CN117210770A - Steel plate for high-strength homogenized ferrite ultra-thick wind power structure and manufacturing method thereof - Google Patents
Steel plate for high-strength homogenized ferrite ultra-thick wind power structure and manufacturing method thereof Download PDFInfo
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- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 6
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 4
- 229910001568 polygonal ferrite Inorganic materials 0.000 claims abstract description 4
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- 238000001816 cooling Methods 0.000 claims description 14
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- 239000002131 composite material Substances 0.000 description 4
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- 239000013078 crystal Substances 0.000 description 2
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- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
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- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- 229910000742 Microalloyed steel Inorganic materials 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- 241000519995 Stachys sylvatica Species 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 229910011214 Ti—Mo Inorganic materials 0.000 description 1
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- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 1
Classifications
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Abstract
The invention provides a high-strength homogenized ferrite ultra-thick steel plate for a wind power structure and a manufacturing method thereof, wherein the steel plate comprises the following components in percentage by weight: c:0.10 to 0.22 percent, mn:0.05 to 1.88 percent, P is less than or equal to 0.022 percent, S is less than or equal to 0.010 percent, cr:0.01 to 0.60 percent of Ni:0.001% -0.009%, mo:0.001% -0.010%, cu:0.001% -0.009%, nb:0.010 to 0.020 percent, 0.001 to 0.027 percent of V, ti:0.001 to 0.028 percent, 0.02 to 0.05 percent of CaO, la:5ppm to 15ppm, B:0.0011 to 0.0029 percent, and the balance of Fe and unavoidable impurities; the manufacturing method comprises smelting, continuous casting, assembling, rolling and quenching; the thickness of the steel plate for the wind power structure produced by the invention is 80-150mm, and the positions of 1/2T and 1/4T of the steel plate are fine polygonal ferrite and pearlite structures, and the grain size is more than or equal to 8.5 levels.
Description
Technical Field
The invention belongs to the field of metal materials, and particularly relates to a high-strength homogenized ferrite steel plate for an ultra-thick wind power structure and a manufacturing method thereof.
Background
The normalized steel plate can obtain higher comprehensive mechanical property and better machining property, and is an important heat treatment means for improving the structural uniformity and toughness of the steel plate. The normalizing steel plate is widely applied to the fields of pressure vessels, high-rise buildings, bridges, engineering machinery and the like, and particularly for some wind power and vessel projects, the normalizing steel plate is compulsorily required to be used in project design.
The conventional normalizing adopts an air cooling mode, and the phase transition temperature is high due to low cooling speed, so that although a refined pearlite structure can be obtained, the impact energy and the elongation are improved, ferrite grains still grow up while the toughness is improved, and the strength of the steel plate is reduced; the niobium microalloyed steel is normalized and then has a reduced precipitation strengthening effect due to the growth of niobium carbonitride, so that the strength of the steel plate is greatly reduced after normalization, and particularly, the controlled rolling and controlled cooling steel plate often generates unqualified products due to overlarge strength loss.
In order to prevent the strength of the steel plate from being greatly reduced after normalizing, a manufacturing method of an isometric ferrite extra-thick plate with high uniformity is developed: the composite steel plate is directly cooled to room temperature on line after controlled rolling, and is subjected to position allocation through a composite blank, compared with the steel plate directly rolled by a continuous casting blank, the weak T/4 and T/2 positions of the steel plate are not segregated, the toughness is improved, the ferrite and fine pearlite structure with uniform structure is obtained after the steel plate is quenched and the crystal deformation energy is consumed, and the strength and the toughness of each thickness position of the steel plate are well represented through fine grain strengthening and precipitation strengthening means. At present, some researches are carried out on steel plates for ferrite super-thick structures at home and abroad, and partial patents are found through search, but the contents recorded by the steel plates are obviously different from the components, the production methods, the performances, the product types and the like in the technical scheme of the invention.
