CN1840723A - Superhigh strength steel plate with yield strength more than 1100Mpa and method for producing same - Google Patents
Superhigh strength steel plate with yield strength more than 1100Mpa and method for producing same Download PDFInfo
- Publication number
- CN1840723A CN1840723A CN 200510024756 CN200510024756A CN1840723A CN 1840723 A CN1840723 A CN 1840723A CN 200510024756 CN200510024756 CN 200510024756 CN 200510024756 A CN200510024756 A CN 200510024756A CN 1840723 A CN1840723 A CN 1840723A
- Authority
- CN
- China
- Prior art keywords
- steel
- steel plate
- temperature
- rolling
- 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
Abstract
The invention provides a super-strength steel plate comprising the following constituents (by weight percent): C 0.10-0.20%, Si<=0.6%, Mn 0.5-2.5%, Al <=0.03%, N 0.001-0.006%, B 0-0.0025%, Ca 0-0.006%, P<=0.015%, S<=0.005%, Ni 0.2-1.2%, Cr 0-0.8%, Cu 0-0.5% and Mo 0-0.6%, Ti 0.01-0.03%, V 0-0.1%, Nb 0.01-0.1%, balancing Fe and unavoidable foreign substance.
Description
Technical field
The present invention relates to the manufacture method of ferrous materials, particularly above ultrahigh-strength steel plates of yield strength 1100MPa and manufacture method thereof.
Background technology
The manufacture method of the relevant ultrahigh-strength steel plates of yield strength more than 700MPa has formed multinomial patent in the world, among the patent JP 60121219 and JP 89025371 as Sumitomo Metal Industries, silicone content is≤0.015% in employing tempering process production high-strength steel and the steel, nickel content is 1.00%～3.50%, chromium content 0.40%～1.20%;
The patent WO 200039352 of Exxonmobil Upstream Res company application is a kind of Cryogenic Steel, with the good high-strength steel of method production low-temperature flexibility than low carbon content (0.03%～0.12%) and high nickel content (being not less than 1.0%), its adopt lower rate of cooling (10 ℃/s), its tensile strength can only reach more than the 830MPa.
In the low-alloy super-strength steel plate patent WO 9905335 of Exxonmobil Upstream Res and Nippon Steel's cooperation application, though adopt the not tempering of after hot rolling, only quenching, in its composition carbon content low be 0.05～0.10%.
In the high tensile steel plate patent of Sumitomo Metal Industries (JP 59159932), employing direct quenching after hot rolling adds the tempered method, and in its composition design, the scope of the titanium of employing is low to be 0.003～0.010%.
In " production of high-strength steel plate " patent (GB 2132225) of NIPPON KOKAN KK, control the speed of direct quenching after the hot rolling by control discharge, the thickness of producing is greater than 25mm, its composition requires manganese (0.40～1.20%), chromium (0.20～1.50%), and needs the sour molten aluminium of control.
In the patent (98812446.7) of " the ultra-high strength Ausaged steels " of Exxon Mobil with excellent low-temperature flexibility, it need be in the district's controlled rolling of austenite non-recrystallization, the hot rolling postcooling is to Ms～Ms+100 ℃, do not adopt tempering, tensile strength has only more than the 830MPa, and its normal temperature tissue is made up of the micro-lamellar structure based on the lath of fine-grained martensitic and close grain lower bainite of 2～10% (volume ratio) residual austenite thin film layer and about 90～98% (volume ratios).
Unite in the Chinese patent 98802878.6 of " high-tensile-strength steel and production method thereof " of application in Exxon Mobil and Sumitomo Metal Industries, the carbon content of steel plate is 0.02～0.10%, and manganese is 0.2～2.5%, more than the tensile strength 900MPa.
In the Dillimax that Weldox1100 is serial and Dillingen, Germany the is produced series high-strength steel that Sweden SSAB company produces, the method for employing high alumina (total aluminium scope 〉=0.020%, aluminium in kind is about 0.055%) dependence aluminium crystal grain thinning improves the obdurability of steel.
In the patent (98812439.4) of " the ultrahigh-strength steel " of Exxon Mobil with excellent low-temperature flexibility, be quenched to after the hot rolling and be lower than about Ms+200 ℃, quench rates is 10～40 ℃/s, and not only its quench rates is lower, and does not adopt press quenching after the hot rolling.
By above contrast patent as can be known, there are following one or more deficiencies in these patents: 1. added the expensive alloy element of high level, the steel product cost height.Nickel as adding among JP 60121219 and the JP 89025371 is 1.00%～3.50%, chromium content 0.40%～1.20%; Nickel content is not less than 1.0% among the WO 200039352; 2. complex process, the process cost height.Low as carbon content among the patent WO 9905335 is 0.05～0.10%, carbon 0.04%～0.16% among the patent GB 2132225, carbon content is 0.02～0.10% in the patent 98802878.6, and decarburization time was long when low excessively carbon content caused steel-making, and smelting production efficiency is low; In the patent 98812439.4,98812446.7, not only its quench rates is lower, and does not adopt press quenching after the hot rolling, has reduced production efficiency.In the Dillimax series high-strength steel that Weldox1100 series that Sweden SSAB company produces and Dillingen, Germany are produced, adopt high aluminium content (being not less than 0.02%), following some shortcomings are arranged: high aluminum steel molten steel is the easy dross in the mouth of a river when cast, brings the anti-material of ladle nozzle into molten steel easily; Too much aluminium can cause that alumina inclusion significantly increases in the steel, needs the long vacuum outgas time impel inclusion floating; The tiny precipitate of the aluminium nitride of aluminium crystal grain thinning dissolves when steel plate welds fully, thereby makes welded heat affecting zone crystal grain thick.3. the armor plate strength rank is low.As patent WO 200039352 and patent 98812446.7, tensile strength can only reach more than the 830MPa, and patent 98802878.6 tensile strength can only reach more than the 900MPa.
Because the development of industries such as heavy load truck, engineering machinery improves constantly the load-carrying of vehicle and the requirement of physical strength, also require to alleviate deadweight simultaneously, require therefore to adopt that cost is lower, the intensity rank good ultrahigh-strength steel plates of high and low temperature impelling strength more.
Summary of the invention
The object of the present invention is to provide a kind of manufacture method with ultrahigh-strength steel plates of good low-temperature toughness, by rational design of alloy and technology controlling and process, direct quenching and tempering process reach the yield strength of steel plate more than 1100MPa after the employing hot rolling, its low-temperature impact toughness reaches E level above (ballistic work that promptly satisfies～40 ℃ is not less than 27J), and has good plasticity and weldability.
