WO2020073576A1 - 一种风力发电机主轴轴承用钢及其生产方法 - Google Patents

一种风力发电机主轴轴承用钢及其生产方法 Download PDF

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WO2020073576A1
WO2020073576A1 PCT/CN2019/075851 CN2019075851W WO2020073576A1 WO 2020073576 A1 WO2020073576 A1 WO 2020073576A1 CN 2019075851 W CN2019075851 W CN 2019075851W WO 2020073576 A1 WO2020073576 A1 WO 2020073576A1
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steel
main shaft
continuous casting
temperature
wind turbine
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PCT/CN2019/075851
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English (en)
French (fr)
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陈敏
李锋
许晓红
耿克
白云
黄镇
尹青
翟蛟龙
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江阴兴澄特种钢铁有限公司
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Priority to KR1020217012169A priority Critical patent/KR102516710B1/ko
Priority to EP19871603.7A priority patent/EP3865595B1/en
Publication of WO2020073576A1 publication Critical patent/WO2020073576A1/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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/12—Accessories for subsequent treating or working cast stock in situ
    • B22D11/124—Accessories for subsequent treating or working cast stock in situ for cooling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/16—Controlling or regulating processes or operations
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    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/02—Hardening articles or materials formed by forging or rolling, with no further heating beyond that required for the formation
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    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
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    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
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    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/84—Controlled slow cooling
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    • C21D6/00—Heat treatment of ferrous alloys
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    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/02—Modifying the physical properties of iron or steel by deformation by cold working
    • C21D7/04—Modifying the physical properties of iron or steel by deformation by cold working of the surface
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    • C21D7/00—Modifying the physical properties of iron or steel by deformation
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/28—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for plain shafts
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C33/00—Parts of bearings; Special methods for making bearings or parts thereof
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    • F16C33/32—Balls
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
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    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C33/00—Parts of bearings; Special methods for making bearings or parts thereof
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    • F16C33/34—Rollers; Needles
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C33/00—Parts of bearings; Special methods for making bearings or parts thereof
    • F16C33/30—Parts of ball or roller bearings
    • F16C33/58—Raceways; Race rings
    • F16C33/62—Selection of substances
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C33/00—Parts of bearings; Special methods for making bearings or parts thereof
    • F16C33/30—Parts of ball or roller bearings
    • F16C33/58—Raceways; Race rings
    • F16C33/64—Special methods of manufacture
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C2202/00—Solid materials defined by their properties
    • F16C2202/02—Mechanical properties
    • F16C2202/06—Strength or rigidity
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C2202/00—Solid materials defined by their properties
    • F16C2202/02—Mechanical properties
    • F16C2202/10—Porosity
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    • F16C2204/62—Low carbon steel, i.e. carbon content below 0.4 wt%
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    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C2300/00—Application independent of particular apparatuses
    • F16C2300/10—Application independent of particular apparatuses related to size
    • F16C2300/14—Large applications, e.g. bearings having an inner diameter exceeding 500 mm
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
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    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C2360/00—Engines or pumps
    • F16C2360/31—Wind motors

Definitions

  • the invention belongs to the technical field of metallurgy, and more specifically relates to bearing steel and corresponding production processes.
  • Wind energy is currently the most promising renewable energy source, and it is a clean, non-polluting green energy source.
  • the use of wind energy has the broadest prospects and is increasingly valued by countries around the world. huge.
  • the wind turbine bearing is an important transmission device in the wind turbine, and the application bearing of a wind turbine can be up to 32 sets. Therefore, the selection of bearings is very important to ensure the safe and stable operation of wind turbines.
  • the bearings of wind turbines are generally divided into the following types: yaw bearings, pitch bearings, main shaft bearings, gearbox bearings and generator bearings. The technical requirements are different depending on the bearing type.
  • the working conditions of wind turbine bearings are relatively harsh, with a wide range of temperature, humidity and load changes.
  • the main shaft bearing of the wind turbine is the main component for absorbing the wind load and the transmission load. Its performance not only affects the transmission efficiency, but also determines the maintenance cost of the main drive chain. The most important thing is that because of the inconvenience and high cost of lifting and replacing bearings, the cost of one installation and disassembly can be as high as hundreds of thousands to millions, so the 20-year service life and high reliability have become a wind turbine.
  • the basic requirements of the main shaft bearings due to the harsh working conditions of the wind turbine and the long-life and high-reliability use requirements, the bearing has a high technical complexity. It is recognized as one of the most difficult technologies for localization and has become a wind power generation in China. The weakness of manufacturing development.
  • the main shaft bearing steel for wind turbines is mainly produced by electroslag remelting process
  • the carburizing bearing steel G20Cr2Ni4 is mainly produced by electroslag remelting process. Since the steel produced by the electroslag remelting process has many quality advantages such as fine and uniform distribution of non-metallic inclusion particles, high uniformity of structure and high density, the quality stability has been good.
  • the electroslag remelting production process also has obvious disadvantages such as production efficiency, very low production capacity, very high energy consumption and very high production costs. Therefore, the market competitiveness of electroslag remelting steel is very low.
  • this application uses vacuum degassing, continuous casting, and rolling high-efficiency, large-capacity, and low-cost process routes to optimize research and control of key processes to obtain high purity of steel. Degree, high organization uniformity and high density, replace the current electroslag remelting production process, and make the performance meet the requirements of the wind turbine main shaft bearing steel.
  • the present invention invents a new vacuum degassing + continuous Steel for spindle bearings manufactured by casting production technology.