Related patent 1: chinese patent application number CN101613828A discloses a "super-thick steel plate with 460 MPa-grade yield strength and low yield ratio for building and manufacturing method", the steel plate comprises the following components in percentage by weight: 0.14 to 0.18 percent of C, 0.35 to 0.45 percent of Si, 1.40 to 1.50 percent of Mn, 0.025 to 0.035 percent of Nb, 0.040 to 0.050 percent of V, 0.010 to 0.020 percent of Ti, less than 0.020 percent of P, less than 0.008 percent of S and the balance of Fe; the rolling process comprises the following steps: the heating temperature is 1220-1250 ℃, and the two-stage controlled rolling is adopted in an austenite recrystallization region and an austenite non-recrystallization region. The heat treatment process comprises the following steps: heating the steel plate to 800-850 ℃ in a two-phase region, keeping the temperature for 10-20 ℃, adopting water cooling quenching after keeping the temperature, and controlling the final cooling temperature to be less than or equal to 100 ℃; and tempering the quenched steel plate at 450-600 ℃ to finally obtain the steel plate with low yield ratio and high strength for the building. The defects are that: the steel plate heat treatment adopts quenching and tempering, the process is more complex, and the production period is longer.
Related patent 2: chinese patent application number CN201210125992.1 discloses a "a large-thickness easy-welding quenched and tempered high-strength steel plate for hydropower and a production method thereof", discloses a large-thickness easy-welding quenched and tempered high-strength steel plate for hydropower, and simultaneously relates to a production method of the steel plate. The composite material consists of the following chemical components in percentage by weight: c:0.15 to 0.18 percent, si:0.15 to 0.35 percent, mn:0.90 to 1.00 percent, P is less than or equal to 0.012 percent, S is less than or equal to 0.005 percent, ni:1.52 to 1.60 percent, cr:0.30% -0.40%, nb:0.020 to 0.030 percent, al:0.020 to 0.050 percent, mo:0.20 to 0.30 percent, V:0.055% -0.065%, B:0.0007% -0.0015%, ti:0.015 to 0.025 percent, and the balance of Fe and unavoidable impurities. The production method comprises the following steps: electric furnace smelting, LF/VD refining, die casting, steel ingot heating, rolling, water cooling after rolling, hot stacking, heat treatment and finished product obtaining. The large-thickness easy-to-weld quenched and tempered high-strength steel plate for hydropower has the maximum thickness of 230mm, has the characteristics of good welding performance, low yield ratio, excellent low-temperature impact toughness and good thickness direction performance, and has wide application prospect. However, the component design thought and the production process of the invention are different from those of the invention, the manufacturing process is different, the application direction is different, and the high-temperature tensile property and the simulated post-weld heat treatment property of the steel plate are not clear.
Related patent 3: chinese patent application No. CN109797342a discloses a high strength, high toughness, atmospheric corrosion resistant steel sheet for steel structure fabrication and a method for manufacturing the same, the elemental components wt%: c:0.03 to 0.10 percent, si:0.30 to 0.50 percent, mn:1.10 to 1.50 percent, P is less than 0.010 percent, S is less than 0.003 percent, cr: 0.45-0.70%, cu:0.25 to 0.40 percent, ni:0.30 to 0.40 percent, alt: 0.030% or more, ti:0.006 to 0.030 percent, V: 0.040-0.080%, mo: 0.02-0.08%, ca:0.0010 to 0.0030 percent, N:0.0020 to 0.0080 percent, B:0.0002 to 0.0030 percent, ce: 0.001-0.010%, atmospheric corrosion resistance index I >6.5, CEV <0.54, pcm <0.27, and the balance of Fe and unavoidable impurities. The application adopts specific chemical composition design and a steel plate modulation process to obtain the high-performance steel plate with the bainite structure, and can be used for manufacturing steel structures such as bridges and high-rise buildings. However, the invention has the defects that the steel plate has no lower yield ratio and poor safety performance, rare elements such as Ca, B, ce and the like are added, smelting is difficult, and the production cost is increased; the carbon equivalent is too high and the welding performance is poor. And quenching and tempering are needed, and the process is complex.
