CN101565800B - Steel plate with obdurability and strong plasticity and manufacturing method thereof - Google Patents
Steel plate with obdurability and strong plasticity and manufacturing method thereof Download PDFInfo
- Publication number
- CN101565800B CN101565800B CN2008100364163A CN200810036416A CN101565800B CN 101565800 B CN101565800 B CN 101565800B CN 2008100364163 A CN2008100364163 A CN 2008100364163A CN 200810036416 A CN200810036416 A CN 200810036416A CN 101565800 B CN101565800 B CN 101565800B
- Authority
- CN
- China
- Prior art keywords
- steel plate
- steel
- temperature
- relation
- rolling
- 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.)
- Active
Links
Images
Abstract
The invention provides an HT780 steel plate and a manufacturing method thereof. The HT780 steel plate comprises the following components by weight percentage: 0.050 to 0.090 of C, less than or equal to 0.15 of Si, 1.00 to 1.50 of Mn, less than or equal to 0.013 of P, less than or equal to 0.003 of S, 0.40 to 0.80 of Cr, 0.25 to 0.55 of Cu, 0.40 to 0.90 of Ni, 0.25 to 0.55 of Mo, 0.040 to 0.060 of Al, 0.005 to 0.011 of Ti, 0.015 to 0.045 of V, less than or equal to 0.0040 of N, 0.001 to 0.005 of Ca, 0.006 to 0.0013 of B and the balance of Fe and inevitable impurities. The excellent low-temperature flexibility, high strength and extensibility and excellent weldability can be achieved by the design and the process.
Description
Technical field
The present invention relates to a kind of HT780 steel plate and manufacture method thereof, specifically, the present invention relates to a kind of HT780 steel plate and manufacture method thereof with excellent strength-toughness, strong plasticity coupling.
Background technology
As everyone knows, low-carbon (LC) (high strength) low alloy steel is one of most important structural timber, is widely used in petroleum natural gas pipeline, ocean platform, shipbuilding, bridge structure, boiler vessel, building structure, automotive industry, transportation by railroad and the machinofacture.The performance of low-carbon (LC) (high strength) low alloy steel depends on its chemical ingredients and manufacturing process, and its most important performance---intensity, toughness and weldability---finally depends on the microstructure state of finished steel.Continuous development along with science and technology, people propose higher requirement to the obdurability of high-strength steel, strong plasticity coupling, promptly when keeping lower manufacturing cost, wish significantly to improve the comprehensive mechanical performance and the use properties of steel plate, to reduce the consumption of steel, save cost, alleviate the own wt of steel construction, improve stability and security, what is more important further improves the security and stability and the cold and hot working of steel construction.
Traditional yield strength mainly adds tempering (DQT or QT) by quenching greater than the Plate Steel of 800MPa, and promptly so-called hardening and tempering method is produced, and this requires steel plate must have sufficiently high hardening capacity, i.e. hardenability index DI 〉=2 * Finished Steel plate thickness " DI=0.311C
1/2(1+0.64Si) * (1+4.10Mn) * (1+0.27Cu) * (1+0.52Ni) * (1+2.33Cr) * (1+3.14Mo) * 25.4 (mm) ", to guarantee that steel plate has sufficiently high intensity, good low-temperature flexibility and along uniform microstructure of steel plate thickness direction and performance.Therefore, must in steel, add alloying elements such as a large amount of Cr, Mo, Ni, Cu, the content of Mo and Cr generally will be controlled to be 〉=and 0.50%, especially, the content of noble element Ni will be controlled to be 〉=1.00% (clear 59-129724, flat 1-219121).This is not only because the Ni element can improve the intensity and the hardening capacity of steel plate, reduces transformation temperature refinement bainite/martensite lath group grain-size; The more important thing is that Ni is unique element that can improve the low-temperature flexibility of bainite/martensite lath own.Like this, the alloy content of steel plate is higher, and carbon equivalent Ceq and welding cold cracking Sensitivity Index Pcm are also higher, this brings bigger difficulty to site welding, need preheating before the weldering, postwelding needs thermal treatment, and the cost of welding raises, efficient reduces, the work on the spot environmental degradation.Though this hardening and tempering process is produced the requirement that the technical indicators such as intensity, low-temperature flexibility and unit elongation of steel plate can satisfy the user, the unit elongation of this steel plate (δ on the low side
5≤ 20%), cold and hot working performance not only bad for steel plate, and it is bigger to the anti-fatigue performance of steel plate, anti-stress concentration sensitivity and structural stability influence, when using on the tired heavy structures such as pressure water pipe in hydroelectric project and volute, thermoelectricity turbo-generator and offshore oil production platform structure, there is bigger potential safety hazard.
