WO2022161180A1 - 一种球笼式万向节保持架用钢及其生产方法 - Google Patents

一种球笼式万向节保持架用钢及其生产方法 Download PDF

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WO2022161180A1
WO2022161180A1 PCT/CN2022/071755 CN2022071755W WO2022161180A1 WO 2022161180 A1 WO2022161180 A1 WO 2022161180A1 CN 2022071755 W CN2022071755 W CN 2022071755W WO 2022161180 A1 WO2022161180 A1 WO 2022161180A1
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steel
molten steel
class
universal joint
continuous casting
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English (en)
French (fr)
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陈敏
白云
罗元东
吴小林
尹青
李文彬
华刘开
刘烨
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江阴兴澄特种钢铁有限公司
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/0056—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00 using cored wires
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/04—Removing impurities by adding a treating agent
    • C21C7/06—Deoxidising, e.g. killing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/10—Handling in a vacuum
    • 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
    • C21D1/02—Hardening articles or materials formed by forging or rolling, with no further heating beyond that required for the formation
    • 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
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • 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
    • 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
    • C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
    • 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
    • C21D9/0075—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rods of limited length
    • 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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
    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • C21D2211/002—Bainite
    • 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
    • C21D2211/004—Dispersions; Precipitations
    • 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
    • C21D9/0068—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for particular articles not mentioned below

Definitions

  • the invention belongs to the technical field of special steel smelting, and particularly relates to a steel for a cage type universal joint cage and a production method thereof.
  • the constant velocity joints commonly used in cars are spherical joints.
  • the function of the spherical joints is to transmit the power of the engine from the transmission to the two front wheels to drive the car at high speed. It is mainly composed of spherical shell, star-shaped sleeve, cage (ball cage), steel ball and other main parts. Because the constant velocity universal joint transmits heavy driving torque, bears heavy load, has high transmission accuracy, and is in great demand, and is also used as a safety component of automobiles, it has high requirements on the quality of products.
  • the cage material is required to have good thermal conductivity, good wear resistance, small friction coefficient, small density, a certain combination of strength and toughness, good elasticity and stiffness, expansion coefficient similar to the rolling element, and good processing performance.
  • the cage is also subjected to chemical media, such as lubricants, lubricant additives, organic solvents and coolants, so it is also required to have certain corrosion resistance.
  • the current ball cage type universal joint cage is usually made of 20CrMnTi. After carburizing, the grains of the steel are refined and uniform, and it has good surface tensile and bending fatigue strength. The core has sufficient strength and toughness to improve wear resistance. But the cost is high, and the strength and toughness margin is not high.
  • the steel of the invention is redesigned on the basis of 20CrMnTi, and the content of alloy elements Mn and Cr is optimized. At the same time, by adding B and Mo elements, and improving the production process, the hardenability similar to 20CrMnTi can be achieved under the premise of optimizing the cost.
  • the strength and toughness are better than 20CrMnTi, which finally meets the requirements of steel for ball cage type universal joint cage and belongs to carburized steel.
  • the microstructure of the steel developed in this application is bainite, and the austenite grain size is greater than or equal to grade 6.
  • the hardenability of the steel end is evaluated according to the method of GB/T 225, which meets the J5 point: 35-42HRC, the J9 point: 25-35HRC, and the J13 point: 20-30HRC.
  • the strip structure of steel is graded according to GB/T 13299, and the strip structure does not exceed grade 2.0.
  • ASTM E381 is used to grade the low-magnification structure of steel, which satisfies C ⁇ 2.0, R ⁇ 2.0, S ⁇ 2.0 .
  • the steel of the present application meeting the above properties finally meets the use requirements of steel for ball cage type universal joint cage.
  • the technical solution adopted by the present invention to solve the above problems is: a steel for ball cage type universal joint cage, characterized in that the chemical composition wt% of the steel is C: 0.10-0.25%, Si: 0.20-0.40 %, Mn: 0.40-0.65%, Cr: 0.40-0.70%, B: 0.0003-0.0025%, Ti: 0.010-0.035%, Mo: 0.30-0.45%, N: 0.0050-0.0100%, S ⁇ 0.015%, P ⁇ 0.025%, Ni ⁇ 0.25%, Cu ⁇ 0.30%, Al: 0.015 ⁇ 0.035%, O ⁇ 0.0010%, As ⁇ 0.04%, Sn ⁇ 0.03%, Sb ⁇ 0.005%, Pb ⁇ 0.002%, the balance is Fe and inevitable impurities.
  • the chemical composition wt% of the steel is C: 0.10-0.25%, Si: 0.20-0.40 %, Mn: 0.40-0.65%, Cr: 0.40-0.70%, B: 0.0003-0.0025%, Ti: 0.010-0.035%, Mo: 0.3
  • C is an element necessary to ensure the wear resistance of steel. Increasing the carbon content in the steel will increase its martensitic transformation ability, thereby increasing its hardness and strength, thereby improving wear resistance. But too high C content is detrimental to the toughness of steel. In addition, too high C content will also lead to severe central C segregation and thus affect the core toughness of the steel.