Disclosure of Invention
The present invention has been made to overcome the above problems and disadvantages, and an object of the present invention is to provide a high-strength homogenized ferrite super-thick steel plate for wind power structure having excellent mechanical properties, structural uniformity and low-temperature toughness, and a method for manufacturing the same.
The invention aims at realizing the following steps:
a high-strength homogenized ferrite ultra-thick steel plate for a wind power structure comprises the following components in percentage by weight: c:0.10 to 0.22 percent, mn:0.05 to 1.88 percent, P is less than or equal to 0.022 percent, S is less than or equal to 0.010 percent, cr:0.01 to 0.60 percent of Ni:0.001% -0.009%, mo:0.001% -0.010%, cu:0.001% -0.009%, nb:0.010 to 0.020 percent, 0.001 to 0.027 percent of V, ti:0.001 to 0.028 percent, 0.02 to 0.05 percent of CaO, la:5ppm to 15ppm, B:0.0011 to 0.0029 percent, and the balance of Fe and unavoidable impurities.
The thickness of the steel plate for the wind power structure is 80-150mm, and the positions of 1/2T and 1/4T of the steel plate are fine polygonal ferrite and pearlite structures, and the grain size is more than or equal to 8.5 levels.
The yield strength of the steel plate for the wind power structure is more than or equal to 358MPa, the tensile strength is more than or equal to 532MPa, the temperature of minus 40 ℃, the KV2 is more than or equal to 94J, and the TNDT is more than or equal to minus 40 ℃.
The reason for designing the components of the invention is as follows:
(1) Carbon: the C can play a reinforcing role through solid solution to a great extent, can also form fine carbide precipitation through the action of the C and alloying elements such as Nb, V, ti and the like, and is precipitated before rolling deformation or austenite transformation, so that the growth of crystal grains is hindered, the nucleation rate is improved, and the structure is refined; however, the excessive C content can cause the steel plate to form obvious banded structure in the rolling process, and seriously affects the uniformity of the performance of the steel plate in all directions, so the invention C:0.10 to 0.22 percent.
(2) Manganese: the strength of the steel is improved through solid solution strengthening, the austenite transformation temperature is reduced, the growth of transformation grains of the steel plate before accelerated cooling is restrained, the grain refinement effect is exerted, and the strength of the steel plate is improved; however, too high Mn content tends to inhibit ferrite transformation, affect yield strength of steel, be unfavorable for lowering yield ratio, induce segregation, deteriorate structural uniformity and lamellar tearing performance of steel sheet, so that the Mn of the present invention: 0.05 to 1.88 percent.
(3) P, S: the steel of the invention is harmful element, which can have adverse effect on the low temperature impact toughness and lamellar tearing resistance of the steel plate, and increases the brittleness of the steel. Phosphorus reduces the welding performance, reduces the plasticity and deteriorates the cold bending performance; sulfur reduces the ductility and toughness of steel, causing cracking during forging and rolling. Therefore, the lower the control content, the better, but the invention requires controlling P.ltoreq.0.022% and S.ltoreq.0.010% in steel in view of steelmaking conditions and costs.
(4) Chromium: chromium is an element that stabilizes carbides. Chromium addition reduces the dissolution rate of carbides. Therefore, when the thermal deformation tissue refining process is adopted, eutectoid transformation can be avoided even if the heating temperature is increased or the heating time is prolonged, and the refined tissue can be obtained. Chromium also inhibits graphitization of the silicon-containing, aluminum ultra-high carbon steel. The present invention therefore requires Cr in the steel: 0.01 to 0.60 percent.
(5) Nickel: the better solid solution strengthening and hardenability enhancing elements in the steel can enlarge the austenite phase region, reduce the austenite transformation temperature, prevent the transformation from austenite to pearlite, and further reduce the critical transformation temperature of the steel; ni and Fe exist in a mutual-soluble form, so that the toughness of the steel plate can be effectively improved, the steel plate is particularly suitable for improving the core plastic toughness of an extra-thick plate, but the cost is higher, and therefore, the Ni in the invention: 0.001% -0.009%.
