CN101942616A - Bainite steel plate with high elongation, high strength and low carbon and production method thereof - Google Patents
Bainite steel plate with high elongation, high strength and low carbon and production method thereof Download PDFInfo
- Publication number
- CN101942616A CN101942616A CN 201010283882 CN201010283882A CN101942616A CN 101942616 A CN101942616 A CN 101942616A CN 201010283882 CN201010283882 CN 201010283882 CN 201010283882 A CN201010283882 A CN 201010283882A CN 101942616 A CN101942616 A CN 101942616A
- Authority
- CN
- China
- Prior art keywords
- steel plate
- temperature
- rolling
- elongation
- high strength
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Images
Abstract
The invention discloses a bainite steel plate with high elongation, high strength and low carbon and a production method thereof. The production method can produce the steel plates with high elongation, high strength and good low-temperature toughness and welding performance, wherein the elongation is more than or equal to 20% and the yield strength is more than or equal to 1100 MPa. The steel plate comprises the following chemical compositions in percentage by mass: 0.06-0.18% of C, 0.55-1.7% of Si, 1.1-1.7% of Mn, more than or equal to 0.007% of P, more than or equal to 0.006% of S, more than or equal to 0.0040% of N, 0.02-0.06% of Nb, 0.25-0.4% of Mo, 0.01-0.02% of Ti, 0.3-0.5% of Cr, 0.3-0.8% of Ni, 0.3-0.8% of Cu, 0.025-0.05% of V, and 0.0005-0.0015% of B, optionally 0.015-0.02% of ALs, and the balance Fe and inevitable impurities. The microstructure of the steel plate is a multiphase structure and contains bainite structure, martensite structure, a small amount of residual austenite structure and carbide with dispersedly distributed Nb, V, Ti and others elements at the same time. The method for producing the bainite steel plate with high elongation, high strength and low carbon comprises the following steps of preparation of materials, converter or smelting in electric furnace, external refining, continuous casting, reheating of slabs, controlled rolling, controlled cooling, and heat treatment.
Description
Technical field
The present invention relates to a kind of high-elongation high strength low-carbon bainite steel plate and production method thereof, a kind of specifically have a high-intensity engineering machinery steel plate of high-elongation.Be particularly related to the production method of 1100MPa level high-elongation high tensile steel plate, based on martensite/bainite heterogeneous structure, and the performance residual austenite has improving the effect of steel flexible, design a kind of high-elongation high tensile steel plate that mainly contains bainite and martensite two phase composites, this steel plate has good welding property and good low-temperature toughness simultaneously, and has provided suitable production technique.
Background technology
Along with the development of industrial level, the manufacturing of the related various engineering machinery of industrial circles such as machinery, the energy, traffic, building and starting material, bridge, the vehicles, produce increasing to yield strength greater than the demand of the above steel grade of 800MPa level; The purpose that simultaneously to economize on resources, reduces production costs in order to reach has proposed higher performance requriements to the structured material in modern times, not only requires ferrous materials that high strength and good welding property are arranged, and has good plasticity and low-temperature flexibility.Traditional ferrous materials is to reach the purpose that improves intensity by improving carbon content and alloy total amount, but the consequence of doing has like this been sacrificed material welding performance and low-temperature flexibility exactly.
At present yield strength be the carbon content of other super-high strength steel of 1100MPa level substantially about 0.2%～0.4%, mainly be that unit elongation is lower based on tempered martensite, plasticity is relatively poor, brings certain influence to shaping.A kind of production technique of high tensile steel plate is disclosed in one piece " grain refining of low-alloy super-strength bainitic steel and toughness improve " of the 3rd interim publication of Chinese periodical " Acta Metallurgica Sinica " the 43rd volume, when its yield strength reaches 1100MPa when above, unit elongation will drop to about 15%, the carbon content of this steel grade is about 0.25% simultaneously, contain higher Mn, Si content simultaneously, therefore welding property is had very big influence.
