CN104004957A - Method for producing H-type steel with small compression ratio and for low temperature through oxide metallurgy technology - Google Patents
Method for producing H-type steel with small compression ratio and for low temperature through oxide metallurgy technology Download PDFInfo
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- CN104004957A CN104004957A CN201410261664.3A CN201410261664A CN104004957A CN 104004957 A CN104004957 A CN 104004957A CN 201410261664 A CN201410261664 A CN 201410261664A CN 104004957 A CN104004957 A CN 104004957A
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Abstract
The invention discloses a method for producing H-type steel with the small compression ratio and for low temperature through an oxide metallurgy technology. The method sequentially includes the processes of pretreatment of hot metal, converter smelting, LF refining, shaped blank continuous casting, heating, rolling and cooling. In the converter smelting process, the content of a Si component is adjusted to be in the range from 0.05 wt% to 0.25 wt% before steel tapping; in the LF refining process, steel ladles enter a refining station and then ferrozirconium are added to the steel ladles and titanium wires are fed to the steel ladles. Through the reasonable oxide metallurgy technology, nonmetallic inclusions in the steel are controlled, under the condition that an original production process of the H-type steel with the small compression ratio and for low temperature is not changed, evenness and compactness of casting blanks and product structures are improved, and therefore the problem that usually, the low-temperature performance and the mechanical performance of the H-type steel, with the small compression ratio and for low temperature, rolled by shaped blanks are poor and even disqualified is solved.
Description
Technical field
The present invention relates to a kind of hot rolled H-shaped production technical field, particularly a kind of method of utilizing Oxides Metallurgy Technology to produce small reduction ratio low temperature H shaped steel.
Background technology
H shaped steel mechanics distributes rationally, profile cross-section coefficient is large, supporting capacity is large, is convenient to assembled and rivet welding, is that a kind of section area distributes more reasonably economic section high efficiency section bar of optimization, the ratio of strength to weight more, is widely applied.Along with social progress and development in science and technology, various buildings, structure require also more and more higher to the properties of steel, are particularly ensureing to have proposed high requirement aspect the stability of structure, security.Current low-temperature steel product is mainly sheet material, mostly take welding process to obtain for requiring the H shaped steel product with low-temperature impact-resistant performance, and in welding process, the reduction of the performance index of welded heat affecting zone and weld seam is unavoidable, process in addition welding process and also will produce certain expense, the performance measurement of position while welding simultaneously, flaw detection all need expense, and the construction period has also been extended.
Modern H shaped steel is produced as significantly improving production efficiency, improving recovery rate, often adopts casting for shaped blank continuous or near-net-shape casting for shaped blank continuous technology.Thereby the rolling power that adopts Hot Metal in Beam Blank rolled section steel product can improve milling train improves output, but for producing thick specification product, owing to being subject to the impact of strand size, often compression ratio is on the low side, thereby causes the defects such as strand segregation and center porosity to can not get effectively alleviating or improving.In addition, because the complicacy of shaped steel shape of product will be controlled the cold effective means that still lack uniformly.Therefore all there is unstable properties, defect that qualification rate is low in industry, in the time producing the product of low-temperature impact-resistant shaped steel or small reduction ratio low-temperature impact-resistant shaped steel.
In order to address the above problem, industry has proposed various solutions, such as add Ni, B in metallurgical process, make up the deficiency of performance by microalloying, but this scheme because making iron scale in course of hot rolling be difficult to remove, the interpolation of Ni affects product surface quality; Yi You manufacturer sets up control cooling equipment on production line, enhance product performance, but this formula investing is large, later maintenance cost is high thereby improve tissue by controlled rolling and controlled cooling.
Summary of the invention
For the deficiencies in the prior art, the object of the present invention is to provide a kind of method of utilizing Oxides Metallurgy Technology to produce small reduction ratio low temperature H shaped steel.
