CN102080189A - Structural steel for high-heat input welding and manufacturing method thereof - Google Patents
Structural steel for high-heat input welding and manufacturing method thereof Download PDFInfo
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Abstract
The invention discloses structural steel for high-heat input welding and a manufacturing method thereof, belonging to the technical field of high-strength steel plates for welding. The structural steel disclosed by the invention comprises the following chemical components in percentage by mass: 0.03-0.12 wt % of C, 0.10-0.30 wt % of Si, 1.2-2.0 wt % of Mn, less than or equal to 0.015 wt % of P, less than or equal to 0.008 wt % of S, less than or equal to 0.03 wt % of Al, less than or equal to 0.5 wt % of Cr, less than or equal to 0.5 wt % of Mo, less than or equal to 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, 0.0001-0.003 wt % of B, 0.0001-0.008 wt % of Ca, 0.002-0.007 wt % of N, 0.001-0.006 wt % of O, and the balance of Fe and inevitable impurities, wherein the equivalent carbon content is less than 0.40%. The structural steel disclosed by the invention is a steel plate for high-heat input welding, which is manufactured by adopting the thermo mechanical control process and through controlling the type, size and number of inclusions in the steel by using the method of controlling the adding amount of alloys in the refining phase. The structural steel and the manufacturing method thereof disclosed by the invention have the advantages that the steel plate has high normal-temperature comprehensive mechanical properties and good low temperature toughness, and after being subjected to 400 kJ/cm high-heat input welding, the steel plate also has good low temperature toughness; and the average impact force value of the steel plate is greater than 70 J at a temperature of minus 20 DEG C.
Description
Technical field
The invention belongs to welding high strength structure plate technical field, particularly a kind of big heat input welding structural steel and iron and manufacture method thereof.
Background technology
For improving operating efficiency, reducing cost, in the construction of large structure, adopted big heat input such as multifibres union melt welding, electro-gas (enclosed) welding, electroslag welding welding technique in the welding sequence in succession.Develop multiple big heat input steel plate for welding both at home and abroad in succession.
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 the input of heat greatly welding " 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-line energy 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, Ti/N is between 2.4～3.2 in the reasonable control steel, can effectively improve the performance of steel plate and welded heat affecting zone, its welding heat input can reach 150KJ/cm; Open clear 61-253344, spy as Japanese Patent Publication 55-026164 communique, spy and open flat 03-264614, spy and open flat 04-143246 and patent the 2950076th and all disclose the nitride that adopts Ti or multiple joint compound and precipitate and promote ferritic forming core, improve CGHAZ toughness.But 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 under 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 that adopts more dystectic Ti as intracrystalline acicular ferrite nucleating particle, thereby improve the method for welding heat influence area toughness.Open as the spy that clear 61-79745, spy open clear 62-103344, the spy opens clear 61-117245, announced that the steel plate that contains the Ti oxide compound can effectively improve 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 deleterious thick ferrite of toughness is formed, prevent embrittlement.But, the fine dispersion in steel of this Ti oxide compound is very difficult, and thickization or become aggregate in metal easily 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 size is reasonable, quantity many and disperse distributes in the steel, then become the direction that numerous investigators make great efforts.
Summary of the invention
At the problem that prior art exists, the invention provides a kind of big heat input structure iron and manufacture method thereof.The steel plate that this method is made under the big heat input welding conditions of 400KJ/cm, still has good low-temperature flexibility.
Big 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%, B:0.0001～0.003wt%, Ca:0.0001～0.008wt%, N:0.002～0.007wt%, O:0.001～0.006wt%, all the other are Fe and unavoidable impurities.
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 scope of steel of the present invention limits the reason explanation:
C: be the element of guaranteeing that armor plate strength is required.C content is lower than at 0.03% o'clock, can not guarantee high strength; If C content is higher than at 0.12% o'clock, can in big 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 low excessively, and then deoxidation effect can not effectively be brought into play, if the welded heat affecting zone embrittlement of too high then steel plate, so be limited to 0.3% on the Si.
Mn: can guarantee armor plate strength and help toughness that Mn content is lower than 1.2% high strength and the excellent toughness that can not guarantee steel plate; Content is higher than at 2.0% o'clock, HAZ toughness deterioration during the large-line energy welding.
