should be controlled at 1.30% to 1.50%.
  • Mo mainly improves the hardenability and heat resistance of steel. Mo dissolved in the matrix can keep the structure of steel stable during tempering, and can effectively reduce the segregation of impurity elements such as P, S and As at the grain boundary, thereby improving the toughness of steel and reducing temper brittleness. Mo can reduce the stability of M 7 C 3. When the Mo content is high, needle-shaped Mo 2 C will be formed, which will lead to a decrease in the Mo content of the matrix. Mo can improve the strength of steel through the combined effects of solid solution strengthening and precipitation strengthening, and can also change the toughness of steel by changing the precipitation of carbides. Therefore, Mo is controlled at 0.30% to 0.50%.
  • V is a strong C, N compound forming element.
  • V (C, N) forms fine dispersion and maintains a coherent relationship with the matrix, which can play a role in strengthening and refining the structure.
  • the V content is controlled at 0.035% to 0.075%.
  • Nb is the main microalloying element in steel. It exists in steel as a replacement solute atom. Nb atoms are larger than iron atoms and tend to be segregated on dislocation lines, which have a strong drag effect on dislocation climb, thereby achieving the purpose of refining austenite grains. Grain refinement can not only improve the strength and toughness of steel, but a small amount of Nb can stably refine grains, improve strength, toughness and fatigue properties. The mismatch between Nb's carbonitride and the matrix is moderate, which is beneficial to the strengthening and toughening of steel. When the Nb content is too little, less than 0.010%, the dislocation drag effect is extremely small and cannot play a role in improving toughness. Excessive addition of Nb will lead to large carbonitrides, forming large-sized inclusions and losing the strengthening and toughening effect, and Nb is expensive, so the range of Nb can be controlled at 0.010% to 0.030%.
  • Cu expands the austenite phase. Cu alone can significantly improve strength as a second phase, and can improve the tempering stability and strength of the structure. However, excessive Cu will cause Cu brittleness. Therefore, the Cu content is controlled at 0.030% to 0.050%.
  • Al is the main deoxidizer in steelmaking. Al combines with N to form fine dispersed AlN, which maintains a coherent relationship with the matrix, can strengthen and refine the structure, increase the resistance to fatigue crack initiation and expansion, and thus improve the long-term strength of steel.
  • the Al content is controlled at 0.015% to 0.035%.
  • TO forms oxide inclusions in steel, and TO is controlled to be ⁇ 0.0040%; N can form nitrides in steel, forming fine precipitation phases to refine the structure, and can also precipitate Fe 4 N, which has a slow diffusion rate, causing aging of the steel and reducing the processing performance, so N is controlled within 0.0080%.
  • the yaw bearings of large-power wind turbines are large in size and need to ensure sufficient strength and toughness.
  • the addition of alloying elements can effectively improve hardenability and thus strength and toughness.
  • Mn is the most effective in improving hardenability and strength among alloying elements, with a coefficient of 3.34; Mo also contributes greatly to hardenability and strength by improving tempering stability and interacting with Mn, with a coefficient of 3.0; Cr is the main substitutional solid solution element and carbide-forming element, and its contribution to strength is 2.16; Cu does not form carbides in steel, and changes the lattice morphology through solid solution strengthening, thereby improving the hardenability and strength of steel, with coefficients of 0.37 and 0.36 respectively; C is a non-metallic element and the most important interstitial solid solution strengthening element in steel, which has an effect on strength and toughness, so the coefficient is 0.54; Si is a non-metallic element and the main solid solution strengthening element in steel, and its contribution to the performance of steel is 0.70.
  • C and Mn can significantly increase the shallow hardness of steel and improve wear resistance, thereby improving contact fatigue performance
  • Cr, Mo, V, and Nb can form a second phase with C and N in steel. Although the second phase can increase the strength in steel, it is still different from the steel matrix. If the size is large, it can form a contact fatigue crack source, so it is not good for contact fatigue; Cu is beneficial to contact fatigue performance by combining with the matrix at the atomic scale through solid solution strengthening.
  • the carbonitride formed by Nb in steel has the characteristics of high hardness, and the size is difficult to control, which can easily cause peeling and reduce contact fatigue performance.
  • this patent does not add precious metal Ni.
  • the toughness requirement for low temperature environment is achieved through reasonable proportioning of alloying elements and micro-alloying elements. Since the addition of precious metal Ni is reduced in steel, and Ni is beneficial to low temperature toughness, in order to ensure the low temperature toughness of steel, the combination of elements such as Si, Mn, Cr, Mo, and Cu must be controlled. Si significantly deteriorates low temperature toughness and increases temper brittleness, so the coefficient of Si is (-3).
  • Mn can significantly affect the selection of variants in the phase change process, increase the types of variants in the phase change, and thus improve low temperature toughness, but Mn is prone to segregation, so the coefficient of Mn is 0.8.
  • Mo mainly improves low temperature toughness by improving tempering stability, and its contribution to low temperature toughness is limited, so the coefficient of Mo is 1.2.
  • Cu can improve the atomic level bonding with the steel matrix, which is beneficial to toughness, so the coefficient is 1.
