CN102605243A - Wind power H-beams and production method thereof - Google Patents
Wind power H-beams and production method thereof Download PDFInfo
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- CN102605243A CN102605243A CN2012100695139A CN201210069513A CN102605243A CN 102605243 A CN102605243 A CN 102605243A CN 2012100695139 A CN2012100695139 A CN 2012100695139A CN 201210069513 A CN201210069513 A CN 201210069513A CN 102605243 A CN102605243 A CN 102605243A
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- Treatment Of Steel In Its Molten State (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention provides wind power H-beams and a production method thereof. The production method includes: smelting molten steel to obtain target molten steel; subjecting the target molten steel to beam blank continuous casting under full protection; rolling beam blanks, ensuring reduction of finish rolling to be between a austenite field and a ferrite field, and performing strengthened air cooling to obtain the wind power H-beams, wherein the target molten steel comprises, by weight, 0.14-0.22% of C, 0.20-0.50% of Si, 1.20-1.50% of Mn, not more than 0.010% of S, not more than 0.020% of P, 0.010-0.050% of Nb, not more than 40X10-6 of N, not more than 10X10-6 of O, not more than 3X10-6 of H, the balance of Fe and unavoidable impurities. The wind power H-beams are fine in low temperature impact toughness and strength, fine in internal quality and lamellar tearing resistance, fine in surface quality and fine in corrosion resistance, and can meet the requirements of wind power generation on high performance steel.
Description
Technical field
The present invention relates to H shaped steel technical field, more particularly, relate to a kind of wind-powered electricity generation that possesses excellent comprehensive performance with H shaped steel and working method thereof.
Background technology
The coastal wind power plant low for envrionment temperature, that wind-force is big and corrodibility is strong, the steel that construction structure is used must possess low-temperature impact-resistant, HS, anti-lamellar tearing and solidity to corrosion preferably.
Flourish along with the new forms of energy industry can welcome increasing coastal wind-powered electricity generation project construction, and the demand that this can greatly stimulate the wind energy turbine set structural steel especially possesses the steel of excellent comprehensive performance.
The one Chinese patent application that disclosed application number was CN101736207A on June 16th, 2010 discloses a kind of niobium and vanadium-containing economical high-strength and high-weather-resistance hot rolled H shaped steel and has used steel.Yet this application has adopted V-Nb-Cu-Cr-Ni compound mode at the composition design aspect of steel, though obtained higher tough combination and good weather resistance, cost of alloy is too high, and the production difficulty is big.
The one Chinese patent application that disclosed application number was CN102021475A on April 20th, 2011 discloses a kind of low temperature resistant structure with hot rolled H-shaped and preparation method thereof.In this application, the design of the composition of steel is not carried out strictness control to nitrogen, oxygen, the hydrogen of refining link.And separating out of nitrogen, hydrogen makes and in the casting for shaped blank continuous process, is easy to occur strand subsurface bubble, pin hole, and in the operation of rolling, elongate, expansion, cause the finished product crack defect to occur.This application has adopted fast cold measure between finish to gauge is to 500-600 ℃ in process of cooling, this process possibly brought very big unrelieved stress on the occasion of the most violent stage of phase transformation, and is unfavorable for the physical dimension and the toughness of product.
Summary of the invention
To the deficiency that prior art exists, one of the object of the invention is to provide a kind of and is used to make economical low-carbon microalloy, high-strength, H.T., is applicable to the method for the abominable wind-powered electricity generation of service condition with H shaped steel of building.Another object of the present invention is to provide a kind of economical low-carbon microalloy, high-strength, H.T., be applicable to that building the abominable wind-powered electricity generation of service condition uses H shaped steel.
One side of the present invention provides a kind of wind-powered electricity generation to use the H shape steel producing method.Said working method may further comprise the steps: smelting molten steel to be obtaining the target molten steel, the composition of said target molten steel by 0.14～0.22% C by weight, 0.20～0.50% Si, 1.20～1.50% Mn, be no more than 0.010% S, be no more than 0.020% P, 0.010～0.050% Nb, be no more than 40 * 10
-6N, be no more than 10 * 10
-6O, be no more than 3 * 10
-6H, and surplus Fe and unavoidable impurities are formed; Said target molten steel is carried out casting for shaped blank continuous, adopt the full guard casting during continuous casting; Rolling special-shaped base, and guarantee that depressing of finish to gauge is in austenite and the ferritic two-phase region, strengthen air cooling then, use H shaped steel to make wind-powered electricity generation.
In the embodiment of wind-powered electricity generation according to the present invention with the H shape steel producing method; When the full guard cast in the said continuous casting step is included in casting ladle nozzle and submerged nozzle are sealed; Adopt alkaline covering agent to cover the tundish liquid level, and adopt crystallizer protecting residue to cover mold liquid level.
In the embodiment of wind-powered electricity generation according to the present invention with the H shape steel producing method, said rolling step comprises roughing and finish rolling, and wherein, the start rolling temperature of roughing is 1150～1200, and the temperature that roughing finishes is 1040～1100; The start rolling temperature of finish rolling is 980～1010, and the finish to gauge end temp is 820～840.
In the embodiment of wind-powered electricity generation according to the present invention with the H shape steel producing method, the rate of cooling of said reinforcement air cooling is 4-6 /s.