P: be the inevitable element of sneaking into as impurity, make steel plate unit elongation and the remarkable deterioration of toughness 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, contain S in right amount, then can be attached to around composite oxides or the nitride with the MnS form as impurity, the forming core that promotes the welded heat affecting zone acicular ferrite with grow up.It is inclusion that the S too high levels then can generate thick MnS and CaS, reduces the steel plate thickness directional properties.And MnS is an inclusion after rolling, can be into strips in the elongation of steel plate heart portion, if size is 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.So S content should be lower than 0.008%.
Al: be the important deoxidant element of smelting process, Al combines with N can also improve armor plate strength.An amount of Al helps the formation of Tiization thing, if greater than 0.03%, will make the toughness deterioration.
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, and big heat input improves HAZ tissue and crystal grain thinning when welding, and improves toughness.Increase if surpass the Ti of 0.03% solid solution, and can form thick Tiization thing, 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, easily produces thermal crack if be higher than 1.0% when welding, reduces HAZ toughness.
B:B can improve slab hardening capacity increases armor plate strength.In the large-line energy welding process, TiN begins dissolving after the HAZ temperature is greater than 1300 ℃, free N is increased, and dissolved N can't separate out TiN again, and B spreads when high temperature soon, be easy at austenite grain boundary poly-partially, combine earlier during cooling and generate BN with N, 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 HAZ flexible and improve.In order to bring into play such effect, the B content requirement is greater than 0.0001%, if surpass the HAZ toughness deterioration of 0.003% steel plate.
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 cost at most if cross.So Ni content optimum range is 0.01～1.0%.
Cr, Mo: all be to the favourable element of raising armor plate strength, surpass 0.5% as if Cr, Mo content, Nb content surpasses 0.03%, then can significantly reduce HAZ toughness.
Ca: can make the MnS system of strip be mingled with nodularization, help to reduce the anisotropy of steel plate and improve the Z directional performance; Simultaneously formed CaO of Ca or CaS are compound and help HAZ toughness with other inclusion.Can form thick inclusion if surpass 0.008%, reduce HAZ toughness.
N: be the bioelement that forms TiN, contain the TiN deficiency that the N amount is then separated out less than 20ppm, if greater than 70ppm, then the N surplus of solid solution reduces HAZ toughness.
O: can guarantee to form the oxide compound of Ti, oxygen level is during greater than 60ppm, and the oxide compound of formation is thick, reduces HAZ toughness.
The manufacture method of big heat input steel plate for welding of the present invention.This method comprises 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 in Ti, Cr, Mo, Cu, Nb, Ni, B, the Ca element two or more successively, and be 0～20min the pitch time of controlling each element interpolation, alloy addition level is pressed steel plate chemical ingredients target value and is added, and carries out continuous casting after reaching the target chemical ingredients;
(2) continuous casting: adopt low overheat cast and solidification end dynamically gently to depress technology and 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 promptly strand adopts strong cooling from going out crystallizer to the aligning point, and the temperature of aligning point is greater than 950 ℃; The aligning back is adopted weak cold.The strand cooling in heap that rolls off the production line;
(3) rolling: as to adopt two stages controlled 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 back steel plate thickness is 20～100mm;
(4) cooling: roll back steel plate online water-cooled, begin to cool down temperature 〉=750 ℃, 5～50 ℃/s of speed of cooling, 400～650 ℃ of cooling finishing temperatures, air cooling is to room temperature then.
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
2The The amount of inclusions that contains the Ti nitride that is of a size of 10～300nm is greater than 3 * 10
6Individual/mm
2, all exceed several times than conventional steel, help 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 control manufacturing 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 big heat input is welded, 1400 ℃ of high temperature positions near welded bonds, form a large amount of intracrystalline 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.
Structure iron is used in big heat input welding of the present invention, rolls attitude steel plate tensile strength 500～800MPa, and after the input of 400KJ/cm welding heat ,-20 ℃ of ballistic work mean values are greater than 70J.Tissue signature after the input of 400KJ/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 big heat input welding high tensile steel plate that uses in the manufacturings such as shipbuilding, bridge, ocean platform, Highrise buildings, pressurized vessel, large-scale petroleum storing tank, in the scope of welding heat input≤400KJ/cm, can effectively guarantee welding heat influence area toughness.
