CN102206788B - Steel and production method thereof - Google Patents
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- CN102206788B CN102206788B CN201110123435.1A CN201110123435A CN102206788B CN 102206788 B CN102206788 B CN 102206788B CN 201110123435 A CN201110123435 A CN 201110123435A CN 102206788 B CN102206788 B CN 102206788B
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Abstract
The invention provides steel and a production method thereof. The steel comprises the following components in percentages by weight: 0.12% to 0.17% of C, 0.20% to 0.50% of Si, 1.15% to 1.55% of Mn, not larger than 0.010% of S, not larger than 0.020% of P, 0.010% to 0.060% of Nb, 0.008% to 0.030% of Ti, 0.010% to 0.060% of V, 0.10% to 0.35% of Ni, 0.015% to 0.060% of Als, not larger than 40*10<-6> of N, not larger than 40*10<-6> of O, not larger than 2*10<-6> of H and the balance of Fe and inevitable impurities, wherein Als indicates acid-soluble aluminium. The production method of the steel comprises the steps of pretreatment of molten iron, smelting of top and bottom combined blown converter, LF (Ladle Furnace) refining and RH (Ruhrstahl Heraeus) vacuum cycle degassing which are conducted sequentially. The steel produced according to one aspect of the invention has excellent lamellar tearing resistant performance, low-temperature impact resistant performance and aseismatic performance and can satisfy the requirements of modern bridge engineering for high-performance bridge steel plates.
Description
Technical field
The present invention relates to a kind of steel and production method thereof, particularly a kind of steel of anti-lamellar tearing and production method thereof.
Background technology
Lamellar tearing be a kind of inner along roll to stress cracking.In general, lamellar tearing is relevant with welding joint, in the Plate Steel multi-run welding fitting of T-shaped, angle-style or cross joint, easily lamellar tearing occurs.For beam-to-column joint and box column bight, the suspension rod plate of suspension bridge and the first-class component of cross joint of decking of ocean structure, large-scale composite beam structure, high-rise steel structure, in weld because the constraint in thickness of slab direction is very large, welding capacity is many again, so the danger producing lamellar tearing is very large.Therefore, the steel plate resisting lamellar tearing usually to be adopted to build, to ensure the security of component this class formation.
Along with the fast development that railway, highway, large span and Large Span Bridges are built, greatly will stimulate the quick growth of bridge steel structure demand, and Long span, heavy duty, the multi-thread demand of (public iron, city rail, pipeline share) bridge of sharing increase gradually, also strengthen the requirement of bridge dead load, the high-strength Bridge Steel of especially anti-lamellar tearing will adopt successively thereupon.
In Chinese patent CN1609257A, in the Composition Design of steel employing pole low-carbon (LC), Cu-Cr-Ni-Mo-Nb add and two or more compound in Ti-Al-Zr-RE or Ca is added, adopt thermomechanical controlled rolling technology+relaxation-precipitation control techniques, produce a kind of Weather-resistance bridge steel based on acicular ferrite structure, the yield strength of this steel is greater than 490MPa, tensile strength is greater than 590MPa,-40 DEG C of striking energys are greater than 210J, excellent combination property, weak point is to the addition of a large amount of Cu-Cr-Ni-Mo-Nb noble metal, and cost is higher.
In Chinese patent CN101403075A, low C height Mn is adopted in the Composition Design of steel, add Cu-Cr-Ni-Ti-Nb element, adopt thermomechanical controlled rolling technique, the yield strength of this steel is greater than 460MPa simultaneously, tensile strength is greater than 590MPa,-40 DEG C of striking energys are greater than 100J, and weak point is to the addition of a large amount of Cu-Cr-Ni noble metal, and cost is higher, and this invention only smelts rolling in laboratory, is not applied to suitability for industrialized production.
In Chinese patent CN101333628A, low C height Mn is adopted in the Composition Design of steel, add Cu-Cr-Ni-Mo-Nb-Ti element, adopt thermomechanical controlled rolling to add tempering process, the yield strength of this steel is greater than 430MPa simultaneously, tensile strength is greater than 550MPa,-40 DEG C of impacts are greater than 200J, and weak point is to the addition of a large amount of Cu-Cr-Ni-Mo noble metal, and will carry out tempering heat treatment, production cycle is long, and cost is higher.
In addition, the performance index of all not mentioned steel plate of above Chinese patent in anti-lamellar tearing.
Summary of the invention
The object of the present invention is to provide a kind of steel and production method thereof of at least one technical problem that can solve in above multiple technical problem.
According to steel of the present invention comprise by weight 0.12% ~ 0.17% C, 0.20% ~ 0.50% Si, 1.15% ~ 1.55% Mn, be no more than 0.010% S, be no more than 0.020% P, 0.010% ~ 0.060% Nb, 0.008% ~ 0.030% Ti, 0.010% ~ 0.060% V, 0.10% ~ 0.35% Ni, 0.015% ~ 0.060% Als, be no more than 40 × 10
-6n, be no more than 40 × 10
-6o, be no more than 2 × 10
-6h, surplus is Fe and inevitable impurity, and wherein Als represents dissolved aluminum.
