CN116536579A - High-toughness easy-to-weld wind power steel and preparation method thereof - Google Patents
High-toughness easy-to-weld wind power steel and preparation method thereof Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 92
- 239000010959 steel Substances 0.000 title claims abstract description 92
- 238000002360 preparation method Methods 0.000 title claims abstract description 10
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 16
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 11
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 11
- 239000000126 substance Substances 0.000 claims abstract description 9
- 229910052742 iron Inorganic materials 0.000 claims abstract description 7
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 238000005096 rolling process Methods 0.000 claims description 36
- 238000010438 heat treatment Methods 0.000 claims description 17
- 238000005242 forging Methods 0.000 claims description 13
- 238000010791 quenching Methods 0.000 claims description 10
- 230000000171 quenching effect Effects 0.000 claims description 10
- 238000000034 method Methods 0.000 claims description 9
- 238000010521 absorption reaction Methods 0.000 claims description 8
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 7
- 238000003723 Smelting Methods 0.000 claims description 6
- 238000001816 cooling Methods 0.000 claims description 6
- 238000004519 manufacturing process Methods 0.000 claims description 6
- 230000008569 process Effects 0.000 claims description 6
- 229910000859 α-Fe Inorganic materials 0.000 claims description 6
- 229910001563 bainite Inorganic materials 0.000 claims description 5
- 238000010079 rubber tapping Methods 0.000 claims 1
- 238000003466 welding Methods 0.000 abstract description 15
- 230000007547 defect Effects 0.000 abstract description 3
- 239000007769 metal material Substances 0.000 abstract description 2
- 229910001566 austenite Inorganic materials 0.000 description 6
- 230000000052 comparative effect Effects 0.000 description 6
- 239000000203 mixture Substances 0.000 description 5
- 238000005728 strengthening Methods 0.000 description 5
- UQSXHKLRYXJYBZ-UHFFFAOYSA-N Iron oxide Chemical compound [Fe]=O UQSXHKLRYXJYBZ-UHFFFAOYSA-N 0.000 description 4
- 229910045601 alloy Inorganic materials 0.000 description 4
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- 238000004088 simulation Methods 0.000 description 4
- 239000006104 solid solution Substances 0.000 description 4
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 3
- 238000007599 discharging Methods 0.000 description 3
- 238000001878 scanning electron micrograph Methods 0.000 description 3
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- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 230000008859 change Effects 0.000 description 1
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- 150000001875 compounds Chemical class 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
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- 238000007254 oxidation reaction Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 229910001562 pearlite Inorganic materials 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 238000005382 thermal cycling Methods 0.000 description 1
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- RMLPZKRPSQVRAB-UHFFFAOYSA-N tris(3-methylphenyl) phosphate Chemical compound CC1=CC=CC(OP(=O)(OC=2C=C(C)C=CC=2)OC=2C=C(C)C=CC=2)=C1 RMLPZKRPSQVRAB-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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
-
- 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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips 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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- 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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
-
- 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
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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
- 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
- C22C38/44—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
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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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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- 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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention provides high-toughness easy-to-weld wind power steel and a preparation method thereof, and belongs to the field of metal materials. The high-toughness easy-to-weld wind power steel comprises the following chemical components in percentage by mass: c: 0.02-0.04%, si:0.15 to 0.25 percent, mn:1.0 to 1.2 percent, mo:0.15 to 0.25 percent, cr:0.1 to 0.3 percent, nb:0.05 to 0.07 percent, ti:0.01 to 0.02 percent, ni:0.2 to 0.4 percent, alt: 0.02-0.04%, P <0.01%, S <0.006%, and the balance iron and unavoidable impurities, wherein the carbon equivalent CEV=C+Mn/6+ (Cr+Mo+V)/5+ (Ni+Cu)/15, 0.25< CEV is less than or equal to 0.38. On the basis of overcoming the defect of poor welding performance of the traditional steel for wind power, the steel provided by the invention has high toughness and easy welding performance by reducing the carbon equivalent on the premise of not affecting the mechanical performance, and meets the requirements of industrial application of the steel for wind power.
Description
Technical Field
The invention relates to the field of metal materials, in particular to high-toughness easy-to-weld wind power steel and a preparation method thereof.