  • the present invention also discloses the production process of the steel for the yaw bearing ring and the yaw bearing ring: electric arc furnace or converter smelting ⁇ LF furnace refining ⁇ RH or VD vacuum degassing ⁇ ⁇ 380mm ⁇ 700mm round billet continuous casting ⁇ round billet heating ⁇ forging ⁇ punching ⁇ ring rolling (semi-finished product) ⁇ heat treatment ⁇ machining ⁇ flaw detection ⁇ packaging and warehousing.
  • the yaw bearing ring is subjected to two tempering heat treatments, and the key heat treatment processes are:
  • the furnace temperature of the semi-finished yaw bearing ring after ring rolling is ⁇ 600°C
  • the primary quenching heating temperature (T 1 , °C) is 900-1000°C
  • the primary quenching holding time (t, min) is determined by the bearing ring wall thickness (S, mm) and the primary quenching heating temperature (T 1 , °C), ST 1 /20 ⁇ t 1 ⁇ ST 1 /80
  • the primary tempering heating temperature (T 2 , °C) is 650-700°C
  • the primary tempering holding time (t 2 , min) is determined by the bearing ring wall thickness (S, mm) and the primary tempering heating temperature (T 2 , °C), ST 2 /10 ⁇ t 2 ⁇ ST 2 /50, water cooling.
  • the secondary quenching heating temperature (T 3 , °C) is 800-900 °C
  • the holding time (t 3 , min) is determined by the bearing ring wall thickness (S, mm) and the secondary quenching heating temperature (T 3 , °C), ST 3 /10 ⁇ t 3 ⁇ ST 3 /50, water cooling
  • the secondary tempering heating temperature (T 4 , °C) is 600-700 °C
  • the secondary tempering holding time (t4 , min) is determined by the bearing ring wall thickness (S, mm) and the secondary tempering heating temperature (T 4 , °C), 1.5 ⁇ ST 4 /10 ⁇ t 4 ⁇ 1.5 ⁇ ST 4 /50, water cooling.
  • the present invention reduces the use of precious metal Ni, so the low-temperature toughness of the steel is poor.
  • the heat treatment process needs to be innovatively optimized. Although the process becomes complicated by using two temperings, the overall cost is reduced.
  • the reason why the present invention uses two temperings is that after the first tempering, the degree of structural refinement of the steel is not sufficient to make up for the lack of precious metals.
  • the second tempering the steel is heated and cooled again to further refine the structure and carbide. At the same time, the second heating temperature is controlled to be lower than the first heating temperature, so that the precipitated phase of the steel does not melt back during the heating process, thereby ensuring a small grain size and improving the overall performance of the steel.
  • the austenite transformation point is affected by the composition, and the normalizing temperature and quenching heating temperature are determined by the austenite transformation point.
  • the tempering heating temperature is selected according to the required precipitate type, content and size.
  • the first tempering heating temperature of the present invention is 900-1000°C, which ensures that the bearing ring is completely austenitized at this temperature, and at the same time controls the temperature not to be higher than 1000°C, ensuring that the size of the second phase precipitated during the forging process is not too coarse, thereby helping to improve the toughness of subsequent products.
  • the precipitated phase is mainly M 23 C 6 and MX type, effectively improving the strength of the steel.
  • the temperature of the second tempering is lower than that of the first tempering.
  • the first precipitate phase can be used as a nucleation point to nucleate the grains again, thereby refining the grains.
  • it helps the precipitate phase to melt back less during the austenitization process, which can improve the toughness and fatigue performance.
  • the tempering temperature is low for the second tempering, so that the growth activation energy of the precipitate phase is insufficient, ensuring that the precipitate phase is small.
  • the type of precipitate phase can be controlled to make the precipitate phase M 7 C 3 , M 23 C 6 and MX. Multiple precipitates can enrich the steel components and avoid the single phase being too large in size, which reduces the fatigue performance.
  • the tensile strength of the bearing ring at 1/2 wall thickness is ⁇ 950MPa, the yield strength is ⁇ 850MPa, and the -40°C KV 2 is ⁇ 80J; under the contact stress of 2000MPa, the contact fatigue life is ⁇ 1 million times, meeting the service requirement of high-power wind power for 20 years.
  • the present invention has the following beneficial effects:
  • a high-strength, high-toughness, high-contact fatigue, high-power wind turbine yaw bearing ring of the present invention can maintain relatively high low-temperature toughness without the addition of precious metal Ni through reasonable chemical ratio and heat treatment process;
  • the high-strength, high-toughness, high-contact fatigue high-power wind turbine yaw bearing ring of the present invention has a tensile strength of ⁇ 950MPa, a yield strength of ⁇ 850MPa, and a -40°C KV 2 ⁇ 80J at 1/2 wall thickness (wall thickness ⁇ 240mm). Under the action of 2000MPa contact stress, the contact fatigue life is ⁇ 1 million times, meeting the service requirement of high-power wind turbines for 20 years.
  • FIG1 is a microscopic morphology of a bearing ring at 1/2 wall thickness obtained in Example 1 of the present invention, (a) after primary quenching; (2) after secondary quenching;
  • FIG2 is a microscopic morphology of the bearing ring at 1/2 wall thickness obtained in Comparative Example 2 of the present invention, (a) after primary quenching; (2) after secondary quenching;
  • FIG3 is an EBSD analysis diagram of the 1/2 wall thickness of the bearing ring obtained in Example 1;
  • FIG4 is an EBSD analysis diagram of the 1/2 wall thickness of the bearing ring prepared in Comparative Example 2.