In the embodiment of wind-powered electricity generation according to the present invention with the H shape steel producing method; C content in the said target molten steel is 0.14～0.18%; Si content is 0.20～0.30%, and Mn content is 1.20～1.40%, and S content is 0.001～0.008%; P content is 0.001～0.020%, and Nb content is 0.025～0.035%.
In the embodiment of wind-powered electricity generation according to the present invention with the H shape steel producing method, the carbon equivalent ce V=C+Mn/6+ (Cr+Mo+V) of said target molten steel/5+ (Cu+Ni)/15≤0.43, and manganese sulphur ratio is not less than 20.
Another aspect of the present invention provides a kind of wind-powered electricity generation to use H shaped steel.Said wind-powered electricity generation adopts aforesaid method to make with H shaped steel.
In the embodiment of wind-powered electricity generation according to the present invention with H shaped steel, said wind-powered electricity generation with the composition of H shaped steel by 0.14～0.22% C by weight, 0.20～0.50% Si, 1.20～1.50% Mn, be no more than 0.010% S, be no more than 0.020% P, 0.010～0.050% Nb, be no more than 40 * 10
-6N, be no more than 10 * 10
-6O, be no more than 3 * 10
-6H, and surplus Fe and unavoidable impurities are formed.
Compared with prior art, wind-powered electricity generation of the present invention has the following advantages with H type and working method thereof: (1) provides a kind of accurate composition scope of design of H shaped steel of excellent comprehensive performance, and simplicity of design is not added noble metal, and is with low cost; (2) adopt hot mechanical controlled rolling technology to produce, obtained normal heat and handled the desirable weave construction that all is beyond one's reach, significantly optimized steel performance; (3) wind-powered electricity generation of the present invention possesses excellent tough coupling with H shaped steel, excellent interior tissue and surface quality and good anti-lamellar tearing and the corrosion resisting property therefore brought.
Description of drawings
The metallographic structure photo of Fig. 1 H shaped steel that to be wind-powered electricity generation according to the present invention obtain with the example 1 of H shape steel producing method.
Embodiment
Hereinafter, will specify exemplary embodiment of the present invention with reference to accompanying drawing.
Wind-powered electricity generation according to the present invention may further comprise the steps with the H shape steel producing method: smelting molten steel to be obtaining the target molten steel, the composition of said target molten steel by 0.14～0.22% C by weight, 0.20～0.50% Si, 1.20～1.50% Mn, be no more than 0.010% S, be no more than 0.020% P, 0.010～0.050% Nb, be no more than 40 * 10
-6N, be no more than 10 * 10
-6O, be no more than 3 * 10
-6H, and surplus Fe and unavoidable impurities are formed; Said target molten steel is carried out casting for shaped blank continuous, adopt the full guard casting during continuous casting; Rolling special-shaped base, and guarantee that finish to gauge depress (or title distortion) is in austenite and the ferritic two-phase region, strengthen air cooling then, use H shaped steel to make wind-powered electricity generation.In the present invention, as do not have opposite explanation, the content of each composition is all represented with weight percent.
Wind-powered electricity generation according to the present invention comprises 0.14～0.22% C, 0.20～0.50% Si, 1.20～1.50% Mn by weight, is no more than 0.010% S, is no more than 0.020% P, 0.010～0.050% Nb, is no more than 40 * 10 with H shaped steel
-6N, be no more than 10 * 10
-6O, be no more than 3 * 10
-6H, all the other are Fe and unavoidable impurities.Preferably, wind-powered electricity generation of the present invention with H shaped steel by 0.14～0.18% C by weight, 0.20～0.30% Si, 1.20～1.40% Mn, be no more than 0.001～0.008% S, be no more than 0.001～0.020% P, 0.025～0.035% Nb, be no more than 40 * 10
-6N, be no more than 10 * 10
-6O, be no more than 3 * 10
-6The Fe and the unavoidable impurities of H and surplus form.Preferably, wind-powered electricity generation of the present invention with H shaped steel in, carbon equivalent ce V=C+Mn/6+ (Cr+Mo+V)/5+ (Cu+Ni)/15≤0.43, and manganese sulphur ratio is not less than 20.
Below describe the effect of each element in the steel of the present invention or the reason of disadvantageous effect and selected limit in detail.
C is a topmost gap solid solution element in the soft steel; Its lattice distortion that causes is very strong; Be most economical strengthening element, still along with the increase of its content, the plasticity of steel, toughness descend; Welding property also worsens simultaneously, is controlled at 0.14～0.22% so take all factors into consideration its suitable content.
Si is the displacement solid solution element in the steel, is insoluble to cementite, only is present in the ferritic, can play the effect of solution strengthening, but its can significantly worsen plasticity, improves ductile-brittle transition temperature, therefore, the content of Si is controlled at 0.20～0.50%.
Mn is the austenite stable element, and its existence can be stablized the supercooled austenite, makes Ar
3Temperature reduces, thereby austenite-perlitic transformation temperature is reduced, and thinning microstructure improves intensity and hardness.Simultaneously, the manganese in the steel is easier to combine with S than Fe, avoids producing lower melting point FeS, avoids producing hot-short, and the MnS of generation has good high-temp plastic, can be with rolling homogeneous deformation.In the soft steel scope, the increase of manganese content significantly reduces the toughness of steel, and can influence carbon equivalent, worsens welding property, takes all factors into consideration, and manganese content is fixed on 1.20～1.50%.