Background
Wind energy is a renewable pollution-free green clean energy, the reserve is abundant, about 2% of solar energy on the earth is converted into wind energy, the wind energy is abundant in China, the world is first, the clean energy represented by wind power is huge in development space, and the development of the wind power industry is significant for the adjustment of the national energy structure.
In the prior art, wind power steel easy to weld is reported, and the wind power steel is searched:
the document of Chinese patent publication No. CN104862589A discloses a steel with excellent low-temperature welding performance for wind power towers and a production method thereof. The invention adopts the controlled rolling and cooling plus normalizing process to produce the steel plate with the yield strength of 355MPa, the tensile strength of 490-630 MPa, the elongation A of more than or equal to 30 percent, the carbon equivalent of less than 0.32, the KV2 of more than or equal to 260J at minus 50 ℃ and the KV2 of more than or equal to 220J at minus 60 ℃. The steel plate of the invention has low strength, higher carbon equivalent and still has insufficient excellent welding performance.
Disclosure of Invention
Aiming at the defects existing in the prior art, the invention provides high-toughness easy-to-weld wind power steel with yield strength more than or equal to 460MPa, tensile strength more than or equal to 550MPa, elongation A more than or equal to 20%, carbon equivalent of 0.25-0.38 and impact absorption energy higher than 100J at-40 ℃ under 40kJ/cm of heat input and a preparation method thereof.
Measures for achieving the above object:
the invention provides high-toughness easy-to-weld wind power steel, which comprises the following chemical components in percentage by mass: c: 0.02-0.04%, si:0.15 to 0.25 percent, mn:1.0 to 1.2 percent, mo:0.15 to 0.25 percent, cr:0.1 to 0.3 percent, nb:0.05 to 0.07 percent, ti:0.01 to 0.02 percent, ni:0.2 to 0.4 percent, alt: 0.02-0.04%, P <0.01%, S <0.006%, and the balance Fe and unavoidable impurities; the microstructure is mainly ferrite and bainite.
The carbon equivalent CEV=C+Mn/6+ (Cr+Mo+V)/5+ (Ni+Cu)/15 of the high-toughness easy-to-weld wind power steel is less than or equal to 0.380.25-0.38, and CEV is more than or equal to 0.25.
The invention provides a preparation method of high-toughness easy-to-weld wind power steel, which comprises the following steps:
(1) Smelting and forging;
(2) Heating;
(3) Rolling: rolling the heated blank;
(4) And (3) cooling: and (3) performing water quenching treatment on the rolled steel plate obtained in the step (3).
Preferably, the final forging temperature in step 1) is greater than 950 ℃.
Preferably, in the step 2), a resistance furnace is used for heating, and the iron scale is removed after discharging.
Preferably, the heating temperature in the step 2) is 1050-1200 ℃ and the heating time is 100-120min.
Preferably, in the step 3), the initial rolling temperature is 1000-1050 ℃, and the final rolling temperature is 750-850 ℃ after multi-pass rolling.
Preferably, the preparation method adopts a process of direct quenching after rolling to produce the high-toughness easy-to-weld wind power steel with room temperature structure mainly comprising ferrite and bainite.
(1) Smelting and forging: smelting in a vacuum induction furnace, precisely controlling alloy components in the process, strictly controlling the content of P, S elements, forging into square billets with the size of 60mm multiplied by 50mm in a laboratory, and the final forging temperature is higher than 950 ℃;
(2) Heating: heating by a KSL-1200X resistance furnace at 1050-1200deg.C for 100-120min, and removing iron oxide scale after discharging;
(3) Rolling: rolling the heated blank, wherein the initial rolling temperature is 1000-1050 ℃, and the final rolling temperature is 750-850 ℃ after multi-pass rolling;
(4) And (3) cooling: and (3) performing water quenching treatment on the rolled steel plate obtained in the step (3).
The function of each element in the invention:
c is the most effective element for improving the strength of the steel, and the tensile strength and the yield strength of the steel are improved along with the increase of the carbon content, but the elongation and the impact toughness are reduced, and the hardening phenomenon also occurs in a welding heat affected zone of the steel, so that welding cold cracks are generated. The content of C element is controlled to be 0.02-0.04%.
Si is an essential element for steelmaking deoxidization, improves the strength of steel in a solid solution strengthening form, has low strength performance when the Si content is less than 0.25%, and has reduced toughness when the Si content is more than 0.35%. The content of Si element in the invention is controlled to be 0.15-0.25%.