When the heavily loaded steel construction of large-scale fatigue adopts high-strength steel, wish that generally high-strength steel has good obdurability, strong plasticity coupling, especially tension unit elongation δ
5〉=20%.Started the research climax that develops high-performance steel iron material of new generation in the Japan and Korea S European Union scope at present, try hard to establish and optimize meter and the innovation manufacturing process technology obtains better tissue coupling, make high-strength steel obtain better obdurability, strong plasticity coupling by alloy combination.Yet, existing a large amount of patent documentation just illustrates intensity and the low-temperature flexibility that how to realize the mother metal steel plate, just improve steel plate welding energy property, the explanation that obtains good welded heat affecting zone HAZ low-temperature flexibility is less, more do not have document how to relate to when improving steel plate tensile strength, improve the tension unit elongation (clear 63-93845, clear 63-79921, clear 60-258410, special flat 4-285119, special flat open 4-308035, flat 3-264614, flat 2-250917, flat 4-143246, U.S. Pat 4855106, US 5183198, the US 4137104 of opening) of steel plate.
Therefore, the object of the present invention is to provide a kind of HT780 steel plate with evenly good obdurability, strong plasticity coupling, this steel plate is specially adapted to hydraulic power pressure water pipe and aspects such as volute, thermoelectricity turbo-generator and offshore oil production platform structure.
Summary of the invention
The invention provides a kind of HT780 steel plate, it is characterized in that, comprise the composition of following mass percent:
C：0.050％～0.090％
Si：≤0.15％
Mn：1.00％～1.50％
P：≤0.013％
S：≤0.003％
Cr：0.40％～0.80％
Cu：0.25％～0.55％
Ni：0.40％～0.90％
Mo：0.25％～0.55％
Als：0.040％～0.060％
Ti：0.005％～0.011％
V：0.015％～0.045％
N：≤0.0040％
Ca：0.001％～0.005％
B：0.0006％～0.0013％
All the other are iron and inevitable inclusion.
Relation between C and the Mn: 10≤Mn/C≤30;
Relation between Als, Ti and the N: Als 〉=(Mn/C) * (N
Total-0.292Ti);
Relation between B, Ti, the N: 5ppm+0.714 (N-0.292Ti)≤B≤12ppm+0.714 (N-0.292Ti);
Relation between Cu and the Ni: Ni/Cu 〉=1.5;
Relation between Ca and the S: 0.80≤Ca/S≤3.0;
F * DI 〉=2 * t, wherein F is the boron steel hardening capacity factor, when having solid solution [B] in the steel, F gets 1.3; T is the Finished Steel plate thickness; DI=0.311C
1/2(1+0.64Si) * (1+4.10Mn) * (1+0.27Cu) * (1+0.52Ni) * (1+2.33Cr) * (1+3.14Mo) * 25.4 (mm).
