CN1415775A - Method for producing superfine integrated ferrite grain and steel of retained austenite - Google Patents
Method for producing superfine integrated ferrite grain and steel of retained austenite Download PDFInfo
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- CN1415775A CN1415775A CN02147762A CN02147762A CN1415775A CN 1415775 A CN1415775 A CN 1415775A CN 02147762 A CN02147762 A CN 02147762A CN 02147762 A CN02147762 A CN 02147762A CN 1415775 A CN1415775 A CN 1415775A
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Abstract
A low-alloy steel containing superfine complete ferrite crystal grains and residual austenite is prepared through smelting in vacuum furnace, casting, heating, cogging rolling, final rolling, water cooling, winding, holding temp and cooling in air. It features that the fast multi-pass rolling with short intervals is performed to ensure superfine crystal grains, use proper amount Si and higher temp for final rolling can ensure complete ferrite, and lower-temp winding can result in residual austenite.
Description
[technical field]
The present invention relates to the production method of complete ferrite crystal grain of a kind of super-refinement and residual austenite steel, belong to low alloy steel and make the field.Here so-called " complete " crystal grain general reference intragranular defective such as dislocation etc. are less, intracrystalline foreign atom such as the less or purified relatively crystal grain of C atom.The less crystal grain of defective is the intensity height not only, and ductile-brittle transition temperature is low.The existence of residual austenite can suppress the germinating of crackle in the steel and expansion and then obviously improve the plasticity of steel.
[background technology]
Before the present invention, just like document ISIJ Int., Vol.41 (2001), No.3, people's such as the Seung Chui BAIK of the disclosed Korea S of pp.290-297 Pu item Iron And Steel Co., Ltd paper " alloying element is to cold rolling TRIP steel mechanical property and effects of phase transition ", the weak point that contains the existence of residual austenite steel of its research is to have added in the steel micro alloying element Nb, brings certain degree of difficulty for the smelting and the rolling technology of steel; Simultaneously, adopted cold rolling and annealing process, for hot-rolled steel sheet, production cost is higher relatively; In addition, organize grain-size not reach the level of the following super-refinement of 5 μ m, ferrite crystal grain does not have the requirement of completeization yet.Document ISIJ Int. and for example, Vol.40 (2000), No.9, the people's such as the Japanese Koh-ichi SUGIMOTO of JP Agencyof Shinshu University of pp.902-908 publication paper " the residual austenite characteristic and the tensile property of TRIP type bainitic steel ", its weak point is that equally production process also passed through cold rolling and annealing process, and ferrite grain size and form do not reach the level of super-refinement and completeization yet.
Except factors such as cost, technology and equipment exist be not enough to, the steel grade of producing under existing processing condition all is residual austenite or the super-refinement crystal grain that merely has some amount, and does not possess the tissue characteristics of residual austenite and grain ultrafining and even complete ferrite crystal grain simultaneously.
The production method that the purpose of this invention is to provide complete ferrite crystal grain of a kind of super-refinement and residual austenite steel, promptly providing does not have harshly to require, only just can obtain to have the feature of super-refinement, the production method of high strength, plasticity, high tenacity and the low yield strength ratio steel of the ferrite crystal grain of intact form and some amount residual austenite weave construction is arranged again by low production cost rolling equipment and technology controlling and process.
[summary of the invention]
In order to achieve the above object, the present invention has designed the production method of complete ferrite crystal grain of a kind of super-refinement and residual austenite steel, vacuum metling, split rolling method roll postcooling, batch, and it is characterized in that steel billet materials is cast into steel ingot after smelting, the chemical ingredients of steel (wt%) is C:0.10～0.20, Si:1.0～2.0, Mn:1.0～2.0, Al:0.005～0.03, P, S≤0.025, surplus are Fe and inevitably are mingled with; Steel rolling comprises split rolling method and two stages of controlled rolling and controlled cooling: 1170～1200 ℃ of the Heating temperatures of split rolling method technology, 1120～1150 ℃ of start rolling temperatures, 850～900 ℃ of finishing temperatures, rolling back air cooling; The cooling controlling and rolling controlling process process is earlier with the steel billet heating, and insulation is carried out multi-pass, come and gone rollingly fast, adopts water spray controlled chilling to coiling temperature, batches at last, insulation and air cooling.
The present invention is that a kind of silicomanganese is the production method of containing of ferrite crystal grain super-refinement and completeization of remaining body steel difficult to understand, and the raw material preparatory stage of control smelting quality and cogging roughing is a critical part of steel of the present invention.The production method of steel of the present invention mainly comprises two stages of moulding of smelting, cogging and controlled rolling and controlled cooling.
