CN102080193B - Structural steel for welding with ultra-great heat input and manufacturing method thereof - Google Patents
Structural steel for welding with ultra-great heat input and manufacturing method thereof Download PDFInfo
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Abstract
A structural steel for welding with ultra-great heat input and a manufacturing method thereof. The invention belongs to the technical field of high-strength steel plate for welding. The steel plate comprises, by mass percent, the following chemical compositions: 0.03-0.12 wt% of C, 0.01-0.30 wt% of Si, 1.2-2.0 wt% of Mn, not more than 0.015 wt% of P, not more than 0.008 wt% of S, not more than 0.03 wt% of Al, not more than 0.5 wt% of Cr, not more than 0.5 wt% of Mo, not more than 0.03 wt% of Nb, 0.005-0.03 wt% of Ti, 0.01-1.0 wt% of Ni, 0.01-1.0 wt% of Cu, 0.002-0.007 wt% of N, and 0.001-0.006 wt% of O, and also comprises one or more elements selected from Mg, Ca, B, Zr, Ta, or REM with the balance being Fe and unavoidable impurities, and the carbon equivalent of the steel plate is less than 0.40%. The type, size and quantity of the inclusions are controlled by controlling the alloy addition method during the refining phase, and the steel plate for welding with great heat input is manufactured by controlled rolling and controlled cooling process. The advantages are that the steel plate has high strength and good toughness, can endure a welding heat input of 400-1000 kJ/cm, still has excellent low-temperature toughness after welding, and has an average impact energy value of above 70 J at -20 DEG C.
Description
Technical field
The invention belongs to welding high strength structure plate technical field, particularly a kind of structural steel for welding with ultra-great heat input plate and manufacture method thereof.
Background technology
For improving operating efficiency, reducing cost, in the construction of large structure, 40mm is in succession to have adopted the welding with ultra-great heat input technology such as mariages electro-gas (enclosed) welding, electroslag welding in the welding sequence of upper steel plate, and the welding heat input reaches 400～1000KJ/cm.In succession develop multiple welding with ultra-great heat input steel plate both at home and abroad.
The method that adopts TiN mechanism to suppress the CGHAZ grain coarsening improves the toughness of welded heat affecting zone, is 200610047899.8 " a kind of low-alloy high-strength steel plate and manufacture method thereof of greatly heat input welding " such as number of patent application; Number of patent application is 200510047672.9 " a kind of Nb-Ti micro-alloyed steel and smelting processes thereof of suitable Large Heat Input Welding ", its mechanism is because Ti and N are combined into TiN, can stop growing up and increasing the ferrite forming core of austenite crystal, rationally Ti/N understands the performance of Effective Raise steel plate and welded heat affecting zone in the control steel between 2.4～3.2.Its welding heat input can reach 150KJ/cm, does not belong to the welding with ultra-great heat input category; All disclose the nitride that adopts Ti or compound compound and precipitate such as Japanese Patent Publication 55-026164 communique, JP 61-253344, Unexamined Patent 03-264614, Unexamined Patent 04-143246 and patent the 2950076th and promoted ferritic forming core, improved CGHAZ toughness.But the TiN that Ti forms in metal or Ti (CN) when near the temperature the welded bonds surpasses 1400 ℃, have then surpassed the fusing point of TiN itself in welding process, and TiN almost all dissolves under this temperature and lost effect.So, utilize TiN mechanism to improve welding heat influence area toughness, can only just can play a significant role being lower than away from the welded bonds temperature in the lower situation of 1300 ℃ zone or welding heat input.
And surpassing 1400 ℃ of zones near the welded bonds temperature, numerous documents have been announced the oxide compound of the more dystectic Ti of employing as intragranular acicular ferrite forming core particle, thereby improve the method for welding heat influence area toughness.Such as JP 61-79745, JP 62-103344, JP 61-117245, having announced the steel plate that contains the Ti oxide compound can the Effective Raise welding heat influence area toughness, its principle is the fusing point that the fusing point of Ti oxide compound is higher than steel, can not dissolve at welding welded bonds position, become stable particle, in the process of cooling after welding, TiN, MnS etc. depend on thereon and separate out, become the forming core particle of fine ferrite, suppress the harmful thick ferrite of toughness is formed, prevent embrittlement.But, the fine dispersion in steel of this Ti oxide compound is very difficult, and easy thickization or become aggregate in metal is if can not control the oxide compound of the Ti that forms fine disperse, then can form the above thick Ti oxide compound of 5 μ m, the formation of crack when becoming works destruction, reduction toughness.So, how to make to form the Ti oxide compound that Sizes, quantity are many and disperse distributes in the steel, then become the direction that numerous investigators make great efforts.