C is very big to the intensity of quenched and tempered steel, low-temperature flexibility, unit elongation and weldability influence, from the angle of low-temperature flexibility, unit elongation and the weldability of improving quenched and tempered steel, wishes that C content is lower in the steel; But the angle of microstructures Control and manufacturing cost from the intensity of quenched and tempered steel, unit elongation, manufacturing process, C content should not be low excessively.When C content is higher, though help improving armor plate strength, can damage low-temperature flexibility, unit elongation and the weldability of steel plate, so C content is unsuitable too high.The above analysis, the C content range selects 0.050～0.090%.
Mn except that the intensity that can improve steel plate, also has the austenite of expansion phase region, reduces Ar as most important alloying element
3Point temperature, refinement hardened and tempered steel plate colony and improve the steel plate low-temperature flexibility, promote low temperature phase change tissue to form and the effect of raising armor plate strength.But segregation takes place easily in Mn in the molten steel solidification process, when especially Mn content is higher, not only can cause the pouring operation difficulty, and easily and element generation conjugation segregation phenomenas such as C, P, S.If C content is higher in the steel, the segregation that also can increase the weight of the strand centre is with loose.Serious strand central zone is segregated in and easily forms abnormal structure in the follow-up rolling and welding process, causes hardened and tempered steel plate low-temperature flexibility and unit elongation low.Therefore, according to the C content range, select suitable Mn content range for its necessity of high-strength hardened and tempered steel plate.Composition of steel system and C content range select 0.06%～0.09% according to the present invention, and the Mn content range selects 1.00%～1.50%, and C content is when high, and Mn content suitably reduces; When C content hanged down, Mn content suitably improved.
Si can promote deoxidation of molten steel and improve armor plate strength, but for the molten steel that adopts the Al deoxidation, the desoxydatoin of Si is little.Though Si can improve the intensity of steel plate, but low-temperature flexibility, unit elongation and the weldability of meeting grievous injury steel plate, especially under than the large-line energy welding conditions, Si not only promotes the M-A island to form, and comparatively thick, the skewness of M-A island size that forms, the toughness of grievous injury welded heat affecting zone (HAZ), so the Si content in the steel should be controlled lowly as far as possible.Consider the economy and the operability of steelmaking process, the Si content range is selected below 0.15%.
P is as harmful being mingled with in the steel, and to the mechanical property of steel, especially low-temperature impact toughness, unit elongation and weldability have huge detrimental effect, and it is low more good more to require in theory.Consider steel-making operability and steel-making cost, for requiring superior weldability ,-40 ℃ of flexible high-strength hardened and tempered steel plates, the P content range selects≤0.013%.
S is as harmful being mingled with in the steel, low-temperature flexibility to steel has very big detrimental effect, the more important thing is, S combines with Mn in steel, form the MnS inclusion, in course of hot rolling, the plasticity-of MnS makes MnS along rolling to extension, form along rolling to MnS inclusion band, the low-temperature impact toughness of grievous injury steel plate, unit elongation, Z are to performance and weldability; S produces hot short principal element in the course of hot rolling simultaneously, and it is low more good more to require in theory.Consider steel-making operability, steel-making cost and the smooth and easy principle of logistics, for the high-strength hardened and tempered steel plate that requires superior weldability ,-40 ℃ of toughness and high-elongation, the S content range selects≤0.003%.
Cr is as weak carbide forming element, add hardening capacity, promotion martensite/bainite formation that Cr not only can improve steel plate, and the position increases to difference between martensite/lath of bainite, increase the resistance that crackle passes martensite/bainite colony, when improving armor plate strength, the tool steel plate flexible effect that has some improvement; But when the Cr addition surpasses 0.80%, the weldability of meeting grievous injury steel plate.Therefore the Cr content range selects 0.40%～0.80%.
