CN102251173B - High-strength and high-toughness steel plate for low-cost and high linear energy welding - Google Patents
High-strength and high-toughness steel plate for low-cost and high linear energy welding Download PDFInfo
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- CN102251173B CN102251173B CN201010173104.4A CN201010173104A CN102251173B CN 102251173 B CN102251173 B CN 102251173B CN 201010173104 A CN201010173104 A CN 201010173104A CN 102251173 B CN102251173 B CN 102251173B
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Abstract
The invention discloses a high-strength and high-toughness steel plate for low-cost and high linear energy welding, comprising the following components in percentage by weight: more than 0.06 and not more than 0.15 percent of C, more than 0.05 percent and not more than 0.25 percent of Si, not less than 1.30 percent and less than 1.80 percent of Mn, less than 0.01 percent of P, less than 0.005 percent of S, more than 0.02 percent and not more than 0.10 percent of Al, not less than 0.006 percent and not more than 0.02 percent of N and more than 0.05 percent and not more than 0.02 percent of Ti; meanwhile, the requirements that the Ti/N is not more than 3.42, the thickness of the steel plate is 20-40mm, the yield strength reaches over 400MPa and the tensile strength is over 500MPa are met; the invention is suitable for a high-strength and high-toughness steel plate of which the welding line energy is 200-400kJ/cm; and the -20oC average impact energy of a steel plate HAZ (Heat Affected Zone) is over 200J. According to the high-strength and high-toughness steel plate disclosed by the invention, by increasing the content of nitrogen in the steel, the low-temperature toughness of a high linear energy welding heat affected zone of the steel plate is greatly improved.
Description
Technical field
The present invention relates to a kind of Hi-Stren steel, relate in particular to a kind of low cost Large Heat Input Welding high-strength high-toughness steel plate.
Background technology
Low alloy steel (comprising micro-alloyed steel) is one of structured material of engineering Application Areas usage quantity maximum, is widely used in the industries such as petroleum natural gas pipeline, shipbuilding, bridge, Highrise buildings, pressurized vessel, petroleum storage tank.In order to enhance productivity, the weldability of above-mentioned industry to steel plate, especially the requirement of Large Heat Input Welding is more and more higher, but Large Heat Input Welding easily brings a more serious problem, be the weld seam toughness severe exacerbation of welded heat affecting zone (Heat Affected Zone is designated hereinafter simply as HAZ) around, brittle failure very easily occurs.For traditional steel plate as for micro-alloyed steel, its weld heat input is generally no more than 50kJ/cm, in this case, HAZ toughness deterioration problem does not show especially out completely, and work as weld heat input, reach certain level, when as even higher above in 200kJ/cm, traditional low alloy steel is just difficult to meet welding requirements, and this just need to solve Large Heat Input Welding HAZ embrittlement problem.From Thermal Cycle angle, in Large Heat Input Welding process, near temperature HAZ can reach 1400
oc is even higher, high-temperature residence time and t
8/5(temperature is from 800
oc is cooled to 500
oc required time) greatly extend cooling time, this just causes austenite crystal significantly to grow up, in Slow cooling process subsequently, form thick to the disadvantageous tissue of toughness, as thick in grain boundaries grain boundary ferrite, ferrite side plate, Widmannstatten structure, M-A (Martensite-Austenite constituent martensite-austenite) island etc.
In existing high input energy welding steel plate all in various degree be added with Ni, Mo, Nb, the precious metal elements such as V, as Chinese patent CN200410017255.5 and Chinese patent CN200580012110.9 have added a large amount of Ni, Mo in steel alloy, Nb, the precious metal elements such as V, although these precious metal elements can improve the welding property of high input energy welding steel plate to a certain extent, these noble metals have improved production cost greatly; Aspect weld heat input, in existing high input energy welding steel plate, weld heat input is all lower, and between 50-150kJ/cm, and welding heat simulated peak temperature is lower (conventionally 1350
oc), welding heat simulation t
8/5cooling time is shorter, is less than 200s.Although Chinese patent CN200580012110.9 can reach the weld heat input of 200-1000kJ/cm, but from the angle of alloy designs, the alloying element adding is too many, as the addition at least 0.8% of noble metal Ni, interpolation noble metal Nb in various degree in addition, V, Mo etc., and this patent adopts is Oxide Metallurgy technique, its gordian technique is steelmaking process, and this also makes production cost greatly improve.