S is the most serious element of segregation in the steel, and there is the interior tissue that has not only worsened steel in it, can form lower melting point FeS simultaneously; Produce hot-short; And combine the MnS that produces with manganese can be to produce Z to the main reason of tearing, so S content should reduce as far as possible with rolling homogeneous deformation; But consider desulphurization cost, it is controlled at below 0.010% gets final product.
P is the element that segregation is only second to S in the steel; Be to improve other important element of banded structure level; Gather partially in a large number on crystal boundary, significantly improve the low temperature brittleness of steel, form amorphous layer except that assembling and improve the steel corrosion resisting property at steel surface; P content has no positive influence, so should be controlled at below 0.020%.
Nb is the thin brilliant element of effect intensive in the steel, also can play stronger precipitation strength effect in the process of separating out rolling inducing simultaneously.Elements such as Nb and C, N are combined in austenite grain boundary and form the anchoring effect, stop austenitic grain growth, thereby play the effect of grain refining.In addition, Nb can also improve the Ar3 temperature, makes the rolling more or less freely realization that becomes in two-phase region.Strengthening effect no longer significantly increased after Nb content surpassed 0.050%, and was easy to form the low melting point eutectic thing with Fe, C etc., increased hot-short risk, therefore Nb content was controlled at 0.010～0.050%.
Below, with describing the exemplary embodiment of wind-powered electricity generation according to the present invention with the H shape steel producing method.
In this exemplary embodiment; Can realize working method of the present invention through the technologies such as hot metal pretreatment, top and bottom combined blown converter smelting, LF refining, casting for shaped blank continuous, two-phase region controlled rolling and reinforcement air cooling of carrying out successively, use H shaped steel to obtain wind-powered electricity generation according to the present invention.Particularly, the wind-powered electricity generation according to this exemplary embodiment can may further comprise the steps with the H shape steel producing method:
(1) hot metal pretreatment
Carry out hot metal pretreatment to remove silicon and the sulphur in the molten iron, make molten iron silicon content be controlled at 0.4～0.5%, sulphur content is controlled at 0.001～0.020%, and molten iron temperature 1250～1300 scratch clean the surperficial slag of molten iron after pre-treatment finishes.
(2) top and bottom combined blown converter smelting
The process of carrying out top and bottom combined blown converter smelting mainly comprises: with adding in the converter in steel scrap behind the pretreated molten iron; The Intake Quantity error adopts height to draw the method for once re-blowing at ± 0.5 ton, and slag charge must add in terminal point in preceding 3 minutes; Finishing slag basicity is controlled in 3.0～3.2 scopes; Terminal point presses the rifle time to be not less than 1 minute, adopts the deoxidation of silico-calcium barium, silico-calcium barium add-on 2.0～2.5kg/t
SteelAdd 6～10kg/t along steel stream during tapping
SteelSynthetic slag begins to be added at 3/4 o'clock and adds when putting steel 1/2; Begin evenly to add silicomanganese, Gao Meng, ferro-niobium during tapping to 1/4 and carry out deoxidation alloying, added to 3/4 o'clock.Synthetic slag is desulfurization, the dephosphorization slag charge that contains CaO 85～95%, and silicomanganese is an alloy siliceous 17%, that contain manganese 65%, and add-on is the 7.5kg/t steel, and high manganese is the iron alloy that contains manganese 68%, and add-on is 9.4kg/t
Steel, ferrocolumbium is the iron alloy that contains niobium 64%, add-on is 0.55kg/t
Steel
(3) LF refining
The LF refining adopts omnidistance BOTTOM ARGON BLOWING to stir, and soft blow guarantees more than 12 minutes before the departures, adopts lime, calcium carbide slag making, and silit, barium are deoxidation, and departures sinciput slag is white slag or yellowish-white slag, finishing slag basicity 3.0～3.5.In addition, in the LF refining process, those of ordinary skills can be according to practical situation with 0.83～1.25kg/t
SteelAmount in molten steel, add the calcium iron wire.
Through above step (1) to (3), can obtain composition by 0.14～0.22% C by weight, 0.20～0.50% Si, 1.20～1.50% Mn, be no more than 0.010% S, be no more than 0.020% P, 0.010～0.050% Nb, be no more than 40 * 10
-6N, be no more than 10 * 10
-6O, be no more than 3 * 10
-6H, and the molten steel formed of surplus Fe and unavoidable impurities.Yet, the invention is not restricted to this, it will be understood by those skilled in the art that the molten steel that can also obtain meeting the mentioned component scope through alternate manner.For example, can obtain meeting the molten steel of above-mentioned composition requirement through electrosmelting and secondary refining bonded step.In addition; Preferably, be used to produce wind-powered electricity generation of the present invention with the molten steel of H shaped steel by 0.14～0.18% C by weight, 0.20～0.30% Si, 1.20～1.40% Mn, be no more than 0.001～0.008% S, be no more than 0.001～0.020% P, 0.025～0.035% Nb, be no more than 40 * 10
-6N, be no more than 10 * 10
-6O, be no more than 3 * 10
-6The Fe and the unavoidable impurities of H and surplus form; To be used for molten steel of the present invention and be defined as this preferred composition, and can accurately control each constituent content of steel, improve the yield rate of steel.