Mn is an important toughening element, the strength of the steel is obviously increased along with the increase of the Mn content, the processing performance of the steel is improved, the impact transition temperature is hardly changed, and the tensile strength is improved by 100MPa by containing 1% of Mn. The content of Mn element in the invention is controlled to be 1.0-1.2%.
Ti is an important microalloy element, a strong solid N element, and forms a tiny TiN precipitated phase stable at high temperature during slab continuous casting. The fine TiN particles can effectively prevent austenite grains from growing up, refine grains and improve the yield strength of the material when the slab is reheated, can also improve the solid solubility of Nb in austenite, and has obvious effect on improving the impact toughness of a heat affected zone. However, tiN is melted at high temperature under the condition of high heat input welding, and cannot effectively prevent the growth of high temperature austenite grains, and then cannot serve as a nucleation core for low temperature acicular ferrite. The Ti content in the invention is controlled to be 0.01-0.02%.
P, S is a harmful impurity element which is difficult to avoid in steel. The high P can cause segregation, influence the uniformity of steel structure, and reduce the plasticity of steel; s is prone to form sulfide inclusions which are detrimental to low temperature toughness and can cause anisotropy in properties, as well as severely affecting the strain aging of the steel. Therefore, the P, S content in the steel should be strictly limited.
Nb can delay austenite recrystallization, reduce phase transition temperature, has obvious grain refinement effect, and can improve low-temperature toughness. Nb obtains a desired strength by mechanisms such as solid solution strengthening, phase change strengthening, precipitation strengthening, and the like. The content of Nb in the invention is controlled to be 0.05-0.07%.
Alt is commonly used as a deoxidizer in steel. However, when the Alt content is less than 0.025%, deoxidation is insufficient, and when the Alt content is more than 0.045%, alumina inclusions increase to lower the cleanliness of the steel. The content of Alt element in the invention is controlled to be 0.02-0.04%.
Mo exists in solid solution and carbide of steel, has solid solution strengthening effect, and can improve hardenability of steel. Mo slows down the dissolution rate of C compounds in austenite, and has a strong inhibition effect on the transformation of steel from austenite to pearlite. The Mo content in the invention is controlled to be 0.15-0.25%.
Ni can toughen the matrix, especially improves the low-temperature toughness of steel, and the ductile-brittle transition temperature is obviously reduced and the low-temperature toughness is obviously improved along with the increase of the Ni content in the steel. The content of Ni element is controlled to be 0.2-0.4%.
Cr can improve the strength and hardness of steel, so that the steel has good corrosion resistance and oxidation resistance, and the hardenability of the steel is improved. The content of Cr element is controlled to be 0.1-0.3 percent in the invention.
The invention controls the carbon equivalent to 0.25-0.38, and aims to ensure that when a steel plate with the thickness of less than 20mm is welded, preheating is not needed under the zero-degree environment, and the low CEV makes the cold cracking tendency of the steel plate lower.
Compared with the prior art, the invention has the advantages that:
1) On the basis of overcoming the defect of poor welding performance of the traditional steel for wind power, the steel provided by the invention has high toughness and easy welding performance by reducing the carbon equivalent on the premise of not affecting the mechanical performance, and meets the requirements of industrial application of the steel for wind power.
2) The invention adopts the process of direct quenching after rolling to produce, obtains the high-toughness easy-to-weld wind power steel with room temperature structure mainly comprising ferrite and bainite, adopts TMCP state delivery, ensures that the yield strength of the produced steel plate is more than or equal to 460MPa, the tensile strength is more than or equal to 550MPa, the elongation is more than or equal to 20 percent, the impact absorption energy under 40kJ/cm heat input is more than or equal to 100J, the carbon equivalent is 0.25-0.38, and the steel plate has excellent welding performance in a low temperature state.
Drawings
FIG. 1 is a graph of weld thermal cycling in a weld thermal simulation experiment for examples and comparative examples;
FIG. 2 is an SEM image of the high-toughness easily-welded wind power steel corresponding to example 1;
FIG. 3 is an SEM image of the high toughness easy-to-weld wind power steel corresponding to example 2;
fig. 4 is an SEM image of the high-toughness easy-to-weld wind power steel according to example 3.
Detailed Description
The technical scheme of the invention is described in detail below with reference to the accompanying drawings and examples.