The production method of complete ferrite crystal grain of super-refinement of the present invention and residual austenite steel is characterized in that described cooling controlling and rolling controlling process, and concrete steps are:
(1) slab at first is heated to 1170～1200 ℃, soaking time 50～60min;
(2) start rolling temperature is 1120～1150 ℃, and finishing temperature is 850～900 ℃, and rolling back adopts water spray controlled chilling to coiling temperature, 10～20 ℃/s of rate of cooling;
(3) the deformation process employing is round rolling, and the deformation passage is 14～16 roads, and pass deformation is 13%～15%, and the deformation passage residence time is less than 0.3s;
(4) coiling temperature is 400～450 ℃, and soaking time is 50～60min, and air cooling is to room temperature subsequently.
C content is chosen in 0.10%～0.20% in the steel of the present invention, and is different fully by C content raising intensity meaning with traditional soft steel, but utilize the residual austenite volume fraction of the C acquisition requirement of some amount, and the intensity of steel is mainly obtained by grain ultrafining.Under existing manufacturing condition, C is less than 0.10%, and the residual austenite ratio is less, and quantity is below 5%; C is greater than 0.20%, and residual austenite quantity is more, more than 5%; Continue to increase C content and surpass 0.20%, residual austenite quantity increases limited.The residual austenite quantity of steel of the present invention has reached maximum 11.4%
Si content is chosen in 1.0%～2.0% in the steel of the present invention, is that simultaneously, Si can also promote the formation of ferrite full die because Si can increase residual austenite quantity on the one hand.So the effect of Si also is different from traditional low alloy steel fully among the present invention, not the intensity that improves steel for simple.Si does not directly increase the quantity of residual austenite, but by improving gathering or the concentration stability and the quantity that indirectly increase residual austenite of C in ferrite.Simultaneously, Si to ferritic cleaning action, promotes the formation of ferrite full die by self.Therefore, 1.0%～2.0% Si is the chemical ingredients basis that steel of the present invention obtains complete ferrite crystal grain.Si in steel of the present invention residual austenite is obtained and the formation of ferrite full die has dual function.
Mn content mainly increases the quantity of residual austenite for the characteristic of utilizing Mn to enlarge austenitic area, raising stabilization of austenite 1.0%～2.0% among the present invention.With regard to residual austenite quantity, the comprehensive action of Mn and C is better than the independent effect of C or Mn.Therefore, C, Si, Mn have the different separately mechanism of action to the formation of residual austenite; Higher relatively C, Si, Mn content are the chemical ingredients bases that remaining body difficult to understand forms.
Except chemical ingredients, with the formation of some amount residual austenite, ferrite crystal grain super-refinement and completeization in the steel of the inventive method production, the crucial effective control that also is each processing parameter of hot rolling.Hot rolling adopts cooling controlling and rolling controlling process to have following technical characterstic:
(1) finishing temperature of the inventive method is higher, is 850～900 ℃, and is higher more than 50 ℃ than the Ultrafine Grained Steel of routine, just in time is in the suitable rolling temperature scope of general milling train.And traditional Ultrafine Grained Steel adopts the low temperature heavy reduction rolling more, and its finishing temperature is lower than 820 ℃ or lower, has therefore strengthened rolling load, has not only increased the milling train burden, also is unfavorable for rolling technology control.And lower finishing temperature, owing to rolling load increases intragranular defective greatly, be unfavorable for the acquisition of full die equally.Therefore, higher finishing temperature is the technology basis that obtains complete ferrite crystal grain.
(2) method of the present invention adopt under the hot conditions, multi-pass, small deformation amount return toward formula rollingly fast, obviously be different from the low temperature heavy reduction rolling of conventional super-refinement steel.The rolling recrystallize repeatedly that helps deformation crystal grain in this high temperature recrystallization zone finally obtains the ultrafine-grained (UFG) microstructure of abundant refinement; The particularly important is, have only the extremely short timed interval between every time is rolling, slowed down growing up of recrystal grain to greatest extent.Little deformation quantity of high temperature and fast speed rolling are the technological factors that the steel of the inventive method production obtains two keys of super-refinement crystal grain.
(3) coiling temperature of steel has only 400～450 ℃ in the method for the present invention, is lower than the coiling temperature of conventional steel plate more than 550 ℃, and its purpose is to obtain the residual austenite of some amount.Lower coiling temperature is the main technique basis that the Can Yushi bodily form becomes.
(4) method process for cooling characteristics of the present invention are: rolling postcooling speed is 10～20 ℃/s, can avoid pearlitic formation.Pearlitic structure because the cementite in the perlite has consumed too much carbon atom, is unfavorable for the formation of residual austenite for what will avoid among the present invention.Simultaneously, speed of cooling can obtain bainite structure, and the formation of bainite structure helps in the steel austenitic residual at 10～20 ℃/s.So finish to gauge suitable speed of cooling later on is another important process basis that obtains the some amount residual austenite.