Interpolation Mo can improve the hardening capacity of steel plate, promotes martensite/bainite to form; But Mo is as the strong carbide forming element, when promoting that martensite/bainite forms, can increase the size of martensite/bainite colony, and the position is very little to difference between the martensite/lath of bainite that forms, and reduces the resistance that crackle passes martensite/bainite colony.Therefore, Mo has reduced the low-temperature flexibility and the unit elongation of hardened and tempered steel plate when increasing substantially hardened and tempered steel plate intensity, and when the Mo addition surpasses 0.55%, the not only unit elongation of grievous injury steel plate and weldability, and increase the production cost of steel plate.Therefore, take all factors into consideration the phase transformation strengthening effect of Mo and to the influence of mother metal steel plate low-temperature flexibility, unit elongation and weldability, the Mo content range selects 0.25%～0.55%.
Add Ni and not only can improve dislocation mobility in the ferritic phase, promote dislocation to hand over slippage, and can increase misorientation between martensite/lath of bainite.Ni can reduce Ar as austenite stabilizer element
3The point temperature, refinement martensite/bainite colony size, so Ni has the function that improves hardened and tempered steel plate intensity, unit elongation and low-temperature flexibility simultaneously.Add the copper brittleness phenomenon that Ni can also reduce Copper Bearing Steel in the steel, alleviate the intergranular cracking of course of hot rolling, improve the resistance to atmospheric corrosion of steel plate.So theoretically, Ni content is high more within the specific limits good more in the steel, and the welded heat affecting zone but too high Ni content can harden is unfavorable to the weldability of steel; Ni is a kind of very noble element simultaneously.Consider that from the ratio of performance to price Ni content range selects 0.40%～0.90%, do not damage the weldability of steel plate with the obdurability level of the hardening capacity of guaranteeing steel plate and steel plate.
Cu also is an austenite stabilizer element, adds Cu and also can reduce Ar
3The point temperature improve the hardening capacity of steel plate and the resistance to atmospheric corrosion of steel plate, but the Cu addition is too much, is higher than 0.50%, causes copper brittleness, cc billet surface quality crackle and implosion problem easily; The Cu addition is very few, is lower than 0.10%, and role is very little.Therefore the Cu content range selects 0.10%～0.50%.The compound interpolation of Cu, Ni except that the copper brittleness phenomenon that reduces Copper Bearing Steel, alleviate the intergranular cracking effect of course of hot rolling, the more important thing is that Cu, Ni are austenite stabilizer element, and the compound interpolation of Cu, Ni can reduce Ar significantly
3, improve the motivating force of austenite to ferrite transformation, cause martensite/lath of bainite can be to each position to growing up, make that the position becomes big to difference between martensite/lath of bainite, increase the resistance that crackle passes martensite/bainite colony.
The B content range selects 0.0006%～0.0013%, when guaranteeing steel plate hardening capacity, does not damage the weldability and the HAZ toughness of steel plate.
The Ti content range selects 0.005%～0.011%, and austenite crystal is grown up in inhibition soaking and the course of hot rolling, improves the steel plate low-temperature flexibility, the more important thing is and suppresses HAZ grain growth in the welding process, improves HAZ toughness.Ti content surpasses at 0.011% o'clock, and the TiN particle of formation is not only more but also comparatively thick, has the ferrite of promotion and forms, and has a strong impact on the hardening capacity in steel plate centre.
Als in the steel is the freedom [N] in the steel fixedly, reduces welded heat affecting zone (HAZ) free [N], improve the low-temperature flexibility effect of welded H AZ, so the Als lower limit is controlled at 0.040%; Not only can cause the casting difficulty but add excessive Als in the steel, and can in steel, form the needle-like Al of a large amount of disperses
2O
3Inclusion, infringement steel plate endoplasm viability, low-temperature flexibility and weldability, so the Als upper limit is controlled at 0.060%.
The span of control of N is corresponding with the span of control of Ti, and for the ultra-large linear energy input welding steel, N content is low excessively, and generation TiN number of particles is few, size is big, can not play the effect of the weldability of improving steel, and is harmful to weldability on the contrary; But during the N too high levels, free [N] increases in the steel, and heat affected zone (HAZ) free [N] content increases, grievous injury HAZ low-temperature flexibility, the weldability of deterioration steel.Therefore.The N content range is selected below 0.0040%.
