CN103667910A - Hot-rolled H-shaped steel with excellent low-temperature impact toughness and manufacturing method thereof - Google Patents
Hot-rolled H-shaped steel with excellent low-temperature impact toughness and manufacturing method thereof Download PDFInfo
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Abstract
The invention discloses hot-rolled H-shaped steel with excellent low-temperature impact toughness. The steel comprises the following chemical components in percentage by mass: 0.05-0.018 percent of C, 0.15-0.40 percent of Si, 1.0-1.50 percent of Mn, 0.010-0.050 percent of V, 0.015-0.050 percent of Nb, 0.005-0.025 percent of Ti, 0-0.035 percent of Al, 0-0.020 percent of P, 0-0.015 percent of S, and Fe and inevitable impurities in balancing amount. The invention further discloses a manufacturing method for the steel. The method has the characteristics of low cost and simple technology, the finished hot-rolled H-shaped steel made through the method has excellent low-temperature impact toughness, the longitudinal impact power at -40 DEG at the one third position of a flange is greater than 201 J, and the longitudinal impact power at -60 DEG at the one third position of the flange is greater than 109 J.
Description
Technical field
The high low-temperature flexibility H shaped steel of low-alloy high-strength that the present invention relates to have under hot-rolled state special purpose, particularly rolls H shaped steel and manufacture method thereof to the strict low-alloy high-strength hot of low-temperature impact toughness requirement.
Background technology
H shaped steel is a kind of economic structure steel, is usually used in requirement bearing capacity large, the heavy construction of cross section good stability (as factory building, Highrise buildings etc.), and bridge, boats and ships, handling machinery, the energy, chemical industry steel structure support, foundation pile etc.Due to the continuous expansion of hot rolling H Application Areas, in special application fields such as high latitude, high altitude localities and offshore oil platform construction, polar region exploitations, to low-temperature impact toughness, require high.The technique means that obtains at present good high low temperature toughness hot rolled H-shaped steel product mainly contains two kinds of approach: be a kind ofly by a certain amount of microalloy composition and coordinate controlled rolling to realize; Another kind is to realize by adding the alloys such as nickel.
Patent of invention CN101255527B disclose a kind of there is favorable low-temperature impact toughness add boron H shaped steel and manufacture method thereof, this invention composition of steel weight percent is: C 0.08～0.20%, Mn 1.00～1.60%, Si 0.10～0.55%, P≤0.025%, S≤0.025%, Nb 0.015～0.035%, B 0.0005～0.0012%, surplus is iron and trace impurity.In smelting process, control the gas content [N]≤0.004% in steel, [O]≤0.0060%.Its feature is to add in composition micro-B element, and needs the nitrogen, the oxygen that keep lower, and production control difficulty is large; simultaneously for guaranteeing good deoxidation effect; need to use aluminium deoxidation, easily cause the nozzle clogging of casting process, to the protection cast of casting process, require high.
Patent of invention CN101812632B discloses a kind of-40 ℃ to-60 ℃ of manufacture method that low-temperature impact toughness is hot rolled H-shaped, it is characterized in that, composition of steel weight percent is: C≤0.20%, Mn0.80～1.70%, Si≤0.55%, P≤0.020%, S≤0.020%, Nb 0.010～～0.070%, Ni 0.30～0.90%, B 0.0003～0.0080%, and surplus is Fe and trace impurity.In smelting process, control gas content in steel: [N]≤40ppm, [O]≤60ppm.Its feature is to add in composition micro-B element, and needs the nitrogen, the oxygen level that keep lower, and production control difficulty is large; For guaranteeing good deoxidation effect, need to use aluminium deoxidation simultaneously, to the protection cast of casting process, require high.Owing to having added a certain amount of nickel, increase production cost in addition, and caused operation of rolling scale on surface to remove difficult problem.
Patent of invention CN102021475B discloses a kind of hot-rolled H-shaped steel for low temperature-resisting structure and manufacture method thereof, relate to a kind of low temperature resistant H shaped steel and manufacture method thereof, the chemical component weight per-cent % of steel is C 0.12～0.22, Si 0.10～0.40, Mn 1.1～1.50, P≤0.025, S≤0.025, Nb 0.02～0.05; All the other are iron and trace impurity.It is characterized in that rolling deformation need adopt heavy reduction cogging, heavy reduction rate finish to gauge, requiring to realize is 30%～40% at last 2 percentage pass reductions of finish to gauge, last pass deflection is controlled at 60%～70%.Mill capacity is had relatively high expectations.