Summary of the invention
For the problem that prior art exists, the invention provides a kind of input of super large heat structure iron and manufacture method thereof.The steel plate that the method is made under the large heat input welding conditions of 400～1000KJ/cm, still has good low-temperature flexibility.
Large heat input steel plate for welding of the present invention, its chemical constitution is by mass percentage: C:0.03～0.12wt%, Si:0.10～0.30wt%, Mn:1.2～2.0wt%, P :≤0.015wt%, S :≤0.008%wt%, Al :≤0.03wt%, Cr :≤0.5wt%, Mo :≤0.5wt%, Nb :≤0.03wt%, Ti:0.005～0.03wt%, Ni:0.01～1.0wt%, Cu:0.01～1.0wt%, N:0.002～0.007wt%, O:0.001～0.006wt%, its chemical composition also includes or Mg simultaneously, or Ca, or B, or Zr, or Ta, or among the REM one or more, its content is respectively by mass percentage: Mg:0.0001～0.005wt%, Ca:0.0001～0.008wt%, B:0.0001～0.003wt%, Zr:0.0001～0.02wt%, Ta:0.0001～0.02wt%, REM:0.0001～0.02wt%, all the other are Fe and inevitable impurity.Ti-containing complex inclusions in the finished steel plate refers to Ti and or Mg or Ca or the oxide compound of B or Zr or Ta or REM or one or more complex inclusions that are compounded to form in the sulfide.
The carbon equivalent Ceq=C+Mn/6+Si/24+Ni/40+Cr/5+Mo/4+V/14 of described steel plate (%)≤0.40%.
The basal component circumscription reason explanation of steel of the present invention:
C: be the element of guaranteeing that armor plate strength is required.When C content is lower than 0.03%, can not guarantee high strength; When if C content is higher than 0.12%, can in large heat input welded heat affecting zone, form a large amount of M-A island tissue, welding crack sensibility increases, and reduces HAZ toughness.
Si: be the element of guaranteeing armor plate strength and smelting deoxidation.Si content is excessively low, and then deoxidation effect can not effectively be brought into play, if the welded heat affecting zone embrittlement of too high then steel plate, therefore be limited to 0.3% on the Si.
Mn: can guarantee armor plate strength and be conducive to toughness, Mn content is lower than 1.2% high strength and the excellent toughness that can not guarantee steel plate; When content was higher than 2.0%, HAZ toughness was deteriorated during Large Heat Input Welding.
P: be the inevitable element of sneaking into as impurity, make steel plate unit elongation and toughness significantly deteriorated if surpass 0.015%, the scope planted agent that can bear in smelting cost reduces as far as possible.
S: be the inevitable element of sneaking into as impurity, contain in right amount S and can form high-melting-point sulfide, simultaneously the S in the steel also can be attached to around composite oxides or the nitride with the MnS form, the forming core that promotes the welded heat affecting zone acicular ferrite with grow up.The S too high levels then can generate thick inclusion, reduces the steel plate thickness directional performance.And MnS is inclusion after rolling, can be in the elongation of steel plate heart section into strips, if size greater than 50 μ m, then can be obviously in the welding process and the iron-based body peel off and become the starting point of crackle, significantly increase welding crack sensibility.Therefore S content should be lower than 0.008%.
Al: be the important deoxidant element of smelting process, Al is combined with N can also improve armor plate strength.An amount of Al is conducive to the formation of Ti compound, if greater than 0.03%, will make toughness deteriorated.
Ti: be important element of the present invention, an amount of Ti content and addition means can obtain a large amount of undersized Ti oxide compounds and nitride, improve HAZ tissue and crystal grain thinning during large heat input welding, improve toughness.Increase if surpass the Ti of 0.03% solid solution, and can form thick Ti compound, significantly reduce toughness.