According to an aspect of the present invention, the C content of this steel is 0.13% ~ 0.16%, Si content is 0.25% ~ 0.50%, Mn content is 1.20% ~ 1.50%, S content be 0.001% ~ 0.007%, P content is 0.006% ~ 0.015%, Nb content is 0.010% ~ 0.055%, V content is 0.015% ~ 0.055%, Ni content be 0.10% ~ 0.30%, Als content is 0.015% ~ 0.060%.
According to an aspect of the present invention, carbon equivalent ce V=C+Mn/6+ (the Cr+Mo+V)/5+ (Ni+Cu)/15≤0.43% of this steel, this obviously can improve the welding property of steel plate, avoid steel plate that the possibility of welding cold cracking and hot tearing occurs, improve the over-all properties of weld simultaneously.
According to an aspect of the present invention, this steel exists with the form of steel plate, and the lower yield strength of this steel plate is not less than 460MPa, tensile strength is not less than 570MPa, and yield tensile ratio is not higher than 0.83, and elongation after fracture is not less than 20%,-40 DEG C of longitudinal AKv are not less than 120J, and Z-direction relative reduction in area is not less than 35%.
According to the production method of steel of the present invention comprise carry out successively hot metal pretreatment, top and bottom combined blown converter smelting, LF refining and RH vacuum circulation degassing.
According to an aspect of the present invention, in hot metal pretreatment step, controlled by molten steel sulfur content 0.001% ~ 0.015%, molten iron temperature is 1250 DEG C ~ 1320 DEG C, scratches clean the slag on molten iron surface after desulfurization.
According to an aspect of the present invention, in top and bottom combined blown converter smelting step, pretreated molten iron enters converter, nickel plate adds converter with steel scrap bucket, slag material adds in terminal for first 1 minute ~ 5 minutes, and finishing slag basicity controls in R=3.0 ~ 5.0, and the terminal pressure rifle time is 30 seconds ~ 120 seconds, adopt the deoxidation of aluminium manganese titanium, aluminium manganese titanium add-on is 1.5 ~ 4.5kg/t
steel; Sweetening agent 2.8 ~ 5.2kg/t is added along steel stream during tapping
steel, start when putting steel 1/2 to add when being added to 3/4; Molten steel go out to 1/4 time, add ferromanganese, ferrosilicon, ferro-niobium and vanadium iron in batches, molten steel go out to 3/4 time add, ferromanganese is the iron alloy containing manganese 75% ~ 95%, and the add-on of ferromanganese is 13 ~ 17kg/t
steel, ferrosilicon is the iron alloy of siliceous 65% ~ 85%, and the add-on of ferrosilicon is 2.0 ~ 6.0kg/t
steel, ferro-niobium is the iron alloy containing niobium 50% ~ 65%, and the add-on of ferro-niobium is 0.3 ~ 1.1kg/t
steel, vanadium iron is the iron alloy containing vanadium 45% ~ 65%, and the add-on of vanadium iron is 0.2 ~ 1.0kg/t
steel, nickel plate is the iron alloy of nickeliferous 95% ~ 99%, and the add-on of nickel plate is 1.0 ~ 5.0kg/t
steel.
According to an aspect of the present invention, in LF refinement step, adopt omnidistance Bottom Argon Stirring, soft blow argon 3 ~ 10 minutes, add lime and carry out slag making, adopt aluminum shot reductor to carry out deoxidation, departures sinciput slag is yellowish-white slag or white slag, and 10 minutes ~ 30 minutes hold-time, finishing slag basicity controls 2.0 ~ 4.0.
According to an aspect of the present invention, in LF refinement step, with 0 ~ 0.92kg/t
steelamount add aluminum steel to molten steel, with 0.32 ~ 1.93kg/t
steelamount add titanium wire to molten steel.
According to an aspect of the present invention, in RH vacuum circulation degassing step, avoid chemical heating when the vacuum tightness in vacuum tank is below 133Pa, RH process, pure degassing time is 3 minutes ~ 12 minutes, feeds CaFe line 0.43 ~ 1.28kg/t before soft blow argon
steel, soft blow argon 8 ~ 18 minutes.
According to an aspect of the present invention, the method also comprises and carries out sheet billet continuous casting and rolling to the molten steel obtained after RH vacuum circulation degassing.
