CN101418418A - Low welding crack sensitivity steel plate with yield strength of 690MPa grade and method for producing the same - Google Patents
Low welding crack sensitivity steel plate with yield strength of 690MPa grade and method for producing the same Download PDFInfo
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Abstract
The invention provides a low crack sensitivity steel plate with the yield strength of 690MPa grade and a method for manufacturing the same. The chemical components of the low crack sensitivity steel plate are as follows: 0.03 to 0.06 weight percent of C, 0.05 to 0.40 weight percent of S, 1.30 to 2.00 weight percent of Mn, 0.05 to 0.15 weight percent of Cr, 0.10 to 0.25 weight percent of Mo, 0.03 to 0.08 weight percent of Nb, 0.04 to 0.12 weight percent of V, 0.02 to 0.04 weight percent of Al, 0.004 to 0.030 weight percent of Ti, 0.0010 to 0.0020 weight percent of B, and the balance being Fe and inevitable impurities, wherein the weld crack sensitivity index Pcm is less than or equal to 0.20 percent. The invention adopts a controlled thermo-mechanical rolling and cooling technology to obtain a matrix structure mainly based on a thinned bainite, which is advantageous for improving the steel strength, the plasticity and the toughness of the steel plate. The yield strength of the low weld crack sensitivity steel plate is greater than 690 MPa; the tensile strength is greater than 700 MPa; the Charpy impact energy Akv (20 DEG C below zero) is more than or equal to 150 J; the plate thickness can reach 60 millimeters; and the welding performance is good.
Description
Technical field
The present invention relates to High Strength Structural Steel, specifically, the present invention relates to the low-crackle sensitive steel of yield strength 690MPa level.
Background technology
Welding cold cracking is the weldprocedure defective of the most normal appearance, and during the strength steel of especially low when welding, interalloy, along with the raising of intensity rank, the tendency that cold crack occurs is increasing.For preventing that cold crack from producing, normally weld preheating, postweld heat treatment, intensity is big more, preheating temperature is also high more, this has caused the complicacy of weldprocedure, not operability in particular cases jeopardizes welded safe reliability, for large-scale steel structure more so.In view of the characteristics of industries such as petrochemical industry, Highrise buildings, bridge, shipbuilding to the not preheating of large-scale high-strength steel structure, not postweld heat treatment, this just requires the welding crack sensibility indices P cm of steel low as much as possible, so metallurgical boundary has begun the development of low welding crack sensibility high-strength steel plate.
The low-welding crack-sensitive high-strength steel, also claim the CF steel, it be a class have superior weldability can and the Hi-Stren steel of low-temperature flexibility, not preheating or preheating and not cracking a little mainly were the welding procedure problems that has solved large-scale steel structure members before its advantage was to weld.The principle of design of low welding crack sensitivity steel reduces carbon and more trace elements alloying exactly, by carbon drop, reduces the tendency of hardenability of steel, improves the toughness of steel, guarantees the intensity of steel simultaneously by more trace elements.Table 1 has been listed the chemical ingredients and the Pcm thereof of more domestic and international similar steel plates.