For achieving the above object, the invention provides the above ultrahigh-strength steel plates of a kind of yield strength 1100MPa, its composition is (weight percent):
C 0.10％～0.20％；
Si≤0.6％；
Mn 0.5％～2.5％；
Al≤0.03％；
N 0.001％～0.006％；
B 0％～0.0025％；
Ca 0％～0.006％；
P≤0.015％；
S≤0.005％；
More than among Ni 0.2%～1.2%, Cr 0%～0.8%, Cu 0%～0.5% and the Mo 0%～0.6% one or more;
More than among Ti 0.01%～0.03%, V 0%～0.1% and the Nb 0.01%～0.1% one or more;
Yu Tie and inevitable impurity.
In order to achieve the above object, the present invention also provides a kind of method of making the above ultrahigh-strength steel plates of yield strength 1100MPa, and wherein said steel plate has the chemical constitution of steel in the claim 1, and described method comprises the steps:
1) steel billet is heated to 1100～1250 ℃;
2) in the temperature range of recrystallize can take place in austenite, adopt one or more passages, described billet rolling is become steel plate, total draft is not less than 50%;
3) at austenite recrystallize not taking place promptly is lower than the Tnr temperature but is higher than Ar
3In the temperature range of transition point, adopt one or more passages, above-mentioned steel plate rolling is become the steel plate of final thickness, total draft is not less than 50%, and finishing temperature is between 860～920 ℃;
4) with the rate of cooling that is not less than about 20 ℃/s with described steel plate press quenching, to being lower than about 200～400 ℃ quenching final temperature;
5) steel plate after quenching is carried out tempering to improve toughness, tempering temperature is 350～750 ℃.
Further, in whole course of hot rolling, allow not adopt the commentaries on classics steel rolling.
Further again, in whole course of hot rolling, allow to use one or many to change steel rolling.
Further, in hot rolling at the end, carry out water-cooled after allowing advanced line space cold, the final temperature scope of air cooling is: 700～950 ℃.
Carbon (C): 0.10% to 0.20%
The height of carbon content has determined the intensity rank of steel plate largely, becomes the requisite element of strengthening phase in the steel such as martensite, bainite because carbon is austenitic transformation.Carbon is the topmost element of decision carbon equivalent size, and carbon equivalent is the important indicator that influences the intensity of steel and weldability etc.The span of control of this patent carbon is 0.10% to 0.20%, be based on the coupling of the obdurability of steel, carbon is lower than does not have enough carbide and solid solution carbon in 0.10% steel, thereby is unfavorable for forming the intensity that enough strengthening phases obtain steel plate in the austenitic transformation process; Otherwise carbon content is higher than at 0.20% o'clock, and then the plasticity of steel and toughness reduce, and weldability is variation also.
Silicon (Si): be not more than 0.6%
Silicon is little to the stability influence of supercooled austenite.Silicon plays the solution strengthening effect in steel, and content can suppress separating out of carbide, raising toughness more for a long time.Add silicon in the steel and can improve purity of steel and deoxidation.
Manganese (Mn): 0.5% to 2.5%
Manganese is the principal element that improves bainitic steel hardening capacity, reduces the transformation temperature of bainitic steel, the thinning microstructure substructure, and the degree of supersaturation of carbon helps the raising of intensity in the increase bainite ferrite.
Aluminium (Al): be not more than 0.03%
Usually the effect of aluminium in high-strength steel comprises: the same desoxydatoin that rises with silicomanganese; The effect of aluminium crystal grain thinning.Only contain a spot of aluminium in the steel of the present invention or do not contain aluminium (≤0.03%), mainly be because: the higher desoxydatoin that fully can substitution of Al of the content of silicon and manganese in the steel on the one hand; The titanium that in steel, adds trace, alloying element such as titanium and copper, niobium and cooperate measure such as technology controlling and process to play the effect of crystal grain thinning jointly like this, and also little titanium is handled the weldability of raising steel very favourable; On the other hand, many defectives (above stating) are arranged if aluminium content is too high.
Nitrogen (N): 0.001% to 0.006%
In adding the steel of titanium, an amount of nitrogen and titanium form titanium nitride, thisly easily second help strengthening matrix mutually what high temperature was separated out, and improve the welding property of steel plate.If but nitrogen is higher than 0.0060%, the solubility product of nitrogen and titanium is higher, just forms titanium nitride when high temperature in the steel, and such titanium nitride particles is thick and be square or rectangle, seriously damages the plasticity and the toughness of steel.
Boron (B): 0% to 0.0025%
The preferable range of boron is 0.0010% to 0.0020%.Boron can improve the hardening capacity and the weldability of steel in steel.
Calcium (Ca): 0% to 0.006%
An amount of calcium can change the shape of sulfide, alleviates the disadvantageous effect of sulphur.When having excessive titanium in the steel, titanium can close with sulfuration and form titanium sulfide or carbon titanium sulfide, so whether the adding of calcium can be decided according to the add-on of titanium and the content of sulphur.
Nickel (Ni): 0.2% to 1.2%
Nickel can improve the toughness of steel, the steel that especially has low-temperature flexibility to require.Adding nickel can increase bainite or martensite border residual austenite film, improves plasticity and toughness.And help the structure refinement after the tempering.
Copper (Cu): 0% to 0.5%
The effect of copper is solution strengthening, amount more for a long time can be after the proper temperature tempering secondary hardening, improve intensity.Not high for the general content of non-hardened steel.
Chromium (Cr): 0% to 0.8%
Chromium can make perlite separate with the bainite transformation curve, in, under the condition of low-carbon (LC), can obviously move to right proeutectoid ferrite and perlite begin to separate out line, but instead of part manganese and molybdenum.Thinning microstructure reduces ductile-brittle transition temperature.It is bigger than manganese that chromium reduces the Bs/Ms value, helps reducing the welding crack tendency.Chromium and manganese element cooperate, and can obtain higher hardenability and full hardening deepness, improve the mechanical property of steel.Chromium is littler than the segregation of manganese tendency, helps reducing the core segregation of steel, raising mechanical property homogeneity with chromium for manganese.
Molybdenum (Mo): 0% to 0.6%
Adding molybdenum mainly is in order to improve intensity.
Titanium (Ti): 0.01% to 0.03%
Titanium can form the compound of titanium with nitrogen, carbon and sulphur.The content of titanium in the control steel makes that titanium is main to form the titanium nitride of small and dispersed, remaining titanium and sulphur, carbon formation compound with nitrification.Therefore, an amount of titanium has not only been fixed the nitrogen in the steel but also has been fixed sulphur and the part carbon in the steel.But titanium content is too high, and not only titanium nitride is thick, and the minimizing of the carbon of solid solution in the steel, is unfavorable for obtaining good obdurability coupling.Change matrix, and improve the weldability of steel plate significantly.
Niobium (Nb): 0.01% to 0.1%; Vanadium (V): 0% to 0.1%
Niobium and vanadium are strong carbon and nitrogen compound forming element.Because add an amount of titanium in the steel, the formation temperature of titanium and nitrogen is higher,, make the main carburet of niobium and vanadium therefore by controlling the content of titanium, nitrogen.Vanadium carbide and niobium carbide to separate out temperature low than titanium nitride and titanium carbide, when hot rolling and the hot rolling technology coupling, separating out thinning microstructure and improving intensity and toughness by control niobium carbide and vanadium carbide.