Cu: improve intensity and do not reduce toughness, and increase the steel plate corrosion resisting property.Be added with in right amount and benefit HAZ toughness, Cu is lower than 0.01% can not obtain high strength, if easily produce thermal crack when being higher than 1.0% welding, reduces HAZ toughness.
Ni: can guarantee armor plate strength and toughness, an amount of interpolation can improve HAZ toughness.Cross low Ni and then can not obtain high strength, increase at most cost if cross.Therefore Ni content optimum range is 0.01～1.0%.
Cr, Mo, Nb: all be to improving the favourable element of armor plate strength, if Cr, Mo content surpass 0.5%, Nb content and surpass 0.03%, then can significantly reduce HAZ toughness.
B:B can improve slab hardening capacity increases armor plate strength.In the Large Heat Input Welding process, TiN begins dissolving after the HAZ temperature is greater than 1300 ℃, free N is increased, and the N of dissolving can't separate out TiN again, and B spreads when high temperature soon, be easy in the austenite grain boundary segregation, be combined with N first during cooling and generate BN, the growing up of inhibition grain boundary ferrite, and when γ → α phase transformation, become the ferritic forming core point of intracrystalline, be of value to the raising of HAZ toughness.In order to bring into play such effect, the B content requirement is greater than 0.0001%, if it is deteriorated to surpass the HAZ toughness of 0.003% steel plate.
Ca, Mg, Zr, Ta, REM: all being strong deoxidant element and oxide compound or sulfide generting element, is most important element of the present invention.An amount of Ca, Mg, Zr, Ta, REM and suitable addition means can make the inclusion miniaturization, increase the forming core particle of acicular ferrite, are conducive to HAZ toughness.Its suitable scope is respectively Ca:0.0001～0.008wt%, Mg:0.0001～0.005wt%, Zr:0.0001～0.02wt%, Ta:0.0001～0.02wt%, REM:0.0001～0.02wt%, then can make thickization of inclusion if surpass the upper limit, on the contrary deteriorated HAZ toughness.
N: be the bioelement that forms TiN, contain the N amount not enough less than the TiN that 20ppm then separates out, if greater than 70ppm, then the N of solid solution is superfluous, reduces HAZ toughness.
O: can guarantee to form the oxide compound of the elements such as Ti, Mg, Zr, Ta, REM, oxygen level is during greater than 60ppm, and the oxide compound of formation is thick, reduces HAZ toughness.
The welding with ultra-great heat input of the present invention manufacture method of steel plate.The method comprises the operations such as smelting that existing production adopts, continuous casting, hot rolling, cooling, and it closes key control operation for smelting and rolling.
(1) smelt: molten iron adds steel scrap and add Si, Mn, Al when converter smelting, adjust molten steel and arrive the oxygen level of LF stove refining stage after 10～300ppm scope, add successively in Ti, Cr, Mo, Cu, Nb, Ni, Mg, Zr, Ta, REM, B, the Ca element two or more, and to control the pitch time that each element adds be 0～20min.Carry out continuous casting after reaching the target chemical composition;
(2) continuous casting: adopt Prepared by Low Superheat Pouring and solidification end dynamic soft-reduction technique to carry out continuous casting, crystallizer adopts weak cooling, and secondary cooling zone evenly cools off, top is cold by force, the bottom is weak cold, and namely strand adopts strong cooling from going out crystallizer to the aligning point, and the temperature of aligning point is greater than 950 ℃; Adopt weak cold behind the aligning.The strand cooling in heap that rolls off the production line;
(3) rolling: as to adopt the two-stage control rolling technology.The recrystallization zone rolling sequence, 1000～1100 ℃ of start rolling temperatures, pass deformation 10～35%; Non-recrystallization district rolling sequence, 800～950 ℃ of start rolling temperatures, cumulative deformation 40～90%; Rolling rear steel plate thickness is 40～100mm;
(4) cooling: roll the online water-cooled of rear steel plate, begin to cool down temperature 〉=750 ℃, 5～50 ℃/s of speed of cooling, 400～650 ℃ of cooling finishing temperatures, then air cooling is to room temperature.