According to an aspect of the present invention; in sheet billet continuous casting step; employing whole process protection is cast; covering slag adopts peritectic steel covering slag; in unit time, the ratio range of the water yield of secondary cooling section of continuous caster ejection and the strand weight of pull-out is 0.3L/kg ~ 0.6L/kg; steel billet stacking slow cooling is sent later is rolled for 24 hours ~ 72 hours again, and peritectic steel covering slag comprises the SiO of 25% ~ 40% by weight
2, 28% ~ 45% CaO, the MgO of 1.0% ~ 7.0%, the Al of 2.0% ~ 5.0%
2o
3, 3.0% ~ 11.0% Li
2o+Na
2o+K
2o, 2.0% ~ 8.0% CaF
2, 3.0% ~ 11.0% C.
According to an aspect of the present invention, in milling step, steel billet tapping temperature is 1150 DEG C ~ 1210 DEG C, rough rolling of steel billets start rolling temperature is 1120 DEG C ~ 1180 DEG C, finishing temperature is 1050 DEG C ~ 1110 DEG C, and finish rolling start rolling temperature is 860 DEG C ~ 920 DEG C, and final cooling temperature is 650 DEG C ~ 700 DEG C, speed of cooling is 5 DEG C/s ~ 12 DEG C/s, and workpiece thickness is not less than 2 times of finished product thickness.
According to an aspect of the present invention, roughing overall compression ratio > 50%, workpiece thickness is 2.1 times ~ 3.5 times of finished product thickness, and final cooling temperature is 650 DEG C ~ 690 DEG C, rolls rear steel plate slow cooling 24 hours ~ 36 hours.
According to an aspect of the present invention, the lower yield strength of the steel plate obtained after rolling is not less than 460MPa, and tensile strength is not less than 570MPa, yield tensile ratio is not higher than 0.83, elongation after fracture is not less than 20%, and-40 DEG C of longitudinal AKv are not less than 120J, and Z-direction relative reduction in area is not less than 35%.
Therefore, steel according to an aspect of the present invention possesses excellent anti-lamellar tearing performance, low-temperature impact property and anti-seismic performance, can meet the requirement of Modern Bridge Engineering construction to high-performance bridge steel plate.
Accompanying drawing explanation
Fig. 1 is the metallographic structure photo of the steel plate that example 1 obtains;
Fig. 2 is the stereoscan photograph of the steel plate that example 1 obtains.
Embodiment
According to steel of the present invention comprise by weight 0.12% ~ 0.17% C, 0.20% ~ 0.50% Si, 1.15% ~ 1.55% Mn, be no more than 0.010% S, be no more than 0.020% P, 0.010% ~ 0.060% Nb, 0.008% ~ 0.030% Ti, 0.010% ~ 0.060% V, 0.10% ~ 0.35% Ni, 0.015% ~ 0.060% Als (dissolved aluminum), be no more than 40 × 10
-6n, be no more than 40 × 10
-6o, be no more than 2 × 10
-6h, surplus is Fe and inevitable impurity.
Below describe the effect of each element in steel of the present invention or disadvantageous effect in detail and choose the reason of above-mentioned limited amount of each element.
C is strengthening element most economical in soft steel, but the increase of carbon content makes the plasticity of steel and impelling strength reduce, and cold short proneness and timeliness proneness improve, and worsen welding property.Build railroad bridge to need to carry out a large amount of field welding jobs, welding condition is severe, and this just requires that bridge steel plate possesses good welding property, should reduce carbon content as far as possible and exceed standard to avoid carbon equivalent.But additionally must increase other valuable microalloy content guarantee armor plate strength while carbon drop, this just causes cost to increase considerably.Through considering, the sufficient quantity of C is controlled 0.12% ~ 0.17%.
Si enters ferrite and plays solution strengthening effect, reduce yield tensile ratio, but Si can improve the ductile-brittle transition temperature of steel significantly, also can worsen plasticity simultaneously.Therefore, the sufficient quantity of Si is controlled 0.20% ~ 0.50%.
Mn can reduce critical transition temperature Ar3, refine pearlite laminated structure, plays and improves the intensity of ferrite and pearlite and the effect of hardness in steel.Because manganese and sulphur have larger avidity, MnS has certain plasticity when high temperature, so avoid the hot-short of steel, but too high Mn can affect the welding property of steel plate, also can aggravate the center segregation of strand, cause product banded structure serious, and then have influence on anti-lamellar tearing performance.Therefore, the sufficient quantity of Mn controls 1.15% ~ 1.55%.
When S is present in steel with the form of FeS, content Gao Shiyi produces hot-short phenomenon.When S is present in steel with the form of MnS, often distribute along rolling direction with bar form, form serious banded structure, destroy the continuity of steel, also can produce material impact to the performance of steel different directions, reduce plasticity and the impelling strength of steel, improve ductile-brittle transition temperature, for requiring the steel grade of anti-lamellar tearing performance, also can reduce Z-direction relative reduction in area, add the possibility of steel plate generation lamellar tearing.Therefore, reducing sulphur content and changing its inclusion morphology in steel is the vital approach obtaining high tenacity and excellent Z-direction performance, and its sufficient quantity controls below 0.010%.