Phosphorus (P) and sulphur (S): be not higher than 0.015% and 0.005%
Sulphur forms the plastic occluded foreignsubstance manganese sulfide with chemical combination such as manganese in steel, especially unfavorable to the horizontal plastic property and the toughness of steel, so the content of sulphur should be low as much as possible.Phosphorus also is the harmful element in the steel, the plasticity of grievous injury steel plate and toughness.
The present invention adopts the relatively more moderate carbon content (0.10% to 0.20%) of other patent, this carbon content neither very low neither be very high, can satisfy the requirement of steel making working procedure, can guarantee that also steel plate is follow-up to the welding performance demands.Wherein the Nb content that adds in carbon content and the steel plate guarantees as far as possible by correlation formula, for example presses solubility product formula Lg[Nb] [C]=2.96-7510/T, the T that calculates is less than 1523K (1250 ℃); If add V, then the total content of V and the Nb T that also will guarantee to calculate by similar formula is less than 1523K, this is that all carbonitrides dissolve fully in the time of will guaranteeing the steel billet reheat, so that the effect of each element is given full play in precipitation strength in follow-up rolling and process of cooling.The element ti and the N content that add guarantee Ti/N 〉=3.42 as far as possible, allow Ti be completely fixed N, make Nb can form enough NbC and strengthen; Allow calcium to handle in the steel, also allow to handle without calcium.Handle if carry out calcium, then Ca of Jia Ruing and S content guarantee Ca/S 〉=0.5～2.0 as far as possible, make complete nodularization of sulfide or approximate fusiform, improve steel plate transverse impact performance.If it is fashionable that the Cu in the steel, Ni, Cr, Mo add simultaneously, can not be simultaneously near the upper limit or lower limit, the purpose of doing like this is proof strength and carbon equivalent.To the suitable control of the above element, purpose is with lower cost of alloy, accurate composition proportion, and simple steel-making, rolling and thermal treatment process obtain over-all properties such as mechanics, welding preferably.
Steel billet is heated to sufficiently high temperature (1100～1250 ℃) and makes the austenite structure homogenizing, and the carbide of niobium, vanadium and titanium etc. in the steel is fully dissolved, and the nitride of niobium, vanadium and titanium etc. also has and is partly dissolved to stop growing up of original austenite grains.
In the temperature range of recrystallize can take place in austenite, adopt one or more passages to be rolled into steel billet, total draft must not be lower than 50%.Along with the reduction of rolling carrying out and temperature, the microalloy element of solid solution in steel plays a part retardance austenite dynamic recrystallization, and the purpose that recrystallize reaches refinement takes place the austenite of deformation repeatedly.In the operation of rolling, allow to adopt one or many to change steel to improve the horizontal plastic property and the toughness of finished product steel plate.
Be lower than austenite generation recrystallize but be higher than in the temperature range of Ar3 transition point, adopt one or more passages and allow to adopt one or many to change steel, above-mentioned steel plate rolling is become the steel plate of final thickness, and total draft is not less than 50%, and finishing temperature is between 860～920 ℃.In the operation of rolling, recrystallize does not take place in austenite, and forms the extended austenite.Have a large amount of dislocations in extended ausforming band, solid solution atoms such as niobium, vanadium and titanium are owing to deformation induced separating out is carbide and carbonitride.
After the finish to gauge of non-recrystallization district, the tissue of steel is made up of the austenite of distortion.Steel plate after the finish to gauge with the rate of cooling direct quenching that is not less than about 20 ℃/s to obtain bainite, martensite or bainite and martensitic (may lingering section austenite) mixed structure.Again through 350～750 ℃ of temper to improve the toughness of steel.
The present invention has the easy to implement and control of composition design, the characteristics that technology controlling and process is simple and easy to do, owing to adopt direct quenching, thereby the rolling cycle is short.Tempered back realizes that steel plate had both had the intensity of superelevation, had good low-temperature flexibility again.
Embodiment
Specific embodiments of the invention are referring to table 1, table 2, table 3.
The chemical ingredients of table 1 embodiment (%)
| Example | C | Si | Mn | P | S | Ni | Cr | Mo | Nb | V | Ti | B | Al | N | Cu | Ca |
| 1 | 0.10 | 0.30 | 1.20 | 0.015 | 0.004 | 0.7 | 0.4 | 0.3 | 0.10 | 0.03 | 0.015 | 0 | 0.004 | 0.002 | 0 | 0 |
| 2 | 0.14 | 0.25 | 0.98 | 0.006 | 0.005 | 0.9 | 0.5 | 0.2 | 0.01 | 0.05 | 0.025 | 0.0018 | 0.015 | 0.002 | 0.2 | 0 |
| 3 | 0.15 | 0.60 | 0.80 | 0.008 | 0.0025 | 0.5 | 0.8 | 0.6 | 0.05 | 0 | 0.025 | 0.0016 | 0.009 | 0.002 | 0.4 | 0 |
| 4 | 0.13 | 0.03 | 2.50 | 0.010 | 0.003 | 0.2 | 0 | 0.5 | 0.08 | 0.02 | 0.010 | 0.0025 | 0.030 | 0.001 | 0.5 | 0.002 |
| 5 | 0.20 | 0.20 | 0.50 | 0.006 | 0.0015 | 1.2 | 0.4 | 0 | 0.04 | 0.10 | 0.03 | 0.0015 | 0.020 | 0.006 | 0.3 | 0 |
The processing parameter of table 2 embodiment
| Example | Reheat temperature ℃ | Finishing temperature ℃ | Quench rates ℃/s | Tempering temperature ℃ |
| 1 | 1250 | 900 | 50 | 600 |
| 2 | 1150 | 900 | 45 | 650 |
| 3 | 1250 | 950 | 45 | 350 |
| 4 | 1100 | 850 | 20 | 450 |
| 5 | 1200 | 900 | 40 | 750 |
The mechanical property of table 3 embodiment
| Example | Thickness mm | Yield strength MPa | Tensile strength MPa | Unit elongation % | Akv J | |
| -20℃ | -40℃ | |||||
| 1 | 16 | 1127 | 1210 | 13 | 36 | 32 |
| 2 | 25 | 1120 | 1283 | 13 | 42 | 36 |
| 3 | 16 | 1147 | 1177 | 14 | 40 | 32 |
| 4 | 16 | 1198 | 1276 | 15 | 47 | 38 |
| 5 | 16 | 1167 | 1250 | 14 | 45 | 36 |
By table as seen, the yield strength of five embodiment is all greater than 1100MPa, and unit elongation is more than or equal to 13%, and-40 ℃ ballistic work has reached the requirement of 1100E level all greater than 32J.