  • Microscopic inclusions include Class A and C plastic inclusions and Class B and D brittle inclusions. Because the brittle inclusions are hard particles in the steel, stress concentration occurs during the operation of the bearing, and at the same time, it is easy to separate from the matrix during the deformation of the steel to generate cracks, which is more likely to cause cracking due to the stress concentration. The longer it is, the greater the harm; and the plastic inclusions are soft particles in the steel, and it is not easy to separate from the matrix during the deformation of the steel, so its harm is less.
  • the present invention requires the microscopic brittle inclusions to be fine: B fine system ⁇ 1.5 grade, B coarse system ⁇ 1.0 grade, D fine system ⁇ 1.0 grade, D coarse system ⁇ 1.0 grade, DS series ⁇ 1.0 grade. Specific requirements are shown in Table 1 below.
  • the macroscopic inclusions significantly reduce the wear resistance of the steel and cause serious stress concentration, which can easily lead to early failure during the use of the bearing.
  • the macro defects of the present invention are according to SEP 1927 (Ultrasonic Determination Method for Purity of Forged Steel Bar Purity) High-frequency immersion flaw detection method inspection, the length of a single inclusion does not exceed 5mm.
  • the uniformity and density of the low-power steel structure have an impact on the life of the bearing.
  • the present invention requires the low-power structure to adopt the GB / T 1979 rating for the low-power steel structure. It requires center looseness ⁇ 1.5, general looseness ⁇ 1.0, ingot type Segregation ⁇ 1.0 grade, central segregation ⁇ 1.5 grade, and no shrinkage holes, cracks and subcutaneous bubbles are allowed.
  • the present invention puts forward the requirements for the grain size, which requires the grain size ⁇ 5, and the tensile strength requirement ⁇ 1200MPa, impact performance AKU requirement ⁇ 65J, in order to ensure the cold workability of the steel , Requires hardness ⁇ 260HBW, and decarburization requires ⁇ 0.8% D (D is the diameter).
  • the hardenability of the steel of the present invention the requirements for hardenability are shown in Table 2 below.
  • a steel for main shaft bearings of wind turbines the chemical composition is: C: 0.10 to 0.30%, Si: 0.10 to 0.50%, Mn: 0.30 to 0.80%, Cr: 1.30 ⁇ 1.60%, S ⁇ 0.025%, P ⁇ 0.025%, Ni: 3.25 ⁇ 3.75%, Cu ⁇ 0.30%, Mo: 0.15 ⁇ 0.25%, Al: 0.005-0.05%, N: 0.005-0.015%, Ca ⁇ 0.0010 %, Ti ⁇ 0.003%, O ⁇ 0.0015%, As ⁇ 0.04%, Sn ⁇ 0.03%, Sb ⁇ 0.005%, Pb ⁇ 0.002%, the balance is Fe and inevitable impurities.
  • the design basis of the chemical composition of the steel for the main shaft bearing of the wind turbine of the present invention is as follows:
  • the carbon content is one of the most important elements that determine the hardness and hardenability of the core of the part after carburizing and quenching. Increasing the C content can increase the hardness and strength of the steel, thereby improving the wear resistance. However, excessively high C content is detrimental to the toughness of steel. Therefore, for carburized bearing steel, the inside of the bearing steel must have sufficient impact resistance and sufficient strength.
  • the present invention controls its content to 0.10-0.30%
  • Si is a deoxidizing element in steel and improves the hardness and strength of steel in the form of solid solution strengthening. It reduces the diffusion rate of C in ferrite, makes carbides precipitated during tempering difficult to aggregate, increases the tempering stability of steel, and enables steel to reduce internal stress in the material when tempering at a lower temperature. Maintain high hardness. In addition, Si reduces oxidation during frictional heating and improves the cold deformation hardening rate of steel to improve the wear resistance of the material. However, when the Si content is high, the toughness of the steel decreases, and Si increases the overheating sensitivity, cracking, and decarburization tendency in the steel. The invention controls the Si content to be 0.10 to 0.50%.
  • Mn is an element that is effective for strengthening steel and plays a role of solid solution strengthening, and Mn can improve the hardenability of steel and improve the hot workability of steel.
  • Mn can eliminate the influence of S (sulfur): Mn can form high melting point MnS with S in steel smelting, thereby weakening and eliminating the adverse effects of S.
  • high Mn content will reduce the toughness of steel.
  • the Mn content of the present invention is controlled at 0.30 to 0.80%.
  • Cr is a carbide-forming element and can improve the hardenability, wear resistance and corrosion resistance of steel. But the Cr content is too high, combined with the carbon in the steel, it is easy to form large carbides, this insoluble carbides reduce the toughness of the steel.
  • chromium can adjust the hardenability, improve the wear resistance of the carburized layer, and improve the mechanical properties of the steel. In addition, chromium can stabilize the heat treatment process of steel, obtain good carburizing properties, and reduce the unevenness of carbides.
  • the range of Cr content of the present invention is determined to be 1.30 to 1.60%.
  • Al is added as a deoxidizing element in steel.
  • Al and N form finely dispersed aluminum nitride inclusions to refine grains.
  • brittle inclusions such as large particles of Al 2 O 3 are easily formed during the molten steel smelting process, which reduces the purity of the molten steel and affects the service life of the finished product.
  • the range of Al content of the present invention is determined to be 0.005% -0.05%.
  • Nickel can reduce the ability of the surface to absorb carbon atoms in steel, accelerate the diffusion of carbon atoms in austenite, and reduce the carbon concentration in the carburized layer, so nickel can slow down the carburizing rate; at the same time, the addition of nickel can improve the steel toughness.
  • the range of Ni content in the present invention is determined to be 3.25% -3.75%.
  • the main role of molybdenum in carburizing bearing steel is to improve the hardenability and improve the mechanical properties of the steel, especially to improve the toughness. In addition, it can also improve the wear resistance and carburizing properties of steel.
  • the range of Mo content of the present invention is determined to be 0.15% -0.25%.
