CN100368577C - Process for producing fine type steel crystal particle - Google Patents
Process for producing fine type steel crystal particle Download PDFInfo
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- CN100368577C CN100368577C CNB2005100224431A CN200510022443A CN100368577C CN 100368577 C CN100368577 C CN 100368577C CN B2005100224431 A CNB2005100224431 A CN B2005100224431A CN 200510022443 A CN200510022443 A CN 200510022443A CN 100368577 C CN100368577 C CN 100368577C
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Abstract
The present invention relates to a producing method of crystal particles of refined profile steel. The method comprises the following steps: (1) smelting molten steel; (2) deoxidizing the molten steel by Al; (3) adding 0.005 to 0.015% of Ti, 0.08 to 0.15% of V and 0.010 to 0.020% of N, and then casting the mixture to obtain casting blanks; (4) heating the casting blanks to 1100 to 1250 DEG C, and rolling casting blanks to obtain the profile steel with a final rolling temperature of 700 to 950 DEG C; (5) cooling the profile steel. The method of the present invention can be used to directly smelting the profile steel without measuring the oxygen concentration of the molten steel. The crystal particle size of the produced profile steel can reach over 9.5 grade, and simultaneously the strength and low-temperature impact performance of the profile steel are improved. Compared with the profile steel which is not produced by the method of the present invention, the profile steel improves yield strength by over 30MPa and low-temperature impact performance at-40 DEG C by over 10J. The method of the present invention is suitable for smelting weathering-proof profile steel, firep-roof profile steel and weathering-proof and firep-roof profile steel.
Description
Technical field
The present invention relates to a kind of shape steel producing method, specially refer to a kind of production method of fine type steel crystal particle.
Background technology
Chinese patent 93119843.7 discloses a kind of " as having the strand of high-intensity high-tenacity and fabulous resistivity against fire shaped steel material and the rolled section steel method of producing this strand ", this patent is 0.04～0.20% C with weight percent content (degree that occurs below is weight percent content), 0.05～0.50% Si, 0.4～2.0% Mn, 0.3～0.7% Mo, 0.003～0.01 5% N, 0.04 carrying out pre-deoxidation ,～0.20% V and the molten steel that is not more than 0.005% Al handle, adjusting oxygen level is 0.003～0.015%, then to wherein adding titanium and satisfying :-0.006≤[Ti%]-2[0%]≤0.008, make titanium-based oxide with 〉=20 particles/mm
2The quantity crystallization, and MnS, TiN and V (C, N) are deposited on the titanium-based oxide, make titanium-based oxide with the composite precipitation disperse in steel, the quick cooling when rolling after water-cooled between each rolling pass and rolling finishing, the high strength, the high tenacity shaped steel that obtain having fabulous resistivity against fire.Also contain in this shaped steel≤0.7% Cr ,≤0.05% Nb ,≤1.0% Cu ,≤0.003% Ca or≤at least a among 0.010 the REM (rare earth element) as chemical composition.
Usually contain elements such as Cu, Cr for weathering steel, contain the Mo element for fire-resistant steel, contain the fire-resistant and weather-resistant steel that is of Cu, Cr, Mo element.The key of above-mentioned patent is to have adopted little Ti treatment technology to produce the shaped steel that contains Cu, Cr, Mo element, and the oxygen concn adding Ti replacement aluminium deoxidation according to molten steel makes in the steel with 〉=20 particles/mm
2The amount tiny Ti-base composite oxide that distributes, in rolling cooling subsequently, from austenite crystal, produce the intracrystalline ferrite thereby make, the tissue of refinement steel improves the intensity and the toughness of steel.But this method must at first be measured the oxygen concn of molten steel with specific equipment, make the producer that does not measure molten steel oxygen concn equipment can not produce such steel like this.In addition, even have the equipment of measuring the molten steel oxygen concn, also may bring difficulty to production because of the accuracy of this equipment.
Summary of the invention
Technical problem to be solved by this invention provides a kind of production method of fine type steel crystal particle, and this method need not be measured the molten steel oxygen concn, and is easy to operate.