Summary of the invention
Problem for the high low temperature toughness hot rolled H-shaped steel of low-alloy high-strength in composition and the smelting operation of rolling, the object of the present invention is to provide a kind of cost is relatively cheap, the relatively simple low-alloy high-strength of production technique has favorable low-temperature impact toughness hot rolling H steel and manufacture method thereof.
To achieve these goals, the present invention has adopted following technical scheme:
A kind of have the hot rolled H-shaped of favorable low-temperature impact toughness, consist of the following composition by mass percentage: C 0.05～0.18%, Si 0.15～0.40%, and Mn 1.0～1.50%, and V 0.010～0.050%, Nb 0.015～0.050%, Ti 0.005～0.025%, Al≤0.035%, P≤0.020%, S≤0.015%, all the other are Fe and inevitable impurity.
The above-mentioned hot rolled H-shaped manufacture method with favorable low-temperature impact toughness, comprises converter or electrosmelting operation, LF refining procedure, continuous casting working procedure and hot-rolled process successively, wherein:
In described converter or electrosmelting operation, that according to steel grades, designs need to be adjusted to 0.010～0.050wt% by the content of V in molten steel when tapping;
In described LF refining procedure, that according to steel grades, designs need to be adjusted to 0.005%～0.025wt% by the content of Ti in molten steel.
In above-mentioned manufacture method, as a kind of preferred implementation, in described converter or electrosmelting operation, when tapping is to 3/4 time, the content that adopts VN alloy to adjust V in molten steel is adjusted to 0.010～0.050wt%.
Above-mentioned manufacturer's ratio juris is mainly: the disperse oxide that (1) forms after utilizing on the one hand titanium to process in steel disperses steel medium sulphide content, can reduce the harm of sulfide to steel performance; The titanium oxide of disperse and nitride can stop steel billet in the AUSTENITE GRAIN COARSENING of heat-processed on the other hand, are conducive to obtain the stocking product that crystal grain is tiny.(2) utilize VN alloy alloying, can increase the nitrogen content in steel, in stocking process of cooling, be conducive to promote the carbonitride nanoparticle of V to be separated out, stop growing up of ferrite crystal grain, final refinement stocking tissue, improves low temperature impact properties.
In above-mentioned manufacture method, as a kind of preferred implementation, in described LF refining procedure, in adjusting molten steel before Ti content, by Control for Oxygen Content in molten steel below 60ppm.
In above-mentioned manufacture method, as a kind of preferred implementation, the continuously cast bloom obtaining at described continuous casting working procedure is nearly terminal different parison or rectangular bloom.
In above-mentioned manufacture method, as a kind of preferred implementation, in described hot-rolled process, the continuously cast bloom first described continuous casting working procedure being obtained was 1200～1280 ℃ of soaking 2.0～3.5 hours; Then carry out hot rolling and control 1/3 temperature≤880 ℃, place, finish to gauge H section steel flange outside; Finally the H shaped steel after hot rolling is naturally cooled to room temperature.
The H shaped steel of manufacturing according to the inventive method, can meet the requirement that low-alloy high-strength hot rolls H shaped steel high/low-temperature impact toughness, its yield strength >=400MPa, tensile strength >=480MPa, unit elongation >=30%, AkV impact of collision merit >=200J under-40 ℃ of conditions, AkV impact of collision merit >=109J under-60 ℃ of conditions.
Compared with prior art, the present invention has following beneficial effect:
The present invention does not need to add the Ni element that cost compare is high and controls the larger B element of difficulty; do not need strictly to control nitrogen in steel content; can whether determine with Al deoxidation and whether adopt full guard cast according to concrete production technique situation to there is with low cost and the simple feature of technique.The finished product manufactured is hot rolled H-shaped has good low-temperature impact toughness, and 1/3 place-40, a edge of a wing ℃ impact of collision merit is greater than 201J ,-60 ℃ of impact of collision merits are greater than 109J.