In order to solve the shortcoming of above-mentioned steel, the present inventor is in conjunction with various strengthening mechanisms, by adding a certain amount of Mn, Si and microalloy element, design a kind of low-carbon bainite steel of high-elongation, the low-carbon bainite Carbon Content Of Steel is lower, the alloying element total content is less, the precipitation strength and the dispersion-strengthened action of the carbonitride of the crystal grain thinning effect of microalloy element and microalloy have been made full use of, thereby reduced carbon equivalent and welding crack sensitivity coefficient, thereby low-carbon bainite steel there is the good combination of high strength and welding property.Better according to the combination of strength and toughness of discovering this heterogeneous structure of bainite/martensite.The interpolation of microalloy element has improved hardening capacity simultaneously, and easier acquisition lower bainite and martensitic heterogeneous structure also contain the toughness that a certain amount of residual austenite is improved steel in the tissue simultaneously.Accurate in process of production controlled rolling and process of cooling, the mixed structure that the acquisition ratio is suitable, thus obtain premium propertiess such as high strength, high-elongation, high tenacity.
Summary of the invention
The purpose of this invention is to provide a kind of high-elongation 〉=20%, yield strength 〉=1100MPa, good low-temperature impact toughness-40 ℃, A
KV〉=30J has high strength, high-elongation, good low-temperature flexibility, good welding property and the bainitic steel and the production method thereof of processing characteristics.
The present invention realizes by following technical proposals:
The alloying element of high-elongation high-strength steel is formed mass percent; C:0.06%～0.18%, Si:0.55%～1.7%, Mn:1.1%～1.7%, P :≤0.007%, S :≤0.006%, N≤0.0040%, Nb:0.02%～0.06%, Mo:0.25%～0.4%, Ti:0.01%～0.02%, Cr:0.3%～0.5%, Ni:0.3%～0.8%, Cu:0.3%～0.8%, V:0.025-0.05%, B:0.0005-0.0015%, other are iron and inevitable impurity.Wherein B:0.005～0.0015, Ti:0.01%～0.02%, Mo:0.25%～0.4% are key feature.
Described high-elongation high strength low-carbon bainitic steel also contains Als:0.015%～0.02%.
Described high-elongation high strength low-carbon bainitic steel, it is characterized in that, the microtexture of described low-carbon bainite steel plate is a kind of heterogeneous structure, and bainite structure, martensitic stucture and a spot of residual austenite tissue are arranged, and contains Nb, the V of disperse distribution, the carbide of Ti element simultaneously.
Chemical Composition to high-elongation high tensile steel plate of the present invention is described in detail below.
C: carbon has very strong solution strengthening effect, but the present invention in order to obtain good welding property and low-temperature flexibility the carbon content that reduced, simultaneously for can obtain the low-carbon bainite lath, and carbon content is fixed on 0.06～0.18%.
Si:Si plays the solution strengthening effect, adds Si and can improve intensity, if improve the above stability that can increase residual austenite of the content to 1.5% of Si, improves the toughness of high-strength steel.Si suppresses separating out of cementite in addition, improves the effect of the tempering temperature of steel.
Mn:Mn plays solution strengthening and improves hardening capacity in steel effect, Mn/C is than the toughness that can improve steel in control, but Mn segregation easily in steel forms MnS and is mingled with, and therefore Mn is controlled at 1.1%～1.7%.
B:B can obviously suppress the forming core of ferrite at austenite grain boundary, can both obtain bainite structure in bigger cooling rate scope, and B has the intensive grain boundary segregation simultaneously, therefore will control B at 0.0005-0.0015%, otherwise can destroy the low-temperature flexibility of steel.
Mo:Mo can suppress ferritic transformation, reduces the bainite transformation temperature, and refinement is effectively organized, and adds 0.25%～0.4% Mo for obtaining bainite and martensitic heterogeneous structure.