The V content range selects 0.015%～0.045%, and along with the increase of steel plate thickness, V content is the capping value suitably.Adding the V purpose is that (C N) separates out in the bainite/martensite lath, improves the intensity of steel plate by V.V content is lower than 0.015%, and (C N) very little, can not effectively improve the intensity of steel plate to the V that separates out; V content is higher than 0.045%, infringement steel plate low-temperature flexibility, unit elongation and weldability.
Steel is carried out Ca to be handled, on the one hand can further pure molten steel, on the other hand sulfide in the steel is carried out denaturing treatment, make it to become non deformable, stablize tiny spherical sulfide, suppress S red brittleness, improve steel low-temperature flexibility, unit elongation and Z to performance, improve steel plate flexible anisotropy.What of Ca add-on are depended on the height of S content in the steel, and the Ca add-on is low excessively, and treatment effect is little; The Ca add-on is too high, and (O, S) oversize, fragility also increases, and can become the fracture crack starting point, reduces the low-temperature flexibility and the unit elongation of steel, also reduces purity of steel simultaneously, pollutes molten steel to form Ca.General control Ca content is pressed ESSP=(wt%Ca) [1-1.24 (wt%O)]/1.25 (wt%S), and wherein ESSP is a sulfide inclusion shape control index, be advisable between the span 0.5～5, so the Ca content range selects 0.0010%～0.0050%.
The present invention also provides the manufacture method of this steel plate, may further comprise the steps: smelting, casting, common rolling, recrystallize controlled rolling, quenching, tempering.
Described casting technique adopts high temperature casting, continuous casting basket pouring superheating temperature Δ T 〉=25 ℃, teeming temperature T=T
L+ Δ T, wherein T
L=1538-(55 * [%C]+80 * [%C]
2+ 13 * [%Si]+4.8 * [%Mn]+1.5 * [%Cr]+3.1 * [%Ni]), adopt and gently to depress technology, light draft is 3%～6% to improve the segregation of strand inside.
Described common rolling employing 8-20% percentage pass reduction carries out continuous rolling, guarantees that refine austenite crystal grain takes place dynamically/static recrystallize the deformation metal.
Controlled rolling start rolling temperature≤950 of described recrystallize controlled rolling ℃, rolling pass draft 〉=8%, recrystallization zone (〉=800 ℃) accumulative total draft 〉=50%, 850 ℃～900 ℃ of finishing temperatures.
To the steel plate of thickness of slab 〉=30mm, steel plate is not more than 60min from stopping the cold junction bundle to the pitch time of going into the burial pit insulation, and heat preservation method is that the steel billet temperature surface is greater than being incubated 24 hours at least under 300 ℃ the condition.
Described quenching temperature (plate temperature) is 900～930 ℃, the hold-time 〉=20min that quenches, the soaking time that the hold-time of quenching picks up counting when reaching the quenching target temperature for the steel plate core temperature.
Described tempering temperature (plate temperature) is 590～650 ℃, tempering temperature was limit on the upper side when steel plate was thin, tempering temperature was limit on the lower side when steel plate was thicker, tempering hold-time 〉=(1.0～1.5) * Finished Steel plate thickness, the soaking time that the tempering hold-time picks up counting when reaching the tempering target temperature for the steel plate core temperature, tempering finish back steel plate natural air cooling to room temperature.