(6) Molybdenum: mo mainly relies on solid solution strengthening and grain boundary strengthening to improve the strength of steel; secondly, mo increases the stability of supercooled austenite, so that the austenite moves to the right of a ferrite transformation curve, and finer ferrite tissues are obtained after transformation; in addition, ti and Mo are combined, a large amount of nano-sized Ti-Mo (CN) carbide is precipitated in the steel, and the refined carbide pins dislocation, so that the toughness of the steel is greatly improved, and the Mo content in the steel is required to be controlled to be 0.001-0.010%.
(7) Copper: the quenching degree of the steel can be improved, the core strength of the thick steel plate can be obviously improved, the steel plate is also an important element for improving weather resistance, and during the slow cooling process of the thick steel plate, a proper amount of Cu can be separated out of epsilon-Cu through self tempering, so that the strength of the steel plate is improved. When the Cu content is too high, hot cracks are generated in the steel sheet, and the plasticity of the steel sheet is lowered. Thus in the present invention Cu:0.001% -0.009%.
(8) Niobium: nb can effectively refine the apparent structure by inhibiting austenite recrystallization in the quenching process, and meanwhile, partial Nb is dissolved into solid solution to play a role in solid solution strengthening, so that the toughness matching of different thickness positions of the steel plate is stabilized. Nb in the steel of the invention: 0.010 to 0.020 percent.
(9) Vanadium: v belongs to microalloy elements, and V microalloying in steel can form tiny second phase particles, so that the effects of pinning grain boundaries and precipitation strengthening are achieved, grains can be effectively refined, the toughness of the steel plate at different thickness positions is greatly improved, and particularly the steel plate T can be improved NDT Performance, therefore V in the present invention: 0.001 to 0.027 percent.
(10) Titanium: ti can exert nitrogen fixation effect, form a precipitated phase mainly containing TiN, inhibit the growth of austenite grains under high temperature conditions, improve toughness of a postweld heat affected zone, prevent the growth of grains of a heat affected coarse-grain zone in the welding process by TiN particles, and improve low-temperature toughness of a welded joint. In addition, ti is easy to appear in a form of phase separation in the transformation process from austenite to ferrite due to lower solid solubility, so that the strength is improved. However, too much Ti reduces the toughness of the steel, so that Ti in the present invention: 0.001 to 0.028 percent.
(11) Calcium oxide: the calcium oxide plays a role of nucleation point in steelmaking, is beneficial to refining grains, and can improve lamellar tearing resistance and fatigue strength. Therefore, the invention requires 0.01 to 0.035 percent of Ca.
(12) Lanthanum: purifying the steel and deteriorating impurities in the steel, thereby playing a role in improving the purity of the steel; the method has a certain hydrogen capturing capacity, reduces defects such as white spots in the ultra-thick plate and the like, and can improve the toughness of the steel plate; the precipitates forming a complex with Nb (C, N) can serve as nucleation bases and further play a role in fine-grain strengthening, so that the content of La is 1ppm to 15ppm in the invention.
(13) Boron: the hardenability of the steel plate can be improved, a trace of B element can obviously improve the hardenability effect, and the strength of the steel plate is ensured, but when the B element is excessive, the brittleness of the steel plate is increased, and the welding crack tendency is increased, so that the invention leads to the following steps: 0.0011 to 0.0029 percent.
The second technical scheme of the invention is to provide a manufacturing method of the steel plate for the high-strength homogenized ferrite ultra-thick wind power structure, which comprises smelting, continuous casting, assembling, rolling and quenching;
(1) Smelting: adding raw materials such as molten iron, scrap steel and the like into a converter or an electric furnace for smelting, adding calcium oxide, lanthanum and boron alloy when the temperature of refined molten steel reaches 1550-1570 ℃, carrying out vacuum degassing, and entering continuous casting after the degassing is finished.
