CN114807773B - High mechanical property wind driven generator shaft steel and preparation process thereof - Google Patents
High mechanical property wind driven generator shaft steel and preparation process thereof Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 114
- 239000010959 steel Substances 0.000 title claims abstract description 114
- 238000002360 preparation method Methods 0.000 title claims abstract description 12
- 238000005096 rolling process Methods 0.000 claims abstract description 83
- 238000000034 method Methods 0.000 claims abstract description 39
- 238000010438 heat treatment Methods 0.000 claims abstract description 33
- 238000009749 continuous casting Methods 0.000 claims abstract description 23
- 239000012535 impurity Substances 0.000 claims abstract description 19
- 229910052760 oxygen Inorganic materials 0.000 claims abstract description 17
- 238000003723 Smelting Methods 0.000 claims abstract description 15
- 238000007670 refining Methods 0.000 claims abstract description 10
- 238000001816 cooling Methods 0.000 claims description 72
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 39
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 29
- 238000010791 quenching Methods 0.000 claims description 22
- 230000000171 quenching effect Effects 0.000 claims description 22
- 238000010079 rubber tapping Methods 0.000 claims description 22
- 229910052698 phosphorus Inorganic materials 0.000 claims description 17
- 238000005496 tempering Methods 0.000 claims description 16
- 229910052742 iron Inorganic materials 0.000 claims description 15
- 239000002893 slag Substances 0.000 claims description 15
- 238000007664 blowing Methods 0.000 claims description 13
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 12
- 229910045601 alloy Inorganic materials 0.000 claims description 12
- 239000000956 alloy Substances 0.000 claims description 12
- 238000005204 segregation Methods 0.000 claims description 12
- 229910052720 vanadium Inorganic materials 0.000 claims description 12
- 238000005266 casting Methods 0.000 claims description 11
- 229910052717 sulfur Inorganic materials 0.000 claims description 11
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 claims description 9
- 239000000203 mixture Substances 0.000 claims description 9
- 229910052757 nitrogen Inorganic materials 0.000 claims description 9
- 239000011574 phosphorus Substances 0.000 claims description 9
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 8
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 8
- 229910052799 carbon Inorganic materials 0.000 claims description 8
- 239000001301 oxygen Substances 0.000 claims description 8
- 238000010583 slow cooling Methods 0.000 claims description 8
- 229910052804 chromium Inorganic materials 0.000 claims description 7
- 238000009628 steelmaking Methods 0.000 claims description 7
- 229910052786 argon Inorganic materials 0.000 claims description 6
- 239000002826 coolant Substances 0.000 claims description 6
- 239000002994 raw material Substances 0.000 claims description 6
- 238000002791 soaking Methods 0.000 claims description 6
- 238000009849 vacuum degassing Methods 0.000 claims description 6
- 238000006477 desulfuration reaction Methods 0.000 claims description 3
- 230000023556 desulfurization Effects 0.000 claims description 3
- 229910052745 lead Inorganic materials 0.000 claims description 2
- 229910052718 tin Inorganic materials 0.000 claims description 2
- 229910052785 arsenic Inorganic materials 0.000 claims 1
- 230000007797 corrosion Effects 0.000 abstract description 7
- 238000005260 corrosion Methods 0.000 abstract description 7
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 abstract description 6
- 229910052739 hydrogen Inorganic materials 0.000 abstract description 6
- 239000001257 hydrogen Substances 0.000 abstract description 6
- 230000035945 sensitivity Effects 0.000 abstract description 4
- 239000000463 material Substances 0.000 description 14
- 230000003009 desulfurizing effect Effects 0.000 description 13
- 229910001566 austenite Inorganic materials 0.000 description 11
- 238000001556 precipitation Methods 0.000 description 10
- 239000006185 dispersion Substances 0.000 description 7
- 150000001247 metal acetylides Chemical class 0.000 description 7
- 230000035882 stress Effects 0.000 description 6
- WUKWITHWXAAZEY-UHFFFAOYSA-L calcium difluoride Chemical compound [F-].[F-].[Ca+2] WUKWITHWXAAZEY-UHFFFAOYSA-L 0.000 description 5
- 239000003795 chemical substances by application Substances 0.000 description 5
- 239000010436 fluorite Substances 0.000 description 5
- 229910052751 metal Inorganic materials 0.000 description 5
- 239000002184 metal Substances 0.000 description 5
- 238000003756 stirring Methods 0.000 description 5
- 229910000859 α-Fe Inorganic materials 0.000 description 5
- 230000007547 defect Effects 0.000 description 4
- 229910001562 pearlite Inorganic materials 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 3
- 238000013461 design Methods 0.000 description 3
- 238000001953 recrystallisation Methods 0.000 description 3
- 238000010998 test method Methods 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 229910000734 martensite Inorganic materials 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- VNWKTOKETHGBQD-UHFFFAOYSA-N methane Chemical compound C VNWKTOKETHGBQD-UHFFFAOYSA-N 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 229910018072 Al 2 O 3 Inorganic materials 0.000 description 1
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- 238000007546 Brinell hardness test Methods 0.000 description 1
- 229910004298 SiO 2 Inorganic materials 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 229910001563 bainite Inorganic materials 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000005540 biological transmission Effects 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 230000003993 interaction Effects 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000000691 measurement method Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 238000004881 precipitation hardening Methods 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 238000000926 separation method Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 239000011593 sulfur Substances 0.000 description 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 1
Classifications
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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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- 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
- C21C1/00—Refining of pig-iron; Cast iron
- C21C1/02—Dephosphorising or desulfurising
-
- 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
- C21D1/18—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
- C21D8/06—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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
-
- 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
- C22C38/06—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
- 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
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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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
- C22C38/40—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
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Mechanical Engineering (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention relates to high mechanical property wind driven generator shaft steel and a preparation process thereof, wherein the steel comprises the following components in percentage by mass: c:0.22 to 0.29 percent, mn:0.55 to 0.85 percent, si:0.15 to 0.35 percent, cr: 0.65-1%, ni:2.7 to 3.2 percent, mo:0.21 to 0.55 percent, V:0.12 to 0.18 percent, S is less than or equal to 0.015 percent, P is less than or equal to 0.015 percent, cu is less than or equal to 0.13 percent, al is less than or equal to 0.015 percent, and N:0.008-0.016%, ti less than or equal to 0.003%, O less than or equal to 0.0015%, B less than or equal to 0.003%, as less than or equal to 0.04%, sn less than or equal to 0.02%, pb less than or equal to 0.003%, and the balance Fe and unavoidable impurities, wherein the preparation process comprises molten steel smelting, LF refining, continuous casting, continuous rolling, cold control and heat treatment procedures, a large-pressure rolling process is adopted, the initial rolling temperature is 950-1000 ℃, the accumulated deformation amount in the finish rolling stage is more than or equal to 22%, the final rolling temperature is 790-860 ℃, the tensile strength is ensured, and simultaneously, excellent hydrogen corrosion resistance and fracture toughness are maintained, and the steel impact toughness, stress set sensitivity, tensile strength and creep resistance meet the use requirements of severe working conditions, long service life and high reliability of the wind driven generator.
