CN101481774B - Low crack sensitivity steel plate with yield strength 500MPa and manufacturing method thereof - Google Patents
Low crack sensitivity steel plate with yield strength 500MPa and manufacturing method thereof Download PDFInfo
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Abstract
The invention discloses a crack sensitivity steel plate with the yield strength of 500MPa, which is characterized by comprising the following chemical elements in terms of weight percentage: 0.010 to 0.09 percent of C, 0.10 to 0.65 percent of Si, 1.10 to 2.00 percent of Mn, less than or equal to 0.010 percent of P, less than or equal to 0.006 percent of S, 0.020 to 0.090 percent of Nb, 0.02 to 0.06 percent of Al, 0.004 to 0.030 percent of Ti, 0.0005 to 0.0025 percent of B and the balance of Fe and inevitable impurities. The manufacturing method comprises the following steps: smelting and casting the raw materials into casting blank or steel ingot; 2) heating; 3) rolling; and 4) entering a cooling accelerator, cooling till the temperature of 450 to 560 DEG C, and air cooling after water drainage. The crack sensitivity steel plate has little sensitivity of welded crack, and the welding performance is good when the yield strength is more than 500MPa.
Description
Technical field
The present invention relates to the ferrous metallurgy field, specifically, relate to a kind of low-crackle sensitive steel of yield strength 500MPa level.
Background technology
For the ease of welding and simplification weldprocedure, for physical construction and the employed high-strength steel of engineering construction, require the welding crack sensibility indices P cm of steel low as far as possible, to reach the purpose that need not preheating before the weldering, this steel is called as the low-welding crack-sensitive high-strength steel, also claims CF steel.It is 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; For yield strength 500MPa grade steel plate, the Pcm of general requirement steel≤0.20%.
The only resource that reduces 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, yet, if adopt hot mechanical controlled rolling and controlled cooling technology (TMCP), then can remedy this defective.In addition, with respect to modified (quenching+tempering) technology, hot mechanical controlled rolling and controlled cooling technology (TMCP) thus also have the benefit that crystal grain thinning improves the low-temperature flexibility of steel.
The contrast of the alloying element design mix of the steel grade that patent No. CN139629 and CN1932063 relate to is as shown in table 1.Because Cr, Cu, Mo and Ni are valuable alloying element, therefore especially Mo and Ni price are higher, analyze from the kind of the alloying element that adds, and these two kinds of steel grade smelting cost are higher, and require respectively steel plate to be quenched+tempering and off-line temper manufacturing process's complexity.
The composition contrast (wt%) of the relevant patent steel of table 1
Summary of the invention
The objective of the invention is by a kind of yield strength 500MPa level low-crackle sensitive steel and manufacture method thereof are provided, thereby obtain a kind of welding crack sensibility indices P cm≤0.17%, possess the high tensile steel plate of good low-temperature flexibility and weldability.
Technical scheme of the present invention is: a kind of yield strength 500MPa level low-crackle sensitive steel, the chemical element that comprises following weight percent proportioning: C:0.010～0.09%, Si:0.10～0.65%, Mn:1.10～2.00%, P≤0.010%, S≤0.006%, Nb:0.020～0.090%, Al:0.02～0.06%, Ti:0.004～0.030%, B:0.0005～0.0025%, surplus are Fe and unavoidable impurities.
Below, the chemical ingredients of yield strength 500MPa level low-crackle sensitive steel of the present invention is done as being described in detail.
C: the effect in steel is solution strengthening, be the maximum element of intensity contribution to steel, but C is unfavorable to welding property and toughness.C content is high more, and welding property is poor more, and for the bainitic steel that adopts the TMCP explained hereafter, the low more then toughness of C content is good more, and lower carbon content can be produced the ductility steel plate of bigger thickness, so C content of the present invention is controlled to be 0.010～0.09%.
Si: the effect in steel mainly is solution strengthening, adds the intensity that Si can significantly improve steel, and the welding property of steel is not had tangible negative impact; But the too much affiliation that adds reduces the toughness of steel, and Si content of the present invention is controlled to be 0.10～0.65%.