Description of drawings
Fig. 1 is the 400KJ/cm heat input welding heat simulation curve figure that embodiment and comparative example adopt.
Fig. 2 (a) is the metallographic structure figure of embodiment 1 steel after 400KJ/cm heat input Thermal Cycle.
Fig. 2 (b) is the metallographic structure figures of embodiment 2 steel after 400KJ/cm heat input Thermal Cycle.
Fig. 2 (c) is the metallographic structure figures of embodiment 3 steel after 400KJ/cm heat input Thermal Cycle.
Embodiment 1,2,3 among Fig. 2 is after the welding heat input of 400KJ/cm, though original austenite grain is fully grown up about 200～400 μ m, inner crisscross acicular ferrite, the no bainite structure of all forming of original austenite grain; And the proeutectoid ferrite of original austenite crystal prevention is the Polygons bulk, does not all have the lath-shaped ferrite, so steel plate still has good toughness after big heat input welding.
Embodiment
Below will by different embodiment and comparative example to recently describing the present invention.These examples only are the purposes that is used to explain, the present invention is not limited among these embodiment, can be adjusted enforcement in aforementioned chemical ingredients and manufacture method scope.
Embodiment 1
The chemical ingredients 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%, Nh:＜0.03wt%, B:＜0.002wt%, Ti:0.005～0.015wt%, Ni:0.01～0.5wt%, Ca:0.0001～0.002wt%, N:0.002～0.007wt%, O:0.002～0.006wt%, all the other are Fe and unavoidable impurities, 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 Ti, Cr, Mo, Nb, Ni, B, Ca alloying element successively, and to control the pitch time that each element adds be 0～20min, carries out continuous casting after reaching the target chemical ingredients.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; The aligning back is adopted weak cold, and speed of cooling is less than 10 ℃/min.And adopt and gently to depress technology and pour into the 260mm continuously cast bloom, the strand back 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 ℃, air cooling is to room temperature then.
The room temperature tensile strength of 40mm thickness steel plate is 700MPa, unit elongation 23%; After the big heat input of 400KJ/cm Thermal Cycle ,-20 ℃ of ballistic work mean values are 195J.The welded bonds position is organized as proeutectoid ferrite and intracrystalline acicular ferrite, and the proeutectoid ferrite average grain size is 30 μ m, and intracrystalline 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 ingredients and other steel plate of same intensity level, carry out after the big heat of aforesaid 400KJ/cm imports Thermal Cycle ,-20 ℃ of ballistic work mean values are 8J.
Embodiment 2
The chemical ingredients of steel plate is by mass percentage: C:0.08～0.12wt%, Si:0.20～0.25wt%, Mn:1.4～2.0wt%, P:＜0.015wt%, S:＜0.008%wt%, Al:＜0.03wt%, Nb:＜0.03wt%, Ti:0.015～0.03wt%, Ni:0.01～1.0wt%, Cu:0.01～1.0wt%, Ca:0.0001～0.002wt%, B:＜0.003wt%, N:＜0.006wt%, O:＜0.005wt%, all the other are Fe and unavoidable impurities, 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 Ti, Cu, Nb, Ni, B, Ca alloying element successively, and to control the pitch time that each element adds be 0～20min, carries out continuous casting after reaching the target chemical ingredients.Continuous casting process is with embodiment 1.
Rolling technology is: 1080 ℃ of recrystallize stage start rolling temperatures, pass deformation 10～35%, 950 ℃ of non-recrystallization stage start rolling temperatures, cumulative deformation 85%; Begin to cool down 780 ℃ of temperature, with 35 ℃/s speed water-cooled to 530 ℃, air cooling is to room temperature then.
The room temperature tensile strength of 20mm thickness steel plate is 660MPa, unit elongation 25%, and after the big heat input of 400KJ/cm Thermal Cycle ,-20 ℃ of ballistic work mean values are 219J.The welded bonds position is organized as proeutectoid ferrite and intracrystalline acicular ferrite, and the proeutectoid ferrite average grain size is 35 μ m, and intracrystalline 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 ingredientss and other steel plate of same intensity level, carry out after the big heat of aforesaid 400KJ/cm imports Thermal Cycle ,-20 ℃ of ballistic work mean values are 7J.