  • the present invention discloses an economical, high-life, high-power wind power yaw bearing ring steel, which contains, by weight percentage: C 0.47% to 0.57%, Si 0.10% to 0.30%, Mn 0.70% to 0.90%, Cr 1.30% to 1.50%, Mo 0.30% to 0.50%, Cu 0.030% to 0.050%, V 0.035% to 0.075%, Nb 0.010% to 0.030%, Cu 0.030% to 0.050%, Al 0.015% to 0.025%, P ⁇ 0.015%, S ⁇ 0.010%, O ⁇ 0.0040%.
  • the rest is Fe and other inevitable impurities.
  • the chemical composition ratio should meet the following requirements:
  • Heat treatment process parameters should meet the following requirements:
  • the invention provides a heat treatment method for the steel, and the obtained steel has excellent toughness and contact fatigue performance, and is suitable for manufacturing yaw bearings for high-power wind power (shaft ring wall thickness ⁇ 240mm).
  • the invention also discloses a process for producing bearing rings using the steel.
  • the present invention adopts steel with specific composition.
  • the steel compositions of the embodiments and comparative examples are shown in Table 1.
  • the production process of the steel of the present invention is as follows:
  • Electric furnace smelting oxygen is determined before steel is tapped, and steel retention is adopted during the steel tapping process to avoid slag;
  • LF furnace adjust elements such as C, Si, Mn, Cr, Mo, V, Nb, Cu to target values;
  • Vacuum degassing Pure degassing time ⁇ 15 minutes, ensuring that the [H] content after vacuum treatment is ⁇ 1.5ppm, avoiding the appearance of white spots in the steel and causing hydrogen embrittlement;
  • the target temperature of the molten steel in the tundish is controlled at 10-40°C above the liquidus temperature, and round billets of ⁇ 380mm- ⁇ 700mm are continuously cast.
  • Bearing ring manufacturing route round billet (diameter 600 and 700mm) heating ⁇ forging ⁇ punching ⁇ ring rolling (semi-finished product).
  • Bearing ring heat treatment trolley furnace heating ⁇ insulation ⁇ normalizing ⁇ quenching ⁇ tempering ⁇ insulation ⁇ water cooling.
  • Bearing ring processing route bearing ring rough turning ⁇ flaw detection ⁇ valve body fine turning ⁇ grinding ⁇ flaw detection ⁇ packaging and warehousing.
  • the performance testing method is as follows:
  • Samples were taken from the extension of the bearing ring, and samples were taken at 12.5 mm on the surface of the extension and within 1/2 thickness (thickness was 240 mm) for metallographic and grain size analysis.
  • Comparative Examples 1 and 2 are inappropriate chemical composition ratios, among which the chemical composition of Comparative Example 2 is improperly controlled, resulting in too low material strength, insufficient plasticity and toughness, and improper heat treatment process resulting in unsatisfactory overall performance; Comparative Example 3 has reasonable composition design, but improper heat treatment process, resulting in insufficient strength and toughness of the material, and insufficient contact fatigue resistance.
  • Figure 1 is a microscopic morphology of the half wall thickness of the bearing ring obtained in Example 1.
  • the grain size after one quenching is about 34 microns, and after two quenchings, the grain size is refined to 26.6 microns.
  • the grain size is refined by corresponding heat treatment, which can effectively improve the strength, low temperature toughness and fatigue performance of the material.
  • Figures 3 and 4 further illustrate the microscopic reasons for the performance gap caused by components and processes.
  • the EBSD analysis in Example 1 shows that the microstructure is fine and uniform.
  • the microstructure of Comparative Example 2 is coarse.
  • the fine structure can increase the crack propagation path when the material is impacted by external forces, consume the impact capacity, and improve the low-temperature toughness; on the other hand, it can increase the internal stress and coordinated deformation ability of the material, thereby improving the fatigue performance of the material.