Compare with traditional smelting process, the smelting process that the present invention adopts can form the inclusion that a large amount of small and disperseds distribute in steel, and the complex inclusion quantity that contains the Ti oxide compound that is of a size of 0.2～5 μ m is 100～3000/mm
2Be of a size of the amount of inclusions that contains the Ti nitride of 10～300nm greater than 3 * 10
6Individual/mm
2, all exceed several times than conventional steel, be conducive to pinning austenite crystal and refinement intergranular structure, improve CGHAZ toughness.Size is mingled with quantity less than 2/cm greater than the MnS of 50 μ m in the steel
2, size greater than the complex inclusion quantity of 5 μ m less than 2/mm
2, all be lower than the quantity in the conventional steel, be of value to and reduce postwelding tiny crack source.The steel plate that controlled rolling and controlled cooling method obtains, precipitate disperse, tiny in the steel, and the M-A island is evenly distributed, and volume fraction is few, and steel plate has high normal temperature comprehensive mechanical property and good low-temperature flexibility.
By the production control processing condition, the complex inclusion that contains Ti oxide compound, nitride that a large amount of small and disperseds that generate distribute, make steel plate when welding with ultra-great heat input, the 1400 ℃ of high temperature positions that surpass near welded bonds, form a large amount of intragranular acicular ferrites, simultaneously temperature be lower than 1400 ℃ away from welded bonds position tissue in, pinning original austenite grain and refinement intergranular structure.The two coefficient net effect and the toughness of welded heat affecting zone is increased substantially.
Structural steel for welding with ultra-great heat input of the present invention rolls attitude steel plate tensile strength 500～800MPa, and after the input of 400～1000KJ/cm welding heat ,-20 ℃ of ballistic work mean values are greater than 70J.Tissue signature after the input of 400～1000KJ/cm welding heat is: the welded bonds position is organized as proeutectoid ferrite and acicular ferrite.Wherein the original austenite crystal prevention place is the proeutectoid ferrite of Polygons bulk, and average grain size is less than 50 μ m, and the area occupied mark is less than 40%; Original austenite grain inside is fine acicular ferrite, and the area occupied mark is greater than 60%.
Be applicable to the high tensile steel plate of 40～100mm thickness of use in the manufacturings such as shipbuilding, bridge, ocean platform, Highrise buildings, pressurized vessel, be input as in the scope of 400～1000KJ/cm in super large heat such as adopting mariages electro-gas (enclosed) welding, electroslag welding, can effectively guarantee welding heat influence area toughness.Simultaneously, steel of the present invention can certainly satisfy the welding heat inputs such as multi-wire submerged-arc automatic welding, monofilament electro-gas (enclosed) welding less than the performance of the large heat input welding requirements of 400KJ/cm.
Description of drawings
Fig. 1 is the 800KJ/cm heat input welding heat simulation curve figure that embodiment and comparative example adopt.
Fig. 2 is the metallographic structure figure of embodiment 1 steel after 500KJ/cm heat input Thermal Cycle.
Fig. 3 is the metallographic structure figures of embodiment 2 steel after 800KJ/cm heat input Thermal Cycle.
Fig. 4 is the metallographic structure figures of embodiment 3 steel after 800KJ/cm heat input Thermal Cycle.
Embodiment 1 steel among Fig. 2 through 500KJ/cm welding heat input and Fig. 3 embodiment 2 steel and Fig. 4 embodiment 3 steel after the 800KJ/cm welding heat is inputted, although original austenite grain is fully grown up, but the inner in a large number crisscross acicular ferrites that form of original austenite grain are without bainite structure; And the proeutectoid ferrite of original austenite crystal prevention is the Polygons bulk, all without the lath-shaped ferrite, therefore steel plate still has good toughness behind welding with ultra-great heat input.
Embodiment
The below will by different embodiment and comparative example to recently describing the present invention.These examples only are that the present invention is not limited among these embodiment, can be adjusted enforcement in aforementioned chemical composition and manufacture method scope for the purpose of explaining.
Embodiment 1
The chemical composition of steel plate is by mass percentage: C:0.03～0.10wt%; Si:0.10～0.25wt%; Mn:1.2～1.6wt%; P:＜0.015wt%; S:＜0.008%wt%; Al:＜0.03wt%; Cr:＜0.5wt%; Mo:＜0.5wt%; Nb:＜0.03wt%; Ti:0.005～0.012wt%; Ni:0.01～0.8wt%; Cu:0.01～0.8wt%; Mg:＜0.005wt%; B:＜0.002wt%; Ca:0.0001～0.003wt%; N:0.002～0.006wt%; O:0.002～0.005wt%; All the other are Fe and inevitable impurity.
