CN101660100B - Super-thick quenched and tempered steel plate with good obdurability matching, and manufacturing method thereof - Google Patents
Super-thick quenched and tempered steel plate with good obdurability matching, and manufacturing method thereof Download PDFInfo
- Publication number
- CN101660100B CN101660100B CN2008100421240A CN200810042124A CN101660100B CN 101660100 B CN101660100 B CN 101660100B CN 2008100421240 A CN2008100421240 A CN 2008100421240A CN 200810042124 A CN200810042124 A CN 200810042124A CN 101660100 B CN101660100 B CN 101660100B
- Authority
- CN
- China
- Prior art keywords
- steel plate
- steel
- temperature
- relation
- als
- 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
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
The invention relates to a super-thick quenched and tempered steel plate with good obdurability matching, which is manufactured by the following steps: adopting a component system of low C-Mn-(Ti+V+B) micro-alloyed steel as a basis to appropriately increase the content of acid soluble Als in the steel, wherein the Als is more than or equal to (Mn equivalent weight/C)*(Ntotal-0.292Ti); controllingthe ratio of (Mn equivalent weight) to C to between 10 and 30; alloying (Cu+Ni+Mo+Cr), wherein Ni/Cu is more than or equal to 1.5; performing Ca processing, wherein the ratio of Ca to S is between 0.80 and 3.00; controlling the F*DI index to be more than or equal to 0.50*the thickness of a finished steel plate and other metallurgy technological means; and performing optimization, crystallization and controlled rolling, and performing a quenching and tempering process (Q+T) so as to ensure that the microscopic structure of the finished steel plate is a tiny tempered bainite (probably containing a minute quantity of ferrite), and the average crystal group size is below 25 mum. Through the method, a large-scale steel structure, which has even and excellent obdurability/strong plastic matching and is particularly suitable for water and electricity pressure water pipes, volutes, ocean platforms and the like, is obtained, and the stable mass industrial production with low cost can be achieved.
Description
Technical field
The present invention relates to a kind of low-carbon (LC) (high strength) low alloy steel/steel plate and manufacture method thereof, be particularly related to good extra-thick quenched and tempered steel plate and the manufacture method thereof of a kind of obdurability coupling, it be by recrystallize controlled rolling+hardening and tempering process (Q+T) acquisition yield strength 〉=500MPa, tensile strength 〉=610MPa ,-40 ℃ Charpy ballistic work (single value) 〉=47J, superior weldability, the extra-thick quenched and tempered steel plate of finished product thickness of slab 〉=60mm in the composition system of the microalloying of the alloying of a kind of low C-Mn-high Als-(Cu+Ni+Mo+Cr)-(Ti+V+B).
Background technology
As everyone knows, low-carbon (LC) (high strength) low alloy steel is one of most important structural timber, is widely used among petroleum natural gas pipeline, ocean platform, shipbuilding, bridge structure, boiler vessel, building structure, automotive industry, transportation by railroad and the machinofacture.
Low-carbon (LC) (high strength) low alloy steel performance depends on the process system of its chemical ingredients, manufacturing processed, and wherein intensity, toughness and weldability are the most important performances of low-carbon (LC) (high strength) low alloy steel, and its final decision is in the microstructure state of finished steel.Along with science and technology constantly advances, people propose higher requirement to the obdurability of high-strength steel, strong plasticity coupling, promptly when keeping lower manufacturing cost, improve the comprehensive mechanical performance and the use properties of steel plate significantly, save cost with the consumption that reduces steel, alleviate own wt, stability and the security of steel construction, what is more important is further to improve steel construction security and stability and cold and hot working.
At present, started the research climax that develops high-performance steel iron material of new generation in Japan and Korea S., the European Union's scope, 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.