Embodiment 3
The chemical ingredients of steel plate is by mass percentage: C:0.05～0.10wt%, Si:0.15～0.25wt%, Mn:1.2～1.7wt%, P:＜0.015wt%, S:＜0.008%wt%, Al:＜0.03wt%, Nb:＜0.03wt%, Ti:0.01～0.02wt%, Ca:0.002～0.008wt%, Ni:＜0.5wt%, Cu:＜0.5wt%, Cr:＜0.5wt%, B:＜0.003wt%, N:＜0.006wt%, O:＜0.005wt%, all the other are Fe and unavoidable impurities, the carbon equivalent Ceq=C+Mn/6+Si/24+Ni/40+Cr/5+Mo/4+V/14 of described steel plate (%)=0.37%.
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 in the elements such as Ti, Cr, Cu, Nb, Ni, B, Ca two or more successively, and to control the pitch time that each element adds be 0～20min.Carry out continuous casting after reaching the target chemical ingredients.Continuous casting process is with embodiment 1.
Rolling technology is: 1000 ℃ of recrystallize stage start rolling temperatures, pass deformation 10～25%, 850 ℃ of non-recrystallization stage start rolling temperatures, cumulative deformation 70%.Begin to cool down 790 ℃ of temperature after rolling, with 15 ℃/s speed water-cooled to 620 ℃, air cooling is to room temperature then.
The room temperature tensile strength of 80mm thickness steel plate is 560MPa, unit elongation 26%; After the big heat input of 400KJ/cm Thermal Cycle ,-20 ℃ of ballistic work mean values are 121J.The welded bonds position is organized as proeutectoid ferrite and intracrystalline acicular ferrite, and the proeutectoid ferrite average grain size is 20 μ m, and intracrystalline 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 ingredientss and other steel plate of same intensity level, carry out after the big heat of aforesaid 400KJ/cm imports Thermal Cycle ,-20 ℃ of ballistic work mean values are 10J.
Present embodiment 1,2,3 has chemical ingredients and technological process is simple, the armor plate strength height, and especially steel plate Chinese People's Anti-Japanese Military and Political College heat input welding property is good, and does not need preheating, postwelding not to need to heat-treat before the weldering.Be applicable to the big heat input welding high tensile steel plate that uses in the manufacturings such as shipbuilding, bridge, ocean platform, Highrise buildings, pressurized vessel, large-scale petroleum storing tank.
Claims (8)
1. one kind big heat input is welded and is used structure iron, it is characterized in that: the chemical ingredients of described steel plate is by mass percentage: C:0.03～0.12wt%, Si:0.10～0.30wt%, Mn:1.2～2.0 wt%, P :≤0.015 wt%, S :≤0.008% wt%, Al :≤0.03 wt%, Cr :≤0.5 wt%, Mo :≤0.5 wt%, Nb :≤0.03 wt%, Ti:0.005～0.03 wt%, Ni:0.01～1.0 wt%, Cu: 0.01～1.0wt%, B:0.0001～0.003 wt%, Ca:0.0001～0.008 wt%, N:0.002～0.007 wt%, O:0.001～0.006 wt%, all the other are Fe and unavoidable impurities, and carbon equivalent is less than 0.40%.
2. the described steel plate of claim 1 is characterized in that: roll attitude steel plate tensile strength 500～800MPa, after the input of 400KJ/cm welding heat ,-20 ℃ of ballistic work mean values are greater than 70J.
3. steel plate as claimed in claim 1, tissue signature after the input of 400KJ/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, 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%.
4. the big heat input welding as claimed in claim 1 manufacture method of structure iron is characterized in that may further comprise the steps:
(1) smelt: molten iron is gone into the refining of LF stove behind converter smelting, carries out continuous casting after reaching the target chemical ingredients;
(2) continuous casting: adopt the low overheat cast, the strand cooling in heap that rolls off the production line;
(3) rolling: as to adopt two stages controlled rolling technology, be rolled into 20～100mm thickness steel plate;
(4) cooling: after rolling, steel plate begins to cool down temperature 〉=750 ℃, first water-cooled, air cooling is to room temperature then.