P belongs to low temperature brittleness element, P significantly expands the two-phase region between liquid phase and solid phase, and in steel process of setting, segregation is between crystal grain, forms high phosphorus brittle layer, improve the rank of banded structure, make the local organization of steel abnormal, cause mechanical property uneven, reduce the plasticity of steel, steel is made easily to produce brittle crack, erosion resistance declines, and also has disadvantageous effect to welding property, increases welding crack sensibility.Therefore, should reduce the content of phosphorus in steel as far as possible, the sufficient quantity of P controls below 0.020%.
Nb can produce significant Grain Refinement Effect and medium precipitation strength effect.In Control Rolling Micro-alloy Steels, crystal grain thinning and the precipitation strength effect of Nb are the most outstanding, often add the Nb of 0.01%, can improve the normal temperature strength 30MPa ~ 50MPa of steel, so adding Nb is one of the most cost-effective means.But when Nb too high levels, easily form Low melting point eutectic with the element such as Fe, C, have the tendency of increase welded heat affecting zone thermal crack.Synthesise various factor, for giving full play to thin crystalline substance and the precipitation strength effect of Nb, the sufficient quantity of Nb controls 0.010% ~ 0.060%.
Ti and C, N have extremely strong avidity.In solidification of molten steel process, form the TiC particle of a large amount of Dispersed precipitate, solid nucleus during solidification of molten steel can be become, be conducive to the crystallization of steel, the tissue of refinement steel, reduce the generation of thick column crystal and treeing, can segregation be reduced, reduce banded structure rank.When in steel, [N] content is higher, easy generation nitride intercrystalline precipitation makes embrittlement of grain boundaries, the formation of Nb bearing steel strand transverse crack can be promoted, if but can [N] content be controlled below 0.004% or add the trace Ti of fix N, TiN particle can be separated out under 1200 DEG C ~ 1300 DEG C high temperature, due to the thick and scattered distribution of particle, detrimentally affect is not had to the plasticity of steel, and can as Nb (C, N) precipitation core, thus reduce the quantity of fine Nb precipitate, and then reduce the crack sensitivity of Nb bearing steel.Ti can form carbide, the nitride particles of tiny titanium, in heating of plate blank process, obtain comparatively tiny austenitic microstructure by stoping the alligatoring of austenite crystal.Ti and N combines and generates stable high diffusive compound, not only can eliminate free nitrogen in steel, helpful to the timeliness impact property improving Bridge Steel, and grain-size can be controlled in the heat affected zone when hot procedure and welding, improve the low-temperature flexibility at each position of steel construction, but too much titanium content can cause TiN liquation, form thick square TiN and be mingled with, be segregated in steel plate thickness centre both impaired low temperature toughness, also can produce adverse influence to Z-direction performance.Synthesise various factor, the sufficient quantity of Ti controls 0.008% ~ 0.030%.
V is present on matrix and crystal boundary with V (C, N) form, mainly plays the effect of precipitation strength and inhibiting grain growth.Because vanadium and nitrogen have very strong avidity, V adds the effect serving free N in fixing steel, thus can avoid the strain aging of steel.Present inventor finds through large quantity research, 15MnVN steel is along with the increase of steel plate thickness, mechanical property change is not remarkable, namely thickness of slab effect is not remarkable, this is because steel interalloy element V and C, N form stable V (C, N), V (C in normalizing process, N) solid solution, separates out V (C, N) subsequently in natural cooling process, in even dispersion particle, crystal grain thinning and precipitating action consumingly, thus steel plate thickness susceptibility is reduced, this is the feature that needs of structural steel for bridge just.On the other hand, V, while playing strong precipitation strength effect, also can improve the ductile-brittle transition temperature of steel, worsens impelling strength.Consider, the sufficient quantity of V controls 0.010% ~ 0.060%.
Ni plays a part reinforced ferrite by forming simple substitutional solid solution, and can improve the intensity of steel, Ni is austenite stable element simultaneously, can significantly improve the low-temperature impact-resistant toughness of steel.But Ni plate price is relatively expensive, considers cost factor, and the sufficient quantity of Ni controls 0.10% ~ 0.35%.
The crystal grain of Al energy refinement steel, improves the intensity of steel, also improves impelling strength simultaneously.Due to the avidity that A1 and N is stronger, the aging sensitivity that N element causes also can be eliminated.Therefore, the sufficient quantity of Al controls 0.015% ~ 0.060%.