Traditional yield strength is greater than the super-thick steel plate of 500MPa, mainly add tempering (Q+T) by quenching, promptly so-called hardening and tempering method is produced, and this just requires the steel plate centre must have sufficiently high hardening capacity, be hardenability index DI 〉=1.0 steel plate thickness, wherein 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 the microstructure of steel plate thickness direction and performance evenly, therefore in steel, add a large amount of Cr inevitably, Mo, Ni, alloying elements such as Cu, Mo and Cr content in this class steel plate generally will be controlled at 〉=and 0.50%, especially noble element Ni content to be controlled at 〉=more than 1.00%, disclosed as Japanese Patent " clear 59-129724; flat 1-219121 ", because the Ni element not only can improve the intensity and the hardening capacity of steel plate, reduce transformation temperature refinement bainite/martensite lath group grain-size; The more important thing is the unique element that can improve the low-temperature flexibility of bainite/martensite lath own of Ni.
So, 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 welding cost raises, welding efficiency reduces, welding work on the spot environmental degradation.
Other existing a large amount of patent documentations are as Japan " clear 63-93845; clear 63-79921; clear 60-258410; special putting down opens 4-285119; spy is flat to open 4-308035; flat 3-264614, flat 2-250917, flat 4-143246 "; United States Patent (USP) " US Patent4855106, US Patent5183198, US Patent4137104 "; they have just realized the intensity and the low-temperature flexibility of mother metal steel plate; can property and just improve steel plate welding; it is less to obtain good welded heat affecting zone HAZ low-temperature flexibility explanation; more do not relate to and how to guarantee that special thick (〉=60mm) hardened and tempered steel plate centre hardening capacity is to guarantee armor plate strength; toughness and along steel plate thickness direction intensity, the toughness homogeneity.
Along with the Chinese national economy development, the requirement of building saving type harmonious society, water power has been put day thing agenda as development of clean energy.China's power engineering construction is in the ascendant at present, the extra-thick quenched and tempered steel plate increase in demand of the critical material of hydroelectric project---pressure water pipe, volute.But pressure water pipe, volute also belong to a kind of brand-new steel grade with extra-thick quenched and tempered steel plate for China, the at present domestic steel plate that can only produce below the 75mm, domestic three big motor groups (breathe out electricity, power on and east) the equal import of required extra-thick quenched and tempered steel plate; 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.
Summary of the invention
The object of the present invention is to provide good extra-thick quenched and tempered steel plate and the manufacture method thereof of a kind of obdurability coupling, unitized design by the steel plate alloying element combines with special hardening and tempering process (RCR+QT), obtain good spy thick (〉=80mm) in hardened and tempered steel plate intensity, low-temperature flexibility and the obdurability coupling, the weldability of steel plate is excellent too, and has successfully solved extra-thick quenched and tempered steel plate along the uneven problem of steel plate thickness direction obdurability.
Technical scheme of the present invention is, the composition system that adopts the micro-alloyed steel of low C-Mn-(Ti+V+B) is as the basis, suitably improves in the steel sour molten Als content and Als 〉=(Mn equivalent/C) * (N
Total-0.292Ti), control (Mn equivalent)/C is than between 10～30, (Cu+Ni+Mo+Cr) alloying and Ni/Cu 〉=1.5, Ca processing and Ca/S are than between 0.80～3.00, control F * DI index 〉=metallurgical technology means such as 0.50 * 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 tempering bainite (ferrite that may contain minute quantity), average colony size is below 25 μ m, obtain evenly good obdurability, strong plasticity coupling, be specially adapted to the hydraulic power pressure water pipe, large-scale steel structure such as volute and ocean platform, and can realize low-cost stable suitability for industrialized production in batches.
Particularly, the good extra-thick quenched and tempered steel plate of obdurability coupling of the present invention, its composition quality per-cent is:
C：0.07％～0.11％
Si≤0.20％
Mn：0.95％～1.45％
P≤0.013％
S≤0.003％
Cr：0.15％～0.45％
Cu：0.10％～0.35％
Ni：0.20％～0.50％
Mo：0.15％～0.45％
Als：0.040％～0.060％
Ti：0.006％～0.011％
V：0.020％～0.060％
N≤0.0070％
Ca：0.00l％～0.005％
B：0.0007％～0.0014％，
All the other are iron and inevitably are mingled with;
And above-mentioned constituent content must satisfy following relation simultaneously:
Relation between C, the Mn equivalent: 10≤(Mn equivalent)/C≤30, wherein Mn equivalent=Mn+0.74Ni+0.16Cu+0.22Cr-0.73Mo;
Relation between Als, Ti and the N: Als 〉=(the Mn equivalent/C) * (N
Total-0.292Ti);
Relation between Cu and the Ni: Ni/Cu 〉=1.5;
Relation between Ca and the S: Ca/S is between 0.80～3.0;
F * DI 〉=0.50 * t; Wherein F is the boron steel hardening capacity factor, and 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); Guarantee that extra-thick quenched and tempered steel plate is even along steel plate thickness direction intensity, toughness, plasticity.