Production method of the present invention is for shaped steel products production feature, by choose reasonable and interpolation trace alloying element, control nonmetallic inclusionsin steel, make it as the core of cenotype heterogeneous nucleation or play the effect of pinning crystal boundary, thus utilize the non-metallic inclusion control steel in steel tissue, improve performance.Oxides Metallurgy Technology is applied to and improves small reduction ratio low temperature H shaped steel, and it is crucial obtaining required oxide compound kind, size and distributing, and oxide compound particle tiny and that disperse distributes is conducive to promote cenotype forming core and pinning crystal boundary.Small reduction ratio low temperature comprises hot metal pretreatment-converter smelting-LF refining-Profiled Slab CCM etc. successively by H shaped steel production technique, the final product of oxide compound and C in molten steel, O equal size are relevant, wherein oxygen level can reflect indirectly by converter control Si content, and relevant with deoxidant element, alloying element and order of addition.
To achieve these goals, the present invention is by the following technical solutions:
Utilize Oxides Metallurgy Technology to produce a method for small reduction ratio low temperature H shaped steel, comprise successively hot metal pretreatment, converter smelting, LF refining, shaped blank continuous casting, heating, rolling and refrigerating work procedure, wherein:
In described converter smelting operation, before tapping, the content of Si composition is adjusted to 0.05-0.25wt%;
In described LF refining procedure, ladle adds ferrozirconium, feeding titanium wire after entering refining station, adds the amount of ferrozirconium to be controlled at 0.07-0.1kg/ ton molten steel, and the amount of feeding titanium wire is controlled at 0.4-0.8m/ ton molten steel;
The H shaped steel that described method obtains is made up of following chemical composition by weight percentage: C0.12-0.20%, Si0.10-0.30%, Mn1.15-1.70%, P≤0.025%, S≤0.010%, Nb≤0.02%, Cu≤0.02%, all the other are Fe and inevitable impurity.
The present invention adopts converter, by cast iron melting and before tapping, the composition of Si is adjusted to 0.05wt%-0.25wt%, after ladle enters refining station, it is line feeding, after feeding mentioned component, generate the complex inclusion of the tiny distribution of disperse, as shown in Figure 7, the inclusion that these are tiny, can promote austenite forming core on the one hand, can stop tissue to be grown up by pinning crystal boundary on the other hand.The oxide type obtaining by Oxide Metallurgy technique of the present invention is tiny and the oxide compound particle of disperse distribution, be conducive to promote cenotype forming core and pinning crystal boundary, for ensureing that Oxide Metallurgy technique obtains excellent results, need implement targetedly production process in converter, refining procedure.In the present invention, owing to being micro-Zr and Ti, therefore in the time of composition detection, the two is not done to requirement, even cannot detect.
In aforesaid method, as a kind of preferred implementation, in described hot metal pre process procedures, molten iron is delivered to desulfurization station, after desulfurization, ensure sulphur content≤0.008wt% in molten iron (such as 0.005wt%, 0.006wt%, 0.007wt%).
In aforesaid method, as a kind of preferred implementation, in described shaped blank continuous casting working procedure, described continuously cast bloom edge of a wing thickness is that 60-80mm, pulling rate are≤1.0m/min (such as 0.7m/min, 0.8m/min, 0.9m/min).
In aforesaid method, as a kind of preferred implementation, in described heating process, the soaking temperature of described continuous casting steel billet is 1200 DEG C-1300 DEG C (such as 1210 DEG C, 1230 DEG C, 1250 DEG C, 1260 DEG C, 1280 DEG C, 1295 DEG C).