Claims (7)
1. the above ultrahigh-strength steel plates of yield strength 1100MPa, its composition is (weight percent):
C 0.10％～0.20％；
Si≤0.6％；
Mn 0.5％～2.5％；
Al≤0.03％；
N 0.001％～0.006％；
B 0％～0.0025％；
Ca 0％～0.006％；
P≤0.015％；
S≤0.005％；
More than among Ni 0.2%～1.2%, Cr 0%～0.8%, Cu 0%～0.5% and the Mo 0%～0.6% one or more;
More than among Ti 0.01%～0.03%, V 0%～0.1% and the Nb 0.01%～0.1% one or more;
Yu Tie and inevitable impurity.
2. steel plate as claimed in claim 1 is characterized in that, the content of Ti and N is Ti/N 〉=3.42.
3. steel plate as claimed in claim 1 is characterized in that, the content of Ca and S is Ca/S 〉=0.5～2.0.
4. make the method for the above ultrahigh-strength steel plates of yield strength 1100MPa, wherein said steel plate has the chemical constitution of steel in the claim 1, and described method comprises the steps:
1) steel billet is heated to 1100～1250 ℃;
2) in the temperature range of recrystallize can take place in austenite, adopt one or more passages, described billet rolling is become steel plate, total draft is not less than 50%;
3) at austenite recrystallize not taking place promptly is lower than the Tnr temperature but is higher than Ar
3In the temperature range of transition point, adopt one or more passages, above-mentioned steel plate rolling is become the steel plate of final thickness, total draft is not less than 50%, and finishing temperature is between 860～920 ℃;
4) with the rate of cooling that is not less than about 20 ℃/s with described steel plate press quenching, to being lower than about 200～400 ℃ quenching final temperature;
5) steel plate after quenching is carried out tempering to improve toughness, tempering temperature is 350～750 ℃.
5. method as claimed in claim 4 is characterized in that, in whole course of hot rolling, allows not adopt the commentaries on classics steel rolling.
6. method as claimed in claim 4 is characterized in that, in whole course of hot rolling, allows to adopt one or many to change steel rolling.
7. method as claimed in claim 4 is characterized in that, the course of hot rolling hot rolling is at the end carried out water-cooled after allowing advanced line space cold, and the final temperature scope of air cooling is: 700～950 ℃.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB2005100247560A CN100372962C (en) | 2005-03-30 | 2005-03-30 | Superhigh strength steel plate with yield strength more than 1100Mpa and method for producing same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB2005100247560A CN100372962C (en) | 2005-03-30 | 2005-03-30 | Superhigh strength steel plate with yield strength more than 1100Mpa and method for producing same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1840723A true CN1840723A (en) | 2006-10-04 |
| CN100372962C CN100372962C (en) | 2008-03-05 |
Family
ID=37029914
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CNB2005100247560A Active CN100372962C (en) | 2005-03-30 | 2005-03-30 | Superhigh strength steel plate with yield strength more than 1100Mpa and method for producing same |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN100372962C (en) |
Cited By (56)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101451212B (en) * | 2007-12-03 | 2011-04-06 | 舞阳钢铁有限责任公司 | High intensity steel plate and preparation method thereof |
| CN101660100B (en) * | 2008-08-27 | 2011-05-11 | 宝山钢铁股份有限公司 | Super-thick quenched and tempered steel plate with good obdurability matching, and manufacturing method thereof |
| CN101487101B (en) * | 2008-01-17 | 2011-05-11 | 宝山钢铁股份有限公司 | Steel for CT70 grade coiled tubing and method of manufacturing the same |
| CN102071359A (en) * | 2011-01-27 | 2011-05-25 | 河北钢铁股份有限公司唐山分公司 | Ultra-high-intensity automobile structural steel and production method thereof |
| CN101376945B (en) * | 2007-08-28 | 2011-06-15 | 宝山钢铁股份有限公司 | 2000MPa grade superhigh intensity high tenacity steel plate and manufacturing method thereof |
| CN102181788A (en) * | 2011-04-18 | 2011-09-14 | 首钢总公司 | Ultra-high strength steel with yield strength level of 1100MPa-1200MPa and production method of steel |
| CN102191442A (en) * | 2011-05-13 | 2011-09-21 | 宝鸡石油机械有限责任公司 | Steel for marine riser flange of marine deepwater drilling and manufacturing method of marine riser flange |
| CN101565800B (en) * | 2008-04-22 | 2011-11-23 | 宝山钢铁股份有限公司 | Steel plate with obdurability and strong plasticity and manufacturing method thereof |
| CN102317493A (en) * | 2009-02-12 | 2012-01-11 | 日本发条株式会社 | Steel for high-strength vehicle stabilizer with excellent corrosion resistance and low-temperature toughness, and process for the production of same, and stabilizer |
| CN102337482A (en) * | 2010-07-23 | 2012-02-01 | 宝山钢铁股份有限公司 | Bainite high strength and toughness steel plate with yield strength of 900 MPa and its manufacture method |
| CN102605252A (en) * | 2012-03-30 | 2012-07-25 | 宝山钢铁股份有限公司 | Steel plate with yield strength grade of 1030MPa and manufacturing method thereof |
| CN102691010A (en) * | 2011-03-23 | 2012-09-26 | 宝山钢铁股份有限公司 | HT 960 steel plate with excellent plasticity and toughness and manufacture method thereof |
| CN102021492B (en) * | 2009-09-15 | 2012-11-28 | 鞍钢股份有限公司 | Low-carbon low-alloy abrasion-resistant steel and production method thereof |
| US8353992B2 (en) | 2006-11-07 | 2013-01-15 | Nippon Steel Corporation | High young's modulus steel plate and method of production of same |
| CN102899583A (en) * | 2012-09-11 | 2013-01-30 | 中昊创业高铁新技术开发有限公司 | High-performance steel material |
| CN102899584A (en) * | 2012-10-26 | 2013-01-30 | 江苏省沙钢钢铁研究院有限公司 | Method for reducing ductile-brittle transition temperature of martensitic high strength steel |
| CN102943204A (en) * | 2012-11-28 | 2013-02-27 | 东北大学 | Yield strength 1100MPa level engineering machinery non-quenched and tempered hot rolled strip and preparation method thereof |
| CN102953003A (en) * | 2012-11-19 | 2013-03-06 | 宝山钢铁股份有限公司 | Pipeline steel 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 |