Beneficial effect
The present invention adopts the composition system of low N-(Ti+V+B) micro-alloyed steel of the low high Mn-of C-as the basis, suitably improves in the steel sour molten Als content and Als 〉=(Mn/C) * (N
Total-0.292Ti), control Mn/C than between 10～30, (Cu+Ni+Mo+Cr) alloying and Ni/Cu 〉=1.5, Ca handles and Ca/S than between 0.80～3.00, control F * DI index 〉=metallurgical technology means such as 2 * Finished Steel plate thickness, optimize recrystallize controlled rolling+hardening and tempering process (Q+T), the microstructure that makes the finished product steel plate is tiny tempered martensite+tempering lower bainite (ferrite that may contain minute quantity), and average colony size is below 20 μ m.Unitized design by the steel plate alloying element combines with special hardening and tempering process (RCR+QT), is obtaining excellent mother metal steel plate low-temperature flexibility, high strength (tensile strength 〉=780MPa), high-elongation (δ
5〉=25%) time, the weldability of steel plate is excellent too, and the intensity that has successfully solved the high-strength hardened and tempered steel plate is conflicted in the design of composition design and processes mutually with unit elongation, the very difficult problem that is in harmonious proportion, security and stability, anti-fatigue performance and the good weldability of steel construction have been improved simultaneously, reduced the cost that user's steel member is made, shortened the time that user's steel member is made, for the user has created huge value.
Steel plate of the present invention is a turbo-generator key part spring plate material, also be the turbo-generator steel plate the highest to material performance requirement, domestic each big steel mill (except that Baosteel) all can not produce at present, and domestic three big motor groups (breathe out electricity, power on and east) the special-purpose Plate Steel of required spring plate is all from Japanese import; Not only steel plate import price costliness, and delivery date can't guarantee, forces the user before design paper comes out, order in advance and have certain size surplus steel plate, so that after design paper comes out, the plate size that requires according to design paper requires the cutting steel plate, causes the huge waste of material.Along with the Chinese national economy development, build the requirement of saving type harmonious society, agenda has been put in the leap of power industry, and China's power engineering construction is in the ascendant at present, and the turbo-generator key part---spring plate has vast market prospect with Plate Steel.Spring plate also belongs to a kind of brand-new steel grade with Plate Steel for China, and except that Baosteel, domestic other iron and steel enterprise never studies and produced.First batch of 150 tons of spring plates have mail to steel plate and have breathed out electric group at present, and customer responsiveness plate property actual achievement has surpassed the level of Japanese like product, and this batch steel plate will be used to make the spring plate member of 700,000 kilowatts of turbo-generator units of world's single-machine capacity.
Description of drawings
Fig. 1 shows the microstructure of steel 2 of the present invention.
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.
The embodiment composition sees Table 1, and one of manufacturing process sees Table 2, and two of manufacturing process sees Table 3, and plate property sees Table 4.
Claims (6)
1. a HT780 steel plate is characterized in that, its mass percent consists of:
C：0.050％～0.090％
Si：≤0.15％
Mn：1.00％～1.50％
P：≤0.013％
S：≤0.003％
Cr：0.40％～0.80％
Cu：0.25％～0.55％
Ni：0.40％～0.90％
Mo：0.25％～0.55％
Als：0.040％～0.060％
Ti：0.005％～0.011％
V：0.015％～0.045％
N：≤0.0040％
Ca：0.001％～0.005％
B：0.0006％～0.0013％
All the other are iron and inevitable inclusion, the wherein relation between C and the Mn: 10≤Mn/C≤30; Relation between Als, Ti and the N: Als 〉=(Mn/C) * (N
Total-0.292Ti); Relation between B, Ti, the N: 5ppm+0.714 (N-0.292Ti)≤B≤12ppm+0.714 (N-0.292Ti); Relation between Cu and the Ni: Ni/Cu 〉=1.5; Relation between Ca and the S: 0.80≤Ca/S≤3.0; F * DI 〉=2 * t, wherein F is the boron steel hardening capacity factor, and when having solid solution [B] in the steel, F gets 1.3, and t is the Finished Steel plate thickness; DI=0.311C
1/2(1+0.64Si) * (1+4.10Mn) * (1+0.27Cu) * (1+0.52Ni) * (1+2.33Cr) * (1+3.14Mo) * 25.4.