The technical scheme that technical solution problem of the present invention is adopted is: a kind of production method of fine type steel crystal particle said method comprising the steps of: 1) smelting molten steel; 2) carry out deoxidation with Al; 3) behind the N of the V of Ti, 0.08～0.15 weight % of adding 0.005～0.015 weight % and 0.010～0.020 weight %, be cast into strand, the content of described V and N meets 6≤V/N≤10; 4) strand is heated to 1100～1250 ℃ after rolled section steel, finishing temperature is 700～950 ℃; 5) cooling.
The invention has the beneficial effects as follows: the inventive method need not be measured the molten steel oxygen concn, directly smelt shaped steel, the producer that does not measure molten steel oxygen concn equipment also can be produced, the crystal grain that this method is produced shaped steel is tiny, can reach more than 9.5 grades by GB/T6394-2002 method grading grain fineness number, can improve the intensity and the low temperature impact properties of shaped steel simultaneously, compare with the shaped steel that does not adopt the inventive method to produce, yield strength improves more than the 30MPa, and-40 ℃ of low temperature impact properties improve more than the 10J.The inventive method is applicable to smelts weather-proof shaped steel (atmosphere corrosion resistance structural steel), fire-resistant shaped steel and fire-resistant and weather-resistant shaped steel.
Description of drawings
Fig. 1 adopts the inventive method to produce the precipitate pattern of shaped steel.
Fig. 2 adopts the metallographic structure of the shaped steel that the present invention produces.
Embodiment
The invention will be further described below in conjunction with drawings and Examples.
General weathering steel chemical composition is that C≤0.20%, Si≤0.80%, Mn≤1.80%, P≤0.035%, S≤0.025%, Cu are 0.15～0.65%, Ni is 0.15～0.65%, Cr is 0.20～1.00%; It is that C≤0.20%, Si≤0.80%, Mn≤1.80%, P≤0.035%, S≤0.025%, Mo are 0.20～0.80% that fire-resistant tempering is learned component; The fire-resistant and weather-resistant steel chemical composition is that C≤0.20%, Si≤0.80%, Mn≤1.80%, P≤0.035%, S≤0.025%, Cu are 0.15～0.65%, Ni is 0.15～0.65%, Cr is 0.20～1.00%, Mo is 0.20～0.80%.
C, Si, Mn are the elements of most economical raising hardness of steel, increase along with C, Si, Mn content in the steel, the intensity of steel can rise significantly, but the toughness and the weldability of steel descend thereupon, and shaped steel usually requires to have good weldability and toughness, so general requirement C≤0.20%, Si≤0.80%, Mn≤1.80%; P can improve the atmospheric corrosion resistance ability of steel, and Cu-P is that the P content of weather resisting steel can be 0.07～0.12%, but P can improve the low temperature brittleness transition temperature again, and the low temperature impact properties of shaped steel is declined to a great extent, so shaped steel general requirement P≤0.035%; Except that free-cutting steel, S is a harmful element, requires S low more good more in the shaped steel; Add 0.15～0.65% Cu, 0.15～0.65% Ni, 0.20～1.00% Cr in the steel and can make steel have good weather resistance, improve the intensity of steel simultaneously; Mo can improve the hot strength of steel, adds 0.20%～0.80% Mo, the hot strength in the time of can improving 600 ℃.
Under the situation of deoxidation fully, add Ti, can form a large amount of Ti (C, N) particle, when steel is heated to more than 1250 ℃, can also find not to be dissolved in austenitic Ti (C, N) particle, stop growing up of austenite crystal.But the Ti content that adds in the steel surpasses at 0.015% o'clock, very easily forms the large size Ti (C, N) about 5 μ m, and these Ti (C, N) are square, and is very sharp hard, is unfavorable for the fatigue property of steel.V can form V (C, N) particle, about 600 ℃, begin to be dissolved in the austenite, 900 ℃～1000 ℃ are dissolved in austenite fully, in rolling cooling subsequently, from austenite, separate out, part of V (C, N) particle becomes the ferrite core, promote the ferritic generation of intracrystalline, make the crystal grain of steel obtain refinement.For guaranteeing to obtain a large amount of V (C, N) particle, the V add-on is 0.08～0.15%.N can bring in the steel with furnace charge and alloy, liquid metal also can suck part N from atmosphere, usually the residual N content of basic oxygen furnace smelting steel is about 0.002～0.008%, the residual N content of electrosmelting steel is about 0.006～0.0015%, in molten steel treating processes subsequently, should be according to different smelting processes, adding N content is 0.010～0.020%, make V and N content in the steel meet 6≤V/N≤10, be equipped with 0.005～0.015% Ti, can make a large amount of particle of disperse distribution on the steel matrix, see Fig. 1.