In order to improve the performance of steel, according to steel of the present invention can comprise by weight 0.13% ~ 0.16% C, 0.25% ~ 0.50% Si, 1.20% ~ 1.50% Mn, 0.001% ~ 0.007% S, 0.006% ~ 0.015% P, 0.010% ~ 0.055% Nb, 0.008% ~ 0.030% Ti, 0.015% ~ 0.055% V, 0.10% ~ 0.30% Ni, 0.015% ~ 0.060% Als, be no more than 40 × 10
-6n, be no more than 40 × 10
-6o, be no more than 2 × 10
-6h, surplus is Fe and inevitable impurity.
Can exist with the form of steel plate according to steel of the present invention.The lower yield strength of described steel plate is not less than 460MPa, and tensile strength is not less than 570MPa, and yield tensile ratio is not higher than 0.83, and elongation after fracture is not less than 20%, and-40 DEG C of longitudinal AKv are not less than 120J, and Z-direction relative reduction in area is not less than 35%.This steel plate does not need thermal treatment, and homogeneous microstructure, properties are excellent, meets one-level flaw detection requirement, can meet the manufacture requirements of high speed double-tracking railways bridge, also can promote for engineering structures such as building, traffic, ocean platforms.
Production method according to steel of the present invention is described below.
Hot metal pretreatment, top and bottom combined blown converter smelting, LF refining, RH vacuum circulation degassing technique by carrying out successively obtain according to steel of the present invention.
In an embodiment of the production method of steel according to the present invention, hot metal pretreatment refers to desulfurizing iron, make the sulphur in molten iron control 0.001% ~ 0.015%, molten iron optimal temperature controls, at 1250 DEG C ~ 1320 DEG C, to scratch clean the slag on molten iron surface after desulfurization.
In an embodiment of the production method of steel according to the present invention, top and bottom combined blown converter smelting is that pretreated molten iron enters converter, nickel plate adds converter with steel scrap bucket, slag material adds in terminal for first 1 minute ~ 5 minutes, finishing slag basicity controls in R=3.0 ~ 5.0, and the terminal pressure rifle time is 30 seconds ~ 120 seconds.In an embodiment of the production method of steel according to the present invention, adopt the deoxidation of aluminium manganese titanium, aluminium manganese titanium add-on is 1.5 ~ 4.5kg/t
steel.In an embodiment of the production method of steel according to the present invention, during tapping, add sweetening agent 2.8 ~ 5.2kg/t along steel stream
steel, start when putting steel 1/2 to add when being added to 3/4; Molten steel go out to 1/4 time, add ferromanganese, ferrosilicon, ferro-niobium and vanadium iron in batches, molten steel go out to 3/4 time add.
Sweetening agent can be a kind of desulfurization slag charge containing CaO 83% ~ 95%.Ferromanganese can for the iron alloy containing manganese 75% ~ 95%, and the add-on of ferromanganese can be 13 ~ 17kg/t
steel.Ferrosilicon can be the iron alloy of siliceous 65% ~ 85%, and the add-on of ferrosilicon can be 2.0 ~ 6.0kg/t
steel.Ferro-niobium can for the iron alloy containing niobium 50% ~ 65%, and the add-on of ferro-niobium can be 0.3 ~ 1.1kg/t
steel.Vanadium iron can for the iron alloy containing vanadium 45% ~ 65%, and the add-on of vanadium iron can be 0.2 ~ 1.0kg/t
steel.Nickel plate can be the iron alloy of nickeliferous 95% ~ 99%, and the add-on of nickel plate can be 1.0 ~ 5.0kg/t
steel.
In an embodiment of the production method of steel according to the present invention, LF refining adopts omnidistance Bottom Argon Stirring, add lime according to practical situation and carry out slag making, aluminum shot reductor is adopted to carry out deoxidation, departures sinciput slag is yellowish-white slag or white slag, and 10 minutes ~ 30 minutes hold-time, finishing slag basicity controls 2.0 ~ 4.0, soft blow argon 3 ~ 10 minutes.
In LF refining process, those skilled in the art can regulate the add-on of aluminum steel, titanium wire according to actual needs.Preferably, the add-on of aluminum steel is 0 ~ 0.92kg/t
steel, the add-on of titanium wire is 0.32 ~ 1.93kg/t
steel.
In an embodiment of the production method of steel according to the present invention, RH vacuum circulation degassing adopts present treatment pattern.Avoid chemical heating during RH process, guarantee that pure degassing time is 3 minutes ~ 12 minutes, before soft blow argon, feed CaFe line 0.43 ~ 1.28kg/t
steel, soft blow argon 8 ~ 18 minutes.When described present treatment pattern is RH vacuum-treat, the vacuum tightness in vacuum tank is below 133Pa.
Deposit in case at steel according to the present invention with the form of steel plate, also comprise the step of sheet billet continuous casting and rolling according to the production method of steel of the present invention.