Chemical ingredients of the domestic and international similar steel plate of table 1 (wt%) and Pcm thereof
| Patent application publication number | C | Si | Mn | Cr | B | Nb | Ni | V | Cu | Mo | Al | Ti | Pcm |
| WO 99/05335 | 0.05 ～0.10 | --- | 1.7 ～2.1 | --- | --- | 0.01 ～0.1 | 0.2 ～1.2 | --- | --- | 0.25 ～0.6 | --- | 0.005 ～0.03 | 0.27 |
| WO 98/38345 | 0.02 ～0.1 | ≤0.6 | 0.2 ～2.5 | 0 ～0.8 | 0 ～0.0025 | 0.01 ～0.1 | 0.2 ～1.2 | 0 ～0.1 | 0 ～0.6 | 0 ～0.6 | ≤0.1 | 0.005 ～0.03 | 0.36 |
| WO 99/05334 | 0.03 ～0.10 | --- | 1.6 ～2.1 | --- | --- | 0.01 ～0.1 | --- | 0.01 ～0.10 | --- | 0.3 ～0.6 | --- | 0.005 ～0.03 | 0.35 |
| CN1521285 | 0.01 ～0.05 | 0.05 ～0.5 | 1.0 ～2.2 | 0.0 ～0.7 | 0.0005 ～0.005 | 0.015 ～0.070 | 0.0 ～1.0 | --- | 0.0 ～1.8 | 0.0 ～0.5 | 0.015 ～0.07 | 0.005 ～0.03 | 0.31 |
| CN1396294 | 0.02 ～0.13 | 0.10 ～0.60 | 0.60 ～1.80 | --- | 0.0005 ～0.002 | 0.008 ～0.04 | ≤0.55 | ≤0.10 | ≤0.65 | ≤0.50 | ≤0.01 | 0.005 ～0.025 | ≤ 0.21 or≤0.23 |
| CN1932063 | 0.06 ～0.09 | 0.15 ～0.55 | 0.85 ～1.10 | ≤0.30 | --- | 0.005 ～0.05 | 0.15 ～0.40 | 0.02 ～0.06 | ≤ 0.30 | ≤0.30 | 0.01 ～0.40 | -- | ≤0.20 |
| CN1932064 | 0.06 ～0.1 | 0.15 ～0.4 | 1.2 ～1.6 | ≤0.3 | --- | 0.015 ～0.045 | 0.15 ～0.4 | 0.02 ～0.06 | --- | 0.15 ～0.3 | 0.015 ～0.045 | 0.01 ～0.034 | ≤0.20 |
From table 1, can find out, except that the disclosed superstrength welding steel of WO99/05334, the chemical ingredients of the disclosed steel of other patent application is all adding alloying element Ni in various degree, alloying element Ni belongs to noble metal, adding Ni can make the steel cost increase, reduce its market competitiveness, and Ni can form oxide skin at surface of steel plate, influence plate surface quality.Except that WO99/05334, WO99/05335 and CN1932064, all added Cu in the chemical ingredients of the disclosed steel of other patent application, that utilizes Cu separates out the increase armor plate strength, avoids copper brittleness but need add Ni simultaneously, has further increased the manufacturing cost of steel plate.Though the disclosed steel grades of WO99/05334 and WO99/05335 is comparatively simple, but all adopted quench treatment, increased the production process of steel plate, caused the increase of steel plate production cost, and their Pcm value is all higher, and welding property is had disadvantageous effect.
In addition, the listed steel grade of table 1 all passes through quenching+temper or temper, owing to reduce the only resource of Pcm is exactly the add-on that reduces carbon and alloying element, and for the high-strength steel that adopts quenching+tempering process to produce, reduce the add-on of carbon and alloying element and will bring the reduction of hardness of steel inevitably, and manufacturing process's complexity.
In order to overcome the above problems, it is steel grade that the present inventor adopts Mn-Nb-Cr-Mo-V-Ti-B, utilizes V to strengthen, by control thermo-mechanical rolling and cooling technology, and need not thermal treatment, designed the low-crackle sensitive steel that a kind of yield strength reaches the 690MPa level, thereby finished the present invention.
Therefore, one object of the present invention is to provide a kind of low-crackle sensitive steel of yield strength 690MPa level.
Another object of the present invention is to provide the manufacture method of described low-crackle sensitive steel.
Summary of the invention
First aspect of the present invention provides a kind of low-crackle sensitive steel of yield strength 690MPa level, the chemical ingredients of this steel plate comprises: C:0.03～0.06wt%, Si:0.05～0.40wt%, Mn:1.30～2.00wt%, Cr:0.05～0.15wt%, Mo:0.10～0.25wt%, Nb:0.03～0.08wt%, V:0.04～0.12wt%, Al:0.02～0.04wt%, Ti:0.004～0.030wt%, B:0.0010～0.0020wt%, surplus is Fe and unavoidable impurities.
Welding crack sensibility indices P cm≤0.20% of described low-crackle sensitive steel.
The welding crack sensibility index .Pcm of low-crackle sensitive steel can determine by following formula:
Pcm＝C+Si/30+Ni/60+(Mn+Cr+Cu)/20+Mo/15+V/10+5B。
Welding crack sensibility indices P cm is the judgement index of the welding cold cracking tendency of reflection steel, and Pcm is low more, and weldability is good more, otherwise then weldability is poor more.Be difficult for when weldability is meant welding well producing welding crack, and the steel of weldability difference is easy to generate crackle, for fear of the generation of crackle, must before welding, carry out preheating to steel, weldability is good more, and then required preheating temperature is low more, otherwise then needs higher preheating temperature.It is generally acknowledged that when Pcm≤0.25%, 80 feather weight (yield strength 690MPa) steel can be realized pre-thermo-welding.