The production method of steel of the present invention has following outstanding advantage:
1. with regard to ferrite crystal grain super-refinement and completeization, present method need not to adopt at present the hot rolling low temperature heavy reduction rolling that rolling equipment ability and controlling of production process are had relatively high expectations, the small deformation amount and the quick rolling technique of high temperature recrystallize have only been adopted, both obtained the super-refinement of crystal grain, also guaranteed the integrity of ferrite crystal grain, thereby obtained than the more excellent weave construction of conventional super-refinement crystal grain steel.
2. with the steel of present method production, succinct C, Si, Mn composition are convenient to produce and are smelted and technological operation; Simultaneously, compare with cold rolling high-strength steel, the characteristic with the delivery of hot rolling attitude is simplified production technique.In addition, the steel that present method is produced does not contain specific alloy element and trace element, compares with Ultrafine Grained Steel with traditional Hi-Stren steel, and low production cost has the remarkable economic efficiency and the powerful market competitiveness.
3. present method has Technological adaptability and controlled strong advantage, the steel of producing with present method integrates high strength, high-ductility and high tenacity, both can alleviate the deadweight of various members, as the deadweight that alleviates auto parts is more than 20%, saved auto producer and made starting material, reduced the fuel consumption of autoist, and had higher impact resistance, the security and the safety of automobile are strengthened, brought bigger economic benefit and social benefit for manufacturing firm and user.
[embodiment]
Embodiment 1: adopt method of the present invention to produce the complete ferrite crystal grain residual austenite of super-refinement steel, smelt at vacuum oven earlier, be cast into the steel ingot of 50kg then, the chemical ingredients of steel (wt%) is C:0.19, Si:1.48, Mn:1.97, P:0.009, S:0.01, and surplus is Fe and inevitably is mingled with.Steel rolling is divided into split rolling method and two stages of controlled rolling and controlled cooling: 1200 ℃ of the Heating temperatures of split rolling method technology, and 1150 ℃ of start rolling temperatures, 880 ℃ of finishing temperatures are rolled the back air cooling, and the slab thickness of acquisition is 20mm, and length and width specifications are 400 * 100mm; 1200 ℃ of the Heating temperatures of cooling controlling and rolling controlling process, soaking time 60min, 1150 ℃ of start rolling temperatures, 880 ℃ of finishing temperatures, rolling pass is 15 roads, every time deflection is 15%, every time timed interval 0.25s, and rolling back control water spray speed of cooling is 10 ℃/s, under 450 ℃ temperature, batch, soaking time is 60min, and last air cooling is to room temperature, and the steel plate finished product thickness specification of acquisition is 2.5mm.The weave construction of steel is: ferrite+bainite+residual austenite+a small amount of martensite, wherein, ferrite is based on the full die form, and grain-size only is 3.0 μ m, the residual austenite volume fraction is 11.4%, and martensite is present in the residual austenite with the island form.The mechanical property of steel is: yield strength 560MPa, and tensile strength 775MPa, rate elongation remains on (δ
50) be 29% higher level, yield tensile ratio reduces to 0.72, and the low temperature ductile-brittle transition temperature is reduced to-60 ℃.
Present method has that production cost is low, Technological adaptability and controlled strong advantage, and the steel of being produced is suitable for making strut member, mine safety member, framework and low temperature oil and gas pipeline in bumper, the car door most.
Claims (2)
1. the production method of complete ferrite crystal grain of super-refinement and residual austenite steel, vacuum metling, split rolling method, roll postcooling, batch, it is characterized in that steel billet materials is cast into steel ingot after smelting, the chemical ingredients of steel (wt%) is C:0.10～0.20, Si:1.0～2.0, Mn:1.0～2.0, Al:0.005～0.03, P, S≤0.025, surplus is Fe and inevitably is mingled with; Steel rolling comprises split rolling method and two stages of controlled rolling and controlled cooling: 1170～1200 ℃ of the Heating temperatures of split rolling method technology, 1120～1150 ℃ of start rolling temperatures, 850～900 ℃ of finishing temperatures, rolling back air cooling; The cooling controlling and rolling controlling process process is earlier with the steel billet heating, and insulation is carried out multi-pass, come and gone rollingly fast, adopts water spray controlled chilling to coiling temperature, batches at last, insulation and air cooling.