  • the present invention controls its content to be 0.10-0.25%.
  • Si is a key element in the present invention.
  • Si is solid-dissolved in the ferrite phase and has a strong solid solution strengthening effect, which can significantly improve the strength of the ferrite, but at the same time reduce the plasticity and toughness of the ferrite.
  • the setting range of the Si content in the present invention is 0.20-0.40% .
  • Mn is an element effective in strengthening steel and plays a role in solid solution strengthening. Moreover, 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 iron and steel smelting, thereby weakening and eliminating the adverse effects of S. However, high Mn content will reduce the toughness of steel.
  • the Mn content of the present invention is controlled at 0.40-0.65%.
  • Cr is a carbide-forming element that can improve the hardenability, wear resistance and corrosion resistance of steel. However, if the Cr content is too high, the hardness of the steel is too large, which is unfavorable for customers to process and use. In summary, the range of the Cr content in the present invention is determined to be 0.40-0.70%.
  • 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 the Al content in the present invention is determined to be 0.015 to 0.035%.
  • B can improve the hardenability of the steel and the high-temperature strength of the steel, and can strengthen the grain boundary in the steel.
  • Molybdenum can refine the grain of steel, improve hardenability and thermal strength, and maintain sufficient strength and creep resistance at high temperatures.
  • the addition of molybdenum to the steel can improve the mechanical properties and also inhibit the brittleness of the alloy steel due to tempering.
  • molybdenum is a ferrite-forming element. When the molybdenum content is large, ferrite delta phase or other brittle phases are prone to appear, which reduces the toughness.
  • the present invention determines the range of Mo content to be 0.30-0.45%
  • Titanium is a strong deoxidizer in steel. It can make the internal structure of the steel dense and refine the grains. However, Ti will form titanium carbonitride inclusions in steel, which are hard and angular, and seriously affect the fatigue life of the material.
  • Nitrogen can improve the strength, low temperature toughness and weldability of steel and increase the sensitivity to aging. Adding an appropriate amount of aluminum to the steel can generate stable AlN, which can suppress the formation and precipitation of Fe 4 N, which not only improves the aging of the steel, but also prevents the growth of austenite grains and refines the grains. However, nitrogen will form nitride non-metallic inclusions with alloying elements in the steel, and more importantly, reduce the effect of alloying elements. When the nitrogen content in the steel is high, the strength of the steel increases and the impact toughness decreases.
  • the N content of the present invention is determined to be 0.0050 to 0.0100%
  • the oxygen content represents the total amount of oxide inclusions.
  • the limitation of oxide brittle inclusions affects the service life of the finished product.
  • a large number of experiments show that the reduction of oxygen content is significantly beneficial to improving the purity of steel, especially reducing the content of oxide brittle inclusions in steel.
  • the range of the oxygen content of the present invention is determined to be ⁇ 0.0010%.
  • the range of the P content in the present invention is determined to be ⁇ 0.025%.
  • S causes hot brittleness of steel and reduces the ductility and toughness of steel, but S can improve the cutting performance of steel, and the range of S content in the present invention is determined to be ⁇ 0.015%.
  • Sn, Sb, Pb and other trace elements are all non-ferrous metals with low melting point. They exist in steel, causing soft spots on the surface of parts and uneven hardness. Therefore, they are regarded as harmful elements in steel.
  • the content of these elements in the present invention The range of As ⁇ 0.04%, Sn ⁇ 0.03%, Sb ⁇ 0.005%, Pb ⁇ 0.002%.
  • the production process of the above steel for ball cage type universal joint cage is that the manufacturing process is electric furnace or converter (primary smelting) ⁇ LF refining outside the furnace ⁇ VD or RH vacuum degassing ⁇ continuous casting ⁇ rolling ⁇ finishing ⁇ driving library.
  • the main production process features are as follows:
  • the primary smelting adopts high-quality molten iron, scrap steel and raw and auxiliary materials to reduce the content of harmful elements in molten steel.
  • deoxidation should be strengthened, and the carbon at the end of tapping in the electric furnace or converter should be controlled.
  • the carbon at the end of tapping should be controlled at 0.05-0.15%.
  • Al iron should be added for pre-deoxidation to create good conditions for subsequent deoxidation. Slag removal technology to remove harmful steel slag.
  • new synthetic slag is added to the LF refining furnace, and at the same time, the deoxidation of the refining process is strengthened.
  • the refining process adopts silicon carbide and aluminum deoxidation to form white slag as soon as possible in the early stage of refining, and maintain the white slag for more than 25min.
  • the aluminum content of the whole refining process It is controlled between 0.025%-0.045% to ensure the deoxidation effect.
  • the steel in this application is a crack-sensitive steel, and vacuum degassing should be strengthened, and the treatment time under high vacuum (below 133Pa) is ⁇ 15min to ensure that the harmful gas H ⁇ 2ppm.
  • silicon-calcium wire should be fed for inclusion denaturation treatment.
  • soft argon blowing should be performed for a long time to ensure that the inclusions float up sufficiently. The soft argon blowing time is ⁇ 25min.