(4) casting for shaped blank continuous
In the casting for shaped blank continuous step, adopt the full guard casting, big water-coating port, submerged nozzle good seal, tundish adopts alkaline covering agent, and covering is good, adopts crystallizer protecting residue to cover the molten steel face of mold.Alkaline covering agent can be used alkaline covering agent for H shaped steel continuous casting commonly used, for example, can use composition to comprise the SiO of 2.9-3.1%
2, the CaO of 40-42%, the MgO of 6-6.1%, the Al of 28-29%
2O
3, about 1% Fe
2O
3Alkaline covering agent.The composition of crystallizer protecting residue is 34～38% SiO
2, 37～38% CaO, 9～10% Al
2O
3, 8～10% C and trace BaS, MgO, Fe
2O
3, MnO, Na
2O, K
2O and F, viscosity 8.8～9.3Pa.s, fusing point 1235～1255, basicity 1.29～1.35.In addition, casting speed can be 0.85～0.95m/min, and steel billet heat is sent.In working method of the present invention, the separating out of nitrogen, hydrogen make and in the casting for shaped blank continuous process, be easy to occur strand subsurface bubble, pin hole, and in the operation of rolling, elongate, expansion, cause the finished product crack defect to occur; Control of Oxygen Content then can significantly reduce inclusion content of steel, improves purity, for improving the steel substrate continuity; Avoiding occurring the flaw detection defective has significant role, and simultaneously, low oxygen level can change the form of manganese sulfide; Make manganese sulfide under lower temperature, to separate out; Thereby obtain more tiny particle, in follow-up rolling elongation process, can not form thick and long sulfide like this, improved Z to performance.Therefore, in the method for the invention, must so that being controlled at, the nitrogen element in the steel be no more than 40 * 10 to carrying out the full guard cast in the casting for shaped blank continuous process
-6, oxygen element is controlled at and is no more than 10 * 10
-6And protium is controlled at and is no more than 3 * 10
-6
(5) two-phase region controlled rolling
In rolling step; The temperature of controlled rolling is following: the temperature that steel billet goes out process furnace is 1200～1260; The start rolling temperature of steel billet roughing is 1150～1200, and the temperature that roughing finishes is 1040～1100, and the start rolling temperature of finish rolling is 980～1010; The finish to gauge end temp is 820～840, and guarantees that depressing of finish to gauge is in austenite and the ferritic two-phase region.In the operation of rolling of working method of the present invention, the single pass draft can be controlled between 15～20% according to the specification difference of steel product.In addition, also can rolled blank a time before finish to gauge be treated warm 60s,, depressing of finish to gauge is in austenite and the ferritic two-phase region with the finishing temperature of accurate controlled rolling base according to process condition.In the finish to gauge process of finish rolling, if the finish to gauge end temp is higher than the said temperature interval, austenite crystal is grown up once more fast, thereby occur the austenite crystal grow up unusually probably, the havoc product performance.In addition, in working method of the present invention, the temperature of each passage, especially finish to gauge is controlled lowlyer and accurate, and this is just for having rolled out performance better, more stable product provides guarantee.
(6) strengthen air cooling
In cooling step, will pass through Rolled Steel and be cooled to below the temperature that its crystalline structure do not change (for example, 150) through strengthening air cooling, form tiny crystal grain and good internal microstructure further to make steel.The rate of cooling of strengthening air cooling can be 4-6 /s.Specifically, in working method of the present invention, the air-cooled measure of the reinforcement that can take; Promptly on cold bed, adopt blower fan to strengthen cooling; Further crystal grain thinning is unlikely to again to produce big internal stress simultaneously, avoids causing product design warpage, lateral bending; And air-cooled more even than water-cooled, can avoid product different zones performance than great fluctuation process.In addition, what pay particular attention to is, in process of cooling; Can not only be cooled between 500～600 passing through Rolled Steel, because this temperature range is on the occasion of the most violent stage of steel phase transformation; Possibly bring very big unrelieved stress, unfavorable for the physical dimension and the toughness of product.
Wind-powered electricity generation of the present invention is following with each item performance of H shaped steel: lower yield strength is not less than 400MPa; Tensile strength is not less than 500MPa, and elongation after fracture is not less than 24%, and-20 impact of collision merits (AKv) are not less than 180J; Z is not less than 25% to relative reduction in area; The ultrasonic inspection rank is not less than 2.4 grades of European standards (being called for short Europe superscript), and the surface quality rank is not less than Europe superscript ClassC Sub class3.That is, wind-powered electricity generation of the present invention has good low-temperature impact toughness with H shaped steel and intensity cooperates, possesses good internal soundness and anti-lamellar tearing performance, favorable surface quality and good corrosion resisting property, can satisfy the requirement of wind-power electricity generation to the high-performance steel.