Steel plate of the present invention has following feature:
C is very big to intensity, low-temperature flexibility, unit elongation and the weldability influence of quenched and tempered steel, from improving extra-thick quenched and tempered steel plate low-temperature flexibility and weldability angle, wishes that C content is controlled lowlyer in the steel; But microstructures Control and manufacturing cost angle from the hardening capacity of quenched and tempered steel, obdurability coupling, manufacturing process, C content should not be controlled lowly excessively; Dimension C content zone of reasonableness is 0.07%～0.11%.
Mn as most important alloying element in steel except that the intensity that improves steel plate, also have the austenite of expansion phase region, reduce Ar
3Point temperature, refinement hardened and tempered steel plate colony and improve the steel plate low-temperature flexibility effect, promote low temperature phase change tissue to form and the effect of raising armor plate strength; But segregation takes place in Mn easily 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, when especially C content is higher in the steel, the segregation that increases the weight of the strand centre is with loose, and serious strand central zone is segregated in follow-up rolling, thermal treatment and the welding process and easily forms abnormal structure, causes the low and welding joint of hardened and tempered steel plate low-temperature flexibility crackle to occur; Therefore according to the C content range, select suitable Mn content range extremely necessary for extra-thick quenched and tempered steel plate, composition of steel system and C content are 0.070～0.110% according to the present invention, being fit to Mn content is 0.95%～1.45%, and when C content was high, Mn content suitably reduced, and vice versa; And when C content hanged down, Mn content suitably improved.
Si promotes deoxidation of molten steel and can improve armor plate strength, but adopt the molten steel of A1 deoxidation, the desoxydatoin of Si is little, though Si can improve the intensity of steel plate, but the low-temperature flexibility of Si grievous injury steel plate, unit elongation and weldability, especially under than the large-line energy welding conditions, Si not only promotes the M-A island to form, and the M-A island size that forms is comparatively thick, skewness, the toughness of grievous injury welded heat affecting zone (HAZ), therefore the Si content in the steel should be controlled lowly as far as possible, considers the economy and the operability of steelmaking process, and Si content is controlled at below 0.20%.
P is as harmful mechanical property that is mingled with steel in the steel, and especially low-temperature impact toughness, unit elongation, weldability and welding joint SR performance have huge detrimental effect, and it is low more good more to require in theory; But consider steel-making operability and steel-making cost, for the extra-thick quenched and tempered steel plate that requires superior weldability ,-40 ℃ of toughness and excellent strength-toughness coupling, P content need be controlled at≤and 0.013%.
S has very big detrimental effect as harmful low-temperature flexibility that is mingled with steel in the steel, the more important thing is that 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, forms along rolling to MnS inclusion band, and the low-temperature impact toughness of grievous injury steel plate, unit elongation, Z are to performance, weldability and welding joint SR performance, S produces hot short principal element in the course of hot rolling simultaneously, and it is low more good more to require in theory; But consider steel-making operability, steel-making cost and the smooth and easy principle of logistics, for the extra-thick quenched and tempered steel plate that requires superior weldability ,-40 ℃ of toughness and excellent strength-toughness coupling, S content need be controlled at≤and 0.003%.
Cr is as weak carbide forming element, add hardening capacity, promotion martensite/bainite formation that Cr not only improves 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 have some improvement effect of steel plate toughness of tool; But when the Cr addition is too much, the weldability of grievous injury steel plate, especially welding joint SR performance; Therefore Cr content is controlled between 0.15%～0.45%.