  • the N content of the present invention is determined to be 0.005-0.015%
  • the Ca content increases the number and size of point oxides in the steel. At the same time, due to the high hardness and poor plasticity of the point oxides, they do not deform when the steel is deformed, and it is easy to form voids at the interface, which deteriorates the performance of the steel.
  • the range of the Ca content of the present invention is determined to be ⁇ 0.001%.
  • Ti element and N element can form titanium nitride inclusions. Due to its high hardness and sharp angle, it is easy to cause stress concentration during bearing operation to have a greater impact on bearing life, so it is determined that Ti ⁇ 0.0030%
  • Oxygen content represents the total amount of oxide inclusions, oxide brittle inclusions limit the service life of finished products, a large number of tests have shown that the reduction of oxygen content is significantly beneficial to improve the purity of steel, especially to reduce the content of steel oxide brittle inclusions.
  • the range of oxygen content of the present invention is determined to be ⁇ 0.0015%.
  • P element causes element segregation during the solidification of steel. Its dissolution in ferrite distorts and coarsens the grains and increases cold brittleness. Therefore, it is determined that P ⁇ 0.025%; S element is easy to cause hot brittleness of steel and reduce ductility And toughness, the sulfide formed also destroys the continuity of the steel, so it is determined that S ⁇ 0.025%.
  • Trace elements such as As, Sn, Sb, and Pb are non-ferrous metals with low melting points. They exist in steel, causing soft spots on the surface of the parts and uneven hardness. Therefore, they are regarded as harmful elements in steel. The range is determined as As ⁇ 0.04%, Sn ⁇ 0.03%, Sb ⁇ 0.005%, Pb ⁇ 0.002%.
  • Another object of the present application is to provide a method for producing steel for main shaft bearings of wind turbines, which uses continuous casting instead of electroslag remelting to smelt blanks.
  • the main steps are as follows,
  • slow cooling of continuous casting slab is to cool the continuous casting slab down to the pit, the temperature of the lower pit is more than 600 °C, the slow cooling time of the lower pit is more than 48 hours, and the pit The temperature is less than 200 °C, and softening annealing is performed within 24 hours after the pit is raised; the softening annealing temperature is 600-700 °C, the heating and holding time is ⁇ 10h, and then it is cooled to 450 °C with the furnace and then air-cooled to room temperature;
  • the rolling temperature is controlled at 800-950 ° C, so that the final rolling is carried out in the non-recrystallization temperature range, so that the deformed austenite grains are elongated, and there are a large number of deformation zones in the grains, making the ferrite grains after phase transformation Refinement to improve the strength and toughness of steel;
  • the rolled bar is slowly cooled in the pit at 480 °C and above, the slow cooling time is more than 60 hours, the pit temperature is less than 200 °C, the bar is 24 hours after the pit Softening annealing treatment is carried out again; the softening annealing temperature is 600-700 °C, the holding time is ⁇ 7h, and then it is cooled to 500 °C with the furnace and then air-cooled to room temperature;
  • step 1 is to sequentially smelt the raw materials through hot metal pretreatment KR, electric furnace or converter smelting, LF refining, RH or VD vacuum degassing to obtain pure molten steel that meets the chemical composition.
  • Smelting raw materials use high-quality hot metal, scrap steel and raw and auxiliary materials, select high-quality refractory materials, smelting uses high-performance refining synthetic slag, control the number and shape of various types of steel inclusions, the ladle maintains a long-term inclusion removal process, allowing non-metallic inclusions Fully float, select special refining slag and tundish slag to absorb the inclusions.
  • continuous casting in step 2 uses tundish induction heating, light reduction and electromagnetic stirring to effectively improve the segregation of the casting slab and the material structure; the use of large-section full-protection continuous casting makes the steel compression ratio greater than 4, effectively ensuring the material Density, continuous casting adopts low superheat casting, continuous casting superheat is controlled at ⁇ 35 °C, which can effectively improve the uniformity of the material.
  • the finishing in the step 6 includes finishing processes such as straightening and flaw detection, so as to obtain a target bar finished product.
  • the main production process features are as follows:
  • Molten steel must be pretreated with molten iron, while strictly controlling the quality of scrap steel, preferably low-titanium alloys, deoxidizers and refractory materials; converter tapping adopts slag blocking and tapping, slag scraping and other control technologies to solve the problem There is a problem of high content of technically harmful elements Ti, Ca, As, Sn, Pb, Sb;
  • Continuous casting adopts low superheat casting, and adopts tundish induction heating, soft reduction and electromagnetic stirring technology to effectively improve the casting billet segregation and material organization; adopts large-section full-protection casting to ensure that the steel compression ratio is greater than 4, thus ensuring The density of the material;
  • the continuous casting billet and rolled material are treated with slow cooling and softening annealing to avoid cracking of the steel due to changes in surface and internal thermal stress and structural stress.
  • the production process using vacuum degassing and continuous casting greatly reduces the production cycle, improves production efficiency, effectively reduces manufacturing costs, and realizes large-scale production, compared with electroslag remelting technology. And help to improve the material composition and product quality stability;
  • the steel for the main shaft bearing of the wind turbine produced by the invention meets the following index requirements:
  • Figure 1 is a low-magnification view of an embodiment product
  • Figure 2 is a low-magnification view of a comparative product.
  • Example 1 of the invention 1.0 1.0 1.0 no no no Embodiment 2 of the present invention 1 1.0 1.0 1.0 no no no Embodiment 3 of the present invention 1 1.0 1.0 1.0 1.0 no no no Contrast steel 1.5 1.0 1.0 1.0 no no no no no
  • the low magnification structure of any product in the examples is shown in FIG. 1, and the low magnification structure of the comparative example is shown in FIG. 2.