Below, the chemical ingredients of low welding crack sensitivity steel plate with yield strength of 690 MPa grade of the present invention is done as being described in detail.
C: the effect in steel is solution strengthening, but C is unfavorable to welding property.C content is high more, welding property is poor more, for the bainitic steel that adopts the TMCP explained hereafter, reduce the C content in the steel, can eliminate C influences the bainite flexible, obtain the superfine bainite matrix that contains high dislocation density, and lower carbon content can produce the ductility steel plate of bigger thickness, so C content of the present invention is controlled to be 0.03～0.06wt%.
Mo: improve the hardening capacity of steel, the present invention only need add the Mo that is no more than 0.25wt%, because Mo is unfavorable to welding property, Mo is a kind of very expensive element simultaneously, its price is the several times of Cr, so the present invention replaced part Mo with Cr, to reach the purpose that reduces cost.
Nb: the present invention is by adding more Nb, to reach the purpose of crystal grain thinning and increase steel plate thickness, be the non-recrystallization temperature that improves steel on the other hand on the one hand, be convenient in the operation of rolling, adopt higher relatively finishing temperature, thereby the quickening roll speed is enhanced productivity.In addition,, make the thickness that to produce steel plate increase, added the Nb of 0.03～0.08wt% in the steel grade of the present invention, can produce the steel plate that thickness reaches 60mm owing to strengthened the grain refining effect.
Si: the effect in steel is solution strengthening, also can improve the hardening capacity of steel, adds intensity and the toughness that the Si that is no more than 0.40wt% helps improving steel in the steel of the present invention.
V: in steel, combine, form fine precipitation particles, play the precipitation strength effect with N and C.The present invention adds the V of 0.04～0.12wt%, can improve the intensity of steel greatly; V and Cu have been the precipitation strength effect in steel, but relative Cu, only need to add the V of minute quantity, can reach equal precipitation strength effect.In addition, Cu causes grain-boundary crack easily in steel, thereby must adding reaches the Ni of its half content at least, just can avoid crackle, and Ni is very expensive alloying element equally.Therefore, can reduce the manufacturing cost of steel significantly with V replaced C u.
B: can significantly increase the hardening capacity of steel, the present invention adds the B of 0.001～0.002wt%, can make steel under certain cooling conditions, obtains the high strength bainite structure with comparalive ease.
Second aspect of the present invention provides a kind of manufacture method of low welding crack sensitivity steel plate with yield strength of 690 MPa grade, this method comprises smelting, casting, heating, rolling, refrigerating work procedure, wherein promptly enters refrigerating work procedure without thermal treatment behind described rolling process.
In a preferred implementation: the continuously cast bloom after the casting or the thickness of steel ingot are not less than 4 times of Finished Steel plate thickness.
In another preferred implementation: in described heat-processed, Heating temperature is 1080～1180 ℃, and soaking time is 120～180 minutes.
In another preferred implementation: describedly rollingly be divided into the fs and subordinate phase is rolling.
In another preferred implementation: in the described fs operation of rolling, start rolling temperature is 1050～1150 ℃, when rolled piece thickness arrives 2～3 times of Finished Steel plate thickness, treats that on roller-way temperature is to 820～860 ℃.
In another preferred implementation: in the described subordinate phase operation of rolling, pass deformation rate is 10～25%, and finishing temperature is 770～830 ℃.
In another preferred implementation: in described process of cooling, steel plate enters accelerated cooling device, is cooled to 450～550 ℃, air cooling after the water outlet with the speed of 12～25 ℃/S.
In another preferred embodiment: air cooling adopts stacking or cold bed cooling.