In sheet billet continuous casting step, adopt whole process protection casting, covering slag adopts peritectic steel covering slag, and secondary cooling water adopts weak cold pattern, and steel billet stacking slow cooling is sent later rolled for 24 hours ~ 72 hours again.Described peritectic steel covering slag comprises by weight: the SiO of 25% ~ 40%
2, 28% ~ 45% CaO, the MgO of 1.0% ~ 7.0%, the Al of 2.0% ~ 5.0%
2o
3, 3.0% ~ 11.0% Li
2o+Na
2o+K
2o, 2.0% ~ 8.0% CaF
2, 3.0% ~ 11.0% C.Described weak cold pattern refers to that the ratio range of the water yield of secondary cooling section of continuous caster ejection and the strand weight of pull-out in the unit time is 0.3L/kg ~ 0.6L/kg.
In milling step, rolling temperature control is as follows: steel billet tapping temperature is 1150 DEG C ~ 1210 DEG C, rough rolling of steel billets start rolling temperature is 1120 DEG C ~ 1180 DEG C, finishing temperature is 1050 DEG C ~ 1110 DEG C, roughing overall compression ratio > 50%, and workpiece thickness is not less than 2 times of finished product thickness, finish rolling start rolling temperature is 860 DEG C ~ 920 DEG C, final cooling temperature is 650 DEG C ~ 700 DEG C, speed of cooling is 5 DEG C/s ~ 12 DEG C/s, rolls rear steel plate slow cooling 24 hours ~ 36 hours.
In an embodiment of the production method of steel according to the present invention, 4300mm Plate rolling adopts two-stage rolling, and roughing and finish rolling rolling adopt four-high reversing mill.In this embodiment, steel billet tapping temperature is 1150 DEG C ~ 1210 DEG C, roughing overall compression ratio > 50%, and at least ensure that 1 percentage pass reduction is not less than 14%, when trimmed size is 20 ~ 68mm, workpiece thickness is 2.1 ~ 3.5 times of finished product thickness, and finish rolling start rolling temperature is 860 DEG C ~ 920 DEG C, final cooling temperature is 650 DEG C ~ 690 DEG C, speed of cooling is 5 DEG C/and s ~ 12 DEG C/s.
Therefore, the invention provides a kind of economical Hi-Stren steel, be applicable to build the abnormal severe bridge structure of service condition.Compared with prior art, tool of the present invention have the following advantages at least one advantage:
(1) the invention provides the accurate span of control of anti-lamellar tearing high-performance bridge Structural Steel Plate composition, Composition Design is simple, does not add the noble metals such as Cu-Cr-Mo-Zr-RE, with low cost;
(2) steel plate that the present invention relates to adopts thermomechanical controlled rolling technology to produce, and does not need heat treatment step, shortens the production cycle, reduce production cost, and overcomes the deficiency of steel plate specification heat-treated stove restriction;
(3) steel of the present invention has splendid obdurability coupling, and excellent anti-lamellar tearing performance and excellent anti-seismic performance, have excellent welding property simultaneously, can carry out union-melt weld, manual welding and shielded welding.
In sum, the comprehensive mechanical property of steel of the present invention is superior, and easy fracture and destruction, not safe and reliable, can meet the manufacture requirements of high speed double-tracking railways bridge, also can promote for engineering structures such as building, traffic, ocean platforms.
Below in conjunction with example, steel according to the present invention and production method thereof are described further, but steel of the present invention and production method thereof are not limited thereto.
example 1:
Steel in this example be used for bridge, its comprise by weight 0.16% C, 0.48% Si, 1.47% Mn, 0.004% S, 0.012% P, 0.050% Nb, 0.021% Ti, 0.052% V, 0.18% Ni, 0.032% Als, be no more than 40 × 10
-6n, be no more than 40 × 10
-6o and be no more than 2 × 10
-6h, surplus is Fe and inevitable impurity.