Mn: the effect in steel mainly is the yield strength that improves steel, can reduce the transition temperature of the austenite of steel to ferrite transformation in addition, by controlled rolling, obtains thinner grain-size, finally increases the intensity and the low-temperature flexibility of steel.
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, owing to strengthened the grain refining effect, make the thickness that can produce steel plate increase, adopt the chemical ingredients of the present invention's design, the maximum ga(u)ge that can produce steel plate is 60mm.
B: can significantly increase the hardening capacity of steel, the present invention adds 0.0005～0.0025% B, can make steel under certain cooling conditions, obtains the high strength bainite structure with comparalive ease.
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%, 60 kg class (yield strength 500MPa) steel can be realized pre-thermo-welding.Welding crack sensibility indices P cm≤0.17% of steel of the present invention.The welding crack sensibility indices P cm 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
A kind of manufacture method of yield strength 500MPa level low-crackle sensitive steel comprises following steps:
(1) smelts, and be cast into strand or steel ingot: the weight percent proportioning by following chemical element is smelted: C:0.010～0.09%, Si:0.10～0.65%, Mn:1.10～2.00%, P≤0.010%, S≤0.006%, Nb:0.020～0.090%, Al:0.02～0.06%, Ti:0.004～0.030%, B:0.0005～0.0025%, surplus are Fe and unavoidable impurities.
(2) heating: Heating temperature is 1080～1180 ℃.
(3) rolling: the breaking down temperature is 1050～1150 ℃ in for the first time rolling, and for the second time rolling, the breaking down temperature is 780～840 ℃, and finishing temperature is 740～850 ℃; For containing the Nb steel, its non-recrystallization temperature is about 950～1050 ℃, rolling steel billet temperature is reduced to 780～840 ℃, purpose is in order to guarantee that it has enough deflections in the non-recrystallization district, increase slip band and dislocation desity in the austenite crystal, increase effective grain boundary area, for the ferritic phase deformed nucleus creates favorable conditions.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 the formation of precipitate and make its more tiny and disperse, simultaneously, tiny and precipitate and pinning effect thereof disperse provide highdensity forming core place and stop it to grow up and alligatoring 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 740～850 ℃, 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.
(4) cooling: steel plate enters accelerated cooling device, is cooled to 450～560 ℃, air cooling after the water outlet.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.
Preferably, in the described step (2), soaking time is 120～180 minutes.
Preferably, in the described step (3), after the breaking down, rolled piece thickness is 2～3 times of Finished Steel plate thickness.
Preferably, in the described step (4), speed of cooling is 5～15 ℃/S, 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.
Preferably, in the described step (4), the mode of air cooling adopts stacking or cold bed cooling.
Beneficial effect of the present invention is:
1. the present invention need not to add noble elements such as Mo, Ni, Cu by rational designing chemical composition, makes full use of the effect of quickening water in the refrigerating work procedure, remedies intensity and toughness reduction that the alloying element disappearance is brought.Therefore raw materials cost reduces greatly, and welding crack sensibility is less, need not preheating before the weldering.
2. steel plate of the present invention adopts hot mechanical controlled rolling and controlled cooling technology (TMCP), need not carry out any extra thermal treatment, thereby simplify manufacturing process, and save energy 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 80mm plate greater than 500MPa, tensile strength greater than 610MPa, Xia Shi ballistic work Akv (20 ℃) 〉=100J, thickness of slab, and steel plate cross section hardness ratio is more even; Welding property is good.
Description of drawings
For a more detailed description below with reference to drawings and Examples to the present invention.
Fig. 1 is the cross section hardness measurement value distribution schematic diagram of the embodiment of the invention 4 steel plates.
Fig. 2 is the welded heat affecting zone maximum hardness measuring result synoptic diagram of the embodiment of the invention 1.
Embodiment
Table 2 is the chemical ingredients (wt%) of the low-crackle sensitive steel of embodiment of the invention 1-6 and the numerical value of welding crack sensibility indices P cm thereof.