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Abstract

一种经济性高寿命大功率风电偏航轴承圈用钢、轴承圈及生产工艺，属于合金钢领域。本发明通过控制化学成分配比，同时采用两次调质，1)一次调质的淬火，S-T1/20≤t1≤S-T1/80；一次调质的回火，S-T2/10≤t2≤S-T2/50；2)二次调质的淬火，S-T3/10≤t3≤S-T3/50；二次调质的回火，1.5×S-T4/10≤t4≤1.5×S-T4/50，制得的轴承圈1/2壁厚(壁厚≥240mm)处抗拉强度≥950MPa、屈服强度≥850MPa、-40℃KV2≥80J，2000MPa接触应力作用下，接触疲劳寿命≥100万次，满足大功率风电服役20年需要。

Description

一种经济性高寿命大功率风电偏航轴承圈用钢、轴承圈及生产工艺
本申请要求于2022年11月04日提交中国专利局、申请号为202211380397.2、发明名称为“一种经济性高寿命大功率风电偏航轴承圈用钢、轴承圈及生产工艺”的中国专利申请的优先权，其全部内容通过引用结合在本申请中。
技术领域
本发明属于合金钢领域，更具体地说，涉及一种经济性高寿命大功率风电偏航轴承圈用钢、轴承圈及生产工艺。
背景技术
在“双碳”背景下清洁能源的需求日益增加，风电作为清洁能源备受关注。截止2021年我国风电装机容量突破30万兆瓦，全球占比超过三分之一。但我国风电的单机功率较低，普遍集中在4兆瓦。国外风电单机功率已达8兆瓦，而我国70米高度、5～50米水深的海洋风力开发资源潜力约50万兆瓦，因此，深度开发大型海上风机是未来风电行业的发展趋势。
风电大型化导致风电关键部件轴承的尺寸增加，据调研，1.5MW风电偏航轴承圈外径约2.1m，而6MW风电偏航轴承圈外径达4.5米，外径扩大2.1倍。另外轴承尺寸增大的同时轴承圈的壁厚增加，导致轴承圈截面性能的一致性不好，因此大功率风电轴承圈对强韧性、均匀性的要求均增加。JB/T 10705也指出“可采用性能相当或更优的材料”制造风电偏航轴承圈。我国海洋风电发展迅速，但目前普遍低于6MW，主要由于关键装备材料不能完全自给。因此开发大功率海洋风电偏航轴承圈用钢已十分迫切。
专利CN 104726783A指出一种风电偏航﹑变桨轴承套圈用钢及其制备方法，采用高Ni(1.30-1.70％)成分设计，经热处理在轴承圈皮下12.5mm处抗拉强度≥1200MPa，-20℃V型冲击功≥32J，满足5MW风电偏航轴承圈性能要求。但是该专利通过大量贵金属Ni的添加，会增加材料成本，经济性不足。另外该材料并未对海洋风电轴承的疲劳性能、耐蚀性能等进行测试评价，对材料的应用支持不足。
专利CN 104178695A公开了采用中碳硼微合金钢制造风电轴承套圈，经热处理轴承圈抗拉强度≥1090MPa，-20℃V型冲击功≥29J。该发明的材料整体强韧性不高，实施热处理淬火保温时间为50-130min，所生产的轴承圈厚度较薄，不能满足大功率风电轴承圈厚壁性能的需要。其并未对海洋风电轴承的疲劳性能等进行测试评价，对材料的应用支持不足。此外，该专利通过大量贵金属Ni的添加，会增加材料成本，经济性不足。
因此，针对大功率风电偏航轴承的服役特点开发出一种具有经济性高寿命的大功率风电偏航轴承圈用钢及其热处理工艺，解决大功率风电发展需要，已十分迫切。
发明内容
1.要解决的问题
针对现有无Ni体系风电轴承圈低温韧性差的问题，本发明提供一种经济性高寿命大功率风电偏航轴承圈用钢、轴承圈及生产工艺，制得的轴承圈在无Ni体系中保持较高的低温韧性。
2.技术方案
为了解决上述问题，本发明所采用的技术方案如下：
本发明公开了一种经济性高寿命大功率风电偏航轴承圈用钢，按重量百分比含有：C 0.47％～0.57％、Si 0.10％～0.30％、Mn 0.70％～0.90％、Cr 1.30％～1.50％、Mo 0.30％～0.50％、Cu 0.030％～0.050％、V 0.035％～0.075％、Nb 0.010％～0.030％、Cu 0.030％～0.050％、Al 0.015％～0.025％、P≤0.015％、S≤0.010％、O≤0.0040％，N≤0.0080％，其余为Fe和其它不可避免的杂质。化学成分配比应符合：
1)10.5≤(0.54×C％)×(1+3.34×Mn％)×(1+0.7×Si％)×(1.2+0.36×Cu％)×(1+0.37×Ni％)×(1+2.61×Cr％)×(1+3×Mo％)×(1+0.6×V％)×(1+0.7Nb％)≤13.8；
2)0.24％≤C％+(Mn％)/6-(Cr％+Mo％+V％+Ti％)/5+(C％u)/15；
3)0.60％≤(-3)×Si％+0.8×Mn％+1.2×Mo％+1×Cu％+2×V％+2×Nb％。