The carbon equivalent Ceq=C+Mn/6+Si/24+Ni/40+Cr/5+Mo/4+V/14 of described steel plate (%)=0.39%.
Manufacturing process is smelting → continuous casting → rolling → cooling, smelting technology is: add Si, Mn, Al in converter, adjust molten steel and arrive the oxygen level of refining stage after 10～300ppm scope, add successively Ti, Cr, Mo, Cu, Nb, Ni, Mg, B, Ca alloying element, and to control the pitch time that each element adds be 0～20min, carries out continuous casting after reaching the target chemical composition.Crystallizer adopts weak cooling, and secondary cooling zone evenly cools off, and strand adopts strong cooling from going out crystallizer to the aligning point, and speed of cooling is 0.1～5 ℃/s; 960 ℃ of the temperature of aligning point; Cold a little less than adopting behind the aligning, speed of cooling is less than 10 ℃/min.And adopt light Reduction Technology to pour into the 260mm continuously cast bloom, the strand rear cooling in heap that rolls off the production line.
Rolling technology is: 1100 ℃ of recrystallize stage start rolling temperatures, pass deformation 10～25%, 890 ℃ of non-recrystallization stage start rolling temperatures, cumulative deformation 70%.Begin to cool down 780 ℃ of temperature after rolling, with 25 ℃/s speed water-cooled to 580 ℃, then air cooling is to room temperature.
The room temperature tensile strength of 40mm thickness steel plate is 700MPa, unit elongation 25%; The welding with ultra-great heat input experimental installation adopts heat simulating tester, and heat transfer model is that the Rykalin-2D two-dimensional model (is asked t with Q
8/5Model), welding heat input 500KJ/cm, 1400 ℃ of peak temperatures, peak temperature residence time 5s, 20 ℃ of initial temperatures, cooling stops 300 ℃ of temperature, t
8/5=550s.Sample is processed into 10 * 10 * 55mm standard impact specimen after the simulation, and recording-20 ℃ of ballistic work mean values is 162J.The welded bonds position is organized as proeutectoid ferrite and intragranular acicular ferrite, and the proeutectoid ferrite average grain size is 25 μ m, and intragranular acicular ferrite area occupied mark is greater than 90%.
Comparative example 1
Adopt that non-method therefor of the present invention steel mill makes with embodiment 1 identical chemical composition and other steel plate of same intensity level, carry out after the large heat of 500KJ/cm is inputted Thermal Cycle as described in Example 1 ,-20 ℃ of ballistic work mean values are 5J.
Embodiment 2
The chemical composition of steel plate is by mass percentage: C:0.08～0.12wt%, Si:0.18～0.25wt%, Mn:1.4～2.0wt%, P:＜0.015wt%, S:＜0.008%wt%, Ti:0.015～0.03wt%, Al:＜0.03wt%, Nb:＜0.03wt%, Ni:＜0.5wt%, Cu:＜0.5wt%, Cr:0.01～0.5wt%, Mg:＜0.003wt%, Ta:0.0001～0.02wt%, B:＜0.003wt%, Ca:0.0001～0.003wt%; N:＜0.006wt%, O:＜0.005wt%, all the other are Fe and inevitable impurity.
The carbon equivalent Ceq=C+Mn/6+Si/24+Ni/40+Cr/5+Mo/4+V/14 of described steel plate (%)=0.36%.
Manufacturing process is smelting → continuous casting → rolling → cooling, smelting technology is: add Si, Mn, Al in converter, adjust molten steel and arrive the oxygen level of refining stage after 10～300ppm scope, add successively Ti, Cr, Cu, Nb, Ni, Mg, Ta, B, Ca alloying element, and to control the pitch time that each element adds be 0～20min, carries out continuous casting after reaching the target chemical composition.Continuous casting process is with embodiment 1.