Table 2
| Embodiment | C | Si | Mn | Nb | Al | Ti | | Fe | Pcm | |
| 1 | 0.01 | 0.65 | 2.00 | 0.090 | 0.050 | 0.030 | 0.0025 | Surplus | 0.14 | |
| 2 | 0.02 | 0.60 | 1.80 | 0.080 | 0.060 | 0.025 | 0.0020 | Surplus | 0.14 | |
| 3 | 0.04 | 0.50 | 1.65 | 0.060 | 0.055 | 0.020 | 0.0015 | Surplus | 0.15 | |
| 4 | 0.06 | 0.40 | 1.55 | 0.040 | 0.040 | 0.015 | 0.0010 | Surplus | 0.16 | |
| 5 | 0.07 | 0.30 | 1.40 | 0.030 | 0.035 | 0.008 | 0.0008 | Surplus | 0.15 | |
| 6 | 0.09 | 0.10 | 1.30 | 0.020 | 0.020 | 0.004 | 0.0007 | Surplus | 0.16 |
Pcm: welding crack sensibility index
Pcm＝C+Si/30+Ni/60+(Mn+Cr+Cu)/20+Mo/15+V/10+5B
The chemical element per distribution ratio of steel of the present invention is: C:0.01%, Si:0.65%, Mn:2.00%, P≤0.010%, S≤0.006%, Nb:0.090%, Al:0.050%, Ti:0.030%, B:0.0025%, surplus is Fe and unavoidable impurities.
Manufacture method is as follows: Heating temperature is 1080 ℃, is incubated 120 minutes; Fs, rolling start rolling temperature was 1060 ℃, and rolled piece thickness is 90mm; The rolling start rolling temperature of subordinate phase is 780 ℃, and finishing temperature is 740 ℃, and the Finished Steel plate thickness is 30mm; The steel plate speed of cooling is 15 ℃/S, and final temperature is 450 ℃.
The chemical element per distribution ratio of steel of the present invention is: C:0.02%, Si:0.60%, Mn:1.80%, P≤0.010%, S≤0.006%, Nb:0.080%, Al:0.060%, Ti:0.025%, B:0.0020%, surplus is Fe and unavoidable impurities.
Manufacture method is as follows: Heating temperature is 1100 ℃, is incubated 160 minutes; Fs, rolling start rolling temperature was 1090 ℃, and rolled piece thickness is 100mm; The rolling start rolling temperature of subordinate phase is 780 ℃, and finishing temperature is 770 ℃, and the Finished Steel plate thickness is 40mm; The steel plate speed of cooling is 5 ℃/S, and final temperature is 560 ℃.
The chemical element per distribution ratio of steel of the present invention is: C:0.04%, Si:0.50%, Mn:1.65%, P≤0.010%, S≤0.006%, Nb:0.060%, Al:0.055%, Ti:0.020%, B:0.0015%, surplus is Fe and unavoidable impurities.
Manufacture method is as follows: Heating temperature is 1120 ℃, is incubated 150 minutes; Fs, rolling start rolling temperature was 1100 ℃, and rolled piece thickness is 150mm; The rolling start rolling temperature of subordinate phase is 800 ℃, and finishing temperature is 790 ℃, and the Finished Steel plate thickness is 60mm; The steel plate speed of cooling is 12 ℃/S, and final temperature is 500 ℃.
The chemical element per distribution ratio of steel of the present invention is: C:0.06%, Si:0.40%, Mn:1.55%, P≤0.010%, S≤0.006%, Nb:0.040%, Al:0.040%, Ti:0.015%, B:0.0010%, surplus is Fe and unavoidable impurities.
Manufacture method is as follows: wherein Heating temperature is 1140 ℃, is incubated 150 minutes; Fs, rolling start rolling temperature was 1100 ℃, and rolled piece thickness is 150mm; The rolling start rolling temperature of subordinate phase is 820 ℃, and finishing temperature is 850 ℃, and the Finished Steel plate thickness is 80mm; The steel plate speed of cooling is 15 ℃/S, and final temperature is 520 ℃.