Embodiment
To describe low-alloy high-strength of the present invention in detail and there is the hot rolled H-shaped and manufacture method of good low-temperature toughness by embodiment below.
Hot rolled H-shaped manufacture method provided by the invention is specific as follows: adopt top and bottom combined blown converter after the mixture melting of molten iron, steel scrap or molten iron and steel scrap, to tap, wherein in tapping, to 3/4 o'clock, in molten steel, add VN alloy, the V in molten steel is adjusted to the 0.010～0.050wt% that accounts for molten steel gross weight; After converter tapping, enter LF refining station, before LF refining, by silicomanganese and Si-Ca-Ba, adjust Oxygen Content in Liquid Steel so that [O] lower than 60ppm(such as oxygen level is 58ppm, 55ppm, 50ppm etc.), then feeding titanium wire, to make Ti content in molten steel be 0.005～0.025wt%, then carry out LF refining, in refining process, first fully stir and make yellowish-white slag, and according to the result of a sample analysis, carry out trimming, before LF refining departures, keep the little argon gas amount of top of the slag fine motion to stir 10min above (being more than soft blow argon 10min, such as soft argon blowing time is 10-15min); By continuous casting mode, make near-net-shape Hot Metal in Beam Blank subsequently, continuous casting adopts half protection cast, the weak cold pattern of two cold employings, and tundish adopts low-carbon (LC) alkaline covering agent, and the casting billet surface obtaining is without web crack defect; Then strand is rolled into H shaped steel after (such as 2.2h, 2.5h, 2.8h or 3.2h) in 2.0～3.5 hours 1200～1280 ℃ of (such as 1210 ℃, 1230 ℃, 1250 ℃ or 1270 ℃) soaking, control 1/3 temperature≤880, place ℃ (such as 830 ℃, 850 ℃, 860 ℃ or 870 ℃), finish to gauge H section steel flange outside, roll rear finished product H shaped steel at cold bed naturally cooling, finally obtain according to H shaped steel of the present invention, adopt the surface imperfection such as stocking surface flawless, non-oxidation iron sheet that aforesaid method obtains are pressed into.NM operation in above manufacture method, all adopts the conventional prior art in this area.The H shaped steel that adopts aforesaid method to obtain consists of the following composition by mass percentage: C 0.05～0.18%, Si 0.15～0.40%, Mn 1.0～1.50%, V 0.010～0.050%, and Nb 0.015～0.050%, and Ti 0.005～0.025%, Al≤0.035%, P≤0.020%, S≤0.015%, all the other are Fe and inevitable impurity.
Enumerate three embodiment that adopt above-mentioned production technique to manufacture H shaped steel below, the Chemical Composition in Cast Billet that these three embodiment obtain is referring to table 1, and concrete technology parameter is in Table 2, and the end properties obtaining is referring to table 3.These embodiment are just for illustrational object, but not intention limits the scope of the invention.
(surplus is Fe and inevitable impurity to the chemical composition of the strand that three embodiment of table 1 obtain, wt%)
| Example | C | Si | Mn | P | S | V | Nb | Al | Ti |
| 1 | 0.07 | 0.25 | 1.33 | 0.013 | 0.004 | 0.034 | 0.030 | 0.007 | 0.015 |
| 2 | 0.13 | 0.18 | 1.40 | 0.014 | 0.003 | 0.020 | 0.037 | 0.007 | 0.005 |
| 3 | 0.10 | 0.21 | 1.37 | 0.015 | 0.007 | 0.018 | 0.036 | 0.004 | 0.007 |
The concrete technology parameter of three embodiment of table 2
The performance of the finished product H shaped steel of three embodiment of table 3
AkV impact of collision merit in table 3 is the impact of collision merit at 1/3 place, the edge of a wing of H shaped steel.
Adopt the performance measurement method of the H shaped steel that manufacture method of the present invention obtains as follows:
The measuring method reference standard GB GB/T2975 of yield strength, tensile strength, unit elongation.
The measuring method reference standard GB GB/T229 of the impact of collision merit at 1/3 place, the edge of a wing.