Description
Technical Field
The invention belongs to the technical field of metal smelting, and particularly relates to high mechanical property wind driven generator shaft steel and a preparation process thereof.
Background
The wind power generator shaft is an important part in the wind power transmission process, and the performance requirements on steel impact toughness, stress concentration sensitivity, tensile strength, creep resistance and other quality requirements are higher and higher. Impurity elements such as sulfur and phosphorus in the smelted CrMoA alloy steel form segregation, nonmetallic inclusions and highly enriched harmful elements are formed, the impurity elements are separated out along grain boundaries to cause material embrittlement, tempering embrittlement tendency exists, the proportion of crystal-along fracture on the fracture is higher, the tensile strength is higher, the hydrogen corrosion resistance and the fracture toughness are reduced, and the service requirements of a wind driven generator on severe working conditions, long service life and high reliability are difficult to meet.
Disclosure of Invention
The invention aims to solve at least one of the technical problems to a certain extent, and provides high mechanical property wind driven generator shaft steel and a preparation process thereof.
The technical scheme adopted for solving the technical problems is as follows:
the high mechanical property wind driven generator shaft steel comprises the following components in percentage by mass: c:0.22 to 0.29 percent, mn:0.55 to 0.85 percent, si:0.15 to 0.35 percent, cr: 0.65-1%, ni:2.7 to 3.2 percent, mo:0.21 to 0.55 percent, V:0.12 to 0.18 percent, S is less than or equal to 0.015 percent, P is less than or equal to 0.015 percent, cu is less than or equal to 0.13 percent, al is less than or equal to 0.015 percent, and N:0.008-0.016%, ti less than or equal to 0.003%, O less than or equal to 0.0015%, B less than or equal to 0.003%, as less than or equal to 0.04%, sn less than or equal to 0.02%, pb less than or equal to 0.003%, and the balance being Fe and unavoidable impurities.
The high mechanical property steel for the wind driven generator shaft is preferable that the sum of the mass percentages of Cr, ni, mo and V in the composition components is less than or equal to 4.6 percent.
The high mechanical properties of the steel for wind turbine shafts described above, preferably, steel properties: the yield strength is 990-1095 MPa, the tensile strength is 1185-1300MPa, the elongation at break is more than or equal to 13%, the normal temperature impact energy is more than or equal to 100J, and the tissue center segregation is less than or equal to 1.5 level.
The design basis of the composition components of the high mechanical property wind driven generator shaft steel is as follows:
(1) Determination of C content: with the increase of the content of C, the yield point and the tensile strength are increased, the hardenability, the hardness and the wear resistance are improved, but the influence of the higher content of C on the hardness is small, massive carbide liquid precipitation, plasticity, toughness and weather resistance are easy to generate, coarse martensitic structure is obtained after quenching, the brittleness is increased, and the content range of C is determined to be 0.22-0.29%;
(2) Determination of Mn content: the steel can be dissolved into a ferrite reinforced matrix, pearlite can be thinned when the steel is cooled after rolling, the pearlite content can be relatively improved, the strength and the hardness can be improved, the hardenability of the steel can be improved, but the brittleness can be increased when the Mn content is higher, the surface quality is affected, the tempering brittleness of the material is increased, and meanwhile, the component segregation is caused, and the Mn content range is determined to be 0.55-0.85%;
(3) Determination of Si content: si is an indispensable deoxidizer in the steelmaking process, ferrite can be dissolved in steel, solid solution strengthening is carried out, the yield point and the tensile strength are improved, but the toughness of the steel is reduced due to the fact that the Si content is higher, and the Si content range is determined to be 0.15-0.35%.