Regarding performance evaluation and organizational observation: a steel welding thermal simulation experiment for high-toughness easy-to-weld wind power is carried out on a Gleeble1500 model thermal simulation tester, and the sizes of samples are 10mm multiplied by 55mm. After the thermal simulation test, V-notch is formed along the welding spot position of the thermocouple wire to be used as an impact sample, and the Charpy V-notch low-temperature impact test is carried out at the temperature of minus 40 ℃. The heating rate of the simulated thermal cycle is 100 ℃/s, the preheating temperature is 20 ℃, and the heating peak temperature T is p The peak residence time was 1s at 1350 ℃. 6 different heat inputs were set, corresponding to cooling times t8/5 from 800 to 500℃as shown in Table 1.
The following examples are given to further illustrate the technical aspects of the present invention, but are not limited thereto.
The embodiment is a high-toughness easy-to-weld wind power steel, the thickness of a finished product is 12mm, and the mass percentages (wt.%) of chemical components and alloy elements are: c: 0.02-0.04%, si:0.15 to 0.25 percent, mn:1.0 to 1.2 percent, mo:0.15 to 0.25 percent, cr:0.1 to 0.3 percent, nb:0.05 to 0.07 percent, ti:0.01 to 0.02 percent, ni:0.2 to 0.4 percent, alt: 0.02-0.04%, P <0.01%, S <0.006%, and the balance Fe and unavoidable impurities. The specific chemical composition and the percentage (wt.%) of the alloy elements are shown in tables 2, 3 and 4.
The invention provides a preparation method of high-toughness easy-to-weld wind power steel, which comprises the following steps:
(1) Smelting and forging: smelting in a vacuum induction furnace, precisely controlling alloy components in the process, strictly controlling the content of P, S elements, forging into square billets with the size of 60mm multiplied by 50mm in a laboratory, and the final forging temperature is higher than 950 ℃;
(2) Heating: heating by a KSL-1200X resistance furnace at 1050-1200deg.C for 100-120min, and removing iron oxide scale after discharging;
(3) Rolling: rolling the heated blank, wherein the initial rolling temperature is 1000-1050 ℃, and the final rolling temperature is 750-850 ℃ after multi-pass rolling;
(4) And (3) cooling: and (3) performing water quenching treatment on the rolled steel plate obtained in the step (3).
Table 1 chemical composition (wt.%) of inventive example 1
Table 2 chemical composition (wt.%) of inventive example 2
Table 3 chemical composition (wt.%) of inventive example 3
Table 4 chemical composition (wt.%) of comparative example
Example 1
The embodiment adopts the component 1 to produce the high-toughness easy-welding wind power steel, the thickness of the finished product plate is 12mm, and the specific production process of the wind power steel is as follows: placing the forging stock in a heating furnace with the set temperature of 1150 ℃, preserving heat for 100min, taking out the heat-preserved steel billet to remove oxidized iron scales, rolling into a steel plate with the thickness of 12mm through multi-pass rolling, wherein the initial rolling temperature is 1050 ℃, the final rolling temperature is 800 ℃, and then directly quenching the steel plate with water to room temperature, so that the high-toughness easy-to-weld wind power steel can be obtained, and the impact absorption energy at the temperature of minus 40 ℃ under the heat input of 40kJ/cm is 127J.
Example 2
The embodiment adopts the component 2 to produce the high-toughness easy-welding wind power steel, the thickness of the finished product plate is 12mm, and the specific production process of the wind power steel is as follows: placing the forging stock in a heating furnace with the set temperature of 1200 ℃, preserving heat for 110min, taking out the heat-preserved steel billet to remove oxidized iron scales, rolling into a steel plate with the thickness of 12mm through multi-pass rolling, wherein the initial rolling temperature is 1100 ℃, the final rolling temperature is 820 ℃, and directly quenching the steel plate with water to room temperature to obtain the high-toughness easy-to-weld wind power steel with the impact absorption energy of 115J at the temperature of minus 40 ℃ under the heat input of 40 kJ/cm.
Example 3
The embodiment adopts the component 3 to produce the high-toughness easy-welding wind power steel, the thickness of the finished product plate is 12mm, and the specific production process of the wind power steel is as follows: placing the forging stock in a heating furnace with the set temperature of 1050 ℃, preserving heat for 100min, taking out the heat-preserved steel billet to remove oxidized iron scales, rolling into a steel plate with the thickness of 12mm through multi-pass rolling, wherein the initial rolling temperature is 1000 ℃, the final rolling temperature is 790 ℃, and then directly quenching the steel plate with water to room temperature, so that the high-toughness easy-to-weld wind power steel can be obtained, and the impact absorption energy at the temperature of minus 40 ℃ under the heat input of 40kJ/cm is 131J.