  • the manufacturing process of the steel for the main shaft bearing of the wind turbine is the use of hot metal pretreatment + top-bottom double-blown converter BOF (high-power electric arc furnace EAF)-ladle refining furnace LF-vacuum circulation degassing furnace RH (VD furnace) -Large-section continuous casting CCM Dalian billet-continuous rolling-finishing forming process produces steel.
  • BOF high-power electric arc furnace EAF
  • RH VD furnace
  • the tapping end point C of the three embodiments is controlled at ⁇ 0.10%
  • the end point P is controlled at ⁇ 0.015% or less
  • the continuous casting superheat is controlled at 10-35 ° C.
  • Slowly cool the lower pit of the continuous casting billet the temperature of the lower pit is greater than 600 ° C
  • the slow cooling time of the lower pit is greater than 48 hours
  • the temperature of the exit pit is less than 200 ° C
  • softening annealing is performed within 24 hours after the pit is lifted.
  • the softening annealing temperature is 600-700 ° C
  • the heating and holding time is ⁇ 10h
  • it is cooled to 450 ° C with the furnace and then air-cooled to room temperature.
  • the steel rolling heating, rolling and cooling processes are shown in Table 8 below. The bar is softened and annealed again within 24 hours after pitting.
  • the softening annealing temperature is 600-700 °C, and the holding time is ⁇ 7h, and then it is cooled to 500 °C with the furnace and then air-cooled to room temperature. Then, the bar is subsequently straightened and flaw-detected to obtain the target bar product.
  • the steel for the main shaft bearing of wind turbines in the embodiments of the present invention has harmful elements such as oxygen, titanium, and non-metallic inclusions.
  • the control level is obviously better, that is, the purity of the steel is significantly better than the products produced by the electroslag remelting technology.
  • the low magnification of the present invention is not worse than the G20Cr2Ni4 steel produced by the electroslag remelting process, reflecting The uniformity and density of the present invention are comparable to the quality of steel produced by the electroslag remelting process.
  • the steel for wind power spindle bearings produced by the vacuum degassing and continuous casting production process of the present invention can replace the original electroslag remelting process, which significantly improves production efficiency, reduces production costs, and significantly enhances product competitiveness.