Above embodiment is the unrestricted technical scheme of the present invention in order to explanation only, although the present invention is had been described in detail with reference to above-described embodiment, those of ordinary skill in the art is to be understood that, still can modify or be equal to replacement the present invention, and not departing from any modification or partial replacement of the spirit and scope of the present invention, it all should be encompassed in the middle of claim scope of the present invention.
Claims (6)
1. one kind has the hot rolled H-shaped of favorable low-temperature impact toughness, it is characterized in that, consist of the following composition by mass percentage: C 0.05～0.18%, Si 0.15～0.40%, Mn 1.0～1.50%, V 0.010～0.050%, and Nb 0.015～0.050%, and Ti 0.005～0.025%, Al≤0.035%, P≤0.020%, S≤0.015%, all the other are Fe and inevitable impurity.
2. hot rolled H-shaped manufacture method described in claim 1, is characterized in that, comprises successively converter or electrosmelting operation, LF refining procedure, continuous casting working procedure and hot-rolled process, wherein:
In described converter or electrosmelting operation, that according to steel grades, designs need to be adjusted to 0.010～0.050wt% by the content of V in molten steel when tapping;
In described LF refining procedure, that according to steel grades, designs need to be adjusted to 0.005%～0.025wt% by the content of Ti in molten steel.
3. manufacture method according to claim 2, is characterized in that, in described converter or electrosmelting operation, when tapping is to 3/4 time, adopts VN alloy to adjust content to the 0.010～0.050wt% of V in molten steel.
4. manufacture method according to claim 2, is characterized in that, in described LF refining procedure, in adjusting molten steel before Ti content, by Control for Oxygen Content in molten steel below 60ppm.
5. manufacture method according to claim 2, is characterized in that, the continuously cast bloom that described continuous casting working procedure obtains is nearly terminal different parison or rectangular bloom.
6. manufacture method according to claim 2, is characterized in that, in described hot-rolled process, the continuously cast bloom first described continuous casting working procedure being obtained was 1200～1280 ℃ of soaking 2.0～3.5 hours; Then carry out hot rolling and control 1/3 temperature≤880 ℃, place, finish to gauge H section steel flange outside; Finally the H shaped steel after hot rolling is naturally cooled to room temperature.
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| CN103938079A (en) * | 2014-05-16 | 2014-07-23 | 莱芜钢铁集团有限公司 | Low-temperature resistant hot rolling H section bar with low compression ratio and super-thick specification and production method thereof |
| CN103966507A (en) * | 2014-05-09 | 2014-08-06 | 莱芜钢铁集团有限公司 | Extra-thick low-temperature-resistant hot-rolled H-shaped steel with yield strength of 275MPa and production method thereof |
| CN104018073A (en) * | 2014-06-19 | 2014-09-03 | 马钢(集团)控股有限公司 | Low-temperature toughness resistant H-shaped steel and production process thereof |
| CN104073717A (en) * | 2014-06-19 | 2014-10-01 | 马钢(集团)控股有限公司 | H-shaped steel as well as application and production method of H-shaped steel |
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| CN104018073A (en) * | 2014-06-19 | 2014-09-03 | 马钢(集团)控股有限公司 | Low-temperature toughness resistant H-shaped steel and production process thereof |
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| CN104846277A (en) * | 2015-06-12 | 2015-08-19 | 武汉钢铁(集团)公司 | Construction steel with yield strength more than or equal to 460 MPa and lamellar tearing resistant property and manufacturing method of construction steel |
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| JP7098828B2 (en) | 2018-05-16 | 2022-07-11 | 山東鋼鉄股▲ふん▼有限公司 | Hot-rolled high toughness and low temperature resistant H-shaped steel with yield strength of 460 Mpa or more and its manufacturing method |
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| CN111349853B (en) * | 2020-03-02 | 2021-08-10 | 河北津西钢铁集团股份有限公司 | Rolling method for hot-rolled H-shaped steel by microalloy treatment |
| WO2022022040A1 (en) | 2020-07-31 | 2022-02-03 | 山东钢铁股份有限公司 | Low temperature-resistant hot-rolled h-type steel for 355mpa marine engineering and preparation method therefor |
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