In aforesaid method, as a kind of preferred implementation, in described rolling process, the start rolling temperature of split rolling method is 1150 DEG C above (such as 1150 DEG C, 1180 DEG C, 1200 DEG C, 1240 DEG C, 1260 DEG C, 1280 DEG C), the start rolling temperature of universal rolling mill group is not less than 970 DEG C (such as 970 DEG C, 1000 DEG C, 1020 DEG C, 1050 DEG C, 1070 DEG C, 1090 DEG C), and finished product finishing temperature is not higher than 920 DEG C (such as 800 DEG C, 820 DEG C, 850 DEG C, 880 DEG C, 900 DEG C, 910 DEG C).More preferably, the start rolling temperature of described split rolling method is 1150-1250 DEG C, the start rolling temperature 970-1100 DEG C of universal rolling mill group, finished product finishing temperature 850-920 DEG C.
The present invention, by the comprehensive action of dispersion-strengthened and refined crystalline strengthening, improves especially low-temperature impact-resistant performance of steel performance.
In aforesaid method, as a kind of preferred implementation, described small reduction ratio refers to that compression ratio is not more than 3.5 (such as 2,2.5,3,3.4).
The processing step not relating in the present invention adopts this area common process.
Compared with prior art, the present invention is by rational Oxides Metallurgy Technology, control nonmetallic inclusionsin steel, in the situation that not changing original small reduction ratio low temperature H shaped steel production technique, improve homogeneity and the compactness of strand and product tissue, thereby improve normal low-temperature performance and the poor even unqualified problem of mechanical property occurring of Hot Metal in Beam Blank rolling small reduction ratio low temperature H shaped steel.Especially to be that the method that solves the normal interpolation Ni alloy adopting of problems has simple to operate, cost is low, do not affect product surface quality and do not increase the advantages such as rolling process de-scaling difficulty compared with industry to make small reduction ratio low temperature H shaped steel obtain excellent low-temperature impact-resistant performance, be under existing weaponry and equipment technical qualification, Hot Metal in Beam Blank is realized the effective ways of stably manufactured small reduction ratio low temperature H shaped steel.The present invention also has the following advantages: be easy to implement in production scene; Operating process is simple, direct; Alloying constituent control is accurate; Cost is lower.
Brief description of the drawings
Fig. 1 is the macrostructure photo of continuous casting special-shaped base described in embodiment;
Fig. 2 is the macrostructure photo of continuous casting special-shaped base described in comparative example;
Fig. 3 is the metallographic structure photo of continuous casting special-shaped base described in embodiment;
Fig. 4 is the metallographic structure photo of continuous casting special-shaped base described in comparative example;
Fig. 5 is the inclusion distribution plan of continuous casting special-shaped base described in embodiment;
Fig. 6 is the inclusion distribution plan of continuous casting special-shaped base described in comparative example;
Fig. 7 is the inclusion scanning electron microscope (SEM) photograph of continuous casting special-shaped base described in embodiment, wherein, and (a) inclusion distribution plan; (b) ZrO
2-TiO
x; (c) TiO
x-ZrO
2.
Embodiment
Below in conjunction with drawings and Examples, comparative example, the present invention will be further described, but be not limited to this.
Embodiment
Adopt 120 tons of conventional smelting equipments of this area, casting for shaped blank continuous equipment, press corresponding composition and alloy content in table 1, adopt Oxides Metallurgy Technology to smelt, and continuous casting is Hot Metal in Beam Blank, then obtain small reduction ratio low temperature H shaped steel of the present invention through process furnace heating, rolling, cooling and aligning.Concrete production method is as follows:
1) hot metal pretreatment: molten iron is delivered to desulfurization station, ensure sulphur content≤0.008wt% in molten iron after desulfurization;
2) converter smelting: before tapping by adjust to≤0.15wt% of the content of Si composition; In converter tapping process, add carbide of calcium to carry out deoxidation, and in converter tapping process, add manganeseirom, ferrocolumbium; In converter, add Cu with steel scrap;
3) LF refining: ladle enters the station, first connects tunger tube, after argon gas blows open, thermometric, determines after oxygen, adds ferrozirconium 10KG/ stove, feeds titanium wire 70m/ stove, and wire-feeding velocity is 4m/s;
4) in shaped blank continuous casting working procedure, continuous casting steel billet is of a size of 555 × 440 × 90 × 70 (web height × flange width × web thickness × edge of a wing thickness), pulling rate is 0.9m/min, and the continuous casting special-shaped base macrostructure of acquisition is shown in that Fig. 1, metallograph be shown in that Fig. 3, inclusion overall distribution situation be shown in Fig. 5;
5) heating: the soaking temperature of continuous casting steel billet is 1250 DEG C, and be 3h heat-up time;
6) rolling: the start rolling temperature of described split rolling method is 1200 DEG C, 1000 DEG C of the start rolling temperatures of universal rolling mill group, 900 DEG C of finished product finishing temperatures;
7) cooling and aligning: deliver to after water-cooled and carry out naturally cooling on cold bed, product temperature is down to 80-120 DEG C of laggard straightener and is aligned, stocking trimmed size is H428 × 407 × 20 × 20 (units: mm), and compression ratio is 3.5, and mechanical property is in table 2.