(2) Continuous casting: the pouring temperature is 1530-1580 ℃, and the superheat degree of the tundish is 25-50 ℃. The whole process of protection pouring, secondary cooling adopts a medium cooling intensity mode, the continuous casting blank pulling speed is controlled to be 0.8-1.3 m/min, the thickness of the casting blank is 200-300 mm, and electromagnetic stirring or light pressing is adopted during continuous casting, so that center segregation is reduced.
(3) And (3) assembling: two or more continuous casting billets are overlapped together and then welded at the edge;
(4) Rolling: the billet heating temperature is 1100-1200 ℃, and rolling is carried out in three stages: the first stage is high temperature austenite dynamic recrystallization rolling, the initial rolling temperature is 1050-1190 ℃, the final rolling temperature is 950-1050 ℃, and the rolling times are 3-5 times; the second stage is austenite and ferrite two-phase region rolling, the initial rolling temperature is 920-980 ℃, the final rolling temperature is 920-970 ℃, and the number of rolling passes is 2-4; the third stage is to refine ferrite rolling, the initial rolling temperature is 920-970 ℃, the final rolling temperature is 900-950 ℃, the number of rolling passes is not limited, and the target thickness is obtained by rolling.
(5) Quenching temperature: cooling rate of 900-950℃: 18-32 ℃/s.
The invention has the beneficial effects that:
(1) The weight of the steel plate is 25-50 t, the weight of the steel plate is more than 25t, the steel plate is difficult to realize toughness matching under the normalizing and rolling and cooling control production process, and the comprehensive performance of the steel plate can not meet the technical requirements of the existing wind power steel plate. The invention can change the weak positions of the original single continuous casting blank in the thickness T/4 and T/2 by a composite blank mode, increase the thickness of the blank, increase the deformation in the thickness direction, increase the penetration in the thickness direction, reduce segregation, improve the uniformity of the steel plate, and improve the strength and toughness of the steel plate by quenching the large single steel plate.
(2) The steel plate produced by the process technology has a uniformly refined internal structure through chemical component optimization and reasonable design of process parameters, and the positions of 1/2T and 1/4T of the steel plate are fine polygonal ferrite and pearlite structures, and the grain size is more than or equal to 8.5 levels.
(3) The thickness of the steel plate is 80-150mm, the yield strength of the steel grade is more than or equal to 358MPa, the tensile strength is more than or equal to 532MPa, -40 ℃, KV2 is more than or equal to 94J, and TNDT is more than or equal to-40 ℃.
Drawings
FIG. 1 is a gold phase diagram of a microstructure at 1/4 of the thickness of a steel sheet according to example 1 of the present invention.
FIG. 2 is a gold phase diagram of the microstructure of the steel sheet of example 1 of the present invention at a thickness of 1/2.
Detailed Description
The invention is further illustrated by the following examples.
According to the component proportions of the technical scheme, smelting, continuous casting, rolling, continuous annealing and flattening are carried out. The composition of the steel of the example of the invention is shown in Table 1. The main technological parameters of the smelting and continuous casting of the steel of the embodiment of the invention are shown in Table 2. The main technological parameters of the rolling of the steel of the embodiment of the invention are shown in Table 3. The main technological parameters of the quenching of the steel of the embodiment of the invention are shown in Table 4. The properties of the inventive example steels are shown in Table 5.
TABLE 1 composition (wt%) of the inventive example steel
TABLE 2 main process parameters for smelting and continuous casting of the inventive example steel
TABLE 3 main process parameters for rolling the inventive example steel
TABLE 4 main process parameters for quenching the inventive example steels
| Examples | Quenching temperature, DEG C | Cooling rate, DEG C/s |
| 1 | 910 | 18 |
| 2 | 902 | 20 |
| 3 | 905 | 22 |
| 4 | 909 | 24 |
| 5 | 913 | 26 |
| 6 | 911 | 27 |
| 7 | 922 | 28 |
| 8 | 927 | 29 |
| 9 | 933 | 30 |
| 10 | 945 | 32 |
TABLE 5 Properties of the inventive example Steel
The example shows that the average mechanical properties of the steel plate are as follows: the room temperature tensile yield strength is more than or equal to 358MPa, the tensile strength is more than or equal to 532MPa, the elongation is more than or equal to 32%, the impact energy at minus 40 ℃ is more than or equal to 94J, the TNDT is more than or equal to minus 40 ℃, and the grain size is more than or equal to 8.5 levels.