2. the manufacture method of the described HT780 steel plate of claim 1, may further comprise the steps: smelting, casting, common rolling, recrystallize controlled rolling, quenching, tempering, it is characterized in that, described casting technique adopts the high temperature casting, continuous casting basket pouring superheating temperature Δ T 〉=25 ℃, teeming temperature T=TL+ Δ T, wherein TL=1538-(55 * [%C]+80 * [%C] 2+13 * [%Si]+4.8 * [%Mn]+1.5 * [%Cr]+3.1 * [%Ni]).
3. manufacture method as claimed in claim 2 is characterized in that, described casting technique adopts the technology of gently depressing, and light draft is 3%～6%.
4. manufacture method as claimed in claim 2 is characterized in that, controlled rolling start rolling temperature≤950 of described recrystallize controlled rolling ℃, rolling pass draft 〉=8%, recrystallization zone accumulative total draft 〉=50%, 850 ℃～900 ℃ of finishing temperatures.
5. manufacture method as claimed in claim 2 is characterized in that, described quenching temperature is 900～930 ℃, and hold-time 〉=20min quenches.
6. manufacture method as claimed in claim 2 is characterized in that, described tempering temperature is 590～650 ℃, tempering hold-time 〉=(1.0～1.5) * Finished Steel plate thickness.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2008100364163A CN101565800B (en) | 2008-04-22 | 2008-04-22 | Steel plate with obdurability and strong plasticity and manufacturing method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2008100364163A CN101565800B (en) | 2008-04-22 | 2008-04-22 | Steel plate with obdurability and strong plasticity and manufacturing method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN101565800A CN101565800A (en) | 2009-10-28 |
| CN101565800B true CN101565800B (en) | 2011-11-23 |
Family
ID=41282159
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN2008100364163A Active CN101565800B (en) | 2008-04-22 | 2008-04-22 | Steel plate with obdurability and strong plasticity and manufacturing method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN101565800B (en) |
Families Citing this family (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102168227B (en) * | 2010-02-25 | 2012-12-12 | 宝山钢铁股份有限公司 | Super-thick quenched-tempered steel plate with 60kg-grade tensile strength and production method of the super-thick quenched-tempered steel plate |
| CN102851616B (en) * | 2011-06-30 | 2014-03-19 | 宝山钢铁股份有限公司 | 60 Kg-scale low temperature-quenched and tempered steel plate with good weldability and manufacture method thereof |
| CN102618799B (en) * | 2012-03-22 | 2014-07-23 | 宝山钢铁股份有限公司 | High-performance quenched and tempered steel plate with 80 kg carbon equivalent and manufacturing method of high-performance quenched and tempered steel plate |
| CN106319389B (en) * | 2015-06-17 | 2018-11-06 | 宝山钢铁股份有限公司 | The steel for engineering machinery and its manufacturing method of inexpensive, high machining property |
| CN110195193B (en) * | 2018-02-27 | 2021-03-12 | 宝山钢铁股份有限公司 | 800 MPa-grade quenched and tempered steel plate with low cost, high toughness and excellent weldability and manufacturing method thereof |
| 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 |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1840723A (en) * | 2005-03-30 | 2006-10-04 | 宝山钢铁股份有限公司 | Superhigh strength steel plate with yield strength more than 1100Mpa and method for producing same |
| CN101045976A (en) * | 2006-03-27 | 2007-10-03 | 宝山钢铁股份有限公司 | Thick steel plate for low temperature use and capable of being welded in superhigh energy and its production process |
| CN101151387A (en) * | 2005-03-29 | 2008-03-26 | 住友金属工业株式会社 | Thick seamless steel pipe for line pipe and method for production thereof |
-
2008
- 2008-04-22 CN CN2008100364163A patent/CN101565800B/en active Active
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101151387A (en) * | 2005-03-29 | 2008-03-26 | 住友金属工业株式会社 | Thick seamless steel pipe for line pipe and method for production thereof |