In the manufacture method of low welding crack sensitivity steel plate with yield strength of 690 MPa grade of the present invention, hot mechanical controlled rolling and controlled cooling technology (TMCP) have been adopted, with respect to modified (quenching+tempering) technology, hot mechanical controlled rolling and controlled cooling technology (TMCP) thus have the benefit that crystal grain thinning improves the low-temperature flexibility of steel.Technology controlling and process principle analysis to the key step in the manufacture method of the present invention is as follows:
1, rolling technology
When rolled piece thickness arrives 2～3 times of Finished Steel plate thickness, treat that on roller-way temperature is to 820～860 ℃.For containing the Nb steel, its non-recrystallization temperature is about 950～1050 ℃, rolling steel billet temperature is reduced to 820～860 ℃, purpose is in order to guarantee that it has enough deflections in the non-recrystallization district, more highdensity dislocation accumulative total is arranged, for ferrite transformation provides more favourable forming core condition in the austenite of distortion.Bigger distortion also helps the separating out of carboritride of Nb, because the effect that deformation inductdion is separated out, bigger pass deformation rate will help forming more tiny and disperse precipitate.Simultaneously, precipitate tiny and disperse provides highdensity forming core place and stops ferrite crystal grain to be grown up and alligatoring by its pinning effect to the interface of growing up for ferrite, and this strength and toughness for steel all plays favourable effect.
Finishing temperature is controlled at the low-temperature zone in non-recrystallization district, and this humidity province is near transformation temperature Ar simultaneously
3, promptly finishing temperature is 770～830 ℃, finish to gauge in this temperature range both for phase transformation provides higher energy accumulation, also was unlikely to bring too high load to milling train, relatively was suitable for slab production.
2, process for cooling
After the rolling end, steel plate enters accelerated cooling device, is cooled to 450～550 ℃ by 12～25 ℃/second speed.Because steel plate has accumulated very high dislocation of density and high strain energy in the operation of rolling, highdensity dislocation will with precipitate Nb (CN) particle interaction of Nb, finish to quickening in refrigerative air cooling (relaxation) process rolling, this interaction impels at the inner tiny Polygons dislocation cell structures in a large number that form of austenite crystal, the Nb atom has been stablized this Polygons cell structure with certain misorientation poly-partially and a large amount of fine Nb (CN) the separating out on the dislocation cell wall on the dislocation wall.Simultaneously, the moderate finite deformation of a passage has the effect of inducing ferrite transformation, under this inducing action, and Ar
3Point increases, and so-called " strain-induced transformation " phenomenon promptly occurs, at the bigger deflection in non-recrystallization humidity province, will help the intracrystalline forming core of acicular ferrite, can make martensite island on the bainite matrix even dispersion more that distributes simultaneously.
Adopting faster, cooling rate is for higher condensate depression is provided for bainite transformation, increase phase driving force, obtain more highdensity nucleation rate, thereby obtain matrix, make steel plate of the present invention have higher intensity and good toughness based on the bainite of refinement.
Beneficial effect of the present invention is:
1, passes through rational designing chemical composition, reduce C content significantly, and substitute part Mo with cheap alloying elements such as Mn and Cr, C, the fine precipitation particles of N chemical combination with V are made precipitation strength, and the precipitation strength effect of replaced C u need not to add noble elements such as Ni, and alloying element content is few, raw materials cost is lower, and welding crack sensibility is less, need not preheating before the weldering.
2, steel plate of the present invention need not carry out any extra thermal treatment, thereby has simplified manufacturing process, has reduced the manufacturing cost of steel.
3, because composition and technological design are reasonable, and from implementation result, process system is looser, can in, Plate Steel produces stably manufactured on the line.
4, low-crackle sensitive steel yield strength of the present invention can reach the 60mm plate greater than 690MPa, tensile strength greater than 770MPa, Xia Shi ballistic work Akv (-20 ℃) 〉=150J, thickness of slab, and steel plate cross section hardness is even.
Description of drawings
Fig. 1 is the low-crackle sensitive steel cross section hardness measured value of the embodiment of the invention 6.
Embodiment
Below for a more detailed description to the present invention in conjunction with the accompanying drawings with embodiment.These embodiment only are the descriptions to best mode for carrying out the invention, scope of the present invention are not had any restriction.
Embodiment 1
Press chemical ingredients electric furnace or the converter smelting shown in the table 2, and be cast into continuously cast bloom or steel ingot, continuously cast bloom or steel ingot are heated to 1080 ℃, are incubated 120 minutes, the fs, rolling start rolling temperature was 1050 ℃, when rolled piece thickness is 60mm, treat temperature to 850 ℃ on roller-way, it is rolling to carry out subordinate phase subsequently, and subordinate phase rolling pass deformation rate is 15～20%, finishing temperature is 830 ℃, and the Finished Steel plate thickness is 20mm.After the rolling end, steel plate enters and quickens cooling (ACC) device, is cooled to 450 ℃, stacking or cold bed cooling after the water outlet with the speed of 25 ℃/S.
