CN101619422A - Steel plate for low-carbon high-niobium extra-high strength welding structure and method for manufacturing same - Google Patents
Steel plate for low-carbon high-niobium extra-high strength welding structure and method for manufacturing same Download PDFInfo
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Abstract
The invention provides a steel plate for a low-carbon high-niobium high strength welding structure. The steel plate comprises the following chemical components in percentage by weight: 0.015 to 0.075 percent of C, 0.20 to 0.50 percent of Si, 1.63 to 2.0 percent of Mn, 0.081 to 0.12 percent of Nb, 0.005 to 0.030 percent of Ti, 0.0005 to 0.0030 percent of B, 0.50 to 0.95 percent of Cr, 0.70 to 1.25 percent of Cu, 0.50 to 1.50 percent of Ni, 0.30 to 0.60 percent of Mo, 0.010 to 0.050 percent of Als, and the balance of Fe and inevitable impurities. The method for manufacturing the steel plate comprises the steps of molten iron pretreatment, rotary furnace smelting, refining, continuous casting and rolling, wherein the rolling process adopts the HTP plus RPC process, the heating temperature before rolling is between 1,140 and 1,220 DEG C, and two-stage controlled rolling is adopted. The steel plate is low in carbon content and high in Nb content, so that the initial rolling temperature of the non-recrystallization controlled rolling is increased, the temperature holding time is short, and the manufacturing efficiency is high; because the carbon content and the carbon equivalent are low, the welding performance is good; and with the HTP plus RPC plus annealing process, the steel plate for the welding structure with good toughness and plasticity and the yield strength more than or equal to 960N/mm<2> can be manufactured.
Description
Technical field
The invention belongs to the metallic substance technical field, relate in particular to a kind of low-alloy quality plate and manufacture method thereof.
Background technology
The development trend in fields such as engineering machinery, heavy load truck, cement pump truck, semitrailer, freight container, hydropower station pressure pipeline is to use increasing high strength, superstrength Welded Structural Steel at present, its purpose mainly is to alleviate deadweight, improve carrying capacity, save energy.Simultaneously also require ultrahigh-strength steel plates to have characteristics such as cost is low, welding property is good, low-temperature impact toughness height.
The manufacture method of the relevant ultrahigh-strength steel plates of yield strength about 960MPa has formed multinomial patent in the world, for example:
Nippon Steel Manufacturing Corp is called for the CN1148416A name in the patent of " the high strength line pipes steel with low yielding ratio and good low-temperature flexibility " and at its another publication number at the publication number of China application and is called in the patent of " weldable high-tensile steel of excellent in low temperature toughness " for the CN1146784A154 name, discloses a kind of low-temperature flexibility, tensile strength that weldability is good is the above ultrahigh-strength steel of 950MPa.It is at low C, and---------Mo---Nb---trace Ti is further to add elements such as Cu, B, Cr, Ca, V in the steel to Ni to high Mn.Its Nb content 0.01%～0.10%, and its Nb content causes non-recrystallization district start rolling temperature to make middle time of staying temperature longer like this below 950 ℃ below 0.041% among the embodiment, its yield strength fails to reach more than the 960MPa simultaneously.
A kind of superstrength boron-containing steel is disclosed in the Granted publication of ExxonMobil Upstream Research Company and Nippon Steel Manufacturing Corp application number is called the Chinese patent of " superstrength with excellent toughness can be welded boron-containing steel " for CN1087356C, this tensile strength of steel is at least about 900MPa, employing is thinned to steel plate by one or multi-channel hot rolling with slab in first temperature range of austenite generation recrystallize, then begin to be transformed into second temperature range of ferrite temperature by one or multi-channel hot rolling being lower than above-mentioned first temperature range and being higher than the cooling period austenite, the quenching finishing temperature that above-mentioned steel plate quenching to is suitable, stop to quench, with above-mentioned steel plate air cooling to room temperature.The interpolation element that contains iron and following weight per-cent in this steel: 0.03%～0.10%C, 1.6%～2.1%Mn, 0.01%～0.10%Nb, 0.01%～0.10%V, 0.2%～0.5%Mo, 0.005%～0.03%Ti, 0.0005%～0.0020%B, further be characterized as in this steel: 0.3≤Ceq≤0.7, and Pcm≤0.35, and can add other alloying element.Its Nb content 0.01%～0.10% is optimized interval 0.03%～0.06%, and its Nb content is below 0.032% among the embodiment, and final yield strength is difficult to reach more than the 960MPa.