(4) Determination of Cr content: cr can obviously improve strength, hardness and wear resistance, partially form various carbides, play a role in dispersion strengthening, improve oxidation resistance and corrosion resistance of steel, and slow down methane reaction on the surface and inside of the steel with Mo. The hydrogen corrosion resistance is improved, but the plasticity and toughness are reduced when the Cr content is higher, the cost and the production difficulty are increased, and the Cr content range is determined to be 0.65-1%;
(5) Determination of Ni content: the ferrite is strengthened in the steel, the pearlite is refined, ni can improve the strength of the steel, good plasticity and toughness are maintained, the hardenability of the steel is improved to a certain extent, but the creep resistance of the ferrite cannot be improved due to the fact that Ni is high, the hot brittleness of the pearlite steel is increased, and the Ni content range is determined to be 2.7-3.2%;
(6) Determination of Mo content: mo can refine the crystal grains of steel, improve the hardenability and the heat strength, maintain enough strength and creep resistance at high temperature, inhibit brittleness of the steel caused by quenching, have strong interaction with impurity elements such as phosphorus and the like, can generate precipitation phases in the crystal and prevent the grain boundary segregation of the phosphorus, but Mo is Yi Tuotan, the heat processing and heat treatment temperature ranges are narrow, and the Mo content range is determined to be 0.21-0.55%;
(7) Determination of V content: v is an excellent deoxidizer of steel, can increase the hardenability of steel when being melted into austenite at high temperature, refine structural grains, improve strength and toughness, increase the ductility and fracture resistance of alloy, and the carbide formed by vanadium and carbon can improve the hydrogen corrosion resistance at high temperature and high pressure, but V increases the mean free path again and reduces the bending resistance and strength, the V content range is determined to be 0.12-0.18%, the sum of the mass percentages of Cr, ni, mo and V is less than or equal to 4.6%, and the strength is higher and has good comprehensive performance;
(8) Determination of S, P content: s can cause the steel to generate hot shortness, and reduce the plasticity and toughness of the steel; p is melted in ferrite to easily form defects such as segregation, inclusion and the like, and the tempering brittleness is increased; the content range of Cu and S is less than or equal to 0.015 percent, and the content range of P is less than or equal to 0.015 percent;
(9) Determination of Cu content: cu can improve strength and toughness, but Cu is high again and is easy to generate thermal embrittlement during hot working, and the Cu content range is determined to be less than or equal to 0.20 percent;
(10) Determination of Al, N and Ti contents: alN formed by combining Al and N can effectively prevent coarsening of austenite grains, but Al is easy to form due to the higher content of Al 2 O 3 The brittle inclusions are equal, the purity of molten steel is reduced, and the content range of Al is less than or equal to 0.015 percent; n has the effects of solidification and strong melting, but precipitation hardening and strain aging occur when the N is tempered again, the toughness is reduced, the notch brightness is increased while the strength and the hardness are improved, and the range of the N content is determined to be 0.008-0.016; ti and N are combined to refine grains, but Ti is high, tiN and Ti (CN) are used as hard and brittle inclusions in steel to easily cause stress concentration and deteriorate the fatigue life of the steel, and the content range of Ti is determined to be less than or equal to 0.02 percent;
(11) Determination of O, B, as, sn, pb content: o is mainly composed of Al in steel 2 O 3 、MnO、SiO 2 The existence of the iso-oxide inclusion forms is easy to cause stressThe fatigue life of the concentrated and deteriorated steel is set to 0.0015% or less, the content of O is set to 0.003% or less, the content of B is set to 0.003% or less, as, sn and Pb are likely to cause soft spots on the surface of the part, the hardness is uneven, the content of As is set to 0.04% or less, the content of Sn is set to 0.02% or less, and the content of Pb is set to 0.003% or less, while the content of B is set to O, N.
The preparation process of the high mechanical property wind driven generator shaft steel comprises the following steps:
s1: smelting molten steel: the steel-making raw material is desulfurized by a molten iron pretreatment KR, molten steel is obtained by smelting by an electric furnace or a converter by an oxygen top-blowing and double slag method, caO and fluorite are adopted as a desulfurizing agent for the molten iron pretreatment KR, S is controlled to be less than or equal to 0.005 percent, the carbon content of a tapping end point is controlled to be 0.14-0.22 percent, the phosphorus content of the end point is controlled to be less than or equal to 0.014 percent, the tapping temperature is controlled to be 1620-1730 ℃, slag is blocked, steel is tapped, al is added for deoxidization during tapping, the number of inclusions is reduced from the source, the inclusions are prevented from becoming fatigue crack sources, and the fatigue life of a shaft is reduced, so that the molten steel is obtained;
s2: LF refining: carrying out VD vacuum degassing treatment on the molten steel obtained in the step S1 after Al+SiC combined deoxidation, wherein the ultimate vacuum degree is less than or equal to 68Pa, the pressure maintaining time is not less than 20min, slag formation and deoxidization inclusion removal are ensured, feSiMn alloy is adopted for component adjustment, and the FeSiMn comprises the following components in percentage by mass: 14-17%, mn:60-70%, al less than or equal to 0.02%, ti less than or equal to 0.02%, and the balance Fe and unavoidable impurities, wherein the soft argon blowing time is more than or equal to 40min, so that nonmetallic inclusions fully float upwards, the purity of steel and the service life of a shaft are improved, and refined molten steel meeting component requirements is obtained;