Cr: add the intensity that Cr can significantly improve steel, too much can influence firm low-temperature flexibility but add.Therefore addition is fixed on 0.3%～0.5%.
Microalloy elements such as V, Ti, Nb: add these microalloy elements and can play effects such as crystal grain thinning and precipitation strength, solution strengthening.
The manufacture method of high-elongation high tensile steel plate of the present invention comprise get the raw materials ready, converter or electrosmelting, external refining, continuous casting, slab reheat, controlled rolling, controlled chilling, thermal treatment.
The processing method of described process furnace heating: Heating temperature is between 1200 ℃～1250 ℃, and heat-up time is between 1.5～2.5 hours.
The processing method of described controlled rolling: rolling technology is two stage rolling, and the fs start rolling temperature is 1150～1200 ℃, and the roughing final temperature is greater than 1040 ℃, and the accumulative total draft is greater than 60%, and last 3 percentage pass reductions are not less than 15%.The subordinate phase start rolling temperature is 900～950 ℃, and finishing temperature is 840～780 ℃, and percentage pass reduction is not less than 10%, and the accumulative total draft is greater than 60%.
The processing method of described controlled chilling: speed of cooling is 20～60 ℃/S, and final cooling temperature is 260～300 ℃;
Described thermal treatment process: quenching temperature is the critical temperature A that α-Fe changes γ-Fe into
C3+ 30～50 ℃, be 1.6～3.2min/mm * thickness of slab h+0～20min heat-up time; The tempering Heating temperature is 550～680 ℃, and soaking time is 2.5min/mm * thickness of slab h+30～50min, and the back water-cooled of coming out of the stove is to room temperature.Carry out low-temperaturetempering again one time, tempering temperature is 200～230 ℃, and soaking time is for being 2.5min/mm * thickness of slab h+30～50min, and the back air cooling of coming out of the stove is to room temperature.
Compared with prior art, the present invention has following advantage:
1. by optimizing the alloy ingredient design, control carbon content, reduced the interpolation total amount of alloying element, reduced carbon equivalent and welding crack sensitivity coefficient.
2. the cooperation of pricking cooling control technology by composition design and control, bainite, martensitic heterogeneous structure have been obtained, wherein contain the residual austenite tissue of some, and be Nb, V, Ti carbide that disperse distributes, make steel plate obtain good intensity, plasticity and low-temperature flexibility.
3. develop the steel plate of high-elongation, high strength, high tenacity, can significantly reduce the usage quantity of steel for engineering mechanism purpose, improve the life-span of engineering machinery, saved resource.The present invention is applicable to and produces the high-elongation high tensile steel plate.
Description of drawings
Fig. 1 rolls the transmission electron microscope picture of attitude tissue for the 1100MPa high-elongation high tensile steel plate of the embodiment of the invention 2.
Fig. 2 is the sem photograph after the 1100MPa high-elongation high tensile steel plate temper of the embodiment of the invention 2.
Embodiment
Below for a more detailed description to the present invention in conjunction with the accompanying drawings with embodiment.These embodiment only are the descriptions to best mode for carrying out the invention, scope of the present invention are not had any restriction.
Embodiment 1
Press Chemical Composition mass percent C:0.075%, Si:0.55%, Mn:1.7%, P:0.0069%, S:0.005%, Cr:0.4%, Mo:0.37%, Cu:0.8%, Nb:0.06%, Ti:0.02%, B:0.0015%, Ni:0.79%, V:0.036%, smelting molten steel in the vacuum electromagnetic induction furnace, and being cast into steel ingot, steel ingot thickness is 70mm, and steel billet is heated to 1230 ℃, be incubated 2 hours, be rolled on duo mill, start rolling temperature is 1160 ℃, to 1050 ℃ of finish to gauges, the accumulative total draft is 62%, treat that then temperature is rolling to 950 ℃ of beginning subordinate phase, finishing temperature is 800 ℃, and rolling the back thickness of slab is 10mm, treat that temperature is quenched to 300 ℃ after 780 ℃, air cooling is to room temperature; Reheat to 930 ℃ insulation 45 minutes is quenched to room temperature.Water-cooled is to room temperature after 1 hour 650 ℃ of tempering, and air cooling is to room temperature behind 220 ℃ of low-temperaturetempering 1h then, and having obtained yield strength is 1130MPa, and unit elongation is 20.5% ,-40 ℃ a low-temperature flexibility, A
KVThe steel plate of=35J.