The application number of Baoshan Iron ﹠ Steel Co., Ltd application is that " above ultrahigh-strength steel plates of yield strength 960MPa and manufacture method thereof " patent of 200510024775.3 provides a kind of yield strength can reach ultrahigh-strength steel plates more than the 960MPa, C0.08%-0.18% in its composition, Nb0.01%～0.1%.Its production method: steel billet is heated to 1100～1250 ℃, at austenite the recrystallization zone can takes place billet rolling is become steel plate; At austenite the recrystallization zone not taking place, steel plate rolling is become the steel plate of final thickness, 860～920 ℃ of finishing temperatures; With the speed of cooling that is not less than about 5 ℃/S steel plate is cooled to and is lower than MS～MS+100 ℃ cooling termination temperature; Cooled steel plate is carried out tempering to improve performance.Its Nb content is below 0.071% among the embodiment, and its carbon content major part so not only influence welding property and low-temperature flexibility, and middle time of staying temperature is longer all in (except that an example is 0.08%) more than 0.11%, and production efficiency is low.
By above patent documentation as can be known, the ultrahigh-strength steel plate technique of yield strength about 960MPa has the following disadvantages at present: 1. owing to continue to use traditional cooling controlling and rolling controlling process, Nb content is generally lower in the steel, cause non-recrystallization controlled rolling start rolling temperature low, mill load is big, time of staying temperature is long, and production efficiency is low.2. C content is higher, influences welding property.3. the armor plate strength rank is on the low side, and major part is difficult to reach more than the 960MPa.
Summary of the invention
The non-recrystallization controlled rolling temperature that exists in view of above-mentioned prior art is low, and mill load is big, and time of staying temperature is long, production efficiency is low, defectives such as welding property is poor, and the armor plate strength rank is on the low side, the objective of the invention is to overcome the deficiencies in the prior art provides a kind of yield strength 〉=960N/mm
2Level other superstrength steel for welded structures and production method thereof.
The chemical component weight per-cent of steel plate for low-carbon high-niobium extra-high strength welding structure plate of the present invention is: C0.015%～0.075%, Si0.20%～0.50%, Mn1.63%～2.0%, Nb0.081%～0.12%, Ti0.005%～0.030%, B0.0005%～0.0030%, Cr0.50%～0.95%, Cu0.70%～1.25%, Ni0.50%～1.50%, Mo0.30%～0.60%, Al
s0.010%～0.050%, P≤0.025%, S≤0.015%, surplus is Fe and unavoidable impurities.
Steel plate for low-carbon high-niobium extra-high strength welding structure plate of the present invention also contains V≤0.07% by weight percentage; Ni content in the described steel is decided according to Cu content, and Ni/Cu 〉=0.5.
The manufacture method of steel plate for low-carbon high-niobium extra-high strength welding structure plate of the present invention comprises following processing step: hot metal pretreatment-converter smelting-refining-continuous casting-rolling, be characterized in that the operation of rolling adopts HTP+RPC technology, Heating temperature is 1140～1220 ℃ before rolling, adopt the controlled rolling of two stages, recrystallization zone rolling temperature 〉=1000 ℃, non-recrystallization district rolling temperature be 970 ℃～(Ar3+0 ℃～100 ℃), non-recrystallization district accumulation of distortion amount is greater than 60%, roll back relaxation time 10～150s, cool off with after-acceleration, speed of cooling is 10～40 ℃/S, stop cooling temperature≤400 ℃, air cooling carries out temper to steel plate at last afterwards, and tempering temperature is 500～680 ℃.