  • the present invention relates to a steel for main shaft bearings of wind turbines and a production method thereof.
  • a high-efficiency, large-capacity, low-cost process of vacuum degassing, continuous casting, and rolling is adopted Route, optimize research and control of key processes, so that the steel has obtained high purity, high uniformity of structure and high density, which can completely replace the original electroslag remelting process. More competitive in production efficiency, production cost and product quality stability.
  • the present invention also includes other embodiments. Any technical solution formed by equivalent transformation or equivalent replacement should fall within the protection scope of the claims of the present invention.

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Abstract

一种风力发电机主轴轴承用钢及其生产方法，该钢的化学成分为：C：0.10～0.30％，Si：0.10～0.50％，Mn：0.30～0.80％，Cr：1.30～1.60％，S≤0.025％，P≤0.025％，Ni：3.25～3.75％，Cu≤0.30％，Mo：0.15～0.25％，Al：0.005-0.05％，N：0.005-0.015％，Ca≤0.0010％，Ti≤0.003％，O≤0.0015％，As≤0.04％，Sn≤0.03％，Sb≤0.005％，Pb≤0.002％，余量为Fe及不可避免的杂质。生产方法为钢水冶炼-大截面连铸CCM大连铸坯—连轧—精整，连铸坯和轧坯均进行入坑缓冷和软化退火，钢材具有高的纯净度、组织均匀性和致密度，能够替代电渣钢，并满足风力发电机主轴轴承用钢的要求。

Description

一种风力发电机主轴轴承用钢及其生产方法 技术领域
本发明属于冶金技术领域，更具体的是涉及轴承钢及相应的生产工艺。
背景技术
风能是目前最有发展前景的可再生能源，是一种洁净、无污染的绿色能源，在各种可替代能源中，风能的利用前景最为广阔，越来越受到世界各国的重视，其蕴量巨大。
风力发电机轴承是风力发电机组中重要的传动装置，一台风力发电机组应用轴承最多可达32套。所以选好轴承对保证风电机组的安全稳定运行非常重要。风力发电机组轴承一般分为以下几种：偏航轴承、变桨轴承、主轴轴承、增速器轴承和发电机轴承。根据轴承类型不同，技术要求也不同。
风力发电机轴承的工况条件比较恶劣，经受温度、湿度和载荷变化范围很大。其中，风力发电机的主轴轴承是吸收风力作用载荷和传递载荷的主要部件，其性能的好坏不仅对传递效率有影响，而且也决定了主传动链的维护成本。而最关键的是，由于吊装和更换轴承极为不便且成本较高，一次安装拆卸费用即高达几十万到上百万，因此，20年的使用寿命及高可靠性，就成为对风力发电机的主轴轴承的基本要求。综上所述，由于风力发电机组的恶劣工况和长寿命高可靠性的使用要求，使得轴承具有较高的技术复杂度，是公认的国产化难度最大的技术之一，也成为我国风力发电制造业发展的软肋。
目前，在全球风力发电机轴承市场占据统治地位的主要是国外轴承巨头。国内风力发电机轴承企业的产能主要集中在技术门槛相对较低的偏航轴承和变桨轴承上；而主轴轴承和增速器轴承的技术含量很高，还是依靠进口，国内尚处于研制阶段。
当前，风力发电机的主轴轴承用钢主要采用电渣重熔工艺生产的轴承钢，主要采用渗碳轴承钢G20Cr2Ni4，采用电渣重熔工艺生产。由于电渣重熔工艺生产的钢材具有非金属夹杂物颗粒细小且分布均匀、组织均匀性高和致密度高等诸多质量优势，因此，其质量稳定性一直较好。但电渣重熔生产工艺也存在生产效率、产能非常低，能耗和生产成本非常高等明显的劣势，因此，电渣重熔钢的市场竞争力很低。
发明内容
本申请在目前生产渗碳轴承钢的基础上，利用真空脱气、连铸、轧制的高效率、大产能、低成本工艺路线，对关键工序进行优化研究和控制，使钢材获得高的纯净度、高 的组织均匀性和高的致密度，替代当前的电渣重熔生产工艺，并使性能满足风力发电机的主轴轴承用钢的要求。
为了满足风力发电机主轴轴承用钢材的纯净度、均匀性、致密性、耐磨性及淬透性要求，本发明通过对钢材化学成分进行合理设计，发明了一种新的真空脱气+连铸生产技术制造的主轴轴承用钢。
本发明对微观夹杂物及宏观夹杂物都提出严格的要求，微观夹杂物包括A类、C类塑性夹杂物和B类、D类脆性夹杂物。因脆性夹杂物在钢中是硬的质点，在轴承运转时产生应力集中，同时在钢的变形过程中易与基体分离产生裂纹，更加剧了应力集中易引起开裂，夹杂物颗粒越大、长度越长其危害越大；而塑性夹杂物在钢中是软的质点，在钢的变形过程中不易与基体之间产生分离，因此其危害较小。
本发明要求微观脆性夹杂物细小：B细系≤1.5级、B粗系≤1.0级、D细系≤1.0级，D粗系≤1.0级、DS系≤1.0级，具体要求见下表1。而宏观夹杂物显著降低了钢的耐磨性、造成严重的应力集中易引起轴承使用过程中的的早期失效，本发明的宏观缺陷按SEP 1927(锻轧钢棒纯净度水浸超声测定方法)水浸高频探伤方法检验，单个夹杂物长度不超过5mm。
表1
Figure PCTCN2019075851-appb-000001