The chemical element per distribution ratio of steel of the present invention is: C:0.07%, Si:0.30%, Mn:1.40%, P≤0.010%, S≤0.006%, Nb:0.030%, Al:0.035%, Ti:0.008%, B:0.0008%, surplus is Fe and unavoidable impurities.
Manufacture method is as follows: Heating temperature is 1160 ℃, is incubated 180 minutes; Fs, rolling start rolling temperature was 1100 ℃, and rolled piece thickness is 90mm; The rolling start rolling temperature of subordinate phase is 840 ℃, and finishing temperature is 820 ℃, and the Finished Steel plate thickness is 30mm; The steel plate speed of cooling is 8 ℃/S, and final temperature is 510 ℃.
Embodiment 6
The chemical element per distribution ratio of steel of the present invention is: C:0.09%, Si:0.10%, Mn:1.30%, P≤0.010%, S≤0.006%, Nb:0.020%, Al:0.020%, Ti:0.004%, B:0.0007%, surplus is Fe and unavoidable impurities.
Manufacture method is as follows: Heating temperature is 1180 ℃, is incubated 160 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 finishing temperature is 840 ℃, and the Finished Steel plate thickness is 40mm; The steel plate speed of cooling is 10 ℃/S, and final temperature is 490 ℃.
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 1-4
| Embodiment | Yield strength (MPa) | Tensile strength (MPa) | Unit elongation (%) | -20 ℃ of impact of collision merit/tough break ratios (J/%) |
| 1 | 580， 560 | 700， 690 | 21.0， 22.5 | 325/100， 318/100， 339/100 |
| 2 | 565， 580 | 680， 695 | 23.0， 22.0 | 295/100， 275/100， 268/100 |
| Embodiment | Yield strength (MPa) | Tensile strength (MPa) | Unit elongation (%) | -20 ℃ of impact of collision merit/tough break ratios (J/%) |
| 3 | 600， 600 | 740， 740 | 21.0， 22.5 | 201/100， 198/100， 178/100 |
| 4 | 535， 540 | 710， 720 | 21.5， 22.0 | 185/100， 156/100， 151/100 |
| 5 | 570， 565 | 705， 690 | 21.0， 21.5 | 315/100， 328/100， 319/100 |
| 6 | 600， 610 | 735， 740 | 20.0， 19.5 | 275/100， 248/100， 255/100 |
From table 2 and table 3 as can be seen, the Pcm of low-crackle sensitive steel of the present invention≤0.17%, yield strength is all greater than 500MPa, tensile strength is greater than 610MPa, Xia Shi ballistic work Akv (20 ℃) 〉=100J, thickness of slab can reach 80mm, has good low-temperature flexibility and weldability.
Test example 2
By standard GB/T4340-1999 the cross section hardness of the low-crackle sensitive steel of the embodiment of the invention 4 is measured, observed value is seen Fig. 1.
As can be seen from Figure 1, except that the surface chill layer, the thick section hardness ratio of steel plate of the present invention is more even.
Test example 3
With reference to GB/T4675.5-1984 " solderability test welded heat affecting zone maximum hardness test method " present embodiment 1 has been carried out the welded heat affecting zone maximum hardness test.This test is suitable for covered arc welding, and the test piece for welding size is got 200 * 75 * 30mm.Welding setting is: welding current 170A, weldingvoltage 24V, welding speed 150mm/min.Welding material is Atlantic Ocean J707RH.18 ℃ of envrionment temperatures, humidity 55%.The hardness measurement result as shown in Figure 2.By test-results as seen, the HAZ maximum hardness is positioned at apart from 1mm place, point of contact, welded bonds bottom, and maximum hardness is 301.According to the evaluation criteria of maximum hardness test, when the HAZ maximum hardness＜350 of test steel, generally need not to consider welding preheating or after heat.