| CN103014539A (en) * | 2011-09-26 | 2013-04-03 | 宝山钢铁股份有限公司 | High-strength and high-toughness steel plate with 700 Mpa-level yield strength and preparation method of steel plate |
| CN103014545A (en) * | 2011-09-26 | 2013-04-03 | 宝山钢铁股份有限公司 | High-strength steel plate with 900 Mpa-level yield strength and preparation method of steel plate |
| CN103451533A (en) * | 2013-09-12 | 2013-12-18 | 武汉钢铁(集团)公司 | Hot-rolled magnetic yoke steel with yield strength not less than 800Mpa and production method thereof |
| CN103882294A (en) * | 2014-03-04 | 2014-06-25 | 南京钢铁股份有限公司 | Ni-saving type low-temperature steel plate and preparation method thereof |
| US8802241B2 (en) | 2004-01-08 | 2014-08-12 | Nippon Steel & Sumitomo Metal Corporation | Steel sheet having high young's modulus, hot-dip galvanized steel sheet using the same, alloyed hot-dip galvanized steel sheet, steel pipe having high young's modulus, and methods for manufacturing the same |
| CN104651750A (en) * | 2015-03-12 | 2015-05-27 | 上海海隆石油钻具有限公司 | High-strength petroleum drill pipe body and heat treatment process thereof |
| CN105603323A (en) * | 2016-03-07 | 2016-05-25 | 舞阳钢铁有限责任公司 | Large-thickness high-strength high-toughness NM360 steel plate and production method thereof |
| CN105970108A (en) * | 2016-05-27 | 2016-09-28 | 江苏金基特钢有限公司 | Low-chromium-nickel heat resistant steel and heat treatment method thereof |
| CN106544590A (en) * | 2016-10-17 | 2017-03-29 | 江阴兴澄特种钢铁有限公司 | 1000MPa grade high ductilities high-performance uniformity easily welds super-thick steel plate and its manufacture method |
| US9683275B2 (en) | 2011-09-26 | 2017-06-20 | Baoshan Iron & Steel Co., Ltd. | Steel plate with low yield-tensile ratio and high toughness and method of manufacturing the same |
| CN107513669A (en) * | 2017-07-20 | 2017-12-26 | 首钢集团有限公司 | A kind of high-strength cold rolling square and rectangular pipe steel and its manufacture method |
| CN107557674A (en) * | 2016-06-30 | 2018-01-09 | 鞍钢股份有限公司 | A kind of concrete mixer tank steel plate and its production method |
| CN107675086A (en) * | 2017-11-15 | 2018-02-09 | 马鞍山钢铁股份有限公司 | A kind of 800MPa levels engineering truck hot-rolled structural steel and its production method |
| CN108165892A (en) * | 2017-11-23 | 2018-06-15 | 南阳汉冶特钢有限公司 | A kind of low-temperature pressure container 35-50mm thickness Q420R high-strength steel and its production method |
| CN108315671A (en) * | 2018-05-14 | 2018-07-24 | 东北大学 | 1000MPa grades of low yield strength ratio super-high strength steels of yield strength and preparation method thereof |
| CN108411210A (en) * | 2018-06-01 | 2018-08-17 | 东北大学 | A kind of deep-sea dynamic flexible standpipe acidproof super-high strength steel and preparation method thereof |
| CN108914006A (en) * | 2018-08-10 | 2018-11-30 | 武汉钢铁集团鄂城钢铁有限责任公司 | A kind of superhigh intensity hardened and tempered steel plate that thickness directional properties are excellent and its manufacturing method |
| CN109112264A (en) * | 2018-10-26 | 2019-01-01 | 山东钢铁集团日照有限公司 | The high tough medium plate of micro alloying element quenching and tempering type and its manufacturing method on a small quantity |
| CN109338214A (en) * | 2018-10-11 | 2019-02-15 | 石家庄钢铁有限责任公司 | The steel for rock drilling bits and its production method of high-strength and high ductility |
| CN109385570A (en) * | 2018-09-28 | 2019-02-26 | 宝山钢铁股份有限公司 | A kind of high strength steel plate and its manufacturing method |
| US10378073B2 (en) * | 2014-09-26 | 2019-08-13 | Baoshan Iron & Steel Co., Ltd. | High-toughness hot-rolling high-strength steel with yield strength of 800 MPa, and preparation method thereof |
| CN110317994A (en) * | 2018-03-30 | 2019-10-11 | 宝山钢铁股份有限公司 | A kind of high heat input welding unimach and its manufacturing method |
| CN111542638A (en) * | 2017-12-26 | 2020-08-14 | Posco公司 | Hot-rolled steel sheet, steel pipe, and component having excellent impact resistance, and method for producing same |
| CN111549300A (en) * | 2020-05-08 | 2020-08-18 | 包头钢铁（集团）有限责任公司 | Steel with yield strength of 800MPa for engineering machinery and preparation method thereof |
| CN111575609A (en) * | 2020-05-09 | 2020-08-25 | 包头钢铁（集团）有限责任公司 | Steel with high strength, good plasticity and toughness for engineering machinery and preparation method thereof |
| CN111876683A (en) * | 2020-07-31 | 2020-11-03 | 东北大学 | 1000MPa high-toughness steel for coal mine hydraulic support and preparation method thereof |
| CN112267064A (en) * | 2020-09-10 | 2021-01-26 | 邯郸钢铁集团有限责任公司 | Martensite high-temperature wear-resistant steel and production method thereof |
| CN113373374A (en) * | 2021-05-26 | 2021-09-10 | 武汉钢铁有限公司 | 1100 MPa-grade magnet yoke steel for manufacturing hydro-generator rotor and production method |
| CN113373372A (en) * | 2021-05-26 | 2021-09-10 | 武汉钢铁有限公司 | 1300 MPa-grade magnet yoke steel for manufacturing hydro-generator rotor and production method |
| CN113403532A (en) * | 2021-05-26 | 2021-09-17 | 武汉钢铁有限公司 | 1200 MPa-grade magnet yoke steel for manufacturing hydro-generator rotor and production method |
| CN113430451A (en) * | 2021-05-26 | 2021-09-24 | 武汉钢铁有限公司 | 1000 MPa-grade magnet yoke steel for manufacturing hydro-generator rotor and production method |
| CN113718172A (en) * | 2021-07-28 | 2021-11-30 | 唐山钢铁集团有限责任公司 | 1200 MPa-grade low-carbon martensite steel strip and production method thereof |
| CN114480970A (en) * | 2022-01-25 | 2022-05-13 | 上海大学 | High-strength high-toughness steel and preparation method and application thereof |
| CN114540715A (en) * | 2022-02-28 | 2022-05-27 | 衡阳华菱钢管有限公司 | Acid corrosion resistant steel, preparation method thereof and corrosion resistant pipe |
| CN115094346A (en) * | 2022-07-04 | 2022-09-23 | 宁波祥路中天新材料科技股份有限公司 | Hot rolled strip steel with tensile strength not lower than 1200MPa produced by TSR production line and method |
| CN115874116A (en) * | 2022-12-27 | 2023-03-31 | 北京理工大学 | Silicon-aluminum-free superfine bainitic steel and preparation method thereof |