钢材低倍组织的均匀性和致密度对轴承的寿命有影响，本发明要求低倍组织采用GB/T 1979对钢材低倍组织评级，要求中心疏松≤1.5级、一般疏松≤1.0级、锭型偏析≤1.0级，中心偏析≤1.5级，并且不允许出现缩孔、裂纹及皮下气泡。
为保证钢材的强度、韧性及耐冲击性，本发明对晶粒度提出要求，要求晶粒度≥5级，同时对抗拉强度要求≥1200MPa，冲击性能AKU要求≥65J，为保证钢材的冷加工性能，要求硬度≤260HBW，脱碳要求≤0.8％D(D为直径)。为保证适用于主轴轴承使用要求，本发明钢材的淬透性能：对淬透性的要求见下表2。
表2
Figure PCTCN2019075851-appb-000002
本发明解决上述问题所采用的技术方案为：一种风力发电机主轴轴承用钢，化学成分为：C：0.10～0.30％，Si：0.10～0.50％，Mn：0.30～0.80％，Cr：1.30～1.60％，S≤0.025％，P≤0.025％，Ni：3.25～3.75％，Cu≤0.30％，Mo：0.15～0.25％，Al：0.005-0.05％， N：0.005-0.015％，Ca≤0.0010％，Ti≤0.003％，O≤0.0015％，As≤0.04％，Sn≤0.03％，Sb≤0.005％，Pb≤0.002％，余量为Fe及不可避免的杂质。本发明的风力发电机主轴轴承用钢的化学成分设计依据如下：
1)C含量的确定
在渗碳轴承钢中，碳含量是决定渗碳淬火后零件心部硬度和淬透性最重要的元素之一。提高C含量，能够提高钢材的硬度和强度，进而提高耐磨性。但过高的C含量对钢的韧性不利。因此对于渗碳轴承钢，轴承钢内部既要耐冲击还要有足够的强度。本发明控制其含量为0.10-0.30％
2)Si含量的确定
Si是钢中的脱氧元素，并以固溶强化形式提高钢的硬度和强度。它降低C在铁素体中的扩散速度使回火时析出的碳化物不易聚集，增加钢的回火稳定性，使钢材在较低温度回火时既能降低材料中的内应力也使其保持高的硬度。另外，Si减少摩擦发热时的氧化作用和提高钢的冷变形硬化率从而提高材料的耐磨性。但是，Si含量较高时钢材的韧性降低，而且Si使钢中的过热敏感性、裂纹和脱碳倾向增大。本发明控制Si含量为0.10～0.50％。
3)Mn含量的确定
Mn作为炼钢过程的脱氧元素，是对钢的强化有效的元素，起固溶强化作用，而且Mn能提高钢的淬透性，改善钢的热加工性能。Mn能消除S(硫)的影响：Mn在钢铁冶炼中可与S形成高熔点的MnS，进而消弱和消除S的不良影响。但Mn含量高，会降低钢的韧性。本发明的Mn含量控制在0.30～0.80％。
4)Cr含量的确定
Cr是碳化物形成元素，能够提高钢的淬透性、耐磨性和耐腐蚀性能。但Cr含量过高，与钢中的碳结合，容易形成大块碳化物，这种难溶碳化物使钢的韧性降低。在渗碳轴承钢中铬可以调整淬透性，提高渗碳层耐磨性，并改善钢的力学性能。此外，铬还能使钢的热处理工艺稳定，获得良好的渗碳性能，减少碳化物的不均匀性。本发明Cr含量的范围确定为1.30-1.60％。
5)Al含量的确定
Al作为钢中脱氧元素加入，除为了降低钢水中的溶解氧之外，Al与N形成弥散细小的氮化铝夹杂可以细化晶粒。但Al含量过多时，钢水熔炼过程中易形成大颗粒Al 2O 3等脆性夹杂，降低钢水纯净度，影响成品的使用寿命。本发明Al含量的范围确定为0.005％-0.05％。
6)Ni含量的确定
镍在钢中能够降低表面吸收碳原子的能力，加速碳原子在奥氏体中的扩散，减少渗碳层中碳的浓度，所以镍能减缓渗碳速度；同时，镍的加入可以提高钢的韧性。本发明 Ni含量的范围确定为3.25％-3.75％。
7)Mo含量的确定
钼在渗碳轴承钢中主要作用是提高淬透性，改善钢的力学性能，特别是具有提高韧性的效果。此外还可以提高钢的耐磨性和渗碳性能。本发明Mo含量的范围确定为0.15％-0.25％。
8)N含量的确定
当钢中溶有过饱和的氮，在放置较长一段时间后就会发生氮以氮化物形式的析出，并使钢的硬度、强度提高，塑性下降，发生时效。钢中加入适量的铝，可生成稳定的AlN，能够压抑Fe4N生成和析出，不仅改善钢的时效性，还可以阻止奥氏体晶粒的长大，起到细化晶粒的作用。但是氮会与钢中的合金元素生成氮化物非金属夹杂，更重要的是降低了合金元素的作用。钢中氮含量高时，，钢的强度升高，冲击韧性降低。本发明的N含量确定为0.005-0.015％
9)Ca含量的确定
Ca含量会增加钢中点状氧化物的数量和尺寸，同时由于点状氧化物硬度高，塑性差，在钢变形时其不变形，容易在交界面处形成空隙，使钢的性能变差。本发明Ca含量的范围确定为≤0.001％。
10)Ti含量的确定
Ti元素与N元素结合可形成氮化钛夹杂物，由于其硬度很高、呈尖角状，在轴承运转中易引起应力集中对轴承寿命影响较大，因此确定Ti≤0.0030％
11)O含量的确定
氧含量代表了氧化物夹杂总量的多少，氧化物脆性夹杂限制影响成品的使用寿命，大量试验表明，氧含量的降低对提高钢材纯净度特别是降低钢种氧化物脆性夹杂物含量显著有利。本发明氧含量的范围确定为≤0.0015％。
12)P、S含量的确定
P元素在钢的凝固时引起元素偏析，其溶于铁素体使晶粒扭曲、粗大，且增加冷脆性，因此确定P≤0.025％；S元素易使钢产生热脆性，降低钢的延展性和韧性，形成的硫化物还破坏了钢的连续性，因此确定S≤0.025％。
13)As、Sn、Sb、Pb含量的确定
As、Sn、Sb、Pb等微量元素，均属低熔点有色金属，在钢材中存在，引起零件表面出现软点，硬度不均，因此将它们视为钢中的有害元素，本发明这些元素含量的范围确定为As≤0.04％，Sn≤0.03％，Sb≤0.005％，Pb≤0.002％。
本申请的另一目的是提供风力发电机主轴轴承用钢的生产方法，采用连铸代替电渣重熔的方式冶炼坯料，主要步骤如下，
(1)钢水冶炼；
(2)大截面连铸CCM大连铸坯；确保钢材压缩比大于4；
(3)连铸坯缓冷，缓冷后作软化退火：连铸坯缓冷是将连铸坯下坑缓冷，其中下坑温度大于600℃，下坑缓冷时间大于48小时，出坑温度小于200℃，并于起坑后24小时内进行软化退火；软化退火温度为600-700℃，加热保温时间≥10h，随后随炉冷却至450℃后出炉空冷至室温；