s3: continuous casting: continuously casting the refined molten steel in the step S2, controlling the superheat degree to be 20-30 ℃, controlling the segregation by pouring with low superheat degree, controlling the molten steel pouring temperature to be 1510-1630 ℃, improving the uniformity of the cross section components of the casting blank by electromagnetic stirring at the tail end, reducing the segregation of materials, reducing the central looseness and crack defects, improving the material structure and obtaining a rectangular continuous casting blank;
s4: tandem rolling: the rectangular continuous casting blank in the step S3 is processed by adopting a large reduction rolling process, and the rectangular continuous casting blank comprises heating, high-pressure water descaling, 6-pass rough rolling, 8-pass middle rolling, 6-pass pre-finish rolling and 4-pass finish rolling which are sequentially carried out; the preheating section temperature in the heating process is 500-850 ℃, the heating section temperature is 990-1180 ℃, the soaking section temperature is 1050-1120 ℃, the total heating time is controlled to 10-20 h, refined grains and uniformity are effectively controlled, microscopic pores are prevented from being generated, the water pressure in the high-pressure water descaling process is more than or equal to 22MPa, the surface quality of a product is ensured by removing iron scales on the surface of a billet, the initial rolling temperature is 950-1000 ℃, the accumulated deformation amount in the finish rolling stage is more than or equal to 22%, the temperature before pre-finish rolling is 820-945 ℃, the finish rolling temperature is 790-860 ℃, the carbide net is controlled by adopting a water cooling unit before and after intermediate rolling and finish rolling, the dispersed precipitation of refined grains and carbides is ensured, the overall dimension precision is less than or equal to 15-32 dimension precision of less than or equal to +/-0.1 mm, and the dimension precision of phi 32-60 dimension precision is less than or equal to +/-0.15 mm, and the bar is obtained;
s5: and (3) cooling control: slowly cooling the bar in the step S4 in a double-length cooling bed at the cooling speed of 1-2 ℃/S, wherein the temperature of the lower cooling bed is 450-520 ℃, and the bar is obtained by slowly cooling the bar in a slow cooling cover stack after cooling down a line for 48-72 hours, so that the cooling speed is prevented from being too fast, the formation of brittle bainite and martensite structures is prevented, the solubility of carbon in austenite is ensured, and the austenite grain size reaches more than 7 levels;
s6: and (3) heat treatment: the bar in the step S5 is processed by adopting a quenching and tempering procedure, the quenching temperature is 890-915 ℃, the furnace time coefficient is 2-2.8 min/mm, the cooling medium is water after quenching, and the cooling rate is 20-30 ℃/S, so as to improve the hardness and strength of steel; tempering temperature is 520-690 ℃, furnace time coefficient is 2.5-4.0 min/mm, air cooling is performed at 200 ℃ or below, internal stress generated during quenching is eliminated, carbide precipitation coarsening particles and continuous or discontinuous netlike brittleness of alloy precipitation along grain boundary are avoided, grain boundary fracture is improved, and steel meeting comprehensive mechanical properties is obtained.
Compared with the prior art, the invention has the beneficial effects that:
the composition components and the process design are adopted, the yield point and the tensile strength are improved, meanwhile, the hardenability of steel is ensured, KR desulfurization is pretreated, molten steel smelting is performed by an oxygen top-blown and double slag method, LF refining is performed to control components, inclusions are prevented from becoming fatigue crack sources, the fatigue life of a shaft is reduced, material segregation is reduced by low superheat pouring, central porosity and crack defects are reduced, refined grains and uniformity are effectively controlled by a large-pressure rolling and slow cooling controlled cooling process, the dispersion and precipitation of the refined grains and carbide are ensured, the hardness and the strength of steel are improved by quenching and tempering, the edge grain fracture is improved, and the steel performance is: the yield strength is 990-1095 MPa, the tensile strength is 1185-1300MPa, the elongation at break is more than or equal to 13%, the normal-temperature impact energy is more than or equal to 100J, the tissue center segregation is less than or equal to 1.5 level, the tensile strength is ensured, and meanwhile, the excellent hydrogen corrosion resistance and fracture toughness are maintained, and the steel impact toughness, stress concentration sensitivity, tensile strength and creep resistance meet the use requirements of the wind driven generator on severe working conditions, long service life and high reliability.
Detailed Description
The following detailed description of the embodiments of the invention is intended to be illustrative of the invention and is not to be taken as limiting the invention.
Example 1:
in order to provide a preferred implementation mode of the high mechanical performance wind turbine shaft steel, the high mechanical performance wind turbine shaft steel comprises the following components in percentage by mass: c:0.28%, mn:0.59%, si:0.25%, cr:0.8%, ni:2.9%, mo:0.32%, V:0.16%, S:0.005%, P:0.006%, cu:0.1%, al:0.012%, N:0.01%, ti:0.002%, O:0.001%, B:0.001%, as:0.02%, sn:0.01%, pb:0.002%, the balance being Fe and unavoidable impurities, wherein the sum of the mass percentages of Cr, ni, mo and V in the composition components is less than or equal to 4.6%.