As can be known from Fig. 7, contain the content of Ti, Zr in complex inclusion, size is less than 1 μ m, and pattern is spherical in shape, and complex inclusion inside is with ZrO
2be main, outside is with TiO
xbe main.
Adopt the method for the present embodiment to produce altogether 30 H shaped steel finished products, the low-temperature performance in its table 2 and mechanical property are equal 100% qualified.
Comparative example
Adopt and smelting, casting for shaped blank continuous equipment identical in embodiment, press corresponding composition and alloy content in table 1, adopting industry is to solve the unstable Ni-B microalloying using of small reduction ratio low temperature H shaped steel low-temperature impact-resistant performance to smelt scheme (specific as follows), continuous casting goes out the Hot Metal in Beam Blank identical with specification in embodiment, then through with process furnace heating identical in embodiment, rolling pattern and cooling and aligning operation.
In this comparative example, smelting and refining procedure are as follows:
1) hot metal pretreatment: molten iron is delivered to desulfurization station, ensure sulphur content≤0.008wt% in molten iron after desulfurization;
2) converter smelting: before tapping by adjust to≤0.15wt% of the content of Si composition; In tapping process, add appropriate Ni alloy;
3) LF refining: feed appropriate B line before soft blow;
4), in shaped blank continuous casting working procedure, it is 0.9m/min that continuous casting steel billet is of a size of 555 × 440 × 90 × 70 (web height × flange width × web thickness × edge of a wing thickness) pulling rate.
The specification that the present embodiment obtains H shaped steel finished product is identical with embodiment, and mechanical property is in table 2, and its continuously cast bloom macrostructure is shown in that Fig. 2, metallograph be shown in that Fig. 4, inclusion overall distribution situation be shown in Fig. 6.
The chemical composition of table 1 embodiment and comparative example steel
| Composition | C | Si | Mn | P | S | Nb | Ni | Cu | Ti | Zr | B |
| Embodiment | 0.12 | 0.13 | 1.25 | 0.011 | 0.008 | 0.015 | - | 0.02 | 0.007 | 0.004 | - |
| Comparative example | 0.14 | 0.14 | 1.24 | 0.014 | 0.005 | 0.018 | 0.437 | 0.019 | - | - | 0.006 |
The mechanical property of table 2 embodiment and comparative example steel
Wherein, in table 2, mechanical property sample sampling position used is on H section steel flange, and by limit portion, to 1/3 place of heart portion, reference standard is GB/T2975-1998 " steel and product made from steel mechanical property test sample position and sample preparation "; The test method reference standard GB GB/T228-2010 of yield strength, tensile strength, unit elongation; Ballistic work test method reference standard GB GB/T229-2007.
Adopt the method for comparative example to produce altogether 30 H shaped steel finished products, the low-temperature performance in its table 2 and mechanical property are only 60% qualified.
Contrast by Fig. 1 and Fig. 2 is known, by implementing zirconium titanium processing process, the strand center porosity of the embodiment of the present invention and segregation defect be improved significantly, homogeneity and compactness significantly improves.