| CN1840723A (en) * | 2005-03-30 | 2006-10-04 | 宝山钢铁股份有限公司 | Superhigh strength steel plate with yield strength more than 1100Mpa and method for producing same |
| CN101045976A (en) * | 2006-03-27 | 2007-10-03 | 宝山钢铁股份有限公司 | Thick steel plate for low temperature use and capable of being welded in superhigh energy and its production process |
Non-Patent Citations (2)
| Title |
|---|
| 罔野重雄等.焊接性能良好的780N/mm2级高强度钢板.《宽厚板》.1996,第2卷(第2期),41-44. * |
| 胡淑娥等.贝氏体型非调质钢的试制.《钢铁钒钛》.2003,第24卷(第1期),66-70. * |
Also Published As
| Publication number | Publication date |
|---|---|
| CN101565800A (en) | 2009-10-28 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN102337478B (en) | Excellent 100 kg-grade quenched and tempered steel plate with strong toughness and plasticity, and manufacturing method thereof | |
| CN102041459B (en) | Steel plate HT690 capable of being subjected to high heat input welding and manufacturing method thereof | |
| CN101328564B (en) | Low yield ratio HT780 steel plate having superior weldability and manufacturing method thereof | |
| CN101962741B (en) | Quenched and tempered steel sheet and manufacturing method thereof | |
| CN101660105B (en) | High-strength extra-thick quenched and tempered steel plate with good obdurability matching and manufacturing method thereof | |
| CN101660099B (en) | High strength low alloy hot rolling ferrite bainite weathering resistant steel and production method thereof | |
| CN100455692C (en) | High-strength weathering steel and method of manufacturing same | |
| CN102618799B (en) | High-performance quenched and tempered steel plate with 80 kg carbon equivalent and manufacturing method of high-performance quenched and tempered steel plate | |
| CN101660100B (en) | Super-thick quenched and tempered steel plate with good obdurability matching, and manufacturing method thereof | |
| CN102168227B (en) | Super-thick quenched-tempered steel plate with 60kg-grade tensile strength and production method of the super-thick quenched-tempered steel plate | |
| CN102691010B (en) | HT 960 steel plate with excellent plasticity and toughness and manufacture method thereof | |
| CN102965574B (en) | Titanium microalloying hot-rolling thick steel plate with low yield ratio and high strength and production process of steel plate | |
| CN102719757B (en) | Nickel-free high-toughness 80kg-grade high-strength steel and manufacturing method thereof | |
| CN102605282B (en) | 80 feather weight superhigh tenacities, pole Plate Steel and manufacture method thereof | |
| CN103320692A (en) | HT550 steel plate with ultrahigh toughness and excellent weldability and manufacture method thereof | |
| CN102851616B (en) | 60 Kg-scale low temperature-quenched and tempered steel plate with good weldability and manufacture method thereof | |
| CN106319380A (en) | Low compression ratio 690MPa grade extra thick steel plate and production method thereof | |
| CN102409260A (en) | Thick plate with good low-temperature toughness for pressure container and production method of thick plate | |
| CN102618784B (en) | 60kg-level low-cost and high-toughness steel plate and production method thereof | |
| CN101845597B (en) | Low-cost 80-kilo grade super-thick quenched and tempered steel plate and production method thereof | |
| CN102011047A (en) | Production method of steel plate for pressure vessel with low cost and high performance | |
| CN103320719A (en) | Low-cost large-heat-input-weldable high-toughness steel plate and manufacturing method thereof | |
| CN101565800B (en) | Steel plate with obdurability and strong plasticity and manufacturing method thereof | |
| CN106086657A (en) | A kind of yield strength ultra high-strength structural steel plate more than 1300MPa and preparation method thereof | |
| CN101492791B (en) | Electromagnetic steel plate capable of soldering in large energy input 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 |