热处理工艺参数应符合：
1)一次调质的淬火，S-T1/20≤t1≤S-T1/80；一次调质的回火，S-T2/10≤t2≤S-T2/50；
2)二次调质的淬火，S-T3/10≤t3≤S-T3/50；二次调质的回火，1.5×S-T4/10≤t4≤1.5×S-T4/50。
本发明提供了该钢的热处理方法，制得的钢具有优秀的强韧性和接触疲劳性能，适用于制造大功率风电用偏航轴承(轴圈壁厚≥240mm)。本发明还公开了利用该钢生产轴承圈的工艺。
C：C是钢中最低廉的强化元素，每提高0.1％的固溶C，可使强度提高约450MPa，C与钢中的合金元素形成析出相，起到析出强化作用。C能够显著提高淬透性，使大壁厚周期圈心部获得马氏体组织。但随着其含量增大，塑性和韧性降低，故C含量控制在0.47％～0.57％。
Si：Si是钢中有效的固溶强化元素，提高钢的强硬度，Si在炼钢时能够起到脱氧作用，是常用的脱氧剂。但Si易偏聚有奥氏体晶界，降低晶界结合力，引发脆性。另外Si易引起钢中元素偏析。因此，Si含量控制在0.10％～0.30％。
Mn：Mn能够起到固溶强化作用，固溶强化能力弱于Si，Mn是奥氏体稳定化元素能显著提高钢的淬透性，还能够减少钢的脱碳，Mn与S结合能够防止S引起的热脆性。但过量的Mn会降低钢的塑性。所以，Mn含量控制在0.70％～0.90％。
Cr：Cr是碳化物形成元素，Cr能够使钢的淬透性和强度均提高，但易引起回火脆性。Cr能够提高钢的抗氧化性能，增加耐蚀性，但Cr含量过高时将增加裂纹敏感性。应将Cr含量控制在1.30％～1.50％。
Mo：Mo主要提高钢的淬透性和耐热性，固溶于基体的Mo能够使钢的组织在回火过程中保持较高的稳定性，且能有效降低P、S和As等杂质元素在晶界处偏聚，从而提高钢的韧性，降低回火脆性。Mo能降低M7C3的稳定性，当Mo含量较高时将形成针状Mo2C，将导致基体Mo含量减少。Mo能够通过固溶强化和沉淀强化的共同作用提高钢的强度，也能通过改变碳化物的析出来改变钢的韧性。故Mo控制在0.30％～0.50％。
V：V是强C、N化合物形成元素，V(C、N)形成细小弥散，且与基体保持共格关系，能够起到强化和细化组织的作用。V含量控制在0.035％～0.075％。
Nb：Nb是钢中主要的微合金元素，其在钢中以置换溶质原子存在，Nb原子比铁原子尺寸大，易在位错线上偏聚，对位错攀移产生强烈的拖曳作用，从而达到细化奥氏体晶粒的目的，晶粒细化不仅能提高钢材的强韧性，Nb少量添加能够稳定细化晶粒，提高强韧性及疲劳性能。Nb的碳氮化合物与基体的错配度适中，有利于钢的强化及韧化作用。Nb含量过少，低于0.010％时，所产生的位错拖曳作用极其微小，不能起到提高韧性的作用。Nb添加过多会导致碳氮化合物尺寸大，形成大尺寸夹杂从而失去强韧化作用，且Nb价格较贵，故Nb的范围可控制在0.010％～0.030％。
Cu：Cu是扩大奥氏体相区，Cu单质可以作为第二相显著提升强度，能提升组织回火稳定性和强度。但Cu过高将导致Cu脆。因此Cu含量控制在0.030％～0.050％。
Al：Al是炼钢的主要脱氧剂，Al与N结合形成细小弥散分布的AlN，且与基体保持共格关系，能够起到强化和细化组织的作用，能够使疲劳裂纹萌生和扩展抗力增加，从而提高钢的持久强度。Al含量控制在0.015％～0.035％。
O和N：T.O在钢中形成氧化物夹杂，控制T.O≤0.0040％；N在钢中能形成氮化物，形成细小析出相细化组织，又能析出Fe4N，扩散速度慢，导致钢产生时效性，降低加工性能，因此将N控制在0.0080％内。
大功率风电偏航轴承尺寸大，需保证足够的强韧性。通过合金元素的添加能够有效提高淬透性从而提高强韧性。通过研究在合金元素中Mn提高淬透性及强度最为有效，系数为3.34；Mo通过提高回火稳定性及与Mn的交互左右对淬透性及强度贡献也较大，系数为3.0；Cr是主要的置换固溶元素和碳化物形成元素对强度的贡献系数为2.16；Cu在钢中不形成碳化物，通过固溶强化改变晶格形态从而对钢的淬透性及强度提高，系数分别为0.37和0.36；C为非金属元素，是钢中最主要的间隙固溶强化元素，对强度和韧性都有影响，故系数为0.54；Si是非金属元素，也是钢中主要的固溶强化元素，对钢的性能贡献为0.70。由于钢的强度与塑性和韧性具有反比例关系，即强度高时会导致塑性及韧性降低，为保证钢的综合性能不能一味提高强度。令钢中的强化因素用A表示，则10.5≤A≤13.8，
A＝(0.54×C％)×(1+3.34×Mn％)×(1+0.7×Si％)×(1.2+0.36×Cu％)×(1+0.37×Ni％)×(1+2.6
1×Cr％)×(1+3×Mo％)×(1+0.6×V％)×(1+0.7Nb％)。