| WO2023246941A1 (en) * | 2022-06-24 | 2023-12-28 | 宝山钢铁股份有限公司 | Automotive structural steel having a yield strength of ≥1000 mpa and manufacturing method therefor |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103649355B (en) | 2011-07-10 | 2016-08-17 | 塔塔钢铁艾默伊登有限责任公司 | Have the HAZ-of improvement soften repellence hot-rolled high-strength steel band and the method that produces described steel |
Family Cites Families (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS59100214A (en) * | 1982-11-29 | 1984-06-09 | Nippon Kokan Kk <Nkk> | Production of thick walled high tension steel |
| JPS59159932A (en) * | 1983-03-02 | 1984-09-10 | Sumitomo Metal Ind Ltd | Production of high tensile steel plate having excellent strength and toughness |
| JPS60121219A (en) * | 1983-12-05 | 1985-06-28 | Sumitomo Metal Ind Ltd | Production of tempered type high tension heavy-gage steel plate |
| JPH10237583A (en) * | 1997-02-27 | 1998-09-08 | Sumitomo Metal Ind Ltd | High tensile strength steel and its production |
| BR9811051A (en) * | 1997-07-28 | 2000-08-15 | Exxonmobil Upstream Res Co | Steel plate, and, process to prepare it |
| TW454040B (en) * | 1997-12-19 | 2001-09-11 | Exxon Production Research Co | Ultra-high strength ausaged steels with excellent cryogenic temperature toughness |
-
2005
- 2005-03-30 CN CNB2005100247560A patent/CN100372962C/en active Active
Cited By (84)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US8802241B2 (en) | 2004-01-08 | 2014-08-12 | Nippon Steel & Sumitomo Metal Corporation | Steel sheet having high young's modulus, hot-dip galvanized steel sheet using the same, alloyed hot-dip galvanized steel sheet, steel pipe having high young's modulus, and methods for manufacturing the same |
| US8353992B2 (en) | 2006-11-07 | 2013-01-15 | Nippon Steel Corporation | High young's modulus steel plate and method of production of same |
| CN101376945B (en) * | 2007-08-28 | 2011-06-15 | 宝山钢铁股份有限公司 | 2000MPa grade superhigh intensity high tenacity steel plate and manufacturing method thereof |
| CN101451212B (en) * | 2007-12-03 | 2011-04-06 | 舞阳钢铁有限责任公司 | High intensity steel plate and preparation method thereof |
| CN101487101B (en) * | 2008-01-17 | 2011-05-11 | 宝山钢铁股份有限公司 | Steel for CT70 grade coiled tubing and method of manufacturing the same |
| CN101565800B (en) * | 2008-04-22 | 2011-11-23 | 宝山钢铁股份有限公司 | Steel plate with obdurability and strong plasticity and manufacturing method thereof |
| CN101660100B (en) * | 2008-08-27 | 2011-05-11 | 宝山钢铁股份有限公司 | Super-thick quenched and tempered steel plate with good obdurability matching, and manufacturing method thereof |
| CN102317493B (en) * | 2009-02-12 | 2013-10-16 | 日本发条株式会社 | Steel for high-strength vehicle stabilizer with excellent corrosion resistance and low-temperature toughness, and process for the production of same, and stabilizer |
| CN102317493A (en) * | 2009-02-12 | 2012-01-11 | 日本发条株式会社 | Steel for high-strength vehicle stabilizer with excellent corrosion resistance and low-temperature toughness, and process for the production of same, and stabilizer |
| CN102021492B (en) * | 2009-09-15 | 2012-11-28 | 鞍钢股份有限公司 | Low-carbon low-alloy abrasion-resistant steel and production method thereof |
| CN102337482A (en) * | 2010-07-23 | 2012-02-01 | 宝山钢铁股份有限公司 | Bainite high strength and toughness steel plate with yield strength of 900 MPa and its manufacture method |
| CN102337482B (en) * | 2010-07-23 | 2013-11-20 | 宝山钢铁股份有限公司 | Bainite high strength and toughness steel plate with yield strength of 900 MPa and manufacture method thereof |
| CN102071359B (en) * | 2011-01-27 | 2013-03-27 | 河北钢铁股份有限公司唐山分公司 | Ultra-high-intensity automobile structural steel and production method thereof |
| CN102071359A (en) * | 2011-01-27 | 2011-05-25 | 河北钢铁股份有限公司唐山分公司 | Ultra-high-intensity automobile structural steel and production method thereof |
| CN102691010B (en) * | 2011-03-23 | 2014-10-01 | 宝山钢铁股份有限公司 | HT 960 steel plate with excellent plasticity and toughness and manufacture method thereof |
| CN102691010A (en) * | 2011-03-23 | 2012-09-26 | 宝山钢铁股份有限公司 | HT 960 steel plate with excellent plasticity and toughness and manufacture method thereof |
| CN102181788A (en) * | 2011-04-18 | 2011-09-14 | 首钢总公司 | Ultra-high strength steel with yield strength level of 1100MPa-1200MPa and production method of steel |
| CN102191442A (en) * | 2011-05-13 | 2011-09-21 | 宝鸡石油机械有限责任公司 | Steel for marine riser flange of marine deepwater drilling and manufacturing method of marine riser flange |
| CN102191442B (en) * | 2011-05-13 | 2012-10-10 | 宝鸡石油机械有限责任公司 | Steel for marine riser flange of marine deepwater drilling and manufacturing method of marine riser flange |
| 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 |
| CN102953000A (en) * | 2011-08-19 | 2013-03-06 | 鞍钢股份有限公司 | Ultrahigh-strength steel plate and its manufacturing method |
| EP2762594A4 (en) * | 2011-09-26 | 2015-08-12 | Baoshan Iron & Steel | High-strength and high-toughness steel plate with yield strength being 700 mpa and manufacturing method thereof |
| CN103014545B (en) * | 2011-09-26 | 2014-12-24 | 宝山钢铁股份有限公司 | High-strength steel plate with 900 Mpa-level yield strength and preparation method of steel plate |
| WO2013044641A1 (en) * | 2011-09-26 | 2013-04-04 | 宝山钢铁股份有限公司 | High-strength and high-toughness steel plate with yield strength being 700 mpa and manufacturing method thereof |
| CN103014539A (en) * | 2011-09-26 | 2013-04-03 | 宝山钢铁股份有限公司 | High-strength and high-toughness steel plate with 700 Mpa-level yield strength and preparation method of steel plate |
| RU2593567C2 (en) * | 2011-09-26 | 2016-08-10 | Баошан Айрон Энд Стил Ко., Лтд. | High-strength steel strip with high impact strength and yield point of 700 mpa and its production method |
| US9683275B2 (en) | 2011-09-26 | 2017-06-20 | Baoshan Iron & Steel Co., Ltd. | Steel plate with low yield-tensile ratio and high toughness and method of manufacturing the same |
| CN103014545A (en) * | 2011-09-26 | 2013-04-03 | 宝山钢铁股份有限公司 | High-strength steel plate with 900 Mpa-level yield strength and preparation method of steel plate |