Embodiment 2
Embodiment is with embodiment 1, and wherein Heating temperature is 1130 ℃, is incubated 150 minutes; Fs, rolling start rolling temperature was 1060 ℃, and rolled piece thickness is 90mm; The rolling start rolling temperature of subordinate phase is 860 ℃, and pass deformation rate is 10～12%, and finishing temperature is 810 ℃, and the Finished Steel plate thickness is 30mm; The steel plate speed of cooling is 20 ℃/S, and final temperature is 490 ℃.
Embodiment 3
Embodiment is with embodiment 1, and wherein Heating temperature is 1150 ℃, is incubated 150 minutes; Fs, rolling start rolling temperature was 1080 ℃, and rolled piece thickness is 120mm; The rolling start rolling temperature of subordinate phase is 830 ℃, and pass deformation rate is 10～25%, and finishing temperature is 820 ℃, and the Finished Steel plate thickness is 40mm; The steel plate speed of cooling is 15 ℃/S, and final temperature is 530 ℃.
Embodiment 4
Embodiment is with embodiment 1, and wherein Heating temperature is 1120 ℃, is incubated 180 minutes; Fs, rolling start rolling temperature was 1070 ℃, and rolled piece thickness is 150mm; The rolling start rolling temperature of subordinate phase is 830 ℃, and pass deformation rate is 10～15%, and finishing temperature is 800 ℃, and the Finished Steel plate thickness is 50mm; The steel plate speed of cooling is 15 ℃/S, and final temperature is 515 ℃.
Embodiment is with embodiment 1, and wherein Heating temperature is 1180 ℃, is incubated 180 minutes; Fs, rolling start rolling temperature was 1150 ℃, and rolled piece thickness is 120mm; The rolling start rolling temperature of subordinate phase is 840 ℃, and pass deformation rate is 10～15%, and finishing temperature is 810 ℃, and the Finished Steel plate thickness is 60mm; The steel plate speed of cooling is 12 ℃/S, and final temperature is 540 ℃.
Embodiment 6
Embodiment is with embodiment 1, and wherein Heating temperature is 1120 ℃, is incubated 180 minutes; Fs, rolling start rolling temperature was 1070 ℃, and rolled piece thickness is 120mm; The rolling start rolling temperature of subordinate phase is 820 ℃, and pass deformation rate is 10～15%, and finishing temperature is 770 ℃, and the Finished Steel plate thickness is 40mm; The steel plate speed of cooling is 20 ℃/S, and final temperature is 550 ℃.
The chemical ingredients (wt%) and the Pcm thereof of the low-crackle sensitive steel of table 2 embodiment of the invention 1-6
| Embodiment | C | Si | Mn | Nb | V | Al | Ti | Cr | Mo | B | Fe | Pcm |
| 1 | 0.04 | 0.35 | 1.80 | 0.080 | 0.055 | 0.02 | 0.01 | 0.10 | 0.10 | 0.0018 | Surplus | 0.168 |
| 2 | 0.03 | 0.36 | 2.00 | 0.065 | 0.04 | 0.03 | 0.004 | 0.05 | 0.22 | 0.0015 | Surplus | 0.171 |
| 3 | 0.06 | 0.20 | 1.35 | 0.075 | 0.12 | 0.04 | 0.012 | 0.15 | 0.18 | 0.0011 | Surplus | 0.172 |
| 4 | 0.05 | 0.40 | 1.90 | 0.040 | 0.07 | 0.03 | 0.01 | 0.10 | 0.12 | 0.0011 | Surplus | 0.184 |
| 5 | 0.06 | 0.05 | 1.84 | 0.065 | 0.11 | 0.03 | 0.02 | 0.05 | 0.20 | 0.0010 | Surplus | 0.186 |
| 6 | 0.06 | 0.15 | 1.30 | 0.030 | 0.10 | 0.02 | 0.03 | 0.10 | 0.25 | 0.0020 | Surplus | 0.172 |
Test example 1
Low-crackle sensitive steel to embodiment of the invention 1-6 carries out Mechanics Performance Testing, and test result sees Table 3.