轴承在服役过程中需要较好的接触疲劳性能，因此需对C、Mn、Cr、Mo、Cu、V、Nb的配比进行限定。由于C、Mn能显著提高钢浅层硬度、提高耐磨性从而提高接触疲劳性能；Cr、Mo、V、Nb能够与钢中的C、N形成第二相，第二相在钢中虽然能增加强度，但仍然与钢的基体不同，若尺寸较大可形成接触疲劳裂纹源，故对接触疲劳不利；Cu通过固溶强化与基体实现原子尺度结合对接触疲劳性能有利。但Nb在钢中形成的碳氮化合物具有硬度高的特点，且尺寸难以控制，易造成剥离从而降低接触疲劳性能。因此本发明一方面通过控制Nb的含量，另一方面通过热处理两次回火调质调控Nb碳氮化合物的尺寸，令钢中的接触疲劳因素用Y表示，则Y≥0.24％，
Y＝C％+(Mn％)/6-(Cr％+Mo％+V％+Nb％)/5+(Cu％)/15。
为获更好的低温韧性，满足轴承在低温环境工作需要。本专利没有添加贵金属Ni， 通过合金元素及微合金元素合理配比达到低温环境对韧性需求，由于钢中减少了贵金属Ni的添加，而Ni对低温韧性有利，为了保证钢的低温韧性需对Si、Mn、Cr、Mo、Cu等元素的配合进行控制。Si显著恶化低温韧性，增加回火脆性，故Si的系数为(-3)。Mn能够显著影响相变过程中的变体选择，增加相变中变体种类，从而提高低温韧性，但Mn易发生偏聚，故Mn的系数为0.8。Mo主要通过提高回火稳定性来提高低温韧性，对低温韧性的贡献有限，故Mo的系数为1.2。Cu能够提高与钢的基体实现原子程度结合对韧性有利，故系数为1。V、Nb通过第二相钉扎位错阻碍受到冲击后裂纹扩展路径，故系数均为2；即Z≥0.60％，
Z＝(-3)×Si％+0.8×Mn％+1.2×Mo％+1×Cu％+2×V％+2×Nb％。
本发明还公开了上述偏航轴承圈用钢及偏航轴承圈的生产工艺：电弧炉或转炉冶炼→LF炉精炼→RH或VD真空脱气→Φ380mm～Φ700mm圆坯连铸→圆坯加热→锻造→冲孔→辗环(半成品)→热处理→机加工→探伤→包装入库。
偏航轴承圈采用两次调质热处理，关键热处理工艺为：
一次调质：辗环后的偏航轴承圈半成品入炉温度≤600℃，一次淬火加热温度(T1，℃)为900～1000℃，一次淬火保温时间(t，min)由轴承圈壁厚(S，mm)和一次淬火加热温度(T1，℃)决定，S-T1/20≤t1≤S-T1/80；一次回火加热温度(T2，℃)为650～700℃，一次回火保温时间(t2，min)由轴承圈壁厚(S，mm)和一次回火加热温度(T2，℃)决定，S-T2/10≤t2≤S-T2/50，水冷。
二次调质：二次淬火加热温度(T3，℃)为800～900℃,保温时间(t3，min)由轴承圈壁厚(S，mm)和二次淬火加热温度(T3，℃)决定，S-T3/10≤t3≤S-T3/50，水冷；二次回火加热温度(T4，℃)为600～700℃，二次回火保温时间(t4，min)由轴承圈壁厚(S，mm)和二次回火加热温度(T4，℃)决定，1.5×S-T4/10≤t4≤1.5×S-T4/50，水冷。
本发明减少了贵金属Ni的使用，因此钢的低温韧性较差，为使产品达到特点性能需对热处理工艺进行创新优化。采用两次调质，虽然工艺变复杂但总体成本降低。本发明采用两次调质，其原因在于，一次调质后，钢的组织细化程度不够充分，不足以弥补贵金属缺少的不足。二次调质，钢经过再次加热及冷却，使组织和碳化物进一步细化，同时控制二次加热温度低于一次加热温度，使钢在加热过程中析出相不回融，从而保证晶粒尺寸细小，提升钢的整体性能。
奥氏体相变点受成分影响，由奥氏体相变点确定正火温度和淬火加热温度。由所需要的析出相种类、含量及尺寸选择回火加热温度。
本发明第一次调质加热温度为900-1000℃，一方面保证轴承圈在此温度下完全奥氏体化，同时控制温度不高于1000℃，保证钢在锻造过程中析出的第二项的尺寸不过于粗大，从而有助于后续产品韧性提高。在经过回火后，使得析出相主要为M23C6和MX型，有效提高钢的强度。
第二次调质的温度低于第一次调质，一方面能够使得第一次析出相作为形核质点使晶粒再次形核，从而使晶粒细化，另一方面有助于析出相在奥氏体化过程中回融小，能够提高韧性及疲劳性能。再次回火，回火加热温度低，使析出相的长大激活能不足，保证析出相细小。另外能够控制析出相种类，使析出相为M7C3、M23C6和MX，多种析出相能够使钢种组元丰富，避免单一相尺寸过大，降低疲劳性能。
制得的轴承圈1/2壁厚(壁厚≥240mm)处抗拉强度≥950MPa、屈服强度≥850MPa、-40℃KV2≥80J；2000MPa接触应力作用下，接触疲劳寿命≥100万次，满足大功率风电服役20年需要。
3.有益效果
相比于现有技术，本发明的有益效果为：
(1)本发明的一种高强韧高接触疲劳大功率风电偏航轴承圈通过合理的化学配比和热处理工艺，在无贵金属Ni的添加的条件下，仍能保持较高的低温韧性；