  • the whole process of continuous casting is protected against oxidation (ie, isolating molten steel and air) to reduce the number of inclusions in the steel.
  • high-quality refractory materials are selected to reduce the control technology of foreign inclusions on molten steel pollution, and to strengthen the control of the production process.
  • the continuous casting process adopts electromagnetic stirring and light reduction technology. By adjusting the pressure distribution of the light reduction roller, when the molten steel is solidified, the molten steel is fully filled in the center of the steel to avoid shrinkage. At the same time, the electromagnetic stirring of the mold and the end is strengthened to change
  • the solidification flow field of molten steel can improve the internal structure of continuous casting molten steel and reduce segregation.
  • the continuous casting adopts low superheat casting, and the continuous casting superheat is controlled at 10-30°C, which can effectively improve and reduce the composition segregation of the continuous casting billet.
  • the continuous casting billet with a specification of 300mm ⁇ 300mm and above in line with the chemical composition of the finished steel product is continuously cast; the continuous casting billet should be cooled slowly in the pit to prevent the continuous casting billet from cracking, and the slow cooling time should not be less than 24 hours, and then the continuous casting billet should be continuously cast.
  • the billet is sent to the walking furnace for heating and rolled into the target material.
  • the continuous casting billet is heated in the furnace before rolling: the temperature of the preheating section is controlled at 600-850 °C, the temperature of the heating section is controlled at 950-1100 °C, and the temperature of the soaking section is controlled at 1150-1200 °C.
  • the heating time is more than 240min, and the soaking time is more than 180min.
  • the rolling temperature is controlled at 950°C-1050°C, and the final rolling temperature is controlled at 800°C-900°C.
  • the whole rolling process is carried out in the austenite single-phase region.
  • the present invention designs the cooling rate in the cooling interval from the end of the final rolling to the upper cooling bed to be 10-15°C/s, and at the same time, the rolling speed is relatively reduced to control the temperature of the steel in this interval. Through time, the steel can be fully transformed into bainite, and finally the temperature of the cooling bed on the steel is controlled at 600-650 °C.
  • the subsequent cooling on the cooling bed can be done as normal. Speed cooling, the cooling speed is 15-20 °C/min, and then the steel is off the assembly line, and then the target bar product is obtained through subsequent straightening and flaw detection.
  • the steel of the present invention is redesigned on the basis of 20CrMnTi to reduce the content of alloying elements Mn, Cr and harmful elements Ti, because the reduction of the content of Mn and Cr will inevitably affect the hardenability of the steel, so the steel of the present invention simultaneously adds a trace amount of B. element and adding a certain amount of alloying element Mo to improve the hardenability, so that the hardenability of the invention steel is not worse than 20CrMnT.
  • the grain size of the invention steel is comparable to 20CrMnTi.
  • the transformation of the metallographic structure during the manufacturing process ensures that the finished steel forms a bainite structure, so as to ensure that the strength and toughness of the invented steel are not lower than 20CrMnTi, and finally meet the requirements of steel for ball cage universal joint cages.
  • Fig. 1 is the typical metallographic structure diagram of the embodiment of the present invention ⁇ 100;
  • Figure 2 is a typical metallographic structure diagram of the comparative example ⁇ 100.
  • Example C Si Mn P S Cr Cu Ni Al Mo this invention 1 0.15 0.29 0.56 0.015 0.004 0.6 0.02 0.02 0.027 0.34 this invention 2 0.17 0.30 0.57 0.016 0.002 0.59 0.04 0.02 0.023 0.38 this invention 3 0.19 0.30 0.60 0.015 0.001 0.62 0.02 0.03 0.025 0.35 contrast steel 0.20 0.26 0.95 0.016 0.004 1.16 0.02 0.02 0.024 0.01
  • Example B As Sn Sb Pb N Ti O this invention 1 0.0011 0.002 0.003 0.002 0.001 0.0071 0.0229 0.00092 this invention 2 0.0014 0.003 0.002 0.002 0.001 0.0080 0.025 0.00088 this invention 3 0.0013 0.002 0.002 0.001 0.002 0.0078 0.027 0.00085 contrast steel 0.0001 0.005 0.002 0.001 0.002 0.0035 0.0515 0.0013
  • Fig. 1 and Fig. 2 The typical structures of the steels of the embodiments of the present invention and the comparative examples are shown in Fig. 1 and Fig. 2 .
  • the structure shown in Fig. 1 is a bainite structure
  • the structure shown in Fig. 2 is ferrite + pearlite + bainite.
  • Table 6 shows the comparison of the inclusions of the steels of each embodiment and the comparative example.