Here, Z is meant the relative reduction in area of thickness of steel product direction to relative reduction in area, promptly describes the index of anti-lamellar tearing performance, and this value is big more, explains that thickness of steel product direction plasticity, toughness are good more, and difficult more quilt is torn under stress.Z is at two auxiliary steel of thickness of steel product direction both sides butt welding to the testing method of relative reduction in area; In welding process, avoid destroying the original structure of steel to be checked; And carry out tension test on request; The relative reduction in area that obtains these steel is anti-lamellar tearing performance, and the content of this performance and manganese sulfide and finish to gauge attitude have direct relation.2.4 grades of other flaw detections of Europe superscript require: after detecting through whole edges of a wing, web to H shaped steel; For the defective that detects (comprise disappearance and be mingled with), for dimension width more than 8mm, length counting more than 15mm; For the zone of surveying; The local every square meter of the defective of size must not surpass 10 like this, totally then must not surpass 5, then can't stand fully in the situation more than 500 square millimeters for defect area occurring; The defect size of being considered will be got the union consideration, promptly needs only width and all will count greater than 15mm greater than 8mm or length.The surface quality of Europe superscript ClassC Sub class3 requires: according to the specification of product; Stipulated the degree of depth restriction of different thickness (comprising the edge of a wing and web) condition lower surface defective; And if such defective should repair and how to repair according to which kind of method; H shaped steel that for example will production edge of a wing thickness 24mm, the full depth of its surface imperfection must not surpass 1.7mm so, promptly can not carry out repair by welding if surpass this value according to above-mentioned ClassC Sub class3 requirement.
Below in conjunction with concrete example wind-powered electricity generation according to the present invention is described further with H shaped steel and working method thereof, but wind-powered electricity generation of the present invention is not limited thereto with H shaped steel and working method thereof.
Example 1
In this example, wind-powered electricity generation with H shaped steel through hot metal pretreatment, top and bottom combined blown converter smelting, LF refining, BB1 casting for shaped blank continuous, two-phase region controlled rolling with roll the back and strengthen air cooling and produce.Details are as follows.
The strict technological process of carrying out of desulfurizing iron desiliconization, sulphur is controlled at 0.013%, and silicon is controlled at 0.46%, and temperature is controlled at 1280.Add converter in 8 tons of high-quality steel scraps behind the molten iron, the slag making material added in terminal point in preceding 3 minutes, finishing slag basicity 3.2, and oxygen supply time 16 minutes and 40 seconds, terminal point was pressed rifle 70 seconds, 4 minutes and 24 seconds tapping time.Adopt the silicomanganese deoxidation earlier, add-on is 7.5kg/t
Steel, adding the deoxidation of silico-calcium barium again, add-on is 2.2kg/t
Steel, adding with steel stream, tapping 1/2 beginning adds to 3/4.Begin to add Gao Meng, ferro-niobium, carbon dust during tapping to 1/4 in batches, add to 3/4.Molten steel through converter smelting gets into the LF refining furnace, and adding lime, fluorite carry out slag making, cause the white slag or the yellowish-white slag of good fluidity, adopts omnidistance BOTTOM ARGON BLOWING to stir, 12 minutes soft blow time, and finishing slag basicity 3.2, calcium iron wire add-on is the 1.20kg/t steel.Through after the said process, the molten steel composition that obtains is by weight by 0.17% C, 0.30% Si, 1.32% Mn, 0.009% S, 0.014% P, 0.031% Nb, 32 * 10
-6N, 8 * 10
-6O, 2.3 * 10
-6The Fe and the unavoidable impurities of H and surplus form.
Then, the molten steel of above-mentioned composition is carried out the full guard casting for shaped blank continuous, tundish covering flux uses H shaped steel continuous casting commonly used to use alkaline covering agent; Adopt crystallizer protecting residue to cover mold liquid level; Cold pattern a little less than the two cold employings, stationary phase, pulling rate was 0.88m/min, casting blank specification is BB1.In this example, the composition of crystallizer protecting residue is 35% SiO
2, 37% CaO, 10% Al
2O
3, 10% C and BaS, MgO, the Fe of surplus
2O
3, MnO, Na
2O, K
2O and F, viscosity 9.0Pa.s, fusing point 1250, basicity 1.33.
The strand direct heat that continuous casting comes out is fed into process furnace; The steel billet tapping temperature is 1250, roughing start rolling temperature 1155, finish to gauge end temp 1060; The finish rolling start rolling temperature is 1000; The finish to gauge end temp is 830, and a time is treated warm 60s before the finish to gauge, guarantees that depressing of finish to gauge is in the two-phase region.Roll the back steel and strengthen air cooling, speed of cooling is 4-6 /s.
The wind-powered electricity generation that this example is obtained detects with H shaped steel; It is following to obtain this H shaped steel performance: lower yield strength is 412MPa, and tensile strength is 528MPa, and elongation after fracture is 26%;-20 impact of collision merits (AKv) are 210J; Z is 30% to relative reduction in area, and ultrasonic inspection is superior to 2.4 grades of Europe superscripts, and surface quality is superior to Europe superscript ClassC Sub class3.
Example 2
In this example, wind-powered electricity generation with H shaped steel through hot metal pretreatment, top and bottom combined blown converter smelting, LF refining, BB1 casting for shaped blank continuous, two-phase region controlled rolling with roll the back and strengthen air cooling and produce.Details are as follows.