Add the hardening capacity of Mo raising steel plate, promote martensite/bainite to form, but Mo is as the strong carbide forming element, when promoting that martensite/bainite forms, the position is very little to difference between the increase martensite/size of bainite colony and the martensite/lath of bainite of formation, 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 Mo adds when too much, the not only unit elongation of grievous injury steel plate, weldability and welding joint SR performance, 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, Mo content is controlled between 0.15%～0.45%.
Add Ni and not only can improve dislocation mobility in the ferritic phase, promote dislocation to hand over slippage, and increase misorientation between martensite/lath of bainite; Ni reduces 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.Therefore 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 and the welding joint SR performance of steel plate; Simultaneously Ni is a kind of very noble element, considers that from the ratio of performance to price Ni content is controlled between 0.20%～0.50%, does 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 improves 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 0.35%, causes copper brittleness, casting billet surface be full of cracks, implosion problem to reach especially super-thick steel plate welding joint SR performance degradation easily; The Cu addition is very few, is lower than 0.10%, and institute cuts any ice very little; Therefore Cu content is controlled between 0.10%～0.35%; The compound interpolation of Cu, Ni except that the copper brittleness phenomenon that reduces Copper Bearing Steel, alleviate the effect of intergranular cracking of course of hot rolling, the more important thing is that Cu, Ni are austenite stabilizer element, 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, cause that the position becomes big to difference between martensite/lath of bainite, increase the resistance that crackle passes martensite/lath of bainite.
B content is controlled between 0.0007%～0.0014%, when guaranteeing steel plate hardening capacity, does not damage the weldability and the HAZ toughness of steel plate.
Ti content is between 0.006%～0.011%, and austenite crystal is too 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 in addition, and when adopting the die casting cast, 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.
Sour molten aluminium 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%.
When adopting the die casting cast, the N content control difficulty in the steel is bigger, in order to ensure the existence of solid solution in the steel plate [B] and prevent that a large amount of A1N from separating out along original austenite crystal prevention, and the impelling strength of infringement steel plate, the N content in the steel must not surpass 0.007%.
V content is between 0.020%～0.060%, 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 adds very few, is lower than 0.020%, and (C N) very little, can not effectively improve the intensity of extra-thick quenched and tempered steel plate to the V that separates out; The V addition is too much, is higher than 0.060%, 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 plate 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 OK range of Ca content is 0.0010%～0.0050%.
Particularly, in composition design of the present invention, also must satisfy following relation simultaneously:
Relation between C, the Mn equivalent: 10≤(Mn equivalent)/C≤30, wherein Mn equivalent=Mn+0.74Ni+0.16Cu+0.22Cr-0.73Mo; Making steel plate fracture behaviour under-40 ℃ of conditions is plastic fracture, has guaranteed the plasticity and toughness of steel plate;
Relation between Als, Ti and the N: Als 〉=(the Mn equivalent/C) * (N
Total-0.292Ti); Eliminate welded H AZ solid solution N, improved steel plate welded H AZ toughness;
Relation between Cu and the Ni: Ni/Cu 〉=1.5; Improve the toughness and the anti-temper embrittlement performance of welding of steel plate mother metal;
Relation between Ca and the S: Ca/S is between 0.80～3.0; Guarantee steel plate anti-temper embrittlement, when hydrogen causes embrittlement, improve the weldprocedure of steel plate.
F * DI 〉=0.50 * t; Wherein F is the boron steel hardening capacity factor, and 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); Guarantee intensity, the toughness of steel plate, and guarantee that steel plate is even along thickness directional properties (intensity, toughness, plasticity).