In sum, the present invention adopts the crystal grain of following method fine type steel:
1) adopts converter or electrosmelting molten steel.
2) carry out deoxidation with Al after, add 0.005～0.015% Ti, 0.08～0.15% V and 0.010～0.020% N, make that the content of V and N meets 6≤V/N≤10 in the molten steel.
If adopted vacuum outgas that molten steel is handled, the vacuum processing time behind adding Al, Ti, V and the N must be less than 4 minutes.
3) after the strand cooling, strand is heated to 1100～1250 ℃, rolled section steel, finishing temperature is 700～950 ℃, after section rolling is finished, can adopt the air cooling mode to cool off, and promptly obtains the tiny shaped steel of crystal grain, its metallographic structure is as shown in Figure 2.
Weather-proof shaped steel generally is used in the various open-air structural parts, not only requires shaped steel to have high strength and good atmospheric corrosion resistance ability, also requires shaped steel should have good low temperature impact properties and weldability simultaneously.Elements such as the Cr that adds in the steel, Ni, Cu improve the weathering resistance and the intensity of shaped steel, but the weldability of steel and low temperature impact properties can decline to a great extent.Adopt significantly refinement weather resistant crystalline grain of steel of the technology of the present invention, not only improve intensity but also improve low temperature impact properties.Again because to improve intensity be to adopt thin brilliant method, rather than adopt the mode of alloy strengthening, therefore can not reduce the weldability of weather-proof shaped steel.So the shaped steel that adopts the inventive method to produce can satisfy service requirements better.
Embodiment 1-6:
Table 1 is 6 kinds of weather-proof shaped steel that adopt the inventive method to produce, and grain size number wherein and mechanical property are respectively according to GB/T 6394-2002, GB/T 228-2002 and GB/T 229-2002 evaluation.The result shows that the weather resistant crystalline grain of steel that adopts the inventive method to produce is tiny, and rating result reaches 9.5～10.5 grades, and the yield strength of shaped steel reaches more than the 500MPa, low temperature impact properties is good.
Table 1
| Embodiment 1 | Embodiment 2 | Embodiment 3 | Embodiment 4 | Embodiment 5 | Embodiment 6 | |
| C | 0.12 | 0.12 | 0.14 | 0.12 | 0.13 | 0.15 |
| Si | 0.36 | 0.40 | 0.41 | 0.40 | 0.42 | 0.43 |
| Mn | 1.40 | 1.44 | 1.45 | 1.40 | 1.41 | 1.38 |
| P | 0.016 | 0.019 | 0.022 | 0.017 | 0.014 | 0.016 |
| S | 0.009 | 0.012 | 0.010 | 0.010 | 0.009 | 0.009 |
| Cr | 0.29 | 0.30 | 0.28 | 0.28 | 0.28 | 0.29 |
| Ni | 0.29 | 0.28 | 0.28 | 0.28 | 0.27 | 0.24 |
| Cu | 0.28 | 0.29 | 0.27 | 0.29 | 0.29 | 0.29 |
| Ti | 0.008 | 0.007 | 0.010 | 0.013 | 0.009 | 0.009 |
| V | 0.09 | 0.13 | 0.12 | 0.12 | 0.14 | 0.12 |
| N | 0.012 | 0.018 | 0.018 | 0.014 | 0.019 | 0.013 |
| V/N | 7.5 | 7.22 | 6.67 | 8.57 | 7.36 | 9.23 |
| Grain size number | 10.0 | 10.0 | 10.5 | 10.0 | 10.0 | 9.5 |
| Rel/MPa | 500 | 515 | 540 | 500 | 500 | 500 |
| Rm/MPa | 630 | 650 | 680 | 620 | 620 | 625 |
| -40 ℃ of " V " type notch shock merit/J (on average) | 80 | 42 | 49 | 40 | 72 | 54 |
Table 2 is the shaped steel that does not adopt the inventive method rolling, and the result shows that the grain size number of shaped steel, intensity index and low temperature impact properties are all lower.