The strict technological process of carrying out of desulfurizing iron desiliconization, sulphur is controlled at 0.017%, and silicon is controlled at 0.44%, and temperature is controlled at 1280.Add converter in 8.9 tons of high-quality steel scraps behind the molten iron, the slag making material added in terminal point in preceding 3 minutes, finishing slag basicity 3.2, and oxygen supply time 16 minutes and 41 seconds, terminal point was pressed rifle 72 seconds, 4 minutes and 20 seconds tapping time.Adopt the silicomanganese deoxidation earlier, add-on is 7.6kg/t
Steel, adding the deoxidation of silico-calcium barium again, add-on is 2.2kg/t
Steel, adding with steel stream, tapping 1/2 beginning adds to 3/4.Begin to add Gao Meng, ferro-niobium, carbon dust during tapping to 1/4 in batches, add to 3/4.Molten steel through converter smelting gets into the LF refining furnace, and adding lime, fluorite carry out slag making, cause the white slag or the yellowish-white slag of good fluidity, adopts omnidistance BOTTOM ARGON BLOWING to stir, 12 minutes soft blow time, and finishing slag basicity 3.2, calcium iron wire add-on is the 1.20kg/t steel.Through after the said process, the molten steel composition that obtains is by weight by 0.16% C, 0.29% Si, 1.29% Mn, 0.008% S, 0.016% P, 0.030% Nb, 37 * 10
-6N, be no more than 7 * 10
-6O, 1.9 * 10
-6The Fe and the unavoidable impurities of H and surplus form.
Then, the molten steel of above-mentioned composition is carried out the full guard casting for shaped blank continuous, the H shaped steel continuous casting that tundish covering flux is commonly used is used alkaline covering agent; Adopt crystallizer protecting residue to cover mold liquid level; Cold pattern a little less than the two cold employings, stationary phase, pulling rate was 0.90m/min, casting blank specification is BB1.In this example, the composition of crystallizer protecting residue is 34% SiO
2, 38% CaO, 13% Al
2O
3, 11% C and BaS, MgO, the Fe of surplus
2O
3, MnO, Na
2O, K
2O and F, viscosity 9.2Pa.s, fusing point 1236, basicity 1.27.
The strand direct heat that continuous casting comes out is fed into process furnace; The steel billet tapping temperature is 1250, roughing start rolling temperature 1160, finish to gauge end temp 1060; The finish rolling start rolling temperature is 1005; The finish to gauge end temp is 835, and a time is treated warm 60s before the finish to gauge, guarantees that depressing of finish to gauge is in the two-phase region.Roll the back steel and strengthen air cooling, speed of cooling is 4-6 /s.
The wind-powered electricity generation that this example is obtained detects with H shaped steel; It is following to obtain this H shaped steel performance: lower yield strength is 421MPa, and tensile strength is 530MPa, and elongation after fracture is 26%;-20 impact of collision merits (AKv) are 198J; Z is 30% to relative reduction in area, and ultrasonic inspection is superior to 2.4 grades of Europe superscripts, and surface quality is superior to Europe superscript ClassC Sub class3.
Example 3
In this example, wind-powered electricity generation with H shaped steel through hot metal pretreatment, top and bottom combined blown converter smelting, LF refining, BB1 casting for shaped blank continuous, two-phase region controlled rolling with roll the back and strengthen air cooling and produce.Details are as follows.
The strict technological process of carrying out of desulfurizing iron desiliconization, sulphur is controlled at 0.016%, and silicon is controlled at 0.45%, and temperature is controlled at 1270.Add converter in 8.3 tons of high-quality steel scraps behind the molten iron, the slag making material added in terminal point in preceding 3 minutes, finishing slag basicity 3.2, and oxygen supply time 16 minutes and 21 seconds, terminal point was pressed rifle 69 seconds, 4 minutes and 45 seconds tapping time.Adopt the silicomanganese deoxidation earlier, add-on is 7.7kg/t
Steel, adding the deoxidation of silico-calcium barium again, add-on is 2.2kg/t
Steel, adding with steel stream, tapping 1/2 beginning adds to 3/4.Begin to add Gao Meng, ferro-niobium, carbon dust during tapping to 1/4 in batches, add to 3/4.Molten steel through converter smelting gets into the LF refining furnace, and adding lime, fluorite carry out slag making, cause the white slag or the yellowish-white slag of good fluidity, adopts omnidistance BOTTOM ARGON BLOWING to stir, 12 minutes soft blow time, and finishing slag basicity 3.2, calcium iron wire add-on is 1.20kg/t
SteelThrough after the said process, the molten steel composition that obtains is by weight by 0.16% C, 0.34% Si, 1.33% Mn, 0.007% S, 0.015% P, 0.027% Nb, 35 * 10
-6N, 4 * 10
-6O, 2.7 * 10
-6The Fe and the unavoidable impurities of H and surplus form.
Then, the molten steel of above-mentioned composition is carried out the full guard casting for shaped blank continuous, the H shaped steel continuous casting that tundish covering flux is commonly used is used alkaline covering agent; Adopt crystallizer protecting residue to cover mold liquid level; Cold pattern a little less than the two cold employings, stationary phase, pulling rate was 0.87m/min, casting blank specification is BB1.In this example, the composition of crystallizer protecting residue is 37% SiO
2, 35% CaO, 10% Al
2O
3, 11% C and BaS, MgO, the Fe of surplus
2O
3, MnO, Na
2O, K
2O and F, viscosity 9.0Pa.s, fusing point 1250, basicity 1.30.
The strand direct heat that continuous casting comes out is fed into process furnace; The steel billet tapping temperature is 1250, roughing start rolling temperature 1165, finish to gauge end temp 1060; The finish rolling start rolling temperature is 1000; The finish to gauge end temp is 825, and a time is treated warm 60s before the finish to gauge, guarantees that depressing of finish to gauge is in the two-phase region.Roll the back steel and strengthen air cooling, speed of cooling is 4-6 /s.