Summary of the invention
The object of the present invention is to provide a kind of low cost Large Heat Input Welding high-strength high-toughness steel plate, this steel plate chemical composition is simple, and yield strength and tensile strength are high, under the condition of 200-400kJ/cm Large Heat Input Welding, and-20 of steel plate HAZ
omore than the average ballistic work of C reaches 200J.
A kind of low cost Large Heat Input Welding high-strength high-toughness steel plate, below all by weight percentage, contain: 0.06% < C≤0.15%, 0.05% < Si≤0.25%, 1.30%≤Mn < 1.80%, P < 0.01%, S < 0.005%, 0.02% < Al≤0.10%, 0.006%≤N≤0.02%, 0.005% < Ti≤0.02%, its surplus is Fe and inevitable impurity, above-mentioned chemical composition meets simultaneously: Ti/N≤3.42,
Described steel plate thickness is 20-40mm, more than yield strength reaches 400MPa, more than tensile strength 500MPa, is applicable to the high-strength high-toughness steel plate of weld heat input within the scope of 200-400kJ/cm ,-20 of steel plate HAZ
othe average ballistic work of C is more than 200J.
The production technique of a kind of low cost Large Heat Input Welding of the present invention high-strength high-toughness steel plate is: in converter or electrosmelting-vacuum oven secondary refining-strand or steel ingot-steel billet or reheat-TMCP of steel ingot (thermomechanical controlled working)+water, accelerate cooling-steel plate.
The present invention becomes component selections foundation:
(1) carbon is element the most basic in steel, to improving the intensity of steel, plays very important effect, and yield strength to steel, tensile strength etc. have the greatest impact, but unfavorable to the weldability of steel.Conventionally, carbon content in steel (or carbon equivalent) is higher, and the welded H AZ toughness of steel after welding is poorer, particularly especially true when Large Heat Input Welding.Therefore,, in order to improve the Large Heat Input Welding HAZ low-temperature flexibility of steel plate, in steel, the content of carbon should be controlled in lower level as far as possible.Carbon content reduces the quantity that can effectively reduce martensite-austenite constituent, and martensite-austenite constituent has totally unfavorable effect to the large-line energy HAZ of steel.According to armor plate strength rank difference, can adjust accordingly carbon content, but carbon content should not exceed 0.15%, therefore the addition of carbon in steel is controlled in the scope of 0.06% < C≤0.15%.
(2) silicon is one of element the most basic in steel, and the intensity, the purification ferrite that improve steel are played to advantageous effect.In the process of cooling of steel, silicon can postpone cementite and separate out.Silicon is normally disadvantageous to the weldability of steel.In order to improve the Large Heat Input Welding low-temperature flexibility of steel plate HAZ, in steel, the content of silicon also should be controlled in lower level.When the content of silicon is suitable, can make steel there is good over-all properties, therefore the content of silicon in steel is controlled to 0.05% < Si≤0.25%.