| CN103014539B (en) * | 2011-09-26 | 2015-10-28 | 宝山钢铁股份有限公司 | A kind of yield strength 700MPa grade high-strength high-tenacity steel plate and manufacture method thereof |
| US9771639B2 (en) | 2011-09-26 | 2017-09-26 | Baoshan Iron & Steel Co., Ltd. | High-strength and high-toughness steel plate with yield strength of 700 MPa and method of manufacturing the same |
| CN102605252A (en) * | 2012-03-30 | 2012-07-25 | 宝山钢铁股份有限公司 | Steel plate with yield strength grade of 1030MPa and manufacturing method thereof |
| CN102899583A (en) * | 2012-09-11 | 2013-01-30 | 中昊创业高铁新技术开发有限公司 | High-performance steel material |
| CN102899584B (en) * | 2012-10-26 | 2014-07-02 | 江苏省沙钢钢铁研究院有限公司 | Method for reducing ductile-brittle transition temperature of martensitic high strength steel |
| CN102899584A (en) * | 2012-10-26 | 2013-01-30 | 江苏省沙钢钢铁研究院有限公司 | Method for reducing ductile-brittle transition temperature of martensitic high strength steel |
| CN102953003A (en) * | 2012-11-19 | 2013-03-06 | 宝山钢铁股份有限公司 | Pipeline steel and manufacturing method thereof |
| CN102943204A (en) * | 2012-11-28 | 2013-02-27 | 东北大学 | Yield strength 1100MPa level engineering machinery non-quenched and tempered hot rolled strip and preparation method thereof |
| CN103451533A (en) * | 2013-09-12 | 2013-12-18 | 武汉钢铁(集团)公司 | Hot-rolled magnetic yoke steel with yield strength not less than 800Mpa and production method thereof |
| CN103882294A (en) * | 2014-03-04 | 2014-06-25 | 南京钢铁股份有限公司 | Ni-saving type low-temperature steel plate and preparation method thereof |
| US10378073B2 (en) * | 2014-09-26 | 2019-08-13 | Baoshan Iron & Steel Co., Ltd. | High-toughness hot-rolling high-strength steel with yield strength of 800 MPa, and preparation method thereof |
| CN104651750A (en) * | 2015-03-12 | 2015-05-27 | 上海海隆石油钻具有限公司 | High-strength petroleum drill pipe body and heat treatment process thereof |
| CN105603323A (en) * | 2016-03-07 | 2016-05-25 | 舞阳钢铁有限责任公司 | Large-thickness high-strength high-toughness NM360 steel plate and production method thereof |
| CN105970108A (en) * | 2016-05-27 | 2016-09-28 | 江苏金基特钢有限公司 | Low-chromium-nickel heat resistant steel and heat treatment method thereof |
| CN107557674A (en) * | 2016-06-30 | 2018-01-09 | 鞍钢股份有限公司 | A kind of concrete mixer tank steel plate and its production method |
| CN107557674B (en) * | 2016-06-30 | 2019-02-26 | 鞍钢股份有限公司 | A kind of concrete mixer tank steel plate and its production method |
| CN106544590A (en) * | 2016-10-17 | 2017-03-29 | 江阴兴澄特种钢铁有限公司 | 1000MPa grade high ductilities high-performance uniformity easily welds super-thick steel plate and its manufacture method |
| CN106544590B (en) * | 2016-10-17 | 2019-02-12 | 江阴兴澄特种钢铁有限公司 | 1000MPa grade high ductility high-performance uniformity easily welds super-thick steel plate and its manufacturing method |
| CN107513669A (en) * | 2017-07-20 | 2017-12-26 | 首钢集团有限公司 | A kind of high-strength cold rolling square and rectangular pipe steel and its manufacture method |
| CN107675086A (en) * | 2017-11-15 | 2018-02-09 | 马鞍山钢铁股份有限公司 | A kind of 800MPa levels engineering truck hot-rolled structural steel and its production method |
| CN107675086B (en) * | 2017-11-15 | 2019-04-26 | 马鞍山钢铁股份有限公司 | A kind of automobile-used hot-rolled structural steel of 800MPa grades of engineering and its production method |
| CN108165892A (en) * | 2017-11-23 | 2018-06-15 | 南阳汉冶特钢有限公司 | A kind of low-temperature pressure container 35-50mm thickness Q420R high-strength steel and its production method |
| CN111542638A (en) * | 2017-12-26 | 2020-08-14 | Posco公司 | Hot-rolled steel sheet, steel pipe, and component having excellent impact resistance, and method for producing same |
| CN110317994A (en) * | 2018-03-30 | 2019-10-11 | 宝山钢铁股份有限公司 | A kind of high heat input welding unimach and its manufacturing method |
| CN110317994B (en) * | 2018-03-30 | 2021-12-17 | 宝山钢铁股份有限公司 | Ultrahigh-strength steel for high heat input welding and manufacturing method thereof |
| CN108315671A (en) * | 2018-05-14 | 2018-07-24 | 东北大学 | 1000MPa grades of low yield strength ratio super-high strength steels of yield strength and preparation method thereof |
| CN108315671B (en) * | 2018-05-14 | 2019-09-17 | 东北大学 | 1000MPa grades of low yield strength ratio super-high strength steels of yield strength and preparation method thereof |
| CN108411210A (en) * | 2018-06-01 | 2018-08-17 | 东北大学 | A kind of deep-sea dynamic flexible standpipe acidproof super-high strength steel and preparation method thereof |
| CN108411210B (en) * | 2018-06-01 | 2020-01-14 | 东北大学 | Acid-resistant ultrahigh-strength steel for deep-sea dynamic flexible vertical pipe and preparation method thereof |
| CN108914006B (en) * | 2018-08-10 | 2020-12-29 | 宝武集团鄂城钢铁有限公司 | Ultrahigh-strength quenched and tempered steel plate with excellent performance in thickness direction and manufacturing method thereof |
| CN108914006A (en) * | 2018-08-10 | 2018-11-30 | 武汉钢铁集团鄂城钢铁有限责任公司 | A kind of superhigh intensity hardened and tempered steel plate that thickness directional properties are excellent and its manufacturing method |
| CN109385570A (en) * | 2018-09-28 | 2019-02-26 | 宝山钢铁股份有限公司 | A kind of high strength steel plate and its manufacturing method |
| CN109385570B (en) * | 2018-09-28 | 2021-05-14 | 宝山钢铁股份有限公司 | High-strength steel plate and manufacturing method thereof |
| CN109338214A (en) * | 2018-10-11 | 2019-02-15 | 石家庄钢铁有限责任公司 | The steel for rock drilling bits and its production method of high-strength and high ductility |
| CN109112264A (en) * | 2018-10-26 | 2019-01-01 | 山东钢铁集团日照有限公司 | The high tough medium plate of micro alloying element quenching and tempering type and its manufacturing method on a small quantity |
| CN111549300A (en) * | 2020-05-08 | 2020-08-18 | 包头钢铁（集团）有限责任公司 | Steel with yield strength of 800MPa for engineering machinery and preparation method thereof |
| CN111575609A (en) * | 2020-05-09 | 2020-08-25 | 包头钢铁（集团）有限责任公司 | Steel with high strength, good plasticity and toughness for engineering machinery and preparation method thereof |