This steel is produced by hot metal pretreatment, top and bottom combined blown converter smelting, LF refining, RH refining, sheet billet continuous casting, strand slow cooling, 4300mm Plate rolling, finished product slow cooling.Operation steps is as follows:
Desulfurizing iron strict implement technological process, the sulphur in molten iron controls 0.008%, and temperature is 1250 DEG C, the complete slag scratching clean molten iron surface of desulfurization.Pretreated molten iron enters converter, and nickel plate adds converter with steel scrap bucket, and slag material adds in terminal for first 3 minutes, and finishing slag basicity controls at R=4.0, and the terminal pressure rifle time is 69 seconds.Adopt the deoxidation of aluminium manganese titanium, add aluminium manganese titanium 2.5kg/t
steel.Sweetening agent 2.9kg/t recited above is added along steel stream during tapping
steel, add and start when putting steel 1/2 opportunity to add when being added to 3/4.Molten steel go out to 1/4 time, add ferromanganese, ferrosilicon, ferro-niobium and vanadium iron in batches, molten steel go out to 3/4 time add.Molten steel after converter smelting enters LF refining furnace, adds lime carry out slag making according to practical situation, and yellowish-white slag or white slag hold-time are 13 minutes, adopt omnidistance Bottom Argon Stirring, soft blow argon gas 5 minutes, and finishing slag basicity is 3.9, and aluminum steel add-on is 0.45kg/t
steel, titanium wire add-on is 0.96kg/t
steel.Molten steel after LF refining enters RH refining furnace, and RH refining adopts present treatment pattern.Avoid chemical heating during RH process, guarantee that pure degassing time is 5 minutes, soft blow argon gas 10 minutes, before soft blow argon, add CaFe line 1.10kg/t
steel, smelting cycle controlled at 50 minutes.Employing whole process protection is poured into a mould, and covering slag adopts peritectic steel covering slag.Secondary cooling water adopts weak cold pattern, and continuously cast bloom specification is: 300mm × 1800mm, and setting pulling rate stationary phase is 0.85m/min, specific water 0.40L/kg.Require that the steel billet stacking slow cooling of flaw detection is sent for 48 hours later again to roll.Rolling temperature control, ensure to be rolled in the temperature range of regulation, steel billet tapping temperature 1150-1200 DEG C, roughing start rolling temperature is 1140 DEG C, and finishing temperature is 1070 DEG C, roughing overall compression ratio > 50%, and workpiece thickness is 140mm; Trimmed size 68mm, finish rolling start rolling temperature is 860 DEG C, and final cooling temperature is 650 DEG C, and speed of cooling is 10 DEG C/s, rolls rear steel plate slow cooling 36 hours.
The performance of the steel plate that this example obtains is as follows: lower yield strength is 475MPa, and tensile strength is 600MPa, and yield tensile ratio is 0.79, and elongation after fracture is that 23%, 180 degree of clod wash d=3a are qualified, and-40 DEG C of longitudinal AKv are 191J, and Z-direction relative reduction in area is 60%.
example 2:
Steel in this example be used for bridge, its comprise by weight 0.15% C, 0.40% Si, 1.43% Mn, 0.005% S, 0.013% P, 0.042% Nb, 0.023% Ti, 0.042% V, 0.15% Ni, 0.033% Als, be no more than 40 × 10
-6n, be no more than 40 × 10
-6o, be no more than 2 × 10
-6h, surplus is Fe and inevitable impurity.
This steel is produced by hot metal pretreatment, top and bottom combined blown converter smelting, LF refining, RH refining, sheet billet continuous casting, strand slow cooling, 4300mm Plate rolling, finished product slow cooling.Operation steps is as follows:
Desulfurizing iron strict implement technological process, the sulphur in molten iron controls 0.005%, and temperature is 1267 DEG C, the complete slag scratching clean molten iron surface of desulfurization.Pretreated molten iron enters converter, and nickel plate adds converter with steel scrap bucket, and slag material adds in terminal for first 4 minutes, and finishing slag basicity controls at R=2.0, and the terminal pressure rifle time is 80 seconds.Adopt the deoxidation of aluminium manganese titanium, add aluminium manganese titanium 2.8kg/t
steel.Sweetening agent 3.7kg/t recited above is added along steel stream during tapping
steel, add and start when putting steel 1/2 opportunity to add when being added to 3/4.Molten steel go out to 1/4 time, add ferromanganese, ferrosilicon, ferro-niobium and vanadium iron in batches, molten steel go out to 3/4 time add.Molten steel after converter smelting enters LF refining furnace, adds lime carry out slag making according to practical situation, and yellowish-white slag or white slag hold-time are 20 minutes, adopt omnidistance Bottom Argon Stirring, soft blow argon gas 8 minutes, and finishing slag basicity is 3.0, and aluminum steel add-on is 0.21kg/t
steel, titanium wire add-on is 1.73kg/t
steel.Molten steel after LF refining enters RH refining furnace, and RH refining adopts present treatment pattern.Avoid chemical heating during RH process, guarantee that pure degassing time is 9 minutes, soft blow argon gas 18 minutes, before soft blow argon, add CaFe line 0.89kg/t
steel, smelting cycle controlled at 60 minutes.Employing whole process protection is poured into a mould, and covering slag adopts peritectic steel covering slag.Secondary cooling water adopts weak cold pattern, and continuously cast bloom specification is: 300mm × 1800mm, and setting pulling rate stationary phase is 0.85m/min, specific water 0.48L/kg.Require that the steel billet stacking slow cooling of flaw detection is sent for 48 hours later again to roll.Rolling temperature control, ensure to be rolled in the temperature range of regulation, steel billet tapping temperature 1150-1200 DEG C, roughing start rolling temperature is 1120 DEG C, and finishing temperature is 1057 DEG C, roughing overall compression ratio > 50%, and workpiece thickness is 132mm; Trimmed size 50mm, finish rolling start rolling temperature is 880 DEG C, and final cooling temperature is 670 DEG C, and speed of cooling is 8 DEG C/s, rolls rear steel plate slow cooling 36 hours.