  • Example A fine inclusion A coarse inclusion B fine inclusions B coarse inclusions C fine inclusions C coarse inclusions D fine inclusions D coarse inclusions Ds inclusions this invention 1 0.5 ⁇ 1.0 0 ⁇ 0.5 0 ⁇ 0.5 0 ⁇ 0.5 0 ⁇ 0.5 0 0 0 ⁇ 0.5 0 ⁇ 1.0 this invention 2 0.5 ⁇ 1.0 0 ⁇ 0.5 0 ⁇ 0.5 0 ⁇ 0.5 0 ⁇ 0.5 0 0 0 ⁇ 0.5 0 ⁇ 0.5 0 ⁇ 1.0 this invention 3 0 ⁇ 1.0 0 ⁇ 0.5 0 ⁇ 0.5 0 0 0 0 0 0 ⁇ 1.0 0 ⁇ 0.5 0 ⁇ 0.5 contrast steel 0.5 ⁇ 1.0 0.5 ⁇ 1.0 0 ⁇ 0.5 0 ⁇ 0.5 0 ⁇ 0.5 0 0 0.5 ⁇ 1.5 0.5 ⁇ 1.0 1.0 ⁇ 2.0
  • the impact and tensile properties of the present invention are better than those of 20CrMnTi of the comparative example, so the strength and toughness of the final product of the present application are better than those of 20CrMnTi.
  • Other performance indicators of the present invention include hardenability, grain size, Inclusions, strips, low magnifications, etc. are close to the comparison steel, and all properties can meet the steel requirements for ball cage type universal joint cages.
  • Production process electric furnace or converter ⁇ LF refining outside the furnace ⁇ VD or RH vacuum degassing ⁇ continuous casting ⁇ continuous rolling ⁇ finishing ⁇ punching and storage.
  • the tapping end point C of the three embodiments is controlled within 0.05-0.15% respectively, and the end point P is controlled below 0.020%.
  • the electric furnace or converter tapping end point carbon is controlled. The carbon at the end of tapping is controlled at 0.05-0.15%.
  • Al iron is added for pre-deoxidation to create good conditions for subsequent deoxidation.
  • slag removal technology is used to remove harmful steel slag.
  • new synthetic slag is added to the LF refining furnace, and at the same time, the deoxidation of the refining process is strengthened.
  • the refining process adopts silicon carbide and aluminum deoxidation to form white slag as soon as possible in the early stage of refining, and maintain the white slag for more than 25min.
  • the aluminum content of the whole refining process It is controlled between 0.025%-0.045% to ensure the deoxidation effect.
  • the steel of the embodiment is a crack-sensitive steel, and vacuum degassing should be strengthened, and the treatment time under high vacuum (below 133Pa) is ⁇ 15min to ensure that the harmful gas H ⁇ 2ppm.
  • silicon-calcium wire should be fed to denature the inclusions.
  • soft argon blowing should be performed for a long time to ensure that the inclusions are fully floated. The soft argon blowing time is ⁇ 25min.
  • the superheat degree of continuous casting is controlled within 10-30°C, and the pulling speed of continuous casting is 0.45-0.75m/min.
  • the specification of the continuous casting billet is 300mm ⁇ 300mm.
  • the continuous casting billet is slowly cooled in the pit for more than 24 hours, and then the slowly cooled continuous casting billet is sent to the heating furnace to be rolled into the target steel.
  • the specific rolling process is as follows: : The temperature of the preheating section is controlled at 600-850 °C, the temperature of the heating section is controlled at 950-1100 °C, and the temperature of the soaking section is controlled at 1150-1200 °C.
  • the period of time is more than 3h.
  • the rolling temperature is controlled at 950°C-1050°C, and the final rolling temperature is controlled at 800°C-900°C.
  • the steel is controlled to cool at a cooling rate of 10-15°C/min to drive the austenite structure to be completely transformed into Bainite, the temperature of the cooling bed on the steel is controlled at 600-650 °C, and then the target bar product is obtained through subsequent straightening and flaw detection.
  • the present invention also includes other embodiments, and all technical solutions formed by equivalent transformation or equivalent replacement shall fall within the protection scope of the claims of the present invention.