The preparation process of the high mechanical property wind driven generator shaft steel comprises the following steps:
s1: smelting molten steel: desulfurizing the steelmaking raw material by molten iron pretreatment KR, smelting by an oxygen top-blowing and double slag method electric furnace or converter to obtain molten steel, wherein a desulfurizing agent for desulfurizing the molten iron pretreatment KR adopts CaO and fluorite, S is controlled to be less than or equal to 0.005 percent, the carbon content of a tapping endpoint is controlled to be 0.15-0.18 percent, the phosphorus content of the endpoint is controlled to be less than or equal to 0.014 percent, the tapping temperature is controlled to be 1650-1700 ℃, slag is blocked, tapping is carried out, and Al is added in the tapping process for deoxidization to obtain molten steel;
s2: LF refining: carrying out VD vacuum degassing treatment on the molten steel obtained in the step S1 after Al+SiC combined deoxidation, wherein the ultimate vacuum degree is less than or equal to 68Pa, the dwell time is not less than 20min, and carrying out component adjustment on FeSiMn alloy, wherein the FeSiMn alloy comprises the following components in percentage by mass: 16%, mn:65%, al less than or equal to 0.02%, ti less than or equal to 0.02%, and the balance Fe and unavoidable impurities, wherein the soft argon blowing time is more than or equal to 40min, so as to obtain refined molten steel meeting the component requirements;
s3: continuous casting: continuously casting the refined molten steel in the step S2, controlling the superheat degree to be 20-25 ℃, the casting temperature of the molten steel to be 1520-1610 ℃, and carrying out electromagnetic stirring at the tail end to obtain a rectangular continuous casting blank;
s4: tandem rolling: the rectangular continuous casting blank in the step S3 is processed by adopting a large reduction rolling process, and the rectangular continuous casting blank comprises heating, high-pressure water descaling, 6-pass rough rolling, 8-pass middle rolling, 6-pass pre-finish rolling and 4-pass finish rolling which are sequentially carried out; the preheating section temperature in the heating process is 650-750 ℃, the heating section temperature is 990-1080 ℃, the soaking section temperature is 1050-1100 ℃, the total heating time is controlled to 15-18 h, the water pressure in the high-pressure water descaling process is more than or equal to 22MPa, the initial rolling temperature is 950-1000 ℃, the accumulated deformation amount in the finish rolling stage is more than or equal to 22%, the temperature before finish rolling is 850-920 ℃, the finish rolling temperature is 790-830 ℃, the water cooling units are used for controlling cooling before and after intermediate rolling and finish rolling, carbide net is controlled by accumulated deformation rolling in an austenite non-recrystallization region and a low-temperature two-phase region, the dispersion precipitation of refined grains and carbides is ensured, and the external dimension precision reaches phi 30 dimension precision to be less than or equal to +/-0.1 mm, so as to obtain bars;
s5: and (3) cooling control: slowly cooling the bar in the step S4 in a double-length cooling bed at the cooling speed of 1-2 ℃/S, cooling the bar in a lower cooling bed at the temperature of 450-500 ℃, and slowly cooling the bar in a slow cooling cover stack for 48-68 hours after cooling down the bar in a cooling line to prevent the cooling speed from being too fast, wherein the austenite grain size reaches more than 7 levels, thus obtaining the bar;
s6: and (3) heat treatment: the bar material in the step S5 is processed by adopting a quenching and tempering procedure, wherein the quenching temperature is 990-915 ℃, the furnace time coefficient is 2-2.5 min/mm, the cooling medium is water after quenching, the cooling rate is 25-30 ℃/S, the tempering temperature is 550-630 ℃, the furnace time coefficient is 2.5-3.5 min/mm, and the air cooling is carried out at the temperature below 200 ℃ to obtain the steel material conforming to the comprehensive mechanical properties.
Example 2:
in order to provide a preferred implementation mode of the high mechanical performance wind turbine shaft steel, the high mechanical performance wind turbine shaft steel comprises the following components in percentage by mass: c:0.27%, mn:0.7%, si:0.32%, cr:1%, ni:2.7%, mo:0.22%, V:0.14%, S:0.008%, P:0.009%, cu:0.1%, al:0.008%, N:0.013%, ti:0.002%, O:0.001%, B:0.002%, as:0.01%, sn:0.02%, pb:0.001%, the balance being Fe and unavoidable impurities, wherein the sum of the mass percentages of Cr, ni, mo and V in the composition components is less than or equal to 4.6%.
The preparation process of the high mechanical property wind driven generator shaft steel comprises the following steps:
s1: smelting molten steel: desulfurizing the steelmaking raw material by molten iron pretreatment KR, smelting by an oxygen top-blowing and double slag method electric furnace or converter to obtain molten steel, wherein a desulfurizing agent for desulfurizing the molten iron pretreatment KR adopts CaO and fluorite, S is controlled to be less than or equal to 0.005 percent, the carbon content of a tapping endpoint is controlled to be 0.15-0.2 percent, the phosphorus content of the endpoint is controlled to be less than or equal to 0.014 percent, the tapping temperature is controlled to be 1620-1680 ℃, slag is blocked, tapping is carried out, and Al is added for deoxidization in the tapping process to obtain molten steel;
s2: LF refining: carrying out VD vacuum degassing treatment on the molten steel obtained in the step S1 after Al+SiC combined deoxidation, wherein the ultimate vacuum degree is less than or equal to 68Pa, the dwell time is not less than 20min, and carrying out component adjustment on FeSiMn alloy, wherein the FeSiMn alloy comprises the following components in percentage by mass: 16%, mn:67%, al less than or equal to 0.02%, ti less than or equal to 0.02%, and Fe and unavoidable impurities as the rest, wherein the soft argon blowing time is more than or equal to 40min, so as to obtain refined molten steel meeting the component requirements;
s3: continuous casting: continuously casting the refined molten steel in the step S2, controlling the superheat degree to be 25-30 ℃, the casting temperature of the molten steel to be 1510-1580 ℃, and carrying out electromagnetic stirring at the tail end to obtain a rectangular continuous casting blank;
s4: tandem rolling: the rectangular continuous casting blank in the step S3 is processed by adopting a large reduction rolling process, and the rectangular continuous casting blank comprises heating, high-pressure water descaling, 6-pass rough rolling, 8-pass middle rolling, 6-pass pre-finish rolling and 4-pass finish rolling which are sequentially carried out; the preheating section temperature in the heating process is 730-850 ℃, the heating section temperature is 995-1170 ℃, the soaking section temperature is 1070-1120 ℃, the total heating time is controlled to 10-18 h, the water pressure in the high-pressure water descaling process is more than or equal to 22MPa, the starting rolling temperature is 950-1000 ℃, the accumulated deformation amount in the finish rolling stage is more than or equal to 22%, the temperature before pre-finish rolling is 830-930 ℃, the finishing rolling temperature is 835-860 ℃, the carbide net is controlled by adopting a water cooling unit for controlled cooling before and after the middle rolling and finish rolling, the dispersion precipitation of refined grains and carbides is ensured, and the overall dimension precision is less than or equal to +/-0.1 mm, thereby obtaining bars;
s5: and (3) cooling control: slowly cooling the bar in the step S4 in a double-length cooling bed at the cooling speed of 1-2 ℃/S, wherein the temperature of the lower cooling bed is 450-515 ℃, and after the cooling line is cooled down, the bar is slowly cooled in a slow cooling cover stack for 58-72 hours to prevent the cooling speed from being too fast, and the austenite grain size reaches more than 7 levels, so as to obtain the bar;
s6: and (3) heat treatment: the bar material in the step S5 is processed by adopting a quenching and tempering procedure, wherein the quenching temperature is 895-915 ℃, the furnace time coefficient is 2-2.4 min/mm, the cooling medium is water after quenching, the cooling rate is 25-30 ℃/S, the tempering temperature is 540-680 ℃, the furnace time coefficient is 2.8-4.0 min/mm, and the air cooling is carried out at the temperature below 200 ℃ to obtain the steel material conforming to the comprehensive mechanical properties.