In addition, the manufacture method of the extra-thick quenched and tempered steel plate that obdurability coupling of the present invention is good,
A) steel plate composition such as above-mentioned composition;
B) smelt casting, steel ladle pouring superheating temperature Δ T 〉=50 ℃, 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]);
C) rolling, steel plate overall compression ratio (slab thickness/Finished Steel plate thickness) 〉=4.0; Fs is common rolling, adopts big rolling pass draft to carry out continuous rolling, and rolling pass draft 8%～20% guarantees that refine austenite crystal grain takes place dynamically/static recrystallize the deformation metal;
Subordinate phase adopts the recrystallize controlled rolling, controlled rolling start rolling temperature≤950 ℃, rolling pass draft 〉=8%, recrystallization zone (〉=800 ℃) accumulative total draft 〉=50%, 850 ℃～900 ℃ of finishing temperatures;
D) 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 36 hours at least under 300 ℃ the condition;
E) thermal treatment,
Quench, steel plate 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;
Tempering, steel plate 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, time unit is min; Tempering finishes back steel plate natural air cooling to room temperature.
The present invention casts and adopts the die casting casting; Finished product thickness of slab 〉=60mm.
The present invention adopts recrystallize controlled rolling+modifier treatment, and the recrystallize controlled rolling can make the microstructure of the steel plate before modified evenly tiny, guarantees that like this steel plate microstructure after modified is also evenly tiny; Secondly, suppressed thick A1N and separated out, the plasticity and toughness of infringement steel plate along original austenite crystal prevention.
Beneficial effect of the present invention
The present invention combines with special hardening and tempering process (RCR+QT) by the unitized design of steel plate alloying element, promptly adopt the composition system of microalloying of the alloying of low C-Mn-high Als-(Cu+Ni+Mo+Cr)-(Ti+V+B), by recrystallize controlled rolling+hardening and tempering process (Q+T), obtain yield strength 〉=500MPa, tensile strength 〉=610MPa ,-40 ℃ Charpy ballistic work (single value) 〉=47J, superior weldability, the extra-thick quenched and tempered steel plate of finished product thickness of slab 〉=80mm; And successfully solved extra-thick quenched and tempered steel plate, and security and stability, the anti-fatigue performance of steel construction have been improved along the uneven problem of steel plate thickness direction obdurability; Good weldability has been saved the cost that user's steel member is made, and has shortened the time that user's steel member is made, for the user has created huge value.
The special thick water power of the present invention, has been used for the western Lip river of China and has crossed hydroelectric project far above user's technical qualification of ordering goods with extra-thick quenched and tempered steel plate steel plate object performance.
Description of drawings
Fig. 1 is microstructure (1/4 thickness) photo of the embodiment of the invention 2.
Embodiment
The present invention will be further described below in conjunction with embodiment and accompanying drawing.
Embodiments of the invention are referring to table 1～table 3, and table 4 is the performance of steel plate of the present invention.
As can be seen from Figure 1, steel plate microstructure of the present invention is tiny tempering bainite, and average colony size is below 25 μ m.
As can be seen from Table 4, steel plate unit elongation δ of the present invention 5 is minimum to reach 25% (for quenched and tempered steel, this numerical value has been very high unit elongation, generally all be below 20%),-40 ℃ of single Schwellenwert 134J of ballistic work are (for super-thick steel plate, this numerical value is very high, generally all is that 100J is following); The single Schwellenwert 65J of welded heat affecting zone (HAZ)-40 ℃ ballistic work illustrates that steel plate tool of the present invention obtains evenly good obdurability, strong plasticity coupling and weldability again.
In sum, the present invention adopts the composition system of the micro-alloyed steel of low C-Mn-(Ti+V+B) as the basis, suitably improves sour molten Als content in the steel, and Als 〉=(the Mn equivalent/C) * (N
Total-0.292Ti), control (Mn equivalent)/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 0.50 * 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 tempering bainite, average colony size is below 25 μ m, obtain evenly good obdurability, strong plasticity coupling, be specially adapted to large-scale steel structures such as hydraulic power pressure water pipe, volute and ocean platform.