Table 6 shows the mechanical property data for the three examples.
| Examples reference numerals | YS/MPa | UTS/MPa | YS/UTS | EL/％ |
| Example 1 | 499 | 632 | 0.79 | 20.2 |
| Example 2 | 482 | 626 | 0.77 | 20.5 |
| Example 3 | 483 | 627 | 0.77 | 21.4 |
Table 7 shows impact absorption energy (J) at-40℃at different heat inputs for the examples and comparative examples.
| Heat input (kJ/cm) | 20 | 25 | 30 | 40 | 50 | 60 |
| Example 1 | 238 | 190 | 158 | 127 | 65 | 15 |
| Example 2 | 224 | 176 | 149 | 115 | 59 | 11 |
| Example 3 | 227 | 185 | 161 | 131 | 69 | 20 |
| Comparative example | 45 | 24 | 16 | 11 | 16 | 11 |
As can be seen from the data in Table 7, the high-toughness easy-to-weld wind power steel prepared by the invention has excellent post-weld performance compared with the comparative steel, and the impact absorption energy at-40 ℃ under 40kJ/cm heat input is more than 10 times that of the comparative steel.
Finally, it should be noted that the above embodiments are only for illustrating the technical solution of the present invention and are not limiting. Although the present invention has been described in detail with reference to the embodiments, it should be understood by those skilled in the art that modifications and equivalents may be made thereto without departing from the spirit and scope of the present invention, which is intended to be covered by the appended claims.
Claims (10)
1. The high-toughness easy-to-weld steel for wind power is characterized by comprising the following chemical components in percentage by mass: c: 0.02-0.04%, si:0.15 to 0.25 percent, mn:1.0 to 1.2 percent, mo:0.15 to 0.25 percent, cr:0.1 to 0.3 percent, nb:0.05 to 0.07 percent, ti:0.01 to 0.02 percent, ni:0.2 to 0.4 percent, alt: 0.02-0.04%, P <0.01%, S <0.006%, and the balance of iron and unavoidable impurities.
2. The high-toughness easy-to-weld wind power steel according to claim 1, wherein the high-toughness easy-to-weld wind power steel has a carbon equivalent cev=c+mn/6+ (cr+mo+v)/5+ (ni+cu)/15, 0.25< CEV no more than 0.380.25-0.38.
3. The high-toughness easy-to-weld wind power steel according to claim 1, wherein the yield strength of the high-toughness easy-to-weld wind power steel is not less than 460MPa, the tensile strength is not less than 550MPa, the elongation after break is not less than 20%, and the impact absorption energy at-40 ℃ under 40kJ/cm heat input is not less than 100J.
4. The high-toughness easy-to-weld wind power steel according to claim 1, wherein the high-toughness easy-to-weld wind power steel structure is composed mainly of ferrite and bainite.
5. A preparation method of high-toughness easy-to-weld wind power steel comprises the following steps:
(1) Smelting and forging;
(2) Heating;
(3) Rolling: rolling the heated blank;
(4) And (3) cooling: and (3) performing water quenching treatment on the rolled steel plate obtained in the step (3).
6. The method for producing high-toughness, easy-to-weld wind power steel according to claim 5, wherein the finish forging temperature in step 1) is greater than 950 ℃.
7. The method for preparing the high-toughness easy-to-weld wind power steel according to claim 5, wherein in the step 2), a resistance furnace is adopted for heating, and iron scales are removed after tapping.
8. The method for preparing the high-toughness easy-to-weld wind power steel according to claim 5, wherein the heating temperature in the step 2) is 1050-1200 ℃ and the heating time is 100-120min.
9. The method for producing high-toughness easily welded wind power steel according to claim 5, wherein the initial rolling temperature in step 3) is 1000 to 1050 ℃, the final rolling temperature is 750 to 850 ℃ after multi-pass rolling.
10. The method for preparing the high-toughness easy-to-weld wind power steel according to claim 5, wherein the preparation method adopts a process of direct quenching after rolling to produce the high-toughness easy-to-weld wind power steel with room temperature structure mainly comprising ferrite and bainite.
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