Rolling technology is: 1070 ℃ of recrystallize stage start rolling temperatures, pass deformation 10～30%, 900 ℃ of non-recrystallization stage start rolling temperatures, cumulative deformation 75%; Begin to cool down 800 ℃ of temperature, with 35 ℃/s speed water-cooled to 550 ℃, then air cooling is to room temperature.
The room temperature tensile strength of 60mm thickness steel plate is 600MPa, unit elongation 25%.Welding with ultra-great heat input equipment adopts heat simulating tester, and heat transfer model is that the Rykalin-2D two-dimensional model (is asked t with Q
8/5Model), welding heat input 800KJ/cm, 1400 ℃ of peak temperatures, peak temperature residence time 30s, 20 ℃ of initial temperatures, cooling stops 300 ℃ of temperature, t
8/5=730s.Sample is processed into 10 * 10 * 55mm standard impact specimen after the simulation, and recording-20 ℃ of ballistic work mean values is 183J.The welded bonds position is organized as proeutectoid ferrite and intragranular acicular ferrite, and the proeutectoid ferrite average grain size is 35 μ m, and intragranular acicular ferrite area occupied mark is greater than 80%.
Comparative example 2
Adopt that non-method therefor of the present invention steel mill makes with embodiment 2 identical chemical compositions and other steel plate of same intensity level, carry out after the large heat of 800KJ/cm is inputted Thermal Cycle as described in Example 2 ,-20 ℃ of ballistic work mean values are 6J.
Embodiment 3
The chemical composition of steel plate is by mass percentage: C:0.05～0.10wt%; Si:0.10～0.25wt%; Mn:1.2～1.6wt%; P:＜0.015wt%; S:＜0.008%wt%; Al:＜0.03wt%; Cr:＜0.3wt%; Mo:＜0.2wt%; Nb:＜0.03wt%; Ti:0.01～0.02wt%; Ni:＜0.8wt%; B:＜0.002wt%; Ca:0.0001～0.003wt%; Zr:0.0001～0.02wt%, REM:＜0.006wt%, N:0.002～0.006wt%; O:0.002～0.005wt%; All the other are Fe and inevitable impurity.
The carbon equivalent Ceq=C+Mn/6+Si/24+Ni/40+Cr/5+Mo/4+V/14=0.38% of described steel plate.
Manufacturing process is smelting → continuous casting → rolling → cooling, smelting technology is: add Si, Mn, Al in converter, adjust molten steel and arrive the oxygen level of refining stage after 10～300ppm scope, add successively in the elements such as Ti, Cr, Mo, Nb, Ni, Zr, REM, B, Ca two or more, and to control the pitch time that each element adds be 0～20min.Carry out continuous casting after reaching the target chemical composition.Continuous casting process is with embodiment 1.
Rolling technology is: 1050 ℃ of recrystallize stage start rolling temperatures, pass deformation 10～35%, 850 ℃ of non-recrystallization stage start rolling temperatures, cumulative deformation 70%.Begin to cool down 810 ℃ of temperature after rolling, with 15 ℃/s speed water-cooled to 630 ℃, then air cooling is to room temperature.
The room temperature tensile strength of 80mm thickness steel plate is 550MPa, unit elongation 26%; After adopting as described in Example 2 the large heat input of 800KJ/cm Thermal Cycle ,-20 ℃ of ballistic work mean values are 108J.The welded bonds position is organized as proeutectoid ferrite and intragranular acicular ferrite, and the proeutectoid ferrite average grain size is 40 μ m, and intragranular acicular ferrite area occupied mark is greater than 85%.
Comparative example 3
Adopt that non-method therefor of the present invention steel mill makes with embodiment 3 identical chemical compositions and other steel plate of same intensity level, carry out after the large heat of 800KJ/cm is inputted Thermal Cycle as described in Example 3 ,-20 ℃ of ballistic work mean values are 7J.
The present embodiment 1,2,3 has chemical composition and technological process is simple, and armor plate strength is high, the anti-welding with ultra-great heat input excellent property of steel plate especially, and do not need preheating, postwelding not to need to heat-treat before the weldering.The thickness that is applicable to use in the large scale structure manufacturings such as shipbuilding, bridge, ocean platform, Highrise buildings, pressurized vessel is the high tensile steel plate of 40～100mm, use when adopting the welding heat inputs such as electroslag welding, mariages electro-gas (enclosed) welding to reach 400～1000KJ/cm scope, can increase substantially welding efficiency, reducing construction cost, and Low Temperature Impact Toughness of Heat-affected Zone is good.