Steel chemical composition of the present invention is an essential characteristic with the low high Nb of C, as main adding elements, suitably add elements such as Mo, B, with elements such as Mn with low cost, Cr, Cu in order to guarantee plate surface quality, suitably add the Ni element according to Cu content, and guarantee Ni/Cu 〉=0.5.In the present invention, according to the intensity rank that will obtain, suitably determine to add the kind and the content of element, its chemical ingredients scope (Wt%) is: C0.015%～0.075%, Si0.20%～0.50%, Mn1.63%～2.0%, Nb0.081%～0.12%, Ti0.005%～0.030%, B0.0005%～0.0030%, Cr0.50%～0.95%, Cu0.70%～1.25%, Ni0.50%～1.50%, Mo0.30%～0.6%, V0.00%～0.07%, Al
s0.010%～0.050%, surplus is Fe and unavoidable impurities.Impurity element in the steel is controlled at P≤0.025%, S≤0.015%, [N]≤0.0080%.
The alloying element that the present invention selects mainly acts on and being:
C: carbon is very big to intensity, toughness, the welding property influence of steel.C content is lower than at 0.015% o'clock, is difficult to obtain high strength, and welded heat affecting zone is softening; Carbon is higher than at 0.075% o'clock, during heating in the steel solid solution Nb amount few, make the advantage of high Nb content be difficult to embody, and influence the welding property of steel.
Mn: manganese is to improve intensity and flexible effective element, bainite transformation is had bigger promoter action, and effect is more remarkable under the Ultra-low carbon condition, and cost is very cheap, therefore in the present invention the Mn element as main alloy element, Mn content is controlled at 1.63%～2.0%.
B: boron is the composition of outbalance in the ultra-low-carbon bainite steel, and it can improve the hardening capacity of steel, particularly adds the boron of trace in ultra low-carbon steel, can suppress austenite effectively to ferrite, pearlitic transformation.Boron content is lower than at 0.0005% o'clock, is difficult to play above-mentioned effect, and boron content is higher than at 0.0030% o'clock, has a strong impact on steel grade toughness, therefore controls B0.0005%～0.0030%.
Nb: niobium is the important interpolation element in the steel of the present invention, and it is the austenitic recrystallize of delayed deformation effectively, stops austenite crystal to be grown up, improve austenite recrystallization temperature, reduce the rolling rolling load of non-recrystallization, shorten time of staying temperature, boost productivity, improve intensity and toughness simultaneously.It and micro-boron compound action can be improved hardening capacity significantly, promote bainite transformation, can play the effect of Mo element to bainite transformation and raising intensity.Nb content is lower than 0.081% and relatively conventional, and above-mentioned effect is not obvious.Nb content is higher than at 0.120 o'clock, obviously influences steel grade toughness and welding property, therefore controls Nb0.081%～0.120%
Ti: adding the titanium of trace, is for the nitrogen element in the fixing steel, thereby guarantees the raising hardening capacity effect of boron.In the best condition, titanium, nitrogen form titanium nitride, stop steel billet the growing up of crystal grain in heating, rolling, welding process, improve the toughness of mother metal and welded heat affecting zone.Titanium is lower than at 0.005% o'clock, and nitrogen fixation effect is poor, surpasses at 0.03% o'clock, and nitrogen fixation effect reaches capacity, and superfluous titanium will make the toughness of steel worsen.
Si: silicon is the bioelement of deoxidation in steel making, also has certain strengthening effect, when content is lower than 0.2%, smelts difficulty and increases; Content surpasses at 0.5% o'clock, and the degree of cleaning of steel descend, and toughness reduces, and weldability is poor.Therefore control Si0.20%～0.50%.