2. according to the production method of claim 1, it is characterized in that described cooling controlling and rolling controlling process, concrete steps are:
(1) slab at first is heated to 1170～1200 ℃, soaking time 50～60min;
(2) start rolling temperature is 1120～1150 ℃, and finishing temperature is 850～900 ℃, and rolling back adopts water spray controlled chilling to coiling temperature, 10～20 ℃/s of rate of cooling;
(3) the deformation process employing is round rolling, and the deformation passage is 14～16 roads, and pass deformation is 13%～15%, and the deformation passage residence time is less than 0.3s;
(4) coiling temperature is 400～450 ℃, and soaking time is 50～60min, and air cooling is to room temperature subsequently.
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| CNB021477620A CN1151301C (en) | 2002-11-29 | 2002-11-29 | Method for producing superfine integrated ferrite grain and steel of retained austenite |
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| CNB021477620A CN1151301C (en) | 2002-11-29 | 2002-11-29 | Method for producing superfine integrated ferrite grain and steel of retained austenite |
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| CN1415775A true CN1415775A (en) | 2003-05-07 |
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Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1306055C (en) * | 2004-06-10 | 2007-03-21 | 东北大学 | Production process of high-strength cold heading rivet and screw steel |
| CN100584964C (en) * | 2007-07-23 | 2010-01-27 | 宝山钢铁股份有限公司 | Manufacturing method of metallic plate having superfine crystal continuous gradient tissue and metallic plate |
| CN103805838A (en) * | 2012-11-15 | 2014-05-21 | 宝山钢铁股份有限公司 | High formability super strength cold-roll steel sheet and manufacture method thereof |
| CN104328336A (en) * | 2014-11-06 | 2015-02-04 | 东北大学 | Submicron austenite-strengthened high-strength steel sheet and preparation method thereof |
| CN109182697A (en) * | 2018-08-30 | 2019-01-11 | 上海应用技术大学 | A kind of sheet metal surface intensifying method |
| CN113378446A (en) * | 2021-06-09 | 2021-09-10 | 辽宁石油化工大学 | Titanium alloy beta-phase high-temperature solid solution structure simulation method based on Leeb's theory |
| CN114289523A (en) * | 2021-12-28 | 2022-04-08 | 华北理工大学 | Method for refining austenite of carbon steel |
| CN115181897A (en) * | 2021-04-02 | 2022-10-14 | 宝山钢铁股份有限公司 | 1280 MPa-level low-carbon low-alloy ultrahigh-strength dual-phase steel and rapid thermal treatment manufacturing method |
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2002
- 2002-11-29 CN CNB021477620A patent/CN1151301C/en not_active Expired - Fee Related
Cited By (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1306055C (en) * | 2004-06-10 | 2007-03-21 | 东北大学 | Production process of high-strength cold heading rivet and screw steel |
| CN100584964C (en) * | 2007-07-23 | 2010-01-27 | 宝山钢铁股份有限公司 | Manufacturing method of metallic plate having superfine crystal continuous gradient tissue and metallic plate |
| CN103805838A (en) * | 2012-11-15 | 2014-05-21 | 宝山钢铁股份有限公司 | High formability super strength cold-roll steel sheet and manufacture method thereof |
| US10287659B2 (en) | 2012-11-15 | 2019-05-14 | Baoshan Iron & Steel Co., Ltd. | High-formability and super-strength cold-rolled steel sheet |
| CN104328336A (en) * | 2014-11-06 | 2015-02-04 | 东北大学 | Submicron austenite-strengthened high-strength steel sheet and preparation method thereof |
| CN109182697A (en) * | 2018-08-30 | 2019-01-11 | 上海应用技术大学 | A kind of sheet metal surface intensifying method |
| CN115181897A (en) * | 2021-04-02 | 2022-10-14 | 宝山钢铁股份有限公司 | 1280 MPa-level low-carbon low-alloy ultrahigh-strength dual-phase steel and rapid thermal treatment manufacturing method |
| CN115181897B (en) * | 2021-04-02 | 2023-07-11 | 宝山钢铁股份有限公司 | 1280 MPa-level low-carbon low-alloy ultra-high strength dual-phase steel and rapid heat treatment manufacturing method |
| CN113378446A (en) * | 2021-06-09 | 2021-09-10 | 辽宁石油化工大学 | Titanium alloy beta-phase high-temperature solid solution structure simulation method based on Leeb's theory |
| CN113378446B (en) * | 2021-06-09 | 2023-04-25 | 辽宁石油化工大学 | Titanium alloy beta-phase high-temperature solid solution tissue simulation method based on Phyllanthus theory |
| CN114289523A (en) * | 2021-12-28 | 2022-04-08 | 华北理工大学 | Method for refining austenite of carbon steel |
| CN114289523B (en) * | 2021-12-28 | 2023-09-22 | 华北理工大学 | Method for refining carbon steel austenite |
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| CN1151301C (en) | 2004-05-26 |
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