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Abstract

本发明涉及一种球笼式万向节保持架用钢及其生产方法，属于特种钢冶炼技术领域。钢的化学成分wt％为C：0.10～0.25％，Si：0.20～0.40％，Mn：0.40～0.65％，Cr：0.40～0.70％，B：0.0003～0.0025％，Ti：0.010～0.035％，Mo：0.30～0.45％，N：0.0050～0.0100％，S≤0.015％，P≤0.025％，Ni≤0.25％，Cu≤0.30％，Al:0.015～0.035％，O≤0.0010％，As≤0.04％，Sn≤0.03％，Sb≤0.005％，Pb≤0.002％，余量为Fe及不可避免的杂质。钢的微观结构为贝氏体，奥氏体晶粒度≥6级。生产流程为钢水初炼→钢水精炼→钢水真空脱气→连铸→热轧→精整。本申请对化学成分进行优化，降低合金成本。并达到了与20CrMnTi相近的淬透性，该化学成分结合生产方法制造的钢材的强度、韧性都比20CrMnTi更优，综合性能满足球笼式万向节保持架的用钢要求。

Description

一种球笼式万向节保持架用钢及其生产方法 技术领域
本发明属于特种钢冶炼技术领域，具体涉及一种球笼式万向节保持架用钢及其生产方法。
背景技术
目前，轿车上常用的等速万向节是球笼式万向节，球笼式万向节的作用是将发动机的动力从变速器传递到两个前车轮，驱动轿车高速行驶。它主要有球形壳、星形套、保持架(球笼)、钢珠等主要零件组成。由于等速万向节传递繁重的驱动力矩，随受负荷重，传动精度高，需求量很大，同时又是作为汽车的安全部件，因此对产品的质量要求很高。
现代汽车工业的竞争日趋激烈，对汽车的动力性、操作性、舒适性及安全性有更高的要求，再加上能源及环境方法的要求，所以在设计汽车重要功能性零部件时，必须综合考虑其安全性、功能性、经济性和排放性等重要指标，因而对材料提出更高的要求，要求材料在确保性能的前提下更加轻质化，对于汽车万向节用材料而言，部件起传动及支撑的作用，还承受交变载荷应力的长期作用，因此材料必须具备足够的耐磨性、抗疲劳性及良好的韧性。
球笼式万向节在工作时，特别是载荷复杂且高速旋转时，保持架要承受很大的离心力、冲击和振动，保持架和滚动体之间存在较大的滑动摩擦，并产生大量的热量。力和热共同作用的结果会导致保持架故障，严重时会造成保持架烧伤和断裂。因此，要求保持架材料导热性好、耐磨性好、摩擦系数小，有较小的密度，一定的强度和韧性的配合、较好的弹性和刚度，与滚动体相近的膨胀系数，以及良好的加工工艺性能。另外，保持架还要受到化学介质，如润滑剂、润滑剂添加剂、有机溶剂和冷却剂等的作用，因此也要求具有一定耐腐蚀性。
当前球笼式万向节保持架通常选用材料为20CrMnTi，渗碳后钢材晶粒细化，均匀，具有较好的表面抗拉和弯曲疲劳强度。心部有足够的强度和韧性，提高了耐磨性。但造价成本较高，而且强度和韧性富余量不高。
发明内容
本发明钢材在20CrMnTi基础上进行重新设计，优化合金元素Mn、Cr的含量，同时通过添加B和Mo元素，并完善生产工艺，在优化成本前提下达到与20CrMnTi相近的淬透性，同时产品的强度、韧性都比20CrMnTi更优，最终满足球笼式万向节保持架用钢的要求，属于渗碳钢材。
具体的，本申请研发的钢材，其微观结构为贝氏体，奥氏体晶粒度≥6级。屈服强度≥850MPa，抗拉强度≥1080MPa，延伸率≥10％，常温下夏比冲击功AK U≥55J。钢材末端淬透性按照GB/T 225的方法评定，满足J5点：35-42HRC，J9点：25-35HRC，J13点：20-30HRC。钢材带状组织按GB/T 13299评级，带状组织不超过2.0级。非金属夹杂物按GB/T 10561中A法评级，满足A类细系≤1.5，A类粗系≤1.0，B类细系≤1.5，B类粗系≤0.5，C类细系＝0，C类粗系＝0，D类细系≤1.0，D类粗系≤0.5，Ds类≤1.5采用ASTM E381对钢材低倍组织评级，满足C≤2.0级、R≤2.0级、S≤2.0级。
满足上述性能的本申请钢材最终满足球笼式万向节保持架用钢的使用要求。
本发明解决上述问题所采用的技术方案为：一种球笼式万向节保持架用钢，其特征在于：所述钢的化学成分wt％为C：0.10～0.25％，Si：0.20～0.40％，Mn：0.40～0.65％，Cr：0.40～0.70％，B：0.0003～0.0025％，Ti：0.010～0.035％，Mo：0.30～0.45％，N：0.0050～0.0100％，S≤0.015％，P≤0.025％，Ni≤0.25％，Cu≤0.30％，Al:0.015～0.035％，O≤0.0010％，As≤0.04％，Sn≤0.03％，Sb≤0.005％，Pb≤0.002％，余量为Fe及不可避免的杂质。
本申请化学成分的设置依据如下：
1)C含量的确定
C是确保钢材耐磨性所必须的元素，提高钢中的碳含量将会增加它的马氏体转变能力，从而提高它的硬度和强度，进而提高耐磨性。但过高的C含量对钢的韧性不利。另外，过高的C含量也会导致严重的中心C偏析从而影响钢材的芯部韧性。本发明控制其含量为0.10～0.25％。
2)Si含量的确定