Claims (4)
1. an obdurability mates good extra-thick quenched and tempered steel plate, and its composition quality per-cent is:
C：0.07％～0.11％
Si≤0.20％
Mn：0.95％～1.45％
P≤0.013％
S≤0.003％
Cr：0.15％～0.45％
Cu：0.10％～0.35％
Ni：0.20％～0.50％
Mo：0.15％～0.45％
Als：0.040％～0.060％
Ti：0.006％～0.011％
V：0.020％～0.060％
N≤0.0070％
Ca：0.001％～0.005％
B：0.0007％～0.0014％，
All the other are iron and inevitably are mingled with;
And above-mentioned constituent content must satisfy following relation simultaneously:
Relation between C, the Mn equivalent: 10≤(Mn equivalent)/C≤30, wherein Mn equivalent=Mn+0.74Ni+0.16Cu+0.22Cr-0.73Mo;
Relation between Als, Ti and the N: Als 〉=(the Mn equivalent/C) * (N
Total-0.292Ti);
Relation between Cu and the Ni: Ni/Cu 〉=1.5;
Relation between Ca and the S: Ca/S is between 0.80～3.0;
F * DI 〉=0.50 * t; Wherein F is the boron steel hardening capacity factor, and 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) * 25.4mm.
2. the manufacture method of the good extra-thick quenched and tempered steel plate of obdurability coupling, it comprises the steps:
A) its composition quality per-cent is: C:0.07～0.11, Si≤0.20, Mn:0.95～1.45, P≤0.013, S≤0.003, Cr:0.15～0.45, Cu:0.10～0.35, Ni:0.20～0.50, Mo:0.15～0.45, Als:0.040～0.060, Ti:0.006～0.011, V:0.020～0.060, N≤0.0070, Ca:0.001～0.005, B:0.0007～0.0014, surplus are iron and inevitable impurity;
And above-mentioned constituent content must satisfy following relation simultaneously:
Relation between C, the Mn equivalent: 10≤(Mn equivalent)/C≤30, wherein Mn equivalent=Mn+0.74Ni+0.16Cu+0.22Cr-0.73Mo;
Relation between Als, Ti and the N: Als 〉=(the Mn equivalent/C) * (N
Total-0.292Ti);
Relation between Cu and the Ni: Ni/Cu 〉=1.5;
Relation between Ca and the S: Ca/S is between 0.80～3.0;
F * DI 〉=0.50 * t; Wherein F is the boron steel hardening capacity factor, and when having solid solution [B] in the steel, F gets 1.15～1.45; 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) * 25.4mm;
B) press mentioned component and smelt, casting, steel ladle pouring superheating temperature Δ T 〉=50 ℃, 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]);
C) rolling, the steel plate overall compression ratio is slab thickness/Finished Steel plate thickness 〉=4.0;
Fs is common rolling, adopts big rolling pass draft to carry out continuous rolling, and rolling pass draft 8%～20% guarantees that refine austenite crystal grain takes place dynamically/static recrystallize the deformation metal;
Subordinate phase adopts the recrystallize controlled rolling, controlled rolling start rolling temperature≤950 ℃, rolling pass draft 〉=8%, recrystallization zone accumulative total draft 〉=50%, 850 ℃～900 ℃ of finishing temperatures;
D) 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 36 hours at least under 300 ℃ the condition;
E) thermal treatment,
Quench, the steel plate quenching 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;
Tempering, steel plate tempering temperature are 590～650 ℃, tempering hold-time 〉=(1.0～1.5) * Finished Steel plate thickness, and the soaking time that the tempering hold-time picks up counting when reaching the tempering target temperature for the steel plate core temperature, time unit is min; Tempering finishes back steel plate natural air cooling to room temperature.
3. the manufacture method of the extra-thick quenched and tempered steel plate that obdurability coupling as claimed in claim 2 is good is characterized in that, adopts the die casting casting.