Embodiment 2
Mass percent C:0.18% according to chemical composition, Si:1.55%, Mn:1.13%, P:0.0059%, S:0.005%, Cr:0.40%, Mo:0.35%, Cu:0.30%, Nb:0.059%, Ti:0.15%, B:0.001%, Ni:0.76%, V:0.05%, smelting molten steel in the vacuum electromagnetic induction furnace, and be cast into steel ingot, steel ingot thickness is 70mm, steel billet is heated to 1200 ℃ of insulations 2 hours, it is rolling to carry out the two-stage on duo mill, start rolling temperature is 1130 ℃, the fs finishing temperature is 1050 ℃, the accumulative total draft is 62%, treat that temperature is rolling to 950 ℃ of beginning subordinate phase, finishing temperature is 810 ℃, and the accumulative total draft is greater than 60%, and rolling the back thickness of slab is 10mm.Treat that temperature is quenched to 280 ℃ again to 760 ℃, air cooling is to room temperature then; Be warming up to 960 ℃ of insulations 45 minutes, be quenched to room temperature.Be heated to 630 ℃ of tempering after 1 hour water-cooled carry out low-temperaturetempering air cooling after 1 hour to room temperature at 220 ℃, acquisition intensity is 1150MPa, unit elongation is 20% ,-40 ℃ a low-temperature flexibility, A
KVThe steel plate of=30J.Fig. 1 rolls the transmission electron microscope picture of attitude tissue for the 1100MPa high-elongation high tensile steel plate of the embodiment of the invention 2; Fig. 2 is the sem photograph after the 1100MPa high-elongation high tensile steel plate temper of the embodiment of the invention 2; Contain very thin ferrite bainite by accompanying drawing 1 in the attitude tissue with regard to rolling as can be seen, lath substructure width is about 150nm.
Embodiment 3
Mass percent C:0.15% according to chemical composition, Si:1.0%, Mn:1.3%, P:0.004%, S:0.003%, Cr:0.36%, Mo:0.4%, Cu:0.30%, Nb:0.04%, Ti:0.20%, B:0.0015%, Ni:0.7%, V:0.05%, smelting molten steel in the vacuum electromagnetic induction furnace, and be cast into steel ingot, steel ingot thickness is 70mm, steel billet is heated to 1200 ℃ of insulations 2 hours, it is rolling to carry out the two-stage on duo mill, start rolling temperature is 1160 ℃, the fs finishing temperature is 1040 ℃, the accumulative total draft is 62%, treat that temperature is rolling to 950 ℃ of beginning subordinate phase, finishing temperature is 820 ℃, and the accumulative total draft is greater than 60%, and rolling the back thickness of slab is 10mm.Treat that temperature is quenched to 280 ℃ again to 780 ℃, air cooling is to room temperature; Be warming up to 940 ℃ of insulations 45 minutes, be quenched to room temperature.Be warming up to 630 ℃ of tempering after 1 hour water-cooled carry out low-temperaturetempering air cooling after 1 hour to room temperature at 200 ℃, acquisition intensity is 1100MPa, unit elongation is 21% ,-40 ℃ a low-temperature flexibility, A
KVThe steel plate of=37J.
With the high-strength steel sheet with high-elongation of said method production, compare with other high strength steel of same intensity level good low-temperature flexibility is arranged, good welding performance. Can satisfy the need of production of the industries such as engineering machinery, structural steel.