Example 3:
in order to provide a preferred implementation mode of the high mechanical performance wind turbine shaft steel, the high mechanical performance wind turbine shaft steel comprises the following components in percentage by mass: c:0.25%, mn:0.8%, si:0.22%, cr:0.9%, ni:2.8%, mo:0.3%, V:0.17%, S:0.006%, P:0.006%, cu:0.13%, al:0.012%, N:0.009%, ti:0.002%, O:0.001%, B:0.002%, as:0.03%, sn:0.008%, pb:0.002%, the balance being Fe and unavoidable impurities, wherein the sum of the mass percentages of Cr, ni, mo and V in the composition components is less than or equal to 4.6%.
The preparation process of the high mechanical property wind driven generator shaft steel comprises the following steps:
s1: smelting molten steel: desulfurizing the steelmaking raw material by molten iron pretreatment KR, smelting by an oxygen top-blowing and double slag method electric furnace or converter to obtain molten steel, wherein a desulfurizing agent for desulfurizing the molten iron pretreatment KR adopts CaO and fluorite, S is controlled to be less than or equal to 0.005 percent, the carbon content of a tapping endpoint is controlled to be 0.14-0.18 percent, the phosphorus content of the endpoint is controlled to be less than or equal to 0.014 percent, the tapping temperature is controlled to be 1620-1680 ℃, slag is blocked, tapping is carried out, and Al is added for deoxidization in the tapping process to obtain molten steel;
s2: LF refining: carrying out VD vacuum degassing treatment on the molten steel obtained in the step S1 after Al+SiC combined deoxidation, wherein the ultimate vacuum degree is less than or equal to 68Pa, the dwell time is not less than 20min, and carrying out component adjustment on FeSiMn alloy, wherein the FeSiMn alloy comprises the following components in percentage by mass: 17%, mn:65%, al less than or equal to 0.02%, ti less than or equal to 0.02%, and the balance Fe and unavoidable impurities, wherein the soft argon blowing time is more than or equal to 40min, so as to obtain refined molten steel meeting the component requirements;
s3: continuous casting: continuously casting the refined molten steel in the step S2, controlling the superheat degree to be 20-30 ℃, the casting temperature of the molten steel to be 1520-1610 ℃, and carrying out electromagnetic stirring at the tail end to obtain a rectangular continuous casting blank;
s4: tandem rolling: the rectangular continuous casting blank in the step S3 is processed by adopting a large reduction rolling process, and the rectangular continuous casting blank comprises heating, high-pressure water descaling, 6-pass rough rolling, 8-pass middle rolling, 6-pass pre-finish rolling and 4-pass finish rolling which are sequentially carried out; the preheating section temperature in the heating process is 500-750 ℃, the heating section temperature is 990-1140 ℃, the soaking section temperature is 1050-1140 ℃, the total heating time is controlled to be 10-15 h, the water pressure in the high-pressure water descaling process is more than or equal to 22MPa, the initial rolling temperature is 965-1000 ℃, the accumulated deformation amount in the finish rolling stage is more than or equal to 22%, the temperature before finish rolling is 820-925 ℃, the finish rolling temperature is 795-850 ℃, the water cooling unit is adopted for controlled cooling before and after intermediate rolling and finish rolling, carbide meshes are controlled by accumulated deformation rolling in an austenite non-recrystallization region and a low-temperature two-phase region, the dispersion precipitation of refined grains and carbides is ensured, and the overall dimension precision is less than or equal to +/-0.1 mm, so that the bar is obtained;
s5: and (3) cooling control: slowly cooling the bar in the step S4 in a double-length cooling bed at the cooling speed of 1-2 ℃/S, cooling the bar in a lower cooling bed at the temperature of 465-520 ℃, and slowly cooling the bar in a slow cooling cover stack for 58-70h after cooling down the bar to prevent the cooling speed from being too fast, wherein the austenite grain size reaches more than 7 levels, thereby obtaining the bar;
s6: and (3) heat treatment: the bar material in the step S5 is processed by adopting a quenching and tempering procedure, wherein the quenching temperature is 890-905 ℃, the furnace time coefficient is 2-2.4 min/mm, the cooling medium is water after quenching, the cooling rate is 20-28 ℃/S, the tempering temperature is 520-680 ℃, the furnace time coefficient is 2.8-4.0 min/mm, and the air cooling is carried out at the temperature below 200 ℃ to obtain the steel material conforming to the comprehensive mechanical properties.