4. the manufacture method of the extra-thick quenched and tempered steel plate that obdurability coupling as claimed in claim 2 is good is characterized in that finished product thickness of slab 〉=60mm.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2008100421240A CN101660100B (en) | 2008-08-27 | 2008-08-27 | Super-thick quenched and tempered steel plate with good obdurability matching, and manufacturing method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2008100421240A CN101660100B (en) | 2008-08-27 | 2008-08-27 | Super-thick quenched and tempered steel plate with good obdurability matching, and manufacturing method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN101660100A CN101660100A (en) | 2010-03-03 |
| CN101660100B true CN101660100B (en) | 2011-05-11 |
Family
ID=41788354
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN2008100421240A Active CN101660100B (en) | 2008-08-27 | 2008-08-27 | Super-thick quenched and tempered steel plate with good obdurability matching, and manufacturing method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN101660100B (en) |
Families Citing this family (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| 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 |
| CN102115812B (en) * | 2011-03-24 | 2013-04-24 | 南京钢铁股份有限公司 | Prompt tempering heat treatment method for Q690D steel |
| 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 |
| CN105803325B (en) * | 2016-04-28 | 2017-10-27 | 江阴兴澄特种钢铁有限公司 | A kind of low-crackle sensitive low yield strength ratio super-thick steel plate and preparation method thereof |
| CN106555118B (en) * | 2016-12-05 | 2021-08-24 | 中天钢铁集团有限公司 | Micro-alloy high-strength high-toughness steel containing Cu and production method thereof |
| CN109423572B (en) * | 2017-08-31 | 2020-08-25 | 宝山钢铁股份有限公司 | Seawater corrosion resistant steel plate with high crack arrest and strain aging embrittlement resistance and manufacturing method thereof |
| CN111621723B (en) * | 2019-02-28 | 2021-05-14 | 宝山钢铁股份有限公司 | 700 MPa-grade low-temperature quenched and tempered steel plate with excellent weldability and fatigue resistance and manufacturing method thereof |
| CN112080684B (en) * | 2020-07-17 | 2021-11-19 | 南京钢铁股份有限公司 | High-strength container thick plate with excellent core toughness and manufacturing method thereof |
| CN114763593B (en) * | 2021-01-12 | 2023-03-14 | 宝山钢铁股份有限公司 | Marine engineering steel with high humidity and heat atmosphere corrosion resistance 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
- 2008-08-27 CN CN2008100421240A patent/CN101660100B/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 |
Also Published As
| Publication number | Publication date |
|---|---|
| CN101660100A (en) | 2010-03-03 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN101962741B (en) | Quenched and tempered steel sheet and manufacturing method thereof | |
| 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 | |
| CN101660105B (en) | High-strength extra-thick quenched and tempered steel plate with good obdurability matching and manufacturing method thereof | |
| CN101660100B (en) | Super-thick quenched and tempered steel plate with good obdurability matching, and manufacturing method thereof | |
| CN101328564B (en) | Low yield ratio HT780 steel plate having superior weldability 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 | |
| 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 | |
| CN103436811B (en) | High-property super-thick steel plate for 500 MPa-level engineering structure and manufacturing method thereof | |
| CN103361569B (en) | A kind of Ultralow temperature weather-proof structural steel plate and production method thereof | |
| CN101613840B (en) | Super-thick steel plate with obdurability matching and excellent high-temperature performance 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 | |
| CN102691010B (en) | HT 960 steel plate with excellent plasticity and toughness and manufacture method thereof | |
| CN102851616B (en) | 60 Kg-scale low temperature-quenched and tempered steel plate with good weldability and manufacture method thereof | |
| CN102719757B (en) | Nickel-free high-toughness 80kg-grade high-strength steel and manufacturing method thereof | |
| CN106319380A (en) | Low compression ratio 690MPa grade extra thick steel plate and production method thereof | |
| CN101845597B (en) | Low-cost 80-kilo grade super-thick quenched and tempered steel plate and production method thereof | |
| CN103320719B (en) | Low-cost large-heat-input-weldable high-toughness steel plate and manufacturing method thereof | |
| CN102011047A (en) | Production method of steel plate for pressure vessel with low cost and high performance | |
| CN102618784B (en) | 60kg-level low-cost and high-toughness steel plate and production method thereof | |
| CN101565800B (en) | Steel plate with obdurability and strong plasticity and manufacturing method thereof | |
| CN104630655A (en) | Extra-thick steel plate having excellent balance between strength and toughness and used for welded structure and production process thereof | |
| CN103667921B (en) | The uniform high-strong toughness Plate Steel of through-thickness performance and production method thereof | |
| CN102828124A (en) | Non-quenched/tempered heavy plate for low-temperature pressure vessel and production 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 |