Claims (4)
1. high-elongation high strength low-carbon bainite steel plate, it is characterized in that, the composition and the weight percent content of described high-elongation high strength low-carbon bainite steel plate are: C:0.06%～0.18%, Si:0.55%～1.7%, Mn:1.1%～1.7%, P :≤0.007%, S :≤0.006%, N≤0.0040%, Nb:0.02%～0.06%, Mo:0.25%～0.4%, Ti:0.01%～0.02%, Cr:0.3%～0.5%, Ni:0.3%～0.8%, Cu:0.3%～0.8%, V:0.025-0.05%, B:0.0005%-0.0015%, other are iron and inevitable impurity.
2. a kind of high-elongation high strength low-carbon bainite steel plate according to claim 1 is characterized in that described high-elongation high strength low-carbon bainitic steel also contains Als:0.015%～0.02%.
3. a kind of high-elongation high strength low-carbon bainite steel plate according to claim 1 and 2, it is characterized in that, the microtexture of described low-carbon bainite steel plate is a kind of heterogeneous structure, bainite structure, martensitic stucture and a spot of residual austenite tissue are arranged, contain Nb, the V of disperse distribution, the carbide of Ti element simultaneously.
4. the production method of a high-elongation high strength low-carbon bainite steel plate, comprise get the raw materials ready, converter or electrosmelting, external refining, continuous casting, slab reheat, controlled rolling, controlled chilling, thermal treatment is characterized in that:
The slab reheat temperature of described slab reheat is 1200 ℃～1250 ℃, and be 1.5～2.5 hours heat-up time;
The rolling technology of described controlled rolling is two stage rolling, comprise rolling and rolling two stages of non-recrystallization district of recrystallization zone, described recrystallization zone rolling sequence, start rolling temperature 〉=1150 ℃, final temperature＞1040 ℃, and last continuous 3 percentage pass reductions＞15%, recrystallization zone rolling sequence accumulative total draft＞60%; The rolling start rolling temperature in non-recrystallization district of described controlled rolling is 900～950 ℃, 840～780 ℃ of finishing temperatures, and percentage pass reduction 〉=10%, non-recrystallization district accumulative total draft＞60%;
The cold temperature of opening of described controlled chilling is controlled at 800～760 ℃, is cooled to 260～300 ℃ with the speed of cooling of 20 ℃/s～80 ℃/s, and air cooling is to room temperature again;
Described thermal treatment comprises that quenching temperature is the critical temperature A that α-Fe changes γ-Fe into
C3+ 30～50 ℃, soaking time is 1.6～3.2min/mm * thickness of slab h+10～20min, and the back water-cooled of coming out of the stove is to room temperature; The tempering Heating temperature is 550～680 ℃, and soaking time is 2.5min/mm * thickness of slab h+30～50min, and the back water-cooled of coming out of the stove is to room temperature; Carry out low-temperaturetempering again one time, tempering temperature is 200～230 ℃, and soaking time is 2.5min/mm * thickness of slab h+30～50min, and the back air cooling of coming out of the stove is to room temperature.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201010283882A CN101942616B (en) | 2010-09-15 | 2010-09-15 | Bainite steel plate with high elongation, high strength and low carbon and production method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201010283882A CN101942616B (en) | 2010-09-15 | 2010-09-15 | Bainite steel plate with high elongation, high strength and low carbon and production method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN101942616A true CN101942616A (en) | 2011-01-12 |
| CN101942616B CN101942616B (en) | 2012-10-03 |
Family
ID=43434818