Si为本发明中的关键元素。Si固溶在铁素体相中，有较强的固溶强化作用，能显著提高铁素体强度，但同时降低铁素体的塑性和韧性，本发明Si含量的设定范围0.20～0.40％。
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0.40～0.65％。
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，钢材的硬度过大，不利于客户加工使用，综上分析，本发明Cr含量的范围确定为0.40～0.70％。
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0.015～0.035％。
6)B含量的确定
B能提高钢的淬透性，还能提高钢的高温强度，并且在钢中能起到强化晶界的作用，本发明B含量的范围确定为0.0003-0.0025％。
7)Mo含量的确定
钼能使钢的晶粒细化，提高淬透性和热强性能，在高温时保持足够的强度和抗蠕变能力。钢中加入钼，能提高机械性能，还可以抑制合金钢由于回火而引起的脆性。但钼是铁素体形成元素，当钼含量较多时就易出现铁素体δ相或其它脆性相而使韧性降低，本发明将Mo含量的范围确定为0.30～0.45％
8)Ti含量的确定
钛是钢中强脱氧剂。它能使钢的内部组织致密，细化晶粒。但Ti在钢中会形成碳氮化钛夹杂物，这种夹杂物坚硬、呈棱角状，严重影响材料的疲劳寿命，本发明Ti含量的范围确定为0.01～0.035％。
9)N含量的确定
氮能提高钢的强度，低温韧性和焊接性，增加时效敏感性。钢中加入适量的铝，可生成稳定的AlN，能够压抑Fe 4N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0.0050～0.0100％
10)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≤0.0010％。
11)P、S含量的确定
P在钢中严重引起凝固时的偏析，P溶于铁素体使晶粒扭曲、粗大，且增加冷脆性。本发明P含量的范围确定为≤0.025％。S使钢产生热脆性，降低钢的延展性和韧性，但S能提高钢材的切削性能，本发明S含量的范围确定为≤0.015％。
12)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％。
上述球笼式万向节保持架用钢的生产流程为制造流程为电炉或转炉(初炼)→LF炉外精炼→VD或RH真空脱气→连铸→轧制→精整→打件入库。
主要生产工艺特点如下：
(一)钢水冶炼部分：
初炼采用优质铁水、废钢及原辅料，降低钢水中有害元素含量。冶炼过程要加强脱氧，对电炉或转炉出钢终点碳进行控制，出钢终点碳控制在0.05-0.15％，出钢过程中加Al铁进行预脱氧，为后续脱氧创造良好条件，出钢后采用扒渣技术，扒除有害钢渣。
精炼时在LF精炼炉中重新加入新的合成渣、同时加强精炼过程的脱氧，精炼过程采用碳化硅和铝脱氧，在精炼初期尽快形成白渣，并保持白渣25min以上，整个精炼过程铝含量控制在0.025％-0.045％之间，以保证脱氧效果。
本申请钢材属于裂纹敏感钢种，应加强真空脱气，在高真空下(133Pa以下)处理时间≥15min，确保有害气体H≤2ppm。真空脱气后应喂硅钙线进行夹杂物变性处理，在真空脱气后进行长时间软吹氩，保证夹杂物充分上浮，软吹氩时间≥25min。
(二)连铸部分：
连铸全程防氧化保护(即隔绝钢水与空气)来减少钢中的夹杂物数量。另外选用优质耐材减少外来夹杂对钢水污染的控制技术，强化对生产过程的控制。连铸过程采用电 磁搅拌及轻压下技术，通过调整轻压下滚子压力分配，在钢水凝固时，在钢材中心充分得到钢水填充，避免缩孔现象，同时加强结晶器和末端电磁搅拌，改变钢水凝固流场，改善连铸钢水内部组织，减少偏析。连铸采用低过热度浇注，连铸过热度控制在10-30℃，有效改善和降低连铸坯的成分偏析。连铸出与钢材成品化学成分相符的规格为300mm×300mm及以上的连铸方坯；连铸坯应下坑缓冷，防止连铸坯开裂，缓冷时间不小于24小时，随后将连铸坯送至步进式加热炉内加热后并轧制成目标材。
(三)轧制部分：
轧制前连铸坯入炉加热：预热段温度控制在600-850℃，加热段温度控制在950-1100℃，均热段温度控制在1150-1200℃，为保证坯料充分均匀受热，总加热时间在240min以上，均热段时间在180min以上。轧制开轧温度控制在950℃-1050℃，终轧温度控制在800℃-900℃，整个轧制过程在奥氏体单相区进行，为使轧制结束后实现由奥氏体向贝氏体组织转变，终轧结束到上冷床的过程中不宜采用缓冷，防止出现粗大的铁素体晶粒，会降低钢材强度和韧性，但也不宜过快冷却，防止出现马氏体组织，也会降低钢材的韧性，本发明设计从终轧结束到上冷床的这段降温区间的冷却速度为10-15℃/s，同时相对降低轧制速度，以控制钢材在这段区间的通过时间，使钢材能够充分进行贝氏体组织转变，最终钢材上冷床温度控制在600-650℃，由于此时钢材金相组织已基本完成贝氏体转变，后续在冷床上可按照正常冷却速度冷却，冷却速度在15-20℃/min，而后钢材下线，再经后续矫直、探伤，制得目标棒材产品。
与现有技术相比，本发明的优点在于：