Claims (3)
1. structural steel for welding with ultra-great heat input, it is characterized in that: the chemical composition of described steel plate is by mass percentage: C:0.03～0.12wt%, Si:0.10～0.30wt%, Mn:1.2～2.0wt%, P :≤0.015wt%, S :≤0.008%wt%, Al :≤0.03wt%, Cr :≤0.5wt%, Mo :≤0.5wt%, Nb :≤0.03wt%, Ti:0.005～0.03wt%, Ni:0.01～1.0wt%, Cu:0.01～1.0wt%, N:0.002～0.007wt%, O:0.001～0.006wt%, also include simultaneously Mg, Ca, B, Zr, Ta, or among the REM one or more, its content is respectively by mass percentage: Mg:0.0001～0.005wt%, Ca:0.0001～0.008wt%, B:0.0001～0.003wt%, Zr:0.0001～0.02wt%, Ta:0.0001～0.02wt%, REM:0.0001～0.02wt%, all the other are Fe and inevitable impurity, and carbon equivalent is less than 0.40%; The complex inclusion density that contains the Ti oxide compound that is of a size of 0.2～5 μ m in the steel plate is 100～3000/mm
2, be of a size of the amount of inclusions that contains the Ti nitride of 10～300nm greater than 3 * 10
6Individual/mm
2After the input of 400～1000kJ/cm welding heat ,-20 ℃ of ballistic work mean values are greater than 70J; After the input of 400～1000kJ/cm welding heat, the welded bonds position is organized as proeutectoid ferrite and acicular ferrite, and wherein the original austenite crystal prevention place is the proeutectoid ferrite of Polygons bulk, and average grain size is less than 50 μ m, and the area occupied mark is less than 40%; Original austenite grain inside is fine acicular ferrite, and the area occupied mark is greater than 60%.
2. structural steel for welding with ultra-great heat input as claimed in claim 1, it is characterized in that the Ti-containing complex inclusions in this structure iron, refer to the oxide compound of Ti and Mg, Ca, B, Zr, Ta or REM or one or more complex inclusions that are compounded to form in the sulfide.
3. the manufacture method of structural steel for welding with ultra-great heat input as claimed in claim 1 is characterized in that may further comprise the steps:
(1) smelt: molten iron adds steel scrap and add Si, Mn, Al when converter smelting, adjust molten steel and arrive the dissolved oxygen content of refining stage after 10～300ppm scope, add successively in Ti, Cr, Mo, Cu, Nb, Ni, Mg, Zr, Ta, REM, B, the Ca element two or more, and to control the pitch time that each element adds be 0～20min, carries out continuous casting after reaching the target chemical composition;
(2) continuous casting: adopt Prepared by Low Superheat Pouring and solidification end dynamic soft-reduction technique to carry out continuous casting, crystallizer adopts weak cooling, and secondary cooling zone evenly cools off, top is cold by force, the bottom is weak cold, and namely strand adopts strong cooling from going out crystallizer to the aligning point, and the temperature of aligning point is greater than 950 ℃; Adopt behind the aligning weak cold, the strand cooling in heap that rolls off the production line;
(3) rolling: as to adopt the two-stage control rolling technology, recrystallization zone rolling sequence, 1000～1100 ℃ of start rolling temperatures, pass deformation 10～35%; Non-recrystallization district rolling sequence, 800～950 ℃ of start rolling temperatures, cumulative deformation 40～90%; Rolling rear steel plate thickness is 40～100mm;
(4) cooling: roll the online water-cooled of rear steel plate, begin to cool down temperature 〉=750 ℃, 5～50 ℃/s of speed of cooling, 400～650 ℃ of cooling finishing temperatures, then air cooling is to room temperature.
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| Application Number | Priority Date | Filing Date | Title |
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| CN 201110003621 CN102080193B (en) | 2011-01-10 | 2011-01-10 | Structural steel for welding with ultra-great heat input and manufacturing method thereof |
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| CN 201110003621 CN102080193B (en) | 2011-01-10 | 2011-01-10 | Structural steel for welding with ultra-great heat input and manufacturing method thereof |
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