Test example 4
The low welding crack sensitivity steel plate of embodiment 5 is carried out little iron ground test, estimated the anti-cold crack performance of this steel grade.Little iron grinds test to carry out with reference to GB/T4675.1-1984 " the oblique Y type of solderability test groove welding crack test method ".This test is suitable for covered arc welding.Welding setting is: welding current 170A, weldingvoltage 24V, welding speed 150mm/min.Welding material is Atlantic Ocean J707RH.The test plate (panel) group is right, weld contained weld seam, measure groove gap in the scope of standard code.Carry out the welding of testing weld then, postwelding naturally cools to room temperature, places the crackle situation of observing again more than 48 hours.Test-results is as shown in table 4.Under test conditions, do not find welding cold cracking.
The little iron of table 4 grinds test-results
| Preheating temperature | Specimen coding | Surface crack rate % | Root crack rate % | Section crack rate % | Envrionment temperature | Relative humidity |
| RT (room temperature) | 1 | 0 | 0 | 0 | 18℃ | 55％ |
| 2 | 0 | 0 | 0 | |||
| 3 | 0 | 0 | 0 | |||
| 50 |
4 | 0 | 0 | 0 | ||
| 5 | 0 | 0 | 0 |
Claims (5)
1. the manufacture method of a yield strength 500MPa level low-crackle sensitive steel is characterized in that comprising following steps:
(1) smelts, be cast into strand or steel ingot: the weight percent proportioning by following chemical element is smelted: C:0.010～0.09%, Si:0.10～0.65%, Mn:1.10～2.00%, P≤0.010%, S≤0.006%, Nb:0.020～0.090%, Al:0.02～0.06%, Ti:0.004～0.030%, B:0.0005～0.0025%, surplus are Fe and unavoidable impurities;
(2) heating: Heating temperature is 1080～1180 ℃;
(3) rolling: the breaking down temperature of fs is 1050～1150 ℃, and the breaking down temperature of subordinate phase is 780～840 ℃, and finishing temperature is 740～850 ℃;
(4) cooling: steel plate enters accelerated cooling device, is cooled to 450～560 ℃, air cooling after the water outlet.
2. the manufacture method of yield strength 500MPa level low-crackle sensitive steel as claimed in claim 1 is characterized in that in the described step (2), soaking time is 120～180 minutes.
3. the manufacture method of yield strength 500MPa level low-crackle sensitive steel as claimed in claim 1 is characterized in that in the described step (3), and after the fs was rolling, rolled piece thickness was 2～3 times of Finished Steel plate thickness.
4. the manufacture method of yield strength 500MPa level low-crackle sensitive steel as claimed in claim 1 is characterized in that in the described step (4), speed of cooling is 5～15 ℃/S.
5. the manufacture method of yield strength 500MPa level low-crackle sensitive steel as claimed in claim 1 is characterized in that in the described step (4), and the mode of air cooling adopts stacking or cold bed cooling.
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| CN103898406B (en) * | 2014-03-25 | 2016-08-24 | 宝山钢铁股份有限公司 | A kind of yield strength 890MPa level low welding crack sensitivity steel plate and manufacture method thereof |
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| WO2007055387A1 (en) * | 2005-11-09 | 2007-05-18 | Nippon Steel Corporation | HIGH-STRENGTH STEEL SHEET OF 450 MPa OR HIGHER YIELD STRESS AND 570 MPa OR HIGHER TENSILE STRENGTH HAVING LOW ACOUSTIC ANISOTROPY AND HIGH WELDABILITY AND PROCESS FOR PRODUCING THE SAME |
| CN101096738A (en) * | 2006-06-26 | 2008-01-02 | 舞阳钢铁有限责任公司 | Steel plate with low welding crack sensitivity and production method thereof |
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| WO2007055387A1 (en) * | 2005-11-09 | 2007-05-18 | Nippon Steel Corporation | HIGH-STRENGTH STEEL SHEET OF 450 MPa OR HIGHER YIELD STRESS AND 570 MPa OR HIGHER TENSILE STRENGTH HAVING LOW ACOUSTIC ANISOTROPY AND HIGH WELDABILITY AND PROCESS FOR PRODUCING THE SAME |
| CN101096738A (en) * | 2006-06-26 | 2008-01-02 | 舞阳钢铁有限责任公司 | Steel plate with low welding crack sensitivity and production method thereof |
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