The wind-powered electricity generation that this example is obtained detects with H shaped steel; It is following to obtain this H shaped steel performance: lower yield strength is 418MPa, and tensile strength is 526MPa, and elongation after fracture is 26%;-20 impact of collision merits (AKv) are 208J; Z is 31% to relative reduction in area, and ultrasonic inspection is superior to 2.4 grades of Europe superscripts, and surface quality is superior to Europe superscript ClassC Sub class3.
In 1/3 position, the H of example 1 shaped steel edge of a wing sampling and carry out microtexture research, its metallographic structure photo is seen Fig. 1.Therefrom can find out its be organized as typical ferritic+perlite (that is, and F+P) tissue, wherein, ferrite crystal grain is fine and closely woven, grain fineness number reaches 9.5 grades, no banded structure.These advantageous feature are owing to reasonable component design and accurate two-phase region controlled rolling and roll reasonably process for cooling of back; Given full play to the thin brilliant effect of Nb; Cooperate its effect that improves the two-phase region controlled rolling, also improved its impelling strength when improving steel strength; It is extremely low-level that the low-sulfur Composition Control has guaranteed that size and the quantity of sulfide inclusion all are in, and improved its anti-lamellar tearing performance, is equipped with the appearance that no banded structure has then been guaranteed in low-phosphorous control; The full guard casting is effectively controlled the content of overall gas impurity, has guaranteed good internal soundness.Above-mentioned some guaranteed that H shaped steel of the present invention has obtained good obdurability coupling, anti-lamellar tearing performance and excellent inside, surface quality, thereby H shaped steel of the present invention can satisfy the structural steel requirement of wind energy turbine set.
In sum; H shaped steel of the present invention does not need through bakingout process, and tiny, the homogeneous microstructure of its crystal grain, has superior comprehensive mechanical property; Not easy fracture, be difficult for tearing and be difficult for being destroyed; Safe and reliable, can satisfy coastal generating field structure building demand, the wind-powered electricity generation that also can be used as high and cold desert area is simultaneously used structure iron.
Wind-powered electricity generation of the present invention has been described with H shaped steel and working method thereof although combined accompanying drawing and exemplary embodiment above; But those of ordinary skills should be clear; Under the situation of spirit that does not break away from claim and scope, can carry out various modifications to the foregoing description.
Claims (7)
1. a wind-powered electricity generation is used the H shape steel producing method, it is characterized in that, said working method may further comprise the steps:
Smelting molten steel to be obtaining the target molten steel, the composition of said target molten steel by 0.14～0.22% C by weight, 0.20～0.50% Si, 1.20～1.50% Mn, be no more than 0.010% S, be no more than 0.020% P, 0.010～0.050% Nb, be no more than 40 * 10
-6N, be no more than 10 * 10
-6O, be no more than 3 * 10
-6H, and surplus Fe and unavoidable impurities are formed;
Said target molten steel is carried out casting for shaped blank continuous, adopt the full guard casting during continuous casting;
Rolling special-shaped base, and guarantee that depressing of finish to gauge is in austenite and the ferritic two-phase region, strengthen air cooling then, use H shaped steel to make wind-powered electricity generation.
2. wind-powered electricity generation according to claim 1 is used the H shape steel producing method; It is characterized in that; When the full guard cast in the said continuous casting step is included in casting ladle nozzle and submerged nozzle are sealed; Adopt alkaline covering agent to cover the tundish liquid level, and adopt crystallizer protecting residue to cover mold liquid level.
3. wind-powered electricity generation according to claim 1 is used the H shape steel producing method, it is characterized in that, said rolling step comprises roughing and finish rolling,
Wherein, the start rolling temperature of roughing is 1150～1200 ℃, and the temperature that roughing finishes is 1040～1100 ℃;
The start rolling temperature of finish rolling is 980～1010 ℃, and the finish to gauge end temp is 820～840 ℃.
4. wind-powered electricity generation according to claim 1 is used the H shape steel producing method, it is characterized in that, the rate of cooling of said reinforcement air cooling is 4-6 ℃/s.
5. wind-powered electricity generation according to claim 1 is used the H shape steel producing method; It is characterized in that the C content in the said target molten steel is 0.14～0.18%, Si content is 0.20～0.30%; Mn content is 1.20～1.40%; S content is 0.001～0.008%, and P content is 0.001～0.020%, and Nb content is 0.025～0.035%.
6. use the H shape steel producing method according to claim 1 or 5 described wind-powered electricity generations, it is characterized in that, the carbon equivalent ce V=C+Mn/6+ (Cr+Mo+V) of said target molten steel/5+ (Cu+Ni)/15≤0.43, and manganese sulphur ratio is not less than 20.
7. a wind-powered electricity generation is used H shaped steel, it is characterized in that, said wind-powered electricity generation makes with any described method in the H shaped steel employing claim 1 to 6.