1)本发明钢材在20CrMnTi基础上进行重新设计，降低合金元素Mn、Cr及有害元素Ti的含量，由于Mn、Cr元素含量的降低势必影响钢材淬透性，因此发明钢同时通过添加微量的B元素并添加一定量的合金元素Mo，以此提高淬透性，使发明钢淬透性能不差于20CrMnT。另外，通过降低容易形成坚硬不变形夹杂物的Ti元素，并添加能同样细化晶粒的N元素，在改善钢材纯净度的同时，使发明钢的晶粒度与20CrMnTi相当，同时通过控制轧制过程中金相组织的转变，确保成品钢材形成贝氏体组织，从而保证发明钢的强度及韧性不低于20CrMnTi，最终满足球笼式万向节保持架用钢的要求。
2)如上所述，本发明在冶炼过程中通过加强脱氧、脱氢，同时选用优质原料，保证钢材纯洁度高，连铸采用低过热度浇注，并采用电磁搅拌和轻压下控制，控制钢材偏析，可以有效满足球笼式万向节保持架用钢的要求。
附图说明
图1为本发明实施例的典型金相组织图×100；
图2为对比例的典型金相组织图×100。
具体实施方式
以下结合附图对本发明作进一步详细描述，所述实施例是示例性的，旨在用于解释本发明，而不能理解为对本发明的限制。
本发明各实施例钢材的化学成分(wt％)见表1、表2。并与对比钢20CrMnTi的化学成分做对比。
表1
  实施例 C Si Mn P S Cr Cu Ni Al Mo
本发明 1 0.15 0.29 0.56 0.015 0.004 0.6 0.02 0.02 0.027 0.34
本发明 2 0.17 0.30 0.57 0.016 0.002 0.59 0.04 0.02 0.023 0.38
本发明 3 0.19 0.30 0.60 0.015 0.001 0.62 0.02 0.03 0.025 0.35
对比钢   0.20 0.26 0.95 0.016 0.004 1.16 0.02 0.02 0.024 0.01
表2
  实施例 B As Sn Sb Pb N Ti O
本发明 1 0.0011 0.002 0.003 0.002 0.001 0.0071 0.0229 0.00092
本发明 2 0.0014 0.003 0.002 0.002 0.001 0.0080 0.025 0.00088
本发明 3 0.0013 0.002 0.002 0.001 0.002 0.0078 0.027 0.00085
对比钢   0.0001 0.005 0.002 0.001 0.002 0.0035 0.0515 0.0013
各实施例和对比例钢材的力学性能对比数据参见表3。
表3
Figure PCTCN2022071755-appb-000001
各实施例及对比例钢材的热轧金相组织、带状组织、晶粒度数据见表4
表4
Figure PCTCN2022071755-appb-000002
Figure PCTCN2022071755-appb-000003
本发明实施例钢材及对比例的典型组织参见图1、图2，图1所示组织为贝氏体组织，图2所示组织为铁素体+珠光体+贝氏体。
各实施例和对比例钢材的末端淬透性性能对比参见表5，单位HRC。
表5
Figure PCTCN2022071755-appb-000004
各实施例以及对比例钢材的夹杂物对比见表6。
表6
  实施例 A细夹杂 A粗夹杂 B细夹杂 B粗夹杂 C细夹杂 C粗夹杂 D细夹杂 D粗夹杂 Ds夹杂
本发明 1 0.5～1.0 0～0.5 0～0.5 0～0.5 0 0 0～0.5 0～0.5 0～1.0
本发明 2 0.5～1.0 0～0.5 0～0.5 0～0.5 0 0 0～0.5 0～0.5 0～1.0
本发明 3 0～1.0 0～0.5 0～0.5 0 0 0 0～1.0 0～0.5 0～0.5
对比钢   0.5～1.0 0.5～1.0 0～0.5 0～0.5 0 0 0.5～1.5 0.5～1.0 1.0～2.0
各实施例以及对比例钢材的低倍数据对比见表7。
表7
  C R S
本发明实施例1 1.0 1.0 1.0
本发明实施例2 1.0 1.0 1.0
本发明实施例3 1.0 1.0 1.0
对比钢 1.0 1.5 1.0
从上述检验结果看，本发明冲击及拉伸性能优于对比例的20CrMnTi，所以本申请的最终产品的强度及韧性相比20CrMnTi更优，本发明其他性能指标包括淬透性、晶粒度、夹杂物、带状、低倍等与对比钢接近，各项性能均能够满足球笼式万向节保持架用钢要求。
以下对上述各实施例球笼式万向节保持架用钢的生产方法作详细介绍。
生产流程：电炉或转炉→LF炉外精炼→VD或RH真空脱气→连铸→连轧→精整→打件入库。
钢水冶炼时，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0.05-0.15％之内，终点P控制在0.020％以下，要加强脱氧，对电炉或转炉出钢终点碳进行控制，出钢终点碳控制在0.05-0.15％，出钢过程中加Al铁进行预脱氧，为后续脱氧创造良好条件，出钢后采用扒渣技术，扒除有害钢渣。
精炼时在LF精炼炉中重新加入新的合成渣、同时加强精炼过程的脱氧，精炼过程采用碳化硅和铝脱氧，在精炼初期尽快形成白渣，并保持白渣25min以上，整个精炼过程铝含量控制在0.025％-0.045％之间，以保证脱氧效果。