Contrast by Fig. 3 and Fig. 4 is known, and the product banded structure of the embodiment of the present invention obviously improves, and crystal grain is more tiny.
Contrast by Fig. 5 and Fig. 6 is known, and the product inclusion size of the embodiment of the present invention is less, distribution disperse.
Comprehensive Correlation example and embodiment, the present invention can improve slab quality, crystal grain thinning tissue, and obviously improves H shaped steel low-temperature impact-resistant performance.Overcome the problems such as low-temperature performance that especially Hot Metal in Beam Blank rolling of section rolling, small reduction ratio or low temperature resistant H shaped steel is difficult to overcome is unstable by rational Oxides Metallurgy Technology, be effective, convenient and practical scheme, have great importance at H shaped steel production field.
Claims (7)
1. utilize Oxides Metallurgy Technology to produce a method for small reduction ratio low temperature H shaped steel, it is characterized in that, comprise successively hot metal pretreatment, converter smelting, LF refining, shaped blank continuous casting, heating, rolling and refrigerating work procedure, wherein:
In described converter smelting operation, before tapping, the content of Si composition is adjusted to 0.05-0.25wt%;
In described LF refining procedure, ladle adds ferrozirconium, feeding titanium wire after entering refining station, adds the amount of ferrozirconium to be controlled at 0.07-0.1kg/ ton molten steel, and the amount of feeding titanium wire is controlled at 0.4-0.8m/ ton molten steel;
The H shaped steel that described method obtains is made up of following chemical composition by weight percentage: C0.12-0.20%, Si0.10-0.30%, Mn1.15-1.70%, P≤0.025%, S≤0.010%, Nb≤0.02%, Cu≤0.02%, all the other are Fe and inevitable impurity.
2. method according to claim 1, is characterized in that, in described hot metal pre process procedures, molten iron is delivered to desulfurization station, ensures sulphur content≤0.008wt% in molten iron after desulfurization.
3. method according to claim 1, is characterized in that, in described shaped blank continuous casting working procedure, described continuously cast bloom edge of a wing thickness is that 60-80mm, pulling rate are≤1.0m/min.
4. method according to claim 1, is characterized in that, in described heating process, the soaking temperature of described continuous casting steel billet is 1200 DEG C-1300 DEG C.
5. method according to claim 1, is characterized in that, in described rolling process, the start rolling temperature of split rolling method is more than 1150 DEG C, and the start rolling temperature of universal rolling mill group is not less than 970 DEG C, and finished product finishing temperature is not higher than 920 DEG C.
6. method according to claim 5, is characterized in that, more preferably, the start rolling temperature of described split rolling method is 1150-1250 DEG C, the start rolling temperature 970-1100 DEG C of universal rolling mill group, finished product finishing temperature 850-920 DEG C.
7. method according to claim 1, is characterized in that, described small reduction ratio refers to that compression ratio is less than 3.5.
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| CN111229827A (en) * | 2020-03-02 | 2020-06-05 | 马鞍山钢铁股份有限公司 | Hot-rolled H-shaped steel with yield strength of 450MPa and production method thereof |
| CN111304404A (en) * | 2020-03-31 | 2020-06-19 | 鞍钢股份有限公司 | Cored wire for oxide metallurgy of vacuum induction furnace and use method |
| CN112941411A (en) * | 2021-01-29 | 2021-06-11 | 中冶华天南京工程技术有限公司 | Ultra-low carbon bainite super-heavy H-shaped steel and manufacturing method thereof |
| CN115449700A (en) * | 2022-09-20 | 2022-12-09 | 西安建筑科技大学 | Method for improving low-carbon gear steel strip-shaped structure based on oxide metallurgy and low-carbon gear steel |
| CN116770017A (en) * | 2023-08-03 | 2023-09-19 | 昆明理工大学 | Method for modifying inclusions in Ti microalloyed high-strength steel |
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