Example 4:
in order to provide a preferred implementation mode of the high mechanical performance wind turbine shaft steel, the high mechanical performance wind turbine shaft steel comprises the following components in percentage by mass: c:0.22%, mn:0.6%, si:0.26%, cr:0.7%, ni:3.1%, mo:0.4%, V:0.15%, S:0.009%, P:0.007%, cu:0.05%, al:0.008%, N:0.009%, ti:0.002%, O:0.001%, B:0.002%, as:0.03%, sn:0.01%, pb:0.002%, the balance being Fe and unavoidable impurities, wherein the sum of the mass percentages of Cr, ni, mo and V in the composition components is less than or equal to 4.6%.
The preparation process of the high mechanical property wind driven generator shaft steel comprises the following steps:
s1: smelting molten steel: desulfurizing the steelmaking raw material by molten iron pretreatment KR, smelting by an oxygen top-blowing and double slag method electric furnace or converter to obtain molten steel, wherein a desulfurizing agent for desulfurizing the molten iron pretreatment KR adopts CaO and fluorite, S is controlled to be less than or equal to 0.005 percent, the carbon content of a tapping endpoint is controlled to be 0.14-0.18 percent, the phosphorus content of the endpoint is controlled to be less than or equal to 0.014 percent, the tapping temperature is controlled to be 1650-1700 ℃, slag is blocked, tapping is carried out, and Al is added in the tapping process for deoxidization to obtain molten steel;
s2: LF refining: carrying out VD vacuum degassing treatment on the molten steel obtained in the step S1 after Al+SiC combined deoxidation, wherein the ultimate vacuum degree is less than or equal to 68Pa, the dwell time is not less than 20min, and carrying out component adjustment on FeSiMn alloy, wherein the FeSiMn alloy comprises the following components in percentage by mass: 15%, mn:68 percent, less than or equal to 0.02 percent of AL, less than or equal to 0.02 percent of Ti, and the balance of Fe and unavoidable impurities, wherein the soft argon blowing time is more than or equal to 40 minutes, so as to obtain refined molten steel meeting the component requirements;
s3: continuous casting: continuously casting the refined molten steel in the step S2, controlling the superheat degree to be 20-30 ℃, the casting temperature of the molten steel to be 1530-1630 ℃, and carrying out electromagnetic stirring at the tail end to obtain a rectangular continuous casting blank;
s4: tandem rolling: the rectangular continuous casting blank in the step S3 is processed by adopting a large reduction rolling process, and the rectangular continuous casting blank comprises heating, high-pressure water descaling, 6-pass rough rolling, 8-pass middle rolling, 6-pass pre-finish rolling and 4-pass finish rolling which are sequentially carried out; the preheating section temperature is 700-850 ℃ in the heating process, the heating section temperature is 990-1160 ℃, the soaking section temperature is 1060-1120 ℃, the total heating time is controlled to 11-20 h, the water pressure is more than or equal to 22MPa in the high-pressure water descaling process, the initial rolling temperature is 950-1000 ℃, the accumulated deformation amount in the finish rolling stage is more than or equal to 22%, the temperature before finish rolling is 825-925 ℃ and the finish rolling temperature is 795-840 ℃, the water cooling unit is adopted for controlling cooling before and after intermediate rolling and finish rolling, carbide net is controlled by accumulated deformation rolling in an austenite non-recrystallization region and a low-temperature two-phase region, the dispersion precipitation of refined grains and carbides is ensured, and the overall dimension precision reaches phi 30 dimension precision less than or equal to +/-0.1 mm, so as to obtain bars;
s5: and (3) cooling control: slowly cooling the bar in the step S4 in a double-length cooling bed at the cooling speed of 1-2 ℃/S, cooling the bar in a lower cooling bed at the temperature of 460-510 ℃, and slowly cooling the bar in a slow cooling cover stack for 60-72h after cooling down the bar to prevent the cooling speed from being too fast, wherein the austenite grain size reaches more than 7 levels, thereby obtaining the bar;
s6: and (3) heat treatment: the bar material in the step S5 is processed by adopting a quenching and tempering procedure, wherein the quenching temperature is 895-905 ℃, the furnace time coefficient is 2-2.8 min/mm, the cooling medium is water after quenching, the cooling rate is 20-30 ℃/S, the tempering temperature is 570-690 ℃, the furnace time coefficient is 2.5-4.0 min/mm, and the air cooling is carried out at the temperature below 200 ℃ to obtain the steel material conforming to the comprehensive mechanical properties.
Comparative example 1: the CrMoA comprises the following components in percentage by mass: c:0.31%, mn:0.9%, si:0.12%, cr:1.2%, ni:0.34%, mo:0.2%, S:0.035%, P:0.03%, cu:0.2%, and the balance of Fe and unavoidable impurities.
Comparative example 2: the CrMoA comprises the following components in percentage by mass: c:0.39%, mn:0.85%, si:0.4%, cr:1.1%, ni:0.25%, mo:0.15%, S:0.03%, P:0.035%, cu:0.18%, and the balance of Fe and unavoidable impurities.