5. the big heat input welding as claimed in claim 4 manufacture method of structure iron, it is characterized in that: in described step (1), add Si, Mn, Al in converter, adjust molten steel and arrive the oxygen level of refining stage after 10～300ppm scope, add in Ti, Cr, Mo, Cu, Nb, Ni, B or the Ca element two or more successively, alloy addition level is pressed steel plate chemical ingredients target value and is added, and to control the pitch time that each element adds be 0～20min.
6. the big heat input welding as claimed in claim 4 manufacture method of structure iron, it is characterized in that: in described step (2), crystallizer adopts weak cooling, and secondary cooling zone evenly cools off, strand adopts strong cooling from going out crystallizer to the aligning point, and speed of cooling is 0.1 ~ 5 ℃/s; The temperature of aligning point is greater than 950 ℃; The aligning back is adopted weak cold, and speed of cooling is less than 10 ℃/min.
7. the big heat input welding as claimed in claim 4 manufacture method of structure iron is characterized in that: in described step (3), and recrystallization zone rolling sequence, 1000～1100 ℃ of start rolling temperatures, pass deformation 10～35%; Non-recrystallization district rolling sequence, 850～950 ℃ of start rolling temperatures, cumulative deformation 40～90%.
8. the big heat input welding as claimed in claim 4 manufacture method of structure iron, it is characterized in that: in described step (4), roll the back steel plate and begin to cool down temperature 〉=750 ℃, with 10～50 ℃/s speed, online water-cooled to 500～650 ℃, air cooling is to room temperature then.
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| CN104745963A (en) * | 2013-12-31 | 2015-07-01 | 天津冶金集团天材科技发展有限公司 | 21-10Mn7Mo steel ingot |
| CN104745964A (en) * | 2013-12-31 | 2015-07-01 | 天津冶金集团天材科技发展有限公司 | Smelting technology of 21-10Mn7Mo steel ingot |
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| CN112139242A (en) * | 2020-08-24 | 2020-12-29 | 龙岩学院 | Steel for large heat input welding and method for improving toughness of heat affected zone of steel |
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| CN104745962A (en) * | 2013-12-31 | 2015-07-01 | 天津冶金集团天材科技发展有限公司 | Smelting method of 21-10Mn7Mo steel ingot |
| CN104745963A (en) * | 2013-12-31 | 2015-07-01 | 天津冶金集团天材科技发展有限公司 | 21-10Mn7Mo steel ingot |
| CN104745964A (en) * | 2013-12-31 | 2015-07-01 | 天津冶金集团天材科技发展有限公司 | Smelting technology of 21-10Mn7Mo steel ingot |
| CN108624819A (en) * | 2017-03-24 | 2018-10-09 | 宝山钢铁股份有限公司 | Low cost, high heat-input weld 460MPa grades of crack arrest steel plates and its manufacturing method |
| CN108624819B (en) * | 2017-03-24 | 2020-08-25 | 宝山钢铁股份有限公司 | Low-cost large-heat-input welding 460 MPa-grade crack arrest steel plate and manufacturing method thereof |
| CN112899558A (en) * | 2020-06-18 | 2021-06-04 | 宝钢湛江钢铁有限公司 | 550 MPa-grade weather-resistant steel plate with excellent weldability and manufacturing method thereof |
| CN112899558B (en) * | 2020-06-18 | 2022-07-05 | 宝钢湛江钢铁有限公司 | 550 MPa-grade weather-resistant steel plate with excellent weldability and manufacturing method thereof |
| CN112139242A (en) * | 2020-08-24 | 2020-12-29 | 龙岩学院 | Steel for large heat input welding and method for improving toughness of heat affected zone of steel |
| CN112139242B (en) * | 2020-08-24 | 2022-07-08 | 龙岩学院 | Steel for large heat input welding and method for improving toughness of heat affected zone of steel |
| CN114150226A (en) * | 2021-12-06 | 2022-03-08 | 东北大学 | Large heat input welding resistant steel plate and production method thereof |
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