| CN111876683B (en) * | 2020-07-31 | 2021-07-06 | 东北大学 | 1000MPa high-toughness steel for coal mine hydraulic support and preparation method thereof |
| CN111876683A (en) * | 2020-07-31 | 2020-11-03 | 东北大学 | 1000MPa high-toughness steel for coal mine hydraulic support and preparation method thereof |
| CN112267064A (en) * | 2020-09-10 | 2021-01-26 | 邯郸钢铁集团有限责任公司 | Martensite high-temperature wear-resistant steel and production method thereof |
| CN113430451B (en) * | 2021-05-26 | 2022-06-10 | 武汉钢铁有限公司 | 1000 MPa-grade magnet yoke steel for manufacturing hydro-generator rotor and production method |
| CN113403532B (en) * | 2021-05-26 | 2022-06-10 | 武汉钢铁有限公司 | 1200 MPa-grade magnet yoke steel for manufacturing hydro-generator rotor and production method |
| CN113430451A (en) * | 2021-05-26 | 2021-09-24 | 武汉钢铁有限公司 | 1000 MPa-grade magnet yoke steel for manufacturing hydro-generator rotor and production method |
| WO2022247752A1 (en) * | 2021-05-26 | 2022-12-01 | 武汉钢铁有限公司 | 1000 mpa grade magnetic yoke steel for manufacturing rotor of hydroelectric generator, and production method |
| CN113373372A (en) * | 2021-05-26 | 2021-09-10 | 武汉钢铁有限公司 | 1300 MPa-grade magnet yoke steel for manufacturing hydro-generator rotor and production method |
| CN113373374A (en) * | 2021-05-26 | 2021-09-10 | 武汉钢铁有限公司 | 1100 MPa-grade magnet yoke steel for manufacturing hydro-generator rotor and production method |
| CN113373372B (en) * | 2021-05-26 | 2022-06-10 | 武汉钢铁有限公司 | 1300 MPa-grade magnet yoke steel for manufacturing hydro-generator rotor and production method |
| CN113403532A (en) * | 2021-05-26 | 2021-09-17 | 武汉钢铁有限公司 | 1200 MPa-grade magnet yoke steel for manufacturing hydro-generator rotor and production method |
| CN113373374B (en) * | 2021-05-26 | 2022-06-10 | 武汉钢铁有限公司 | 1100 MPa-grade magnet yoke steel for manufacturing hydro-generator rotor and production method |
| CN113718172A (en) * | 2021-07-28 | 2021-11-30 | 唐山钢铁集团有限责任公司 | 1200 MPa-grade low-carbon martensite steel strip and production method thereof |
| CN114480970A (en) * | 2022-01-25 | 2022-05-13 | 上海大学 | High-strength high-toughness steel and preparation method and application thereof |
| CN114540715A (en) * | 2022-02-28 | 2022-05-27 | 衡阳华菱钢管有限公司 | Acid corrosion resistant steel, preparation method thereof and corrosion resistant pipe |
| WO2023246941A1 (en) * | 2022-06-24 | 2023-12-28 | 宝山钢铁股份有限公司 | Automotive structural steel having a yield strength of ≥1000 mpa and manufacturing method therefor |
| CN115094346A (en) * | 2022-07-04 | 2022-09-23 | 宁波祥路中天新材料科技股份有限公司 | Hot rolled strip steel with tensile strength not lower than 1200MPa produced by TSR production line and method |
| CN115874116A (en) * | 2022-12-27 | 2023-03-31 | 北京理工大学 | Silicon-aluminum-free superfine bainitic steel and preparation method thereof |
| CN115874116B (en) * | 2022-12-27 | 2024-01-16 | 北京理工大学 | Silicon-aluminum-free superfine bainitic steel and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN100372962C (en) | 2008-03-05 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN100372962C (en) | Superhigh strength steel plate with yield strength more than 1100Mpa and method for producing same | |
| CN100494451C (en) | Superhigh strength steel plate with yield strength more than 960Mpa and method for producing same | |
| CN100412223C (en) | Ultra-high strength steel with excellent corrosion resistance and fatigue resistance and its making process | |
| CN111187990B (en) | Hot-rolled H-shaped steel with yield strength of 500MPa and production method thereof | |
| CN101935810B (en) | Method for manufacturing low-cost super-high intensity steel plate with yield strength of over 960 MPa for wide process operation window | |
| CN102011068B (en) | 800 MPa-grade low-yield-ratio structural steel plate and production method thereof | |
| CN111229827B (en) | Hot-rolled H-shaped steel with yield strength of 450MPa and production method thereof | |
| EP3859035A1 (en) | Ultrahigh-steel q960e slab and manufacturing method | |
| CN111304531B (en) | Hot-rolled H-shaped steel with yield strength of 550MPa and production method thereof | |
| CN102691018A (en) | Low-compression ratio super-strength steel plate for ocean engineering and manufacturing method thereof | |
| CN101165202A (en) | High-strength steel with high welding heat influence area toughness and manufacturing method thereof | |
| CN114540580A (en) | Production method of low-cost Q345Q series bridge steel plate | |
| CN109338219B (en) | Super-thick steel plate for wind power flange and production method thereof | |
| CN102839330B (en) | 800 Mpa high-strength thick plate for high heat input welding | |
| CN109023149B (en) | 980 MPa-grade cold-rolled dual-phase steel with low requirement on cooling capacity of production line and manufacturing method thereof | |
| CN110616372A (en) | Large-thickness 14Cr1MoR steel plate and production method thereof | |
| CN108411196A (en) | Tensile strength is 680MPa grades of large-scale mobile steelss for pressure vessel use and production method | |
| CN113699437A (en) | Hot continuous rolling dual-phase wear-resistant steel for carriage plate and production method thereof | |
| CN100350065C (en) | High tensile strength low carbon bainite thick steel plate and its production method | |
| CN109097664A (en) | A kind of 900MPa grades of thick-specification high-tenacity hot rolled strip and preparation method thereof | |
| CN107400834A (en) | A kind of reaming hot rolling complex phase steel plate of good performance and its production method | |
| CN100350066C (en) | High toughness low carbon bainite thick steel plate and its production method | |
| CN104264070B (en) | A kind of Thin Specs X80 pipe line steel and manufacture method thereof | |
| CN105420632A (en) | Q690CF hot-rolled steel plate and preparation method thereof | |
| CN115386805A (en) | Low-yield-ratio high-toughness bridge weathering steel and manufacturing method thereof |
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 |