实施例的钢材属于裂纹敏感钢种，应加强真空脱气，在高真空下(133Pa以下)处理时间≥15min，确保有害气体H≤2ppm。真空脱气后应喂硅钙线进行夹杂物变性处理，在真空脱气后进行长时间软吹氩，保证夹杂物充分上浮，软吹氩时间≥25min。
连铸过热度控制在10-30℃之内，连铸拉速0.45-0.75m/min。连铸方坯的规格为300mm×300mm，连铸坯下坑缓冷，缓冷24小时以上，而后将缓冷后的连铸坯送至加热炉轧制成目标钢材，具体的轧制工艺为：预热段温度控制在600-850℃，加热段温度控制在950-1100℃，均热段温度控制在1150-1200℃，为保证坯料充分均匀受热，总加热时间在4小时以上，均热段时间在3h以上。轧制开轧温度控制在950℃-1050℃，终轧温度控制在800℃-900℃，终轧结束后控制钢材以10-15℃/min的冷速冷却，驱动奥氏体组织全部转变为贝氏体，钢材上冷床温度控制在600-650℃，再经后续矫直、探伤，制得目标棒材产品。
各实施例轧制工艺参数如表8所示。
表8
Figure PCTCN2022071755-appb-000005
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 (9)

  1. 一种球笼式万向节保持架用钢，其特征在于：所述钢的化学成分wt％为C：0.10～0.25％，Si：0.20～0.40％，Mn：0.40～0.65％，Cr：0.40～0.70％，B：0.0003～0.0025％，Ti：0.010～0.035％，Mo：0.30～0.45％，N：0.0050～0.0100％，S≤0.015％，P≤0.025％，Ni≤0.25％，Cu≤0.30％，Al:0.015～0.035％，O≤0.0010％，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. 根据权利要求1所述的球笼式万向节保持架用钢，其特征在于：所述钢的微观结构为贝氏体，奥氏体晶粒度≥6级。
  3. 根据权利要求1所述的球笼式万向节保持架用钢，其特征在于：所述钢的屈服强度≥850MPa，抗拉强度≥1080MPa，延伸率≥10％，常温下夏比冲击功AK U≥55J。
  4. 根据权利要求1所述的球笼式万向节保持架用钢，其特征在于：
    钢材末端淬透性按照GB/T 225的方法评定，满足J5点：35-42HRC，J9点：25-35HRC，J13点：20-30HRC；
    钢材带状组织按GB/T 13299评级，带状组织不超过2.0级；
    非金属夹杂物按GB/T 10561中A法评级，满足A类细系≤1.5，A类粗系≤1.0，B类细系≤1.5，B类粗系≤0.5，C类细系＝0，C类粗系＝0，D类细系≤1.0，D类粗系≤0.5，Ds类≤1.5；
    采用ASTM E381对钢材低倍组织评级，满足C≤2.0级、R≤2.0级、S≤2.0级。
  5. 一种球笼式万向节保持架用钢的生产方法，其特征在于：流程为钢水初炼→钢水精炼→钢水真空脱气→连铸→热轧→精整，主要生产工序要求如下：
    钢水冶炼过程要加强脱氧，控制初炼出钢终点碳在0.05～0.15％，出钢过程中加Al铁对钢水预脱氧，为后序脱氧创造良好条件，出钢后进行扒渣，扒除有害钢渣；精炼时重新向钢水中加入合成渣、同时加强精炼过程的脱氧：采用碳化硅和铝脱氧，精炼初期尽快形成白渣，并保持白渣25min以上，整个精炼过程钢水中的铝含量控制在0.025％～0.045％之间以保证脱氧效果；加强真空脱气直至将钢水中的有害气体H≤2ppm，真空脱气后喂硅钙线进行夹杂物变性处理，在真空脱气后对钢水实施软吹氩，搅动钢水，让夹杂物充分上浮，软吹氩时间≥25min；
    连铸工艺得到的连铸方坯应下坑缓冷，缓冷时间不小于24小时；
    轧制前连铸坯入炉加热，设置预热段温度600-850℃，加热段温度950-1100℃，均热段温度1150-1200℃，总加热时间在240min以上，均热段时间在180min以上；出炉后准备轧制，设置开轧温度950℃-1050℃，终轧温度800℃-900℃，整个轧制过程在奥氏体单相区完成，从终轧结束到上冷床的这段区间的冷却速度控制在10-15℃/s，并控制钢材在这段区间的通过时间，此冷却过程是为了控制微观结构由奥氏体向贝氏体转变，使钢材能够充分进行贝氏体组织转变。最终钢材上冷却床的温度为600-650℃，在冷床上继续冷却，最后从冷床下线后经矫直精整后得到目标产品。
  6. 根据权利要求5所述的生产方法，其特征在于：初炼要选用优质铁水、废钢及原辅料，降低钢水中有害元素含量。
  7. 根据权利要求5所述的生产方法，其特征在于：真空脱气是钢水在133Pa以下的高真空条件下保持15min以上。
  8. 根据权利要求5所述的生产方法，其特征在于：连铸过程采用结晶器和末端电磁搅拌及轻压下操作，连铸时钢水过热度控制在10-30℃。
  9. 根据权利要求5所诉的生产方法，其特征在于：钢材在冷床上的冷却速度为15-20℃/min。
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