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Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103540844A (en) * | 2013-10-28 | 2014-01-29 | 莱芜钢铁集团有限公司 | Low temperature resistant H-shaped steel and production method thereof |
| CN104789857A (en) * | 2015-04-13 | 2015-07-22 | 内蒙古包钢钢联股份有限公司 | Low-cost 235 MPa grade low-temperature hot-rolling H section steel and preparation method thereof |
| CN107557681A (en) * | 2017-08-02 | 2018-01-09 | 邢台钢铁有限责任公司 | A kind of middle low carbon steel wire rod and its production method with excellent deformation performance |
| CN110291218A (en) * | 2017-03-15 | 2019-09-27 | 日本制铁株式会社 | H profile steel and its manufacturing method |
| CN114941067A (en) * | 2020-12-30 | 2022-08-26 | 日照钢铁控股集团有限公司 | Steel billet for producing hot-rolled H-shaped steel with flange thickness of 15-35 mm |
| CN116891981A (en) * | 2023-06-15 | 2023-10-17 | 包头钢铁（集团）有限责任公司 | Method for producing hot-rolled H-shaped steel with excellent corrosion resistance by adopting special-shaped blank |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0692009B2 (en) * | 1987-01-08 | 1994-11-16 | 新日本製鐵株式会社 | Shaped steel manufacturing method |
| JP2000045043A (en) * | 1998-07-29 | 2000-02-15 | Nippon Steel Corp | H shape steel for tunnel support having 440n square mm and more in cross-sectional average and good in bending workability |
| CN1421286A (en) * | 2002-09-30 | 2003-06-04 | 马鞍山钢铁股份有限公司 | Rolling process of H-shaped niobium-containing steel |
| CN101407888A (en) * | 2008-05-06 | 2009-04-15 | 首钢总公司 | Steel for tower frame structure of wind power generator and production method thereof |
| CN101906579A (en) * | 2010-08-09 | 2010-12-08 | 江苏沙钢集团淮钢特钢有限公司 | Low temperature resistant wind power flange steel with high welding performance and high strength |
| CN102021475A (en) * | 2010-10-25 | 2011-04-20 | 莱芜钢铁股份有限公司 | Hot-rolled H-shaped steel for low temperature-resisting structure and preparation method thereof |
| CN102330023A (en) * | 2010-07-12 | 2012-01-25 | 马鞍山钢铁股份有限公司 | Steel for H steels at 500MPa level of yield strength and thermomechanical control process thereof |
-
2012
- 2012-03-15 CN CN 201210069513 patent/CN102605243B/en not_active Expired - Fee Related
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0692009B2 (en) * | 1987-01-08 | 1994-11-16 | 新日本製鐵株式会社 | Shaped steel manufacturing method |
| JP2000045043A (en) * | 1998-07-29 | 2000-02-15 | Nippon Steel Corp | H shape steel for tunnel support having 440n square mm and more in cross-sectional average and good in bending workability |
| CN1421286A (en) * | 2002-09-30 | 2003-06-04 | 马鞍山钢铁股份有限公司 | Rolling process of H-shaped niobium-containing steel |
| CN101407888A (en) * | 2008-05-06 | 2009-04-15 | 首钢总公司 | Steel for tower frame structure of wind power generator and production method thereof |
| CN102330023A (en) * | 2010-07-12 | 2012-01-25 | 马鞍山钢铁股份有限公司 | Steel for H steels at 500MPa level of yield strength and thermomechanical control process thereof |
| CN101906579A (en) * | 2010-08-09 | 2010-12-08 | 江苏沙钢集团淮钢特钢有限公司 | Low temperature resistant wind power flange steel with high welding performance and high strength |
| CN102021475A (en) * | 2010-10-25 | 2011-04-20 | 莱芜钢铁股份有限公司 | Hot-rolled H-shaped steel for low temperature-resisting structure and preparation method thereof |
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103540844A (en) * | 2013-10-28 | 2014-01-29 | 莱芜钢铁集团有限公司 | Low temperature resistant H-shaped steel and production method thereof |
| CN103540844B (en) * | 2013-10-28 | 2016-04-06 | 莱芜钢铁集团有限公司 | Low temperature resistant H profile steel and production method thereof |
| CN104789857A (en) * | 2015-04-13 | 2015-07-22 | 内蒙古包钢钢联股份有限公司 | Low-cost 235 MPa grade low-temperature hot-rolling H section steel and preparation method thereof |
| CN110291218A (en) * | 2017-03-15 | 2019-09-27 | 日本制铁株式会社 | H profile steel and its manufacturing method |
| CN110291218B (en) * | 2017-03-15 | 2021-06-22 | 日本制铁株式会社 | H-shaped steel and manufacturing method thereof |
| CN107557681A (en) * | 2017-08-02 | 2018-01-09 | 邢台钢铁有限责任公司 | A kind of middle low carbon steel wire rod and its production method with excellent deformation performance |
| CN107557681B (en) * | 2017-08-02 | 2019-05-17 | 邢台钢铁有限责任公司 | A kind of middle low carbon steel wire rod and its production method with excellent deformation performance |
| CN114941067A (en) * | 2020-12-30 | 2022-08-26 | 日照钢铁控股集团有限公司 | Steel billet for producing hot-rolled H-shaped steel with flange thickness of 15-35 mm |
| CN114941067B (en) * | 2020-12-30 | 2024-05-31 | 日照钢铁控股集团有限公司 | Steel billet for producing hot rolled H-shaped steel with flange thickness of 15-35 mm |
| CN116891981A (en) * | 2023-06-15 | 2023-10-17 | 包头钢铁（集团）有限责任公司 | Method for producing hot-rolled H-shaped steel with excellent corrosion resistance by adopting special-shaped blank |
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