(2)本发明的一种高强韧高接触疲劳大功率风电偏航轴承圈1/2壁厚(壁厚≥240mm)处抗拉强度≥950MPa、屈服强度≥850MPa、-40℃KV2≥80J，2000MPa接触应力作用下，接触疲劳寿命≥100万次，满足大功率风电服役20年需要。
附图说明
以下将结合附图和实施例来对本发明的技术方案作进一步的详细描述，但是应当知道，这些附图仅是为解释目的而设计的，因此不作为本发明范围的限定。此外，除非特别指出，这些附图仅意在概念性地说明此处描述的结构构造，而不必要依比例进行绘制。
图1为本发明实施例1制得的轴承圈1/2壁厚处的微观形貌图，(a)一次淬火；(2)二次淬火后；
图2为本发明对比例2制得的轴承圈1/2壁厚处的微观形貌图，(a)一次淬火；(2)二次淬火后；
图3为实施例1制得的轴承圈1/2壁厚处EBSD分析图；
图4为对比例2制得的轴承圈1/2壁厚处EBSD分析图。
具体实施方式
下文对本发明的示例性实施例的详细描述参考了附图，该附图形成描述的一部分，在该附图中作为示例示出了本发明可实施的示例性实施例。尽管这些示例性实施例被充分详细地描述以使得本领域技术人员能够实施本发明，但应当理解可实现其他实施例且可在不脱离本发明的精神和范围的情况下对本发明作各种改变。下文对本发明的实施例的更详细的描述并不用于限制所要求的本发明的范围，而仅仅为了进行举例说明且不限制对本发明的特点和特征的描述，以提出执行本发明的最佳方式，并足以使得本领域技术人员能够实施本发明。因此，本发明的范围仅由所附权利要求来限定。
本发明公开了一种经济性高寿命大功率风电偏航轴承圈用钢，按重量百分比含有：C 0.47％～0.57％、Si 0.10％～0.30％、Mn 0.70％～0.90％、Cr 1.30％～1.50％、Mo 0.30％～0.50％、Cu 0.030％～0.050％、V 0.035％～0.075％、Nb 0.010％～0.030％、Cu 0.030％～0.050％、Al 0.015％～0.025％、P≤0.015％、S≤0.010％、O≤0.0040％。其余为Fe和其它不可避免的杂质。化学成分配比应符合：
1)10.5≤(0.54×C％)×(1+3.34×Mn％)×(1+0.7×Si％)×(1.2+0.36×Cu％)×(1+0.37×Ni％)×(1+2.61×Cr％)×(1+3×Mo％)×(1+0.6×V％)×(1+0.7Nb％)≤13.8；
2)0.24％≤C％+(Mn％)/6-(Cr％+Mo％+V％+Nb％)/5+(Cu％)/15；
3)0.60％≤(-3)×Si％+0.8×Mn％+1.2×Mo％+1×Cu％+2×V％+2×Nb％。
热处理工艺参数应符合：
1)一次调质的淬火，S-T1/20≤t1≤S-T1/80；一次调质的回火，S-T2/10≤t2≤S-T2/50。
2)二次调质的淬火，S-T3/10≤t3≤S-T3/50；二次调质的回火，1.5×S-T4/10≤t4≤1.5×S-T4/50。
本发明提供了该钢的热处理方法，制得的钢具有优秀的强韧性和接触疲劳性能，适用于制造大功率风电用偏航轴承(轴圈壁厚≥240mm)。本发明还公开了利用该钢生产轴承圈的工艺。
本发明采用特定成分的钢种，实施例和对比例的钢种成分见表1。
表1本发明实施例化学成分(wt％)
本发明的钢的生产工艺如下：
电炉冶炼：出钢前定氧，出钢过程采用留钢操作，避免下渣；
LF炉：将C、Si、Mn、Cr、Mo、V、Nb、Cu等元素调至目标值；
真空脱气：纯脱气时间≥15分钟，保证真空处理后[H]含量≤1.5ppm，避免钢中出现白点，引起氢脆现象；
连铸：中包钢水目标温度控制在液相线温度以上10～40℃，连铸φ380mm～φ700mm圆坯。
轴承圈制造路线：圆坯(直径600及700mm)加热→锻造→冲孔→辗环(半成品)。
轴承圈热处理：台车炉加热→保温→正火→淬火→回火→保温→水冷。
轴承圈加工路线：轴承圈粗车→探伤→阀体精车→修磨→探伤→包装入库。
性能检测方法如下：
组织：在轴承圈延长体上取样，在延长体的表层12.5mm处和1/2厚度(厚度为240mm)位置内取样进行金相、晶粒尺寸分析。
表2本发明实施例及对比例的锻造工艺情况列表
性能：在轴承圈延长体上取样，在延长体的表层12.5mm处和1/2厚度(厚度为240mm)位置内取样取拉伸、冲击、接触疲劳试样，参照GB/T228、GB/T229、JB/T 10510进行力学性能试验。热处理工艺如表2所示，力学性能如表3所示。
表3本发明实施例及对比例的疲劳性能检测情况列表

实施例1～3的钢化学成分组成、生产方法均得到适当控制，其化学成分保证了17.0≤A≤20.3，0.17％≤Y，0.30％≤Z钢的强度、塑性、韧性及接触疲劳性能均较好。对比例1、2是化学组分配比不合适，其中对比例2化学成分控制不当，导致材料强度过低，塑韧性不足，热处理工艺不当导致整体性能不理想；对比例3成分设计合理，但是热处理工艺不当，导致材料的强度、韧性不足，且抗接触疲劳性能不足。