The mechanical property of the low-crackle sensitive steel of table 3 embodiment of the invention 1-6
| Embodiment | Yield strength (MPa) | Tensile strength (MPa) | Unit elongation (%) | -20 ℃ of impact of collision merit/tough break ratios (J/%) |
| 1 | 755/745 | 830/835 | 17.0/16.5 | 333/100，303/100，322/100 |
| 2 | 745/740 | 840/835 | 16.0/16.5 | 344/100，336/100，332/100 |
| 3 | 740/750 | 825/825 | 16.0/16.0 | 299/100，295/100，292/100 |
| 4 | 730/740 | 825/835 | 17.5/18.0 | 309/100，310/100，298/100 |
| 5 | 710/715 | 820/825 | 17.5/18.5 | 320/100，344/100，320/100 |
| 6 | 710/705 | 805/795 | 20.0/20.0 | 299/100，307/100，294/100 |
From table 2 and table 3 as can be seen, the Pcm of low-crackle sensitive steel of the present invention≤0.20%, yield strength is all greater than 690MPa, tensile strength is greater than 770MPa, Xia Shi ballistic work Akv (-20 ℃) 〉=150J, thickness of slab can reach 60mm, has good low-temperature flexibility and weldability.
Test example 2
By standard GB/T 4340-1999 the cross section hardness of the low-crackle sensitive steel of the embodiment of the invention 6 is measured, observed value is seen Fig. 1.
As can be seen from Figure 1, the cross section hardness of steel plate of the present invention is even.
Test example 3
Low-crackle sensitive steel to the embodiment of the invention 1 carries out welding performance test (little iron grinds test), under the condition of 0 ℃, room temperature and 50 ℃, all do not find crackle (seeing Table 4), illustrate that the welding property of steel plate of the present invention is good, generally do not need preheating during welding.
The low-crackle sensitive steel welding performance test result of table 4 embodiment of the invention 1
Claims (10)
1, a kind of low welding crack sensitivity steel plate with yield strength of 690 MPa grade, it is characterized in that, the chemical ingredients of described low-crackle sensitive steel comprises: C:0.03～0.06wt%, Si:0.05～0.40wt%, Mn:1.30～2.00wt%, Cr:0.05～0.15wt%, Mo:0.10～0.25wt%, Nb:0.03～0.08wt%, V:0.04～0.12wt%, Al:0.02～0.04wt%, Ti:0.004～0.030wt%, B:0.0010～0.0020wt%, surplus is Fe and unavoidable impurities.
2, low welding crack sensitivity steel plate with yield strength of 690 MPa grade according to claim 1 is characterized in that, welding crack sensibility indices P cm≤0.20% of described steel plate.
3, the manufacture method of the described low welding crack sensitivity steel plate with yield strength of 690 MPa grade of claim 1 comprises smelting, casting, heating, rolling, refrigerating work procedure, it is characterized in that, promptly enters refrigerating work procedure without thermal treatment behind described rolling process.
4, the manufacture method of low welding crack sensitivity steel plate with yield strength of 690 MPa grade according to claim 3 is characterized in that, the continuously cast bloom after the casting or the thickness of steel ingot are not less than 4 times of Finished Steel plate thickness.
5, the manufacture method of low welding crack sensitivity steel plate with yield strength of 690 MPa grade according to claim 3 is characterized in that, in described heat-processed, Heating temperature is 1080～1180 ℃, and soaking time is 120～180 minutes.
6, the manufacture method of low welding crack sensitivity steel plate with yield strength of 690 MPa grade according to claim 3 wherein saidly rollingly is divided into the fs and subordinate phase is rolling.
7, the manufacture method of low welding crack sensitivity steel plate with yield strength of 690 MPa grade according to claim 6, it is characterized in that, in the described fs operation of rolling, start rolling temperature is 1050～1150 ℃, when rolled piece thickness arrives 2～3 times of Finished Steel plate thickness, treat that on roller-way temperature is to 820～860 ℃.
8, the manufacture method of low welding crack sensitivity steel plate with yield strength of 690 MPa grade according to claim 6 is characterized in that, in the described subordinate phase operation of rolling, pass deformation rate is 10～25%, and finishing temperature is 770～830 ℃.
9, the manufacture method of low welding crack sensitivity steel plate with yield strength of 690 MPa grade according to claim 3, it is characterized in that in described process of cooling, steel plate enters accelerated cooling device, speed with 12～25 ℃/S is cooled to 450～550 ℃, air cooling after the water outlet.
10, the manufacture method of low welding crack sensitivity steel plate with yield strength of 690 MPa grade according to claim 9, wherein said air cooling adopt stacking or cold bed cooling.
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