(3) manganese is the element that expands austenite phase region, can reduce the critical cooling velocity of steel, and stable austenite is postponed austenite to pearlitic transformation.Within the scope of low levels, steel is had to very large strengthening effect, thereby simultaneously manganese can also refinement ferrite crystal grain improves the low-temperature flexibility of steel plate.Do not adding in the situation of other alloying elements (as Cu, Ni, Cr, Mo, W etc.), the content of manganese generally should be controlled at more than 1.3% to guarantee the intensity of steel plate; And in the situation that adding above-mentioned alloying element, the content of manganese can be reduced to 1.0% left and right; But then, in steel, the content of manganese is unsuitable too high, as easily in continuously cast bloom, form segregation while exceeding 1.8%, simultaneously the sulphur in steel is combined and is formed thicker MnS and be mingled with, in the follow-up operation of rolling, the thick MnS with certain toughness will be along rolling to extension, the anti-lamellar tearing performance of the Z-direction of performance, the especially steel plate of severe exacerbation mother metal steel plate.The Large Heat Input Welding HAZ toughness of manganese on steel plate affect more complicated, manganese content is different with welding conditions, the toughness of HAZ also shows different effects.Therefore, in steel, the content of manganese is controlled at the steel plate that can obtain welding property excellence between 1.3%≤Mn < 1.8%.
(4), in steel during the content of phosphorus higher (>=0.1%), form Fe
2p separates out around crystal grain, reduces plasticity and the toughness of steel, therefore its content is more low better, is controlled at P < 0.01% during actual production.
(5) when sulphur content is higher in steel, with the eutectiferous form of FeS-Fe, be present in around the crystal grain of steel, reduce the mechanical property of steel, its content and seemingly Phosphorus, is also more low better, is conventionally controlled at S < 0.005% during actual production.
(6) aluminium is one of key element in the present invention, and the effect of aluminium in steel is mainly in steelmaking process, to carry out deoxidation.In addition, aluminium also can the nitrogen in steel be combined and be formed AlN, in Thermal Cycle process, because TiN particle partly or entirely dissolves the nitrogen-atoms discharging, can in cooling process, combine with the part aluminium in steel, thereby play the effect of fixed nitrogen.Therefore, in steel, the addition of aluminium and the content of nitrogen have certain dependency.Conventionally the content of nitrogen in steel is higher, the content of the especially sour molten aluminium of the content of aluminium also should correspondingly improve, therefore the addition of aluminium is higher than traditional micro-alloyed steel outline, in steel, the content of aluminium will be controlled within the specific limits, is controlled at 0.02% < Al≤0.10%.
(7) add-on of titanium is corresponding with the add-on of nitrogen in steel.For high input energy welding steel plate, Ti/N is controlled at the stoichiometric ratio of Ti/N and is advisable below 3.42.If Ti/N is greater than 3.42, in steel, will form thicker TiN particle, and comparatively small amt, not only do not have the effect of pinning original austenite grain in welding process, and the impelling strength of HAZ is caused to very disadvantageous consequence, thick TiN particle can become the formation of crack of fracture.In addition,, in Thermal Cycle process, also will there is alligatoring at hot stage in TiN particle, further aggravate this detrimental action.Therefore, in steel, the content of titanium will be controlled at suitable lower level, and the add-on of titanium is controlled at 0.005% < Ti≤0.02%.
(8) nitrogen is one of key element in the present invention.Under normal circumstances, in steel-making starting material, all contain to some extent a certain amount of nitrogen, its scope is between 0.002-0.004%.In the situation that Ti content is certain, increase solid solubility temperature that N content can make TiN in welding process from original 1400
oc brings up to 1450 below
omore than C.The raising of TiN solid solubility temperature can greatly suppress the high temperature of welded heat affecting zone austenite crystal grows up, thereby improves intensity and the toughness of HAZ.At Ti content, fix, in the lower situation of N content, the solid solubility temperature of TiN can be reduced to 1400
obelow C.In the process of welding, thereby TiN particle can be solidly soluted into the coarsening that causes austenite crystal in austenite, does not just have the effect of " pinning " refine austenite crystal grain, and the toughness nature after welding is just very poor.But the content of N is also unsuitable too high, otherwise in welding process, owing to there is unnecessary " free nitrogen " in steel, this will reduce the Large Heat Input Welding HAZ toughness of steel greatly.Therefore, the add-on of nitrogen can be controlled in 0.006%≤N≤0.02%.