图1为实施例1制得的轴承圈1/2壁厚处的微观形貌图，一次淬火后晶粒尺寸约为34微米，经过2次淬火晶粒细化为26.6微米。通过相应的热处理使晶粒细化，晶粒细化后能有效提高材料的强度、低温韧性和疲劳性能。
而对比例2中的钢虽然采用了2次调质，但是化学组分和工艺配合不恰当，如图2所示，晶粒并未显著细化，晶粒尺寸达33.9微米，导致性能较差。
图3和图4进一步说明了组分及工艺造成性能差距的微观原因。实施例1中的EBSD分析显示，微观组织细小，均匀。而对比例2的微观组织粗大。细小的组织一方面能够使材料在受到外界作用冲击时，裂纹扩展的路径增加、消耗冲击能力，提高低温韧性；另一方面提高材料的内应力及协调变形能力，从而提高材料的疲劳性能。

Claims (9)

  1. 一种经济性高寿命大功率风电偏航轴承圈用钢，其特征在于，按重量百分比含有：C 0.47％～0.57％、Si 0.10％～0.30％、Mn 0.70％～0.90％、Cr 1.30％～1.50％、Mo 0.30％～0.50％、Cu 0.030％～0.050％、V 0.035％～0.075％、Nb 0.010％～0.030％、Cu 0.030％～0.050％、Al 0.015％～0.025％、P≤0.015％、S≤0.010％、O≤0.0040％，N≤0.0080％，其余为Fe和其它不可避免的杂质。
  2. 根据权利要求1所述一种经济性高寿命大功率风电偏航轴承圈用钢，其特征在于，化学成分配比应符合：
    1)10.5≤(0.54×C％)×(1+3.34×Mn％)×(1+0.7×Si％)×(1.2+0.36×Cu％)×(1+0.37×Ni％)×(1+2.61×Cr％)×(1+3×Mo％)×(1+0.6×V％)×(1+0.7Nb％)≤13.8；
    2)0.24％≤C％+(Mn％)/6-(Cr％+Mo％+V％+Nb％)/5+(Cu％)/15；
    3)0.60％≤(-3)×Si％+0.8×Mn％+1.2×Mo％+1×Cu％+2×V％+2×Nb％。
  3. 根据权利要求2所述一种高强韧高接触疲劳大功率风电偏航轴承圈用钢，其特征在于，所述钢中的析出相包括M7C3、M23C6和MX。
  4. 一种利用权利要求1-3任一项所述经济性高寿命大功率风电偏航轴承圈用钢生产轴承圈的工艺，其特征在于，包括：电弧炉或转炉冶炼→LF炉精炼→RH或VD真空脱气→圆坯连铸→圆坯加热→锻造→冲孔→辗环→热处理→机加工→探伤→包装入库。
  5. 根据权利要求4所述一种经济性高寿命大功率风电偏航轴承圈的生产工艺，其特征在于，所述热处理包括两次调质，包括：
    一次调质：一次淬火；一次回火；
    二次调质：二次淬火；二次回火。
  6. 根据权利要求5所述一种经济性高寿命大功率风电偏航轴承圈的生产工艺，其特征在于，一次调质过程中，入炉温度≤600℃，一次淬火加热温度(T1，℃)为900～1000℃，一次淬火保温时间(t，min)由轴承圈壁厚(S，mm)和一次淬火加热温度(T1，℃)决定，S-T1/20≤t1≤S-T1/80；一次回火加热温度(T2，℃)为650～700℃，一次回火保温时间(t2，min)由轴承圈壁厚(S，mm)和一次回火加热温度(T2，℃)决定，S-T2/10≤t2≤S-T2/50，水冷。
  7. 根据权利要求6所述一种经济性高寿命大功率风电偏航轴承圈的生产工艺，其特征在于，二次调质过程中，二次淬火加热温度(T3，℃)为800～900℃,保温时间(t3，min)由轴承圈壁厚(S，mm)和二次淬火加热温度(T3，℃)决定，S-T3/10≤t3≤S-T3/50，水冷；二次回火加热温度(T4，℃)为600～700℃，二次回火保温时间(t4，min)由轴承圈壁厚(S，mm)和二次回火加热温度(T4，℃)决定，1.5×S-T4/10≤t4≤1.5×S-T4/50，水冷。
  8. 一种根据权力要求4-7任一项所述经济性高寿命大功率风电偏航轴承圈的生产工艺制得的轴承圈，其特征在于，轴承圈壁厚≥240mm，制得的轴承圈1/2壁厚处抗拉强度≥950MPa、屈服强度≥850MPa、-40℃KV2≥80J；2000MPa接触应力作用下，接触疲劳寿命≥100万次。
  9. 根据权利要求8所述一种高强韧高接触疲劳大功率风电偏航轴承圈，其特征在于，所述轴承圈回火后表层12.5mm处的索氏体含量为100％，1/2壁厚处的索氏体含量≥91％。
PCT/CN2023/114602 2022-11-04 2023-08-24 一种经济性高寿命大功率风电偏航轴承圈用钢、轴承圈及生产工艺 WO2024093461A1 (zh)

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