Al
s: aluminium is deoxidant element, can be used as the AlN forming element, crystal grain thinning effectively, and when it contained quantity not sufficient 0.01%, effect was less; Surpass at 0.05% o'clock, it is saturated that desoxydatoin is tending towards, and increases steel inclusion, harmful to mother metal and welding heat influence area toughness.Therefore control Al
s0.010%～0.050%.
Mo: molybdenum helps the refinement of austenite crystal when rolling and the generation of fine bainite, but its cost height, and weldability and toughness reduce.The present invention controls Mo0.30%～0.6%.
Cu:, except gaining in strength, also help the acquisition good low-temperature flexibility as alloying element.Can utilize the comprehensive action of Cu-B further to improve the hardening capacity of steel, promote the formation of bainite.The present invention controls Cu0.70%～1.25%
Ni: the purpose of adding the Ni element in the present invention mainly is to stop to contain the tendency that the high steel billet of Cu amount cracks when heating or hot rolling, considers economy, in the present invention Ni content is controlled at 0.50%～1.50%.
Cr: chromium is the important interpolation element in the steel of the present invention, to improve the intensity of steel.Consider from aspects such as economy, welding property and intensity, in the present invention Cr content is controlled at 0.50%～0.95%.
The upper limit of the impurity element in the steel is controlled at P≤0.02%, and S≤0.01% is advisable, and content is low more, and the steel grade performance is good more.
The manufacture method of steel plate for low-carbon high-niobium extra-high strength welding structure plate of the present invention is in smelting process: carries out hot metal pretreatment, adopts converter smelting, and by top blast or top bottom blowing, dark as far as possible decarburization; Adopt VD, RH, LF etc. to carry out refining treatment, and carry out microalloying; Ca handles, and in conjunction with S content and tap in the steel, feeds the Si-Ca line, and the control oxide morphology improves ductility and toughness, reduces the horizontal and vertical poor performance of steel plate; Continuous casting adopts induction stirring, reduces element segregation; In the operation of rolling: adopt high temperature rolling (HTP)+relaxation---to separate out---control phase transformation (RPC) technology; The heating top temperature is determined at 1220 ℃ before rolling, to guarantee to obtain tiny austenite crystal, be limited to 1140 ℃ under the Heating temperature, so that can there be the Nb of q.s to dissolve in austenite, help the delay of operation of rolling recrystallize and roll the precipitation strength of bainite in the postcooling process, martensitic formation and drawing process; Adopt the controlled rolling of two stages, the recrystallization zone rolling temperature is controlled at 〉=1000 ℃, non-recrystallization district rolling temperature be controlled at 970 ℃～(Ar3+0 ℃～100 ℃); Non-recrystallization district accumulation of distortion amount is greater than 60%, so that accumulate sufficiently high dislocation desity; Roll back relaxation time 10～150s, with the after-acceleration cooling, the speed of cooling scope is controlled at 10～40 ℃/S, and cooling rate is lower than 10 ℃/S, undercapacity; Stop cooling temperature≤400 ℃, afterwards air cooling.Stop cooling temperature and be higher than 400 ℃ of then undercapacities.In order to obtain best effect, steel plate of the present invention need carry out temper, and optimum tempering temperature is 500 ℃～680 ℃.In drawing process, the precipitation strength by Cu, Nb improves the intensity of steel, improves the toughness and the plasticity of steel simultaneously.
Beneficial effect of the present invention: low C and high Nb content are adopted in composition design of the present invention, have improved non-recrystallization controlled rolling start rolling temperature, and rolling load is little, and time of staying temperature is short, and the production efficiency height has reduced production cost; Because of carbon content and carbon equivalent are all lower, welding property is good; In conjunction with HTP+RPC+T (tempering) technology can obtain toughness, plasticity is good, yield strength is greater than 960N/mm
2Other superstrength steel for welded structures plate of level.
Embodiment
The present invention is further described by the following embodiment.
The chemical ingredients of embodiment of the invention steel grade sees Table 1.
The processing parameter of the corresponding steel grade of the embodiment of the invention sees Table 2.
The mechanical property of the corresponding steel grade of the embodiment of the invention sees Table 3.