(9) oxygen is inevitable impurity element in steelmaking process, and for the purpose of the present invention, in steel, the content of oxygen generally can reach 0.003% by after aluminium deoxidation, on the performance of steel plate, can not cause significant adverse impact.Therefore, by the Control for Oxygen Content in steel in 0.003%.
The present invention has following beneficial effect: more than steel plate yield strength reaches 400MPa, more than tensile strength 500MPa, and thickness is in 40mm, and this steel plate is applicable to the Large Heat Input Welding of heat input within the scope of 200-400kJ/cm, and beneficial effect comprises following 3 aspects:
(1) the Large Heat Input Welding HAZ excellent in low temperature toughness of steel plate.Steel plate is 400kJ/cm at weld heat input, peak temperature 1400
oc, high-temperature residence time 3s, and t
8/5be that under the welding heat simulated conditions of 383s, the HAZ of steel plate is-20 cooling time
oaverage ballistic work under C condition is up to more than 200J, and this shows to adopt the steel plate that the present invention produces to have very excellent Large Heat Input Welding low-temperature flexibility.
(2) production cost of steel plate significantly reduces, and this is also one of feature of the present invention.The present invention is on the composition basis of traditional Ti micro-alloyed steel, by improving the content of nitrogen in steel, greatly improved the Large Heat Input Welding heat affected zone low-temperature flexibility of steel plate, realizing that low cost fabrication goes out can Large Heat Input Welding and have a steel plate of excellent HAZ low-temperature flexibility.
Accompanying drawing explanation
The rolling technology flow process of Fig. 1 for adopting in the embodiment of the present invention;
The welding thermal cycle curve of Fig. 2 for adopting in the embodiment of the present invention.
Embodiment
Table 1 is listed the chemical composition of 1# ~ 6# steel billet steel (ingot) in the embodiment of the present invention, and its surplus is Fe and inevitable impurity, and above-mentioned chemical composition meets simultaneously: Ti/N≤3.42.The production technique of a kind of low cost Large Heat Input Welding of the present invention high-strength high-toughness steel plate is: in converter or electrosmelting-vacuum oven secondary refining-strand or steel ingot-steel billet or reheat-TMCP of steel ingot (thermomechanical controlled working)+water, accelerate cooling-steel plate.Steel billet or steel ingot reheat temperature and rolling technological parameter is: steel billet or steel ingot reheat temperature: 1100 ~ 1200
oc, soaking time: 1 ~ 2 hour, start rolling temperature: 900 ~ 1070
oc, depresses greatly and accumulative total deflection>=80% at the above multi-pass of non-recrystallization temperature (Non-recrystallization temperature is referred to as Tnr), 850
oc left and right intermediate blank is treated temperature, then carries out last 2-3 passage rolling; Finishing temperature 800-850
oc finally accelerates coolingly in water, and concrete rolling technology route is referring to Fig. 1.According to the rolling technological parameter processing of table 2, finally make the steel plate of thickness at 20-40mm in an embodiment, the mechanical property of steel plate is in Table 2.
As can be seen from Table 1 and Table 2, do not adding precious metal element Ni, Mo, Nb, in the situation of V etc., more than steel plate yield strength all reaches 400MPa, more than tensile strength 500MPa.
Embodiment 1# to 6# steel plate is heated by the welding thermal cycle curve setting in advance, referring to Fig. 2, under the condition of weld heat input 400kJ/cm, rate of heating 500
oc/s, peak temperature 1400
oc, peak temperature residence time 3s, t
8/5cooling time 383s, thus obtained HAZ is-20
othe average ballistic work of C is referring to table 2.The HAZ that can find out steel plate from the mechanical property parameters of table 2 is-20
oaverage ballistic work under C condition, up to more than 200J, has very excellent Large Heat Input Welding low-temperature flexibility.