The present invention has been properly and fully described in the foregoing embodiments by way of example only, and not by way of limitation, and various changes and modifications may be made by one skilled in the art without departing from the spirit and scope of the invention, any modification, equivalent substitution, improvement, etc. should be included in the scope of the invention, and the scope of the invention is defined by the claims.
Claims (6)
1. A high-strength homogenized ferrite steel plate for ultra-thick wind power structure is characterized in that: 0.10 to 0.22 percent, mn:0.05 to 1.88 percent, P is less than or equal to 0.022 percent, S is less than or equal to 0.010 percent, cr:0.01 to 0.60 percent of Ni:0.001% -0.009%, mo:0.001% -0.010%, cu:0.001% -0.009%, nb:0.010 to 0.020 percent, 0.001 to 0.027 percent of V, ti:0.001 to 0.028 percent, 0.02 to 0.05 percent of CaO, la:5ppm to 15ppm, B:0.0011 to 0.0029 percent, and the balance of Fe and unavoidable impurities.
2. The steel plate for the high-strength homogenized ferrite ultra-thick wind power structure according to claim 1, wherein the thickness of the steel plate for the wind power structure is 80-150mm, and the positions of 1/2T and 1/4T of the thickness of the steel plate are fine polygonal ferrite and pearlite structures, and the grain size is not less than 8.5 grade.
3. The steel sheet for a high-strength homogenized ferritic extra-thick wind power structure according to claim 1, wherein the steel sheet for a wind power structure has a yield strength of 358MPa or more, a tensile strength of 532MPa or more, and KV at-40 ℃ 2 ≥94J，TNDT≥-40℃。
4. A method for producing a high-strength homogenized ferritic extra-thick steel sheet for wind power construction according to any one of claims 1 to 3, comprising smelting, continuous casting, assembling, rolling, quenching; the method is characterized in that:
(3) And (3) assembling: two or more continuous casting billets are overlapped together and then welded at the edge;
(4) Rolling: the billet heating temperature is 1100-1200 ℃, and rolling is carried out in three stages: the first stage is high temperature austenite dynamic recrystallization rolling, the initial rolling temperature is 1050-1190 ℃, the final rolling temperature is 950-1050 ℃, and the rolling times are 3-5 times; the second stage is austenite and ferrite two-phase region rolling, the initial rolling temperature is 920-980 ℃, the final rolling temperature is 920-970 ℃, and the number of rolling passes is 2-4; the third stage is to refine ferrite rolling, the initial rolling temperature is 920-970 ℃, the final rolling temperature is 900-950 ℃, the number of rolling passes is not limited, and the target thickness is obtained by rolling;
(5) Quenching temperature: cooling rate of 900-950℃: 18-32 ℃/s.
5. The method for producing a steel sheet for a high-strength homogenized ferritic extra-thick wind power structure according to claim 4, characterized by:
smelting: adding raw materials such as molten iron, scrap steel and the like into a converter or an electric furnace for smelting, adding calcium oxide, lanthanum and boron alloy when the temperature of refined molten steel reaches 1550-1570 ℃, and carrying out vacuum degassing.
6. The method for producing a steel sheet for a high-strength homogenized ferritic extra-thick wind power structure according to claim 4, characterized by:
continuous casting: the pouring temperature is 1530-1580 ℃, the superheat degree of the tundish is 25-50 ℃, the whole-process protection pouring is performed, the secondary cooling adopts a medium cooling intensity mode, the continuous casting blank pulling speed is controlled to be 0.8-1.3 m/min, the thickness of the casting blank is 200-300 mm, and electromagnetic stirring is adopted during continuous casting: 430-520A, adopting light rolling reduction for continuous casting billets: 15-30 mm.
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