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201010283882A Expired - Fee Related CN101942616B (en) | 2010-09-15 | 2010-09-15 | Bainite steel plate with high elongation, high strength and low carbon and production method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN101942616B (en) |
Cited By (18)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102230143A (en) * | 2011-06-07 | 2011-11-02 | 南京钢铁股份有限公司 | High-toughness pipeline steel produced on basis of steekle mill and production process thereof |
| CN102691017A (en) * | 2012-03-27 | 2012-09-26 | 北京科技大学 | Low-cost wear resistant steel plate with hardness of NM550 and manufacturing method thereof |
| CN102953000A (en) * | 2011-08-19 | 2013-03-06 | 鞍钢股份有限公司 | Ultrahigh-strength steel plate and its manufacturing method |
| CN103882335A (en) * | 2012-12-21 | 2014-06-25 | 鞍钢股份有限公司 | Hot-rolled high-strength steel with yield strength of 800 MPa and production method thereof |
| CN104278216A (en) * | 2014-10-15 | 2015-01-14 | 山东钢铁股份有限公司 | Steel plate with thickness of larger than 60mm and yield strength of 690MPa and preparation method of steel plate |
| CN104946977A (en) * | 2015-05-28 | 2015-09-30 | 武汉钢铁(集团)公司 | Low temperature-resistant high strength anchor bar steel and production method thereof |
| WO2015143932A1 (en) * | 2014-03-25 | 2015-10-01 | 宝山钢铁股份有限公司 | Steel plate with yield strength at 890mpa level and low welding crack sensitivity and manufacturing method therefor |
| CN107385308A (en) * | 2017-06-28 | 2017-11-24 | 包头钢铁（集团）有限责任公司 | The cooling controlling and rolling controlling process of railway high-strength wearable shellfish horse heterogeneous structure rail |
| CN107779759A (en) * | 2016-08-26 | 2018-03-09 | 鞍钢股份有限公司 | The excellent boracic bainite rail of resistance for delayed fracture and its production method |
| CN108893734A (en) * | 2018-07-02 | 2018-11-27 | 中北大学 | A kind of surface of low-carbon steel duplex heat treatment and preparation method thereof |
| CN109500099A (en) * | 2018-09-27 | 2019-03-22 | 东南大学 | The experimental method that a kind of pair of mild steel DSIT rolling mill practice optimizes |
| CN110079734A (en) * | 2019-05-16 | 2019-08-02 | 武汉科技大学 | A kind of low-carbon bainite steel and preparation method thereof |
| CN110358970A (en) * | 2019-06-20 | 2019-10-22 | 天津大学 | 1100MPa grades of yield strength of welding structure bainite high-strength steel and preparation method thereof |
| WO2019223209A1 (en) * | 2018-05-24 | 2019-11-28 | 南京钢铁股份有限公司 | 500 mpa-grade engineering machinery steel and manufacturing method therefor |
| CN113025882A (en) * | 2021-02-04 | 2021-06-25 | 首钢集团有限公司 | Hot-base galvanized ferrite bainite high-strength steel plate and preparation method thereof |
| CN114000034A (en) * | 2021-11-02 | 2022-02-01 | 攀钢集团攀枝花钢铁研究院有限公司 | Low-yield-ratio high-strength bainite steel rail and production method thereof |
| CN114058945A (en) * | 2021-10-14 | 2022-02-18 | 首钢集团有限公司 | High-strength bainite wear-resistant steel plate and production method thereof |
| CN114525388A (en) * | 2022-02-21 | 2022-05-24 | 刘鑫 | Upper bainite lamellar structure steel and preparation method thereof |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6245290B1 (en) * | 1997-02-27 | 2001-06-12 | Exxonmobil Upstream Research Company | High-tensile-strength steel and method of manufacturing the same |
| CN1786246A (en) * | 2004-12-08 | 2006-06-14 | 鞍山钢铁集团公司 | High tensile strength high toughness low yield ratio bainite steel and its production method |
| CN101513695A (en) * | 2009-04-03 | 2009-08-26 | 燕山大学 | Welding method of Q420qE grade ultra-low-carbon bainite steel for bridges |
-
2010