The present invention is on the composition basis of traditional Ti micro-alloyed steel, by improving the content of nitrogen in steel, has greatly improved the Large Heat Input Welding heat affected zone low-temperature flexibility of steel plate, has realized low cost fabrication and has gone out Large Heat Input Welding high-strength high-toughness steel plate.
Claims (1)
1. a low cost Large Heat Input Welding high-strength high-toughness steel plate, it is characterized in that: below all by weight percentage, contain: 0.06% < C≤0.15%, 0.05% < Si≤0.25%, 1.30%≤Mn < 1.80%, P < 0.01%, S < 0.005%, 0.02% < Al≤0.10%, 0.012%≤N≤0.02%, 0.005% < Ti≤0.02%, its surplus is Fe and inevitable impurity, above-mentioned chemical composition meets simultaneously: Ti/N≤2.0,
Described steel plate thickness is 20-40mm, more than yield strength reaches 400MPa, more than tensile strength 500MPa, is applicable to the high-strength high-toughness steel plate of weld heat input within the scope of 200-400kJ/cm ,-20 of steel plate HAZ
omore than the average ballistic work of C reaches 200J.
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| JP5418662B2 (en) * | 2012-01-30 | 2014-02-19 | Ｊｆｅスチール株式会社 | Base material of high toughness clad steel plate excellent in weld zone toughness and method for producing the clad steel plate |
| CN102965572A (en) * | 2012-11-19 | 2013-03-13 | 宝山钢铁股份有限公司 | High-strength high-flexibility steel plate and manufacture method thereof |
| CN106148832B (en) * | 2015-03-28 | 2018-04-03 | 鞍钢股份有限公司 | Normalized general-strength marine steel plate and production method thereof |
| CN105648329A (en) * | 2016-03-09 | 2016-06-08 | 山东钢铁股份有限公司 | Control rolling and high strength ship-plate steel and producing method thereof |
| CN106756543B (en) * | 2016-12-12 | 2018-05-22 | 南京钢铁股份有限公司 | A kind of TMCP states low cost Large Heat Input Welding high strength ship plate steel and its manufacturing method |
| CN106702265A (en) * | 2016-12-13 | 2017-05-24 | 苏州纽东精密制造科技有限公司 | High-strength ship plate steel |
| CN108707828B (en) * | 2018-06-21 | 2019-09-03 | 江苏利淮钢铁有限公司 | A kind of super high impact toughness, high cleanliness steel for low-temperature pressure container and its production method |
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| CN101082104A (en) * | 2006-05-30 | 2007-12-05 | 宝山钢铁股份有限公司 | Nickel-free micro-alloy low-temperature pressure vessel steel and manufacturing method thereof |
| CN101213316A (en) * | 2005-08-15 | 2008-07-02 | 株式会社神户制钢所 | Thick steel plate excelling in toughness of large heat input welded joint |
| CN101525721A (en) * | 2008-03-03 | 2009-09-09 | 株式会社神户制钢所 | Heavy steel plate |
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| CN101153370B (en) * | 2006-09-27 | 2012-06-13 | 鞍钢股份有限公司 | Low-alloy high-strength steel plate capable of being welded at high heat input and manufacturing method thereof |
| CN100523252C (en) * | 2007-05-10 | 2009-08-05 | 武汉科技大学 | Soldering boat deck steel in high intensity by large line energy, and manufacturing method |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN101213316A (en) * | 2005-08-15 | 2008-07-02 | 株式会社神户制钢所 | Thick steel plate excelling in toughness of large heat input welded joint |
| CN101082104A (en) * | 2006-05-30 | 2007-12-05 | 宝山钢铁股份有限公司 | Nickel-free micro-alloy low-temperature pressure vessel steel and manufacturing method thereof |
| CN101525721A (en) * | 2008-03-03 | 2009-09-09 | 株式会社神户制钢所 | Heavy steel plate |
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