Table 2
| 1 | 2 | |
| C | 0.10 | 0.13 |
| Si | 0.28 | 0.51 |
| Mn | 1.40 | 1.53 |
| P | 0.015 | 0.020 |
| S | 0.026 | 0.025 |
| Cr | 0.25 | 0.32 |
| Ni | 0.38 | 0.33 |
| Cu | 0.35 | 0.38 |
| N | 0.004 | 0.004 |
| Grain size number | 8.0 | 7.5 |
| Rel/MPa | 395 | 425 |
| Rm/MPa | 540 | 610 |
| -40 ℃ of " V " type ballistic work/J (on average) | 24 | 21 |
Claims (3)
1. the production method of fine type steel crystal particle is characterized in that, said method comprising the steps of: 1) smelting molten steel; 2) carry out deoxidation with Al; 3) behind the N of the V of Ti, 0.08～0.15 weight % of adding 0.005～0.015 weight % and 0.010～0.020 weight %, be cast into strand, the content of described V and N meets 6≤V/N≤10; 4) strand is heated to 1100～1250 ℃ after rolled section steel, finishing temperature is 700～950 ℃; 5) cooling.
2. the production method of fine type steel crystal particle as claimed in claim 1 is characterized in that, the air cooling mode is adopted in the described cooling of step 5.
3. the production method of fine type steel crystal particle as claimed in claim 1 is characterized in that, described shaped steel is weather-proof shaped steel, fire-resistant shaped steel or fire-resistant and weather-resistant shaped steel.
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| CN101343713B (en) * | 2008-08-19 | 2010-12-22 | 攀钢集团研究院有限公司 | High-strength atmospheric corrosion resistant hot-rolled strip steel and method of manufacturing the same |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH05105947A (en) * | 1991-10-16 | 1993-04-27 | Nippon Steel Corp | Production of rolled shape steel excellent in refractoriness and toughness |
| JPH05132716A (en) * | 1991-11-12 | 1993-05-28 | Nippon Steel Corp | Manufacture of rolled shape steel excellent in toughness |
| JPH05163516A (en) * | 1991-12-13 | 1993-06-29 | Kobe Steel Ltd | Production of steel plate for welding structure having excellent welded joint toughness |
| CN1088628A (en) * | 1992-09-24 | 1994-06-29 | 新日本制铁株式会社 | High-intensity high-tenacity and fabulous resistivity against fire shaped steel material and the method for producing the rolled section steel of this material |
| RU1352958C (en) * | 1986-02-21 | 1995-03-20 | Нижнетагильский металлургический комбинат | Method for production of microalloyed steel |
| CN1167157A (en) * | 1996-01-19 | 1997-12-10 | 川崎制铁株式会社 | Method for making ultralow carbon cold-rolled steel plate |
-
2005
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Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| RU1352958C (en) * | 1986-02-21 | 1995-03-20 | Нижнетагильский металлургический комбинат | Method for production of microalloyed steel |
| JPH05105947A (en) * | 1991-10-16 | 1993-04-27 | Nippon Steel Corp | Production of rolled shape steel excellent in refractoriness and toughness |
| JPH05132716A (en) * | 1991-11-12 | 1993-05-28 | Nippon Steel Corp | Manufacture of rolled shape steel excellent in toughness |
| JPH05163516A (en) * | 1991-12-13 | 1993-06-29 | Kobe Steel Ltd | Production of steel plate for welding structure having excellent welded joint toughness |
| CN1088628A (en) * | 1992-09-24 | 1994-06-29 | 新日本制铁株式会社 | High-intensity high-tenacity and fabulous resistivity against fire shaped steel material and the method for producing the rolled section steel of this material |
| CN1167157A (en) * | 1996-01-19 | 1997-12-10 | 川崎制铁株式会社 | Method for making ultralow carbon cold-rolled steel plate |
Non-Patent Citations (4)
| Title |
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| Ti-V-N钢的工艺特征和性能. Siwech，T.，et，al.钢铁钒钛，第4期. 1984 * |
| 含钒钛低合金钢国外发展动态. 单麟天.钢铁钒钛，第4期. 1984 * |
| 氮在非调质钢中的作用. 季怀忠等.钢铁，第35卷第7期. 2000 * |
| 铌微合金化生产HRB400钢筋. 吴绍杰等.钢铁研究，第4期卷. 2005 * |
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