Examples 1 to 4 and comparative examples 1 and 2 were tested according to the GB/T229 metal Charpy notch test method, the GB/T231 metal Brinell hardness test method, the GB/T2039 metal tensile creep and endurance test method, the nonmetallic inclusion microscopic assessment method in GB/T10561 steel, the mechanical property test method of ASTMA370 steel products and the YB/5148 metal average grain size measurement method, and the results are as follows:
from the above table, the steel properties: the yield strength is 990-1095 MPa, the tensile strength is 1185-1300MPa, the elongation at break is more than or equal to 13%, the normal temperature impact power is more than or equal to 100J, the tissue center segregation is less than or equal to 1.5 level, the D-type brittle inclusions are fewer, the stress concentration and crack propagation generated by separation from a matrix in the deformation process of steel are reduced, the composition and the process design are adopted, the yield point and the tensile strength are improved, meanwhile, the hardenability of the steel is ensured, KR desulfurization is pretreated, the molten steel is smelted by an oxygen top blowing method and a double slag method, LF refining control components are used for avoiding inclusions becoming fatigue crack sources to reduce the fatigue life of a shaft, the material segregation is reduced by pouring at a low superheat degree, the center looseness and crack defects are reduced, the rolling under a large pressure and the slow cooling control cooling process are effectively controlled, the dispersion and the uniformity of refined grains and carbides are ensured, the hardness and the strength of the quenched steel are improved, the along-grain fracture is ensured, the excellent hydrogen corrosion resistance and the fracture toughness are ensured, and the steel impact toughness, the stress concentration sensitivity, the tensile strength and the creep resistance are met, and the service requirements of a severe working condition and a long service life of a wind driven generator are met.
The above list of detailed descriptions is only specific to practical embodiments of the present invention, and they are not intended to limit the scope of the present invention, and all equivalent embodiments or modifications that do not depart from the spirit of the present invention should be included in the scope of the present invention.
Claims (4)
1. The high mechanical property wind driven generator shaft steel is characterized by comprising the following components in percentage by mass: c:0.22 to 0.29 percent, mn:0.55 to 0.85 percent, si:0.15 to 0.35 percent, cr: 0.65-1%, ni:2.7 to 3.2 percent, mo:0.21 to 0.55 percent, V: 0.12-0.18%, S is less than or equal to 0.015%, P is less than or equal to 0.015%, cu is less than or equal to 0.13%, al is less than or equal to 0.015%, and N:0.008-0.016 percent of Ti less than or equal to 0.003 percent, less than or equal to 0.0015 percent of O less than or equal to 0.003 percent of B less than or equal to 0.04 percent of As less than or equal to 0.02 percent of Sn less than or equal to 0.003 percent of Pb less than or equal to 0.003 percent of Fe and unavoidable impurities, and the balance of Fe and unavoidable impurities, wherein the total mass percent of Cr, ni, mo and V in the composition components is less than or equal to 4.6 percent;
steel properties: yield strength is 990-1095 MPa, tensile strength is 1185-1300MPa, elongation at break is more than or equal to 13%, normal-temperature impact energy is more than or equal to 100J, and tissue center segregation is less than or equal to 1.5 level;
the preparation process comprises the steps of molten steel smelting, LF refining, continuous casting, continuous rolling, controlled cooling and heat treatment which are sequentially carried out;
in the LF refining process, VD vacuum degassing treatment is adopted after Al+SiC combined deoxidation, the ultimate vacuum degree is less than or equal to 68Pa, the dwell time is not less than 20min, feSiMn alloy is adopted for component adjustment, and the FeSiMn comprises the following components in percentage by mass: 14-17%, mn:60-70%, al less than or equal to 0.02%, ti less than or equal to 0.02%, and Fe and unavoidable impurities as the rest, wherein the soft argon blowing time is more than or equal to 40min;
in the heating process of the continuous rolling process, the temperature of a preheating section is 500-850 ℃, the temperature of a heating section is 990-1180 ℃, the temperature of a soaking section is 1050-1120 ℃, the total heating time is controlled to be 10-20 h, a large-reduction rolling process is adopted, the initial rolling temperature is 950-1000 ℃, the accumulated deformation of a finish rolling stage is more than or equal to 22%, and the final rolling temperature is 790-860 ℃;
the cooling control procedure is carried out in a double-length cooling bed, the cooling speed is 1-2 ℃/S, the temperature of the lower cooling bed is 450-520 ℃, and the cooling line is cooled down slowly in a slow cooling cover stack for 48-72;
the heat treatment process adopts a quenching and tempering process, the quenching temperature is 890-915 ℃, the furnace time coefficient is 2-2.8 min/mm, the cooling medium is water after quenching, and the cooling rate is 20-30 ℃/s; tempering temperature is 520-690 ℃, furnace time coefficient is 2.5-4.0 min/mm, and air cooling is performed below 200 ℃.
2. The high mechanical property wind driven generator shaft steel according to claim 1, wherein in the molten steel smelting process, steel-making raw materials are subjected to KR desulfurization in molten iron pretreatment, molten steel is smelted by an electric furnace or a converter through an oxygen top-blowing and double slag method, the carbon content of a tapping terminal point is controlled to be 0.14-0.22%, the phosphorus content of the terminal point is less than or equal to 0.014%, the tapping temperature is controlled to be 1620-1730 ℃, slag is blocked, and Al is added for deoxidization in the tapping process.
3. The high mechanical property wind driven generator shaft steel according to claim 1, wherein the superheat degree is controlled to be 20-30 ℃ in the continuous casting process, and the casting temperature of molten steel is 1510-1630 ℃.
4. The high mechanical property wind turbine shaft steel according to claim 1, wherein the continuous rolling process comprises heating, high-pressure water descaling, 6-pass rough rolling, 8-pass intermediate rolling, 6-pass pre-finish rolling and 4-pass finish rolling which are sequentially carried out; the water pressure in the high-pressure water descaling process is more than or equal to 22MPa, and the temperature before pre-finish rolling is 820-945 ℃.
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