- 2010-09-15 CN CN201010283882A patent/CN101942616B/en not_active Expired - Fee Related
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6245290B1 (en) * | 1997-02-27 | 2001-06-12 | Exxonmobil Upstream Research Company | High-tensile-strength steel and method of manufacturing the same |
| CN1786246A (en) * | 2004-12-08 | 2006-06-14 | 鞍山钢铁集团公司 | High tensile strength high toughness low yield ratio bainite steel and its production method |
| CN101513695A (en) * | 2009-04-03 | 2009-08-26 | 燕山大学 | Welding method of Q420qE grade ultra-low-carbon bainite steel for bridges |
Cited By (22)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102230143A (en) * | 2011-06-07 | 2011-11-02 | 南京钢铁股份有限公司 | High-toughness pipeline steel produced on basis of steekle mill and production process thereof |
| CN102953000A (en) * | 2011-08-19 | 2013-03-06 | 鞍钢股份有限公司 | Ultrahigh-strength steel plate and its manufacturing method |
| CN102953000B (en) * | 2011-08-19 | 2015-12-09 | 鞍钢股份有限公司 | A kind of ultrahigh-strength steel plates and manufacture method thereof |
| CN102691017A (en) * | 2012-03-27 | 2012-09-26 | 北京科技大学 | Low-cost wear resistant steel plate with hardness of NM550 and manufacturing method thereof |
| CN103882335A (en) * | 2012-12-21 | 2014-06-25 | 鞍钢股份有限公司 | Hot-rolled high-strength steel with yield strength of 800 MPa and production method thereof |
| WO2015143932A1 (en) * | 2014-03-25 | 2015-10-01 | 宝山钢铁股份有限公司 | Steel plate with yield strength at 890mpa level and low welding crack sensitivity and manufacturing method therefor |
| CN104278216A (en) * | 2014-10-15 | 2015-01-14 | 山东钢铁股份有限公司 | Steel plate with thickness of larger than 60mm and yield strength of 690MPa and preparation method of steel plate |
| CN104946977A (en) * | 2015-05-28 | 2015-09-30 | 武汉钢铁(集团)公司 | Low temperature-resistant high strength anchor bar steel and production method thereof |
| CN107779759B (en) * | 2016-08-26 | 2019-05-31 | 鞍钢股份有限公司 | The excellent boracic bainite rail of resistance for delayed fracture and its production method |
| CN107779759A (en) * | 2016-08-26 | 2018-03-09 | 鞍钢股份有限公司 | The excellent boracic bainite rail of resistance for delayed fracture and its production method |
| CN107385308A (en) * | 2017-06-28 | 2017-11-24 | 包头钢铁（集团）有限责任公司 | The cooling controlling and rolling controlling process of railway high-strength wearable shellfish horse heterogeneous structure rail |
| WO2019223209A1 (en) * | 2018-05-24 | 2019-11-28 | 南京钢铁股份有限公司 | 500 mpa-grade engineering machinery steel and manufacturing method therefor |
| CN108893734A (en) * | 2018-07-02 | 2018-11-27 | 中北大学 | A kind of surface of low-carbon steel duplex heat treatment and preparation method thereof |
| CN109500099A (en) * | 2018-09-27 | 2019-03-22 | 东南大学 | The experimental method that a kind of pair of mild steel DSIT rolling mill practice optimizes |
| CN110079734A (en) * | 2019-05-16 | 2019-08-02 | 武汉科技大学 | A kind of low-carbon bainite steel and preparation method thereof |
| CN110079734B (en) * | 2019-05-16 | 2020-06-26 | 武汉科技大学 | Low-carbon bainite steel and preparation method thereof |
| CN110358970A (en) * | 2019-06-20 | 2019-10-22 | 天津大学 | 1100MPa grades of yield strength of welding structure bainite high-strength steel and preparation method thereof |
| CN110358970B (en) * | 2019-06-20 | 2021-01-12 | 天津大学 | Welded structure bainite high-strength steel with yield strength of 1100MPa and preparation method thereof |
| CN113025882A (en) * | 2021-02-04 | 2021-06-25 | 首钢集团有限公司 | Hot-base galvanized ferrite bainite high-strength steel plate and preparation method thereof |
| CN114058945A (en) * | 2021-10-14 | 2022-02-18 | 首钢集团有限公司 | High-strength bainite wear-resistant steel plate and production method thereof |