The smelting composition (Wt%) of table 1, embodiment of the invention steel grade
| Embodiment | ??C | ??Si | ??Mn | ??P | ??S | ??Cu | ??Ni | ??Cr | ??Mo | ??Nb | ??Ti | ??V | ??Bt | ??Als |
| ??0# | ??0.05 | ??0.22 | ??1.65 | ??0.010 | ??0.005 | ??1.25 | ??1.50 | ??0.81 | ??0.3 | ??0.075 | ??0.02 | ??0.07 | ??0.0013 | ??0.03 |
| ??51#52#53# | ??0.047 | ??0.25 | ??1.63 | ??0.010 | ??0.010 | ??1.14 | ??1.00 | ??0.52 | ??0.59 | ??0.089 | ??0.02 | ??0.03 | ??0.0013 | ??0.03 |
| ??21# | ??0.074 | ??0.36 | ??1.74 | ??0.018 | ??0.006 | ??0.93 | ??0.93 | ??0.51 | ??0.51 | ??0.098 | ??0.022 | ??0 | ??0.0024 | ??0.021 |
| ??22# | ??0.073 | ??0.36 | ??1.68 | ??0.018 | ??0.005 | ??0.91 | ??0.96 | ??0.50 | ??0.53 | ??0.098 | ??0.018 | ??0 | ??0.0016 | ??0.04 |
| ??71#72#73#74# | ??0.035 | ??0.37 | ??1.87 | ??0.016 | ??0.005 | ??0.98 | ??0.87 | ??0.55 | ??0.45 | ??0.105 | ??0.017 | ??0 | ??0.0021 | ??0.037 |
| ??66# | ??0.060 | ??0.36 | ??1.78 | ??0.016 | ??0.005 | ??0.91 | ??0.93 | ??0.65 | ??0.41 | ??0.100 | ??0.014 | ??0.007 | ??0.0023 | ??0.038 |
| ??91#92#93# | ??0.019 | ??0.45 | ??1.90 | ??0.013 | ??0.009 | ??0.72 | ??0.56 | ??0.94 | ??0.53 | ??0.12 | ??0.026 | ??0.03 | ??0.003 | ??0.023 |
The processing parameter of table 2, steel grade embodiment of the present invention
| Embodiment | Thickness mm | Heating temperature ℃ | Finishing temperature ℃ | Two-stage accumulation of distortion rate % | Secondary start rolling temperature ℃ | Finishing temperature ℃ | Relaxation time s | Stop cooling temperature ℃ | Speed of cooling ℃/s |
| ??0# | ??16 | ??1140 | ??1050 | ??69 | ??970 | ??910 | ??20 | ??216 | ??29.15 |
| ??51# | ??16 | ??1158 | ??1069 | ??69 | ??950 | ??860 | ??20 | ??253 | ??26.85 |
| ??52# | ??16 | ??1143 | ??1025 | ??69 | ??960 | ??901 | ??13 | ??290 | ??23.38 |
| ??53# | ??16 | ??1209 | ??1116 | ??69 | ??955 | ??862 | ??17 | ??345 | ??19.62 |
| ??21# | ??16 | ??1175 | ??1025 | ??70 | ??970 | ??885 | ??20 | ??300 | ??24.00 |
| ??22# | ??16 | ??1168 | ??1020 | ??70 | ??970 | ??890 | ??18 | ??400 | ??13.89 |
| ??71# | ??16 | ??1185 | ??1010 | ??60 | ??956 | ??885 | ??60 | ??360 | ??11.39 |
| ??73# | ??16 | ??1149 | ??1001 | ??60 | ??905 | ??848 | ??57 | ??180 | ??16.33 |
| ??72# | ??16 | ??1140 | ??1005 | ??60 | ??965 | ??890 | ??25 | ??180 | ??35.53 |
| ??74# | ??16 | ??1140 | ??1000 | ??60 | ??920 | ??860 | ??24 | ??275 | ??28.87 |
| ??91# | ??10 | ??1195 | ??1030 | ??75 | ??980 | ??800 | ??120 | ??120 | ??31.43 |
| ??92# | ??10 | ??1170 | ??1009 | ??75 | ??950 | ??801 | ??90 | ??70 | ??39.87 |
| ??93# | ??10 | ??1157 | ??1040 | ??75 | ??950 | ??790 | ??20 | ??200 | ??38.31 |
| ??66# | ??25 | ??1140 | ??1029 | ??70 | ??970 | ??924 | ??150 | ??386 | ??22.22 |
The mechanical property of table 3, steel grade embodiment of the present invention
Claims (4)
1. a steel plate for low-carbon high-niobium extra-high strength welding structure plate is characterized in that the chemical component weight per-cent of this steel is: C0.015%～0.075%, Si0.20%～0.50%, Mn1.63%～2.0%, Nb0.081%～0.12%, Ti0.005%～0.030%, B0.0005%～0.0030%, Cr0.50%～0.95%, Cu0.70%～1.25%, Ni0.50%～1.50%, Mo0.30%～0.60%, Al