(4)连轧：在中性或弱氧化性气氛的加热炉内加热至1150℃-1280℃，加热保温时间≥7h，出炉后的连铸坯经高压水除磷后进入粗轧-中轧-精轧机组并轧制呈的圆棒材，总压缩比≥4，粗轧开轧温度为1000-1150℃，使经高温加热的奥氏体晶粒进行再结晶使之得到细化，终轧温度控制在800-950℃，使终轧在非再结晶温度区间内进行，使变形的奥氏体晶粒被拉长，晶粒内存在大量变形带，使相变后铁素体晶粒细化以提高钢材的强度和韧性；
(5)轧材缓冷、软化退火：将轧后棒材在480℃及以上温度进行下坑缓冷，缓冷时间大于60小时，出坑温度小于200℃，棒材于起坑后24小时内再次进行软化退火处理；软化退火温度为600-700℃，保温时间≥7h，随后随炉冷却至500℃后出炉空冷至室温；
(6)精整。
优选地，步骤1是将冶炼原料依次经铁水预处理KR、电炉或转炉冶炼、LF精炼、RH或VD真空脱气得到符合化学成分的纯净钢水。
冶炼原料选用优质铁水、废钢及原辅料，选用优质耐材，冶炼采用高性能精炼合成渣，控制钢材各类夹杂物的数量及形态，钢包保持长时间的夹杂物去除过程，让非金属夹杂物充分上浮，选择专用精炼渣和中间包保护渣吸附夹杂物。
优选地，步骤2连铸采用中间包感应加热、轻压下和电磁搅拌，有效改善铸坯偏析和材料组织；采用大断面全程保护连铸使钢材压缩比大于4，有效地保证了材料的致密度，连铸采用低过热度浇注，连铸过热度控制在≤35℃，有效改善材料的均匀度，连铸出与钢材成品化学成分相符的规格为390×510mm及以上的矩形坯或φ600及以上的圆形连铸坯。
具体地，所述步骤6精整包括矫直、探伤等精整工序，制得目标棒材成品。
所有产品需100％经过无损检测，检测合格才为合格产品。
主要生产工艺特点如下：
1、钢水冶炼须通过铁水预处理铁，同时严格控制废钢的质量，优选低钛合金、脱氧剂及耐火材料；转炉出钢采用挡渣出钢，炉后扒渣等控制等工艺技术，解决现有技术有害元素Ti、Ca、As、Sn、Pb、Sb含量偏高的问题；
2、采用脱氧技术及RH真空循环脱气将钢中的O、H含量降低至极低水平，有效控制夹杂物数量和尺寸，经检测，本发明产品的夹杂物数量和尺寸均达到了世界领先水平；
3、连铸采用低过热度浇注，并采用中间包感应加热、轻压下和电磁搅拌技术，有效改善铸坯偏析和材料组织；采用大断面全程保护浇注，确保钢材压缩比大于4，从而保证了材料的致密度；
4、对连铸坯及轧材均进行下坑缓冷+软化退火处理，避免钢材因表面及内部的热应力及组织应力变化而出现开裂的现象。
5、从制造工艺上讲，采用真空脱气加连铸的生产工艺，相比电渣重熔技术，大大缩减了生产周期，提高了生产效率，有效降低了制造成本，实现了规模化生产，并有利于提高材料成分和产品质量稳定性；
6、本发明生产的风力发电机主轴轴承用钢满足如下指标要求：
微观夹杂物根据GB/T 10561 A法检验，B细系≤1.5级、B粗系≤1.0级、D细系≤1.0级，D粗系≤1.0级、DS系≤1.0级；宏观缺陷要求是按SEP 1927法检验，单个夹杂物长度不超过5mm；低倍组织要求采用GB/T 1979对钢材低倍组织评级，要求中心疏松≤1.5级、一般疏松≤1.0级、锭型偏析≤1.0级，中心偏析≤1.5级，并且不允许出现缩孔、裂纹及皮下气泡。
附图说明
图1为实施例产品低倍视图；
图2为对比例产品低倍视图。
具体实施方式
以下结合实施例对本发明作进一步详细描述。
本发明各实施例和(作为对比的)目前市场上所用的电渣重熔的G20Cr2Ni4的化学成分(wt％)见表3。
表3
Figure PCTCN2019075851-appb-000003
表3
Figure PCTCN2019075851-appb-000004
表4各实施例钢材的夹杂物
Figure PCTCN2019075851-appb-000005
表5各实施例钢材的末端淬透性数据
  J1.5 J3 J5 J7 J9 J11 J13 J15 J20 J25 J30 J35 J40 J45 J50
本发明实施例1 44 43.5 43.5 43 43 43 43 43 43 43 41 41 41 40 39.5
本发明实施例2 45 42 42 42 42 42 42 42 41.5 41.5 41 40 40 38 38
本发明实施例3 44 43 43 43 43 43 43 43 43 42.5 41.5 41.5 40 39.5 39
对比钢 43 41.5 41 41.5 40 40 39.5 39 39 39 38.5 38 38 37 37
表6各实施例的晶粒度、硬度及力学性能数据
Figure PCTCN2019075851-appb-000006
表7各实施例钢材的低倍数据
  中心疏松 一般疏松 锭型偏析 中心偏析 裂纹 缩孔 皮下气泡
本发明实施例1 1 1.0 1.0 1.0 无 无 无
本发明实施例2 1 1.0 1.0 1.0 无 无 无
本发明实施例3 1 1.0 1.0 1.0 无 无 无
对比钢 1.5 1.0 1.0 1.0 无 无 无
实施例中任一产品的低倍组织参见图1，对比例的低倍组织参见图2。
本发明实施例的风力发电机主轴轴承用钢的制造流程为采用铁水预处理+顶底复吹转炉BOF(大功率电弧炉EAF)-钢包精炼炉LF-真空循环脱气炉RH(VD炉)-大截面连铸CCM大连铸坯—连轧—精整的成型工艺生产钢材。
具体地，冶炼时选用优质铁水、废钢及原辅料，选用优质脱氧剂及耐火材料。在电炉/转炉生产过程中，三个实施例的出钢终点C分别控制在≥0.10％，终点P控制在≤0.015％以下，连铸过热度控制在10-35℃之内。将生产连铸坯下坑缓冷，其中下坑温度大于600℃，下坑缓冷时间大于48小时，出坑温度小于200℃，并于起坑后24小时内进行软化退火。软化退火温度为600-700℃，加热保温时间≥10h，随后随炉冷却至450℃后出炉空冷至室温。将上述连铸圆坯抛丸处理后，送至中性或弱氧化性气氛的加热炉内加热并轧制成目标棒材，轧制完成后将棒材下坑缓冷。轧钢加热、轧制及冷却工艺如下表8所示。棒材于起坑后24小时内再次进行软化退火处理。软化退火温度为600-700℃，保温时间≥7h，随后随炉冷却至500℃后出炉空冷至室温。再随后将棒材经后续矫直、探伤，制得目标棒材成品。
表8