| CN114000034A (en) * | 2021-11-02 | 2022-02-01 | 攀钢集团攀枝花钢铁研究院有限公司 | Low-yield-ratio high-strength bainite steel rail and production method thereof |
| CN114525388A (en) * | 2022-02-21 | 2022-05-24 | 刘鑫 | Upper bainite lamellar structure steel and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN101942616B (en) | 2012-10-03 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN101942616B (en) | Bainite steel plate with high elongation, high strength and low carbon and production method thereof | |
| CN101613828B (en) | Super-thick steel plate for low yield ratio buildings with 460 MPa grade yield strength and manufacturing method | |
| CN101487096B (en) | Low-alloy high-strength C-Mn-Al Q & P steel and method of manufacturing the same | |
| CN101985722B (en) | Pipeline steel plate with low yield ratio, fine grains and high strength and production method thereof | |
| WO2017219938A1 (en) | 980 mpa-grade hot-rolled ferritic bainite dual-phase steel and manufacturing method therefor | |
| CN101649420B (en) | Ultra-strength, high toughness and low yield ratio steel and steel plate and manufacturing method thereof | |
| KR102291866B1 (en) | Steel Plate with Yield Strength at 890MPa Level and Low Welding Crack Sensitivity and Manufacturing Method Therefor | |
| KR20210095156A (en) | 980 MPa grade cold-rolled steel sheet having a high hole expansion ratio and relatively high elongation and a method for manufacturing the same | |
| CN110484834B (en) | Cr and Mn alloyed TRIP steel and preparation method thereof | |
| CN107974636A (en) | A kind of high rigidity high-hardenability pre-hardening plastic die steel and preparation method thereof | |
| CN106811698A (en) | A kind of high strength steel plate and its manufacture method based on tissue precise controlling | |
| CN102534417A (en) | High-performance bridge weathering steel containing Mo and preparation method thereof | |
| CN102888565A (en) | High-strength steel plate with yield strength at 690MPa level and manufacture method thereof | |
| CN102719753B (en) | Low-yield-ratio high-strength steel plate and manufacturing method thereof | |
| CN103343281A (en) | Lamellar double-phase high-strength and high-toughness steel and preparation method thereof | |
| CN102943214A (en) | Automotive cold-rolled diaphragm spring steel and production method thereof | |
| CN103255341A (en) | High-strength and high-toughness hot-rolled wear-resistant steel and preparation method thereof | |
| CN103805851A (en) | Ultrahigh strength low-cost hot rolling Q and P (quenching and partitioning) steel and production method thereof | |
| CN102021483B (en) | Cold-rolled dual-phase steel plate with 1,200 MPa-level tensile strength and preparation method thereof | |
| CN101775561A (en) | Low-yield-ratio and high strength thick plate and preparation process thereof | |
| CN104278194A (en) | High-strength high-plasticity cold-rolled steel plate for automobiles and production method thereof | |
| CN105543676A (en) | Martensite-ferrite double-phase wear-resisting steel plate and preparing method thereof | |
| CN107747039A (en) | A kind of high reaming performance cold-rolled biphase steel and preparation method thereof | |
| CN104831185A (en) | Low-cost high-strength steel plate for engineering machinery, and production method thereof | |
| KR20150109461A (en) | High Strength Steel Sheet and Manufacturing Method Therefor |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| CF01 | Termination of patent right due to non-payment of annual fee | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20121003 Termination date: 20170915 |