s0.010%～0.050%, P≤0.025%, S≤0.015%, surplus is Fe and unavoidable impurities.
2. steel plate for low-carbon high-niobium extra-high strength welding structure plate according to claim 1 is characterized in that also containing by weight percentage in described steel: V≤0.07%.
3. steel plate for low-carbon high-niobium extra-high strength welding structure plate according to claim 1 and 2 is characterized in that the Ni content in the described steel is decided according to Cu content, and Ni/Cu 〉=0.5.
4. the manufacture method of the described steel plate of claim 1, comprise following processing step: hot metal pretreatment-converter smelting-refining-continuous casting-rolling, it is characterized in that the operation of rolling adopts HTP+RPC technology, Heating temperature is 1140～1220 ℃ before rolling, adopt the controlled rolling of two stages, recrystallization zone rolling temperature 〉=1000 ℃, non-recrystallization district rolling temperature be 990 ℃～(Ar3+0 ℃～100 ℃), non-recrystallization district accumulation of distortion amount is greater than 60%, rolls back relaxation time 10～150s, cool off with after-acceleration, speed of cooling is 10～40 ℃/S, stops cooling temperature≤400 ℃, afterwards air cooling, at last steel plate is carried out temper, tempering temperature is 500～680 ℃.
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN102312173A (en) * | 2010-06-29 | 2012-01-11 | 鞍钢股份有限公司 | 700MPa-tensile strength steel for large heat input welding structure and manufacturing method thereof |
| CN112143958A (en) * | 2019-06-27 | 2020-12-29 | 宝山钢铁股份有限公司 | 1000 MPa-grade steel plate with super-thick, super-high toughness and excellent weldability and manufacturing method thereof |
| CN113430452A (en) * | 2021-05-26 | 2021-09-24 | 武汉钢铁有限公司 | Steel with excellent surface quality for hydraulic generator rotor yoke and production method thereof |
-
2008
- 2008-06-30 CN CN200810012146A patent/CN101619422A/en active Pending
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102312173A (en) * | 2010-06-29 | 2012-01-11 | 鞍钢股份有限公司 | 700MPa-tensile strength steel for large heat input welding structure and manufacturing method thereof |
| CN112143958A (en) * | 2019-06-27 | 2020-12-29 | 宝山钢铁股份有限公司 | 1000 MPa-grade steel plate with super-thick, super-high toughness and excellent weldability and manufacturing method thereof |
| CN112143958B (en) * | 2019-06-27 | 2021-08-17 | 宝山钢铁股份有限公司 | 1000 MPa-grade steel plate with super-thick, super-high toughness and excellent weldability and manufacturing method thereof |
| CN113430452A (en) * | 2021-05-26 | 2021-09-24 | 武汉钢铁有限公司 | Steel with excellent surface quality for hydraulic generator rotor yoke and production method thereof |
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Application publication date: 20100106 |