Figure PCTCN2019075851-appb-000007
由表3、4、5、6、7对比可知，本发明各实施例中的风力发电机主轴轴承用钢与电渣重熔的G20Cr2Ni4钢相比，有害元素如氧、钛以及非金属夹杂物控制水平明显要好，即钢材纯净度要明显优于电渣重熔技术生产的产品，从低倍检验结果看，本发明的低倍质量并不差于电渣重熔工艺生产的G20Cr2Ni4钢，反映出本发明的均匀性、致密度与电渣重熔工艺生产的钢材质量相当。综合上述分析，本发明采用真空脱气加连铸生产工艺生产的风电主轴轴承用钢，能够替代原先的电渣重熔工艺，显著提高了生产效率，降低了生产成本，显著增强产品竞争力。
综上，本发明涉及的一种风力发电机主轴轴承用钢及其生产方法，通过提高钢的纯净度总体思路，采取真空脱气、连铸、轧制的高效率、大产能、低成本工艺路线，对关键工序进行优化研究和控制，从而使钢材获得了高的纯净度、高的组织均匀性和高的致密度，能够完全替代原先的电渣重熔工艺。在生产效率、生产成本和产品质量稳定性上更具竞争力。
除上述实施例外，本发明还包括有其他实施方式，凡采用等同变换或者等效替换方 式形成的技术方案，均应落入本发明权利要求的保护范围之内。

Claims (10)

  1. 一种风力发电机主轴轴承用钢，其特征在于：该钢的化学成分为：C：0.10～0.30％，Si：0.10～0.50％，Mn：0.30～0.80％，Cr：1.30～1.60％，S≤0.025％，P≤0.025％，Ni：3.25～3.75％，Cu≤0.30％，Mo：0.15～0.25％，Al：0.005-0.05％，N：0.005-0.015％，Ca≤0.0010％，Ti≤0.003％，O≤0.0015％，As≤0.04％，Sn≤0.03％，Sb≤0.005％，Pb≤0.002％，余量为Fe及不可避免的杂质。
  2. 一种风力发电机主轴轴承用钢，其特征在于：钢材晶粒度≥5级，硬度≤260HBW，脱碳要求≤0.8％D(D为直径)，采用金相法检测微观脆性夹杂物B细系≤1.5级、B粗系≤1.0级、D细系≤1.0级、D粗系≤1.0级、DS系≤1.0级；采用SEP 1927水浸高频探伤检测，要求夹杂物长度不允许超过5mm，采用GB/T 1979对钢材低倍组织评级，要求中心疏松≤1.5级、一般疏松≤1.0级、锭型偏析≤1.0级，中心偏析≤1.5级，并且不允许出现缩孔、裂纹及皮下气泡；
    抗拉强度要求≥1200MPa，冲击性能AKU≥65J；
    末端淬透性应满足：位置J1.5：43-48，J3：42-47，J5：42-47，J7：41-46，J9：41-46，J11：41-46，J13：41-46，J15：40-46，J20：40-46，J25：39-46，J30：38-45，J35：37-45，J40：36-44，J45：35-44，J50：34-43。
  3. 一种风力发电机主轴轴承用钢的生产方法，其特征在于：包括步骤，
    (1)钢水冶炼；
    (2)大截面连铸CCM大连铸坯；
    (3)连铸坯缓冷，缓冷后作软化退火：软化退火温度为600-700℃，加热保温时间≥10h，随后随炉冷却至450℃后出炉空冷至室温；
    (4)连轧：在中性或弱氧化性气氛的加热炉内加热至1150℃-1280℃，加热保温时间≥7h，出炉后的连铸坯经高压水除磷后进入粗轧-中轧-精轧机组并轧制呈的圆棒材，总压缩比≥4，粗轧开轧温度为1000-1150℃，使经高温加热的奥氏体晶粒进行再结晶使之得到细化，终轧温度控制在800-950℃，使终轧在非再结晶温度区间内进行，使变形的奥氏体晶粒被拉长，晶粒内存在大量变形带，使相变后铁素体晶粒细化；
    (5)轧材缓冷、软化退火：软化退火温度为600-700℃，保温时间≥7h，随后随炉冷却至500℃后出炉空冷至室温；
    (6)精整。
  4. 根据权利要求3所述的风力发电机主轴轴承用钢的生产方法，其特征在于：步骤1是将冶炼原料依次经铁水预处理KR、电炉或转炉冶炼、LF精炼、RH或VD真空脱气。
  5. 根据权利要求4所述的风力发电机主轴轴承用钢的生产方法，其特征在于：冶 炼原料选用优质铁水、废钢及原辅料，选用优质耐材，冶炼采用高性能精炼合成渣，控制钢材各类夹杂物的数量及形态，钢包保持长时间的夹杂物去除过程，让非金属夹杂物充分上浮，选择专用精炼渣和中间包保护渣吸附夹杂物。
  6. 根据权利要求3所述的风力发电机主轴轴承用钢的生产方法，其特征在于：步骤2采用中间包感应加热、轻压下和电磁搅拌，有效改善铸坯偏析和材料组织；采用全程保护浇注，连铸采用低过热度浇注，连铸过热度控制在≤35℃，连铸出与钢材成品化学成分相符的规格为390×510mm及以上的矩形坯或φ600及以上的圆形连铸坯。
  7. 根据权利要求3所述的风力发电机主轴轴承用钢的生产方法，其特征在于：步步骤3连铸坯缓冷是将连铸坯下坑缓冷，其中下坑温度大于600℃，下坑缓冷时间大于48小时，出坑温度小于200℃，并于起坑后24小时内进行软化退火。
  8. 根据权利要求3所述的风力发电机主轴轴承用钢的生产方法，其特征在于：步骤5轧材缓冷是将轧后棒材在480℃及以上温度进行下坑缓冷，缓冷时间大于60小时，出坑温度小于200℃，棒材于起坑后24小时内再次进行软化退火处理。
  9. 根据权利要求3所述的风力发电机主轴轴承用钢的生产方法，其特征在于：所述步骤6精整包括矫直、探伤。
  10. 根据权利要求3所述的风力发电机主轴轴承用钢的生产方法，其特征在于：步骤2连铸坯的化学成分满足C：0.10～0.30％，Si：0.10～0.50％，Mn：0.30～0.80％，Cr：1.30～1.60％，S≤0.025％，P≤0.025％，Ni：3.25～3.75％，Cu≤0.30％，Mo：0.15～0.25％，Al：0.005-0.05％，N：0.005-0.015％，Ca≤0.0010％，Ti≤0.003％，O≤0.0015％，As≤0.04％，Sn≤0.03％，Sb≤0.005％，Pb≤0.002％，余量为Fe及不可避免的杂质。
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