The performance of the steel plate that this example obtains is as follows: lower yield strength is 515MPa, and tensile strength is 635MPa, and yield tensile ratio is 0.81, and elongation after fracture is that 24%, 180 degree of clod wash d=3a are qualified, and-40 DEG C of longitudinal AKv are 176J, and Z-direction relative reduction in area is 65%.
example 3:
Steel in this example be used for bridge, its comprise by weight 0.13% C, 0.26% Si, 1.24% Mn, 0.005% S, 0.010% P, 0.017% Nb, 0.024% Ti, 0.021% V, 0.10% Ni, 0.025% Als, be no more than 40 × 10
-6n, be no more than 40 × 10
-6o, be no more than 2 × 10
-6h, surplus is Fe and inevitable impurity.
This steel is produced by hot metal pretreatment, top and bottom combined blown converter smelting, LF refining, RH refining, sheet billet continuous casting, strand slow cooling, 4300mm Plate rolling, finished product slow cooling.Operation steps is as follows:
Desulfurizing iron strict implement technological process, the sulphur in molten iron controls 0.013%, and temperature is 1310 DEG C, the complete slag scratching clean molten iron surface of desulfurization.Pretreated molten iron enters converter, and nickel plate adds converter with steel scrap bucket, and slag material adds in terminal for first 3 minutes, and finishing slag basicity controls at R=4.5, and the terminal pressure rifle time is 91 seconds.Adopt the deoxidation of aluminium manganese titanium, add aluminium manganese titanium 3.0kg/t
steel.Sweetening agent 4.4kg/t recited above is added along steel stream during tapping
steel, add and start when putting steel 1/2 opportunity to add when being added to 3/4.Molten steel go out to 1/4 time, add ferromanganese, ferrosilicon, ferro-niobium and vanadium iron in batches, molten steel go out to 3/4 time add.Molten steel after converter smelting enters LF refining furnace, adds lime carry out slag making according to practical situation, and yellowish-white slag or white slag hold-time are 30 minutes, adopt omnidistance Bottom Argon Stirring, soft blow argon gas 8 minutes, and finishing slag basicity is 2.2, and aluminum steel add-on is 0.81kg/t
steel, titanium wire add-on is 0.43kg/t
steel.Molten steel after LF refining enters RH refining furnace, and RH refining adopts present treatment pattern.Avoid chemical heating during RH process, guarantee that pure degassing time is 12 minutes, soft blow argon gas 8 minutes, before soft blow argon, add CaFe line 0.50kg/t
steel, smelting cycle controlled at 55 minutes.Employing whole process protection is poured into a mould, and covering slag adopts peritectic steel covering slag.Secondary cooling water adopts weak cold pattern, and continuously cast bloom specification is: 200mm × 1800mm, and setting pulling rate stationary phase is 1.3m/min, specific water 0.55L/kg.Require that the steel billet stacking slow cooling of flaw detection is sent for 24 hours later again to roll.Rolling temperature control, ensure to be rolled in the temperature range of regulation, steel billet tapping temperature 1150-1200 DEG C, roughing start rolling temperature is 1180 DEG C, and finishing temperature is 1101 DEG C, roughing overall compression ratio > 50%, and workpiece thickness is 70mm; Trimmed size 20mm, finish rolling start rolling temperature is 920 DEG C, and final cooling temperature is 690 DEG C, and speed of cooling is 6 DEG C/s, rolls rear steel plate slow cooling 24 hours.
The performance of the steel plate that this example obtains is as follows: lower yield strength is 480MPa, and tensile strength is 623MPa, and yield tensile ratio is 0.77, and elongation after fracture is that 22%, 180 degree of clod wash d=3a are qualified, and-40 DEG C of longitudinal AKv are 189J, and Z-direction relative reduction in area is 63%.
Carry out microtexture research to the high-performance bridge steel plate plate of example 1, its metallographic structure photo and stereoscan photograph are shown in Fig. 1 and Fig. 2 respectively.As can be seen from Figure 1, the metallographic structure of the steel plate of example 1 is that typical ferrite adds pearlitic structure, and ferrite crystal grain is comparatively thin, and band shape is lighter.As can be seen from Figure 2, the perlite lamella of the steel plate of example 1 is fine and closely woven, and crystal grain is tiny.This mainly owing to reasonable component design and thermomechanical controlled rolling technique, has given full play to refined crystalline strengthening effect and the precipitation strength effect of Nb-V-Ti, coordinates the dislocations strengthening effect that the dislocation structure in ferrite matrix provides simultaneously.The comprehensive action of above-mentioned several strengthening effect, ensure that steel plate of the present invention obtains the performances such as excellent obdurability coupling and anti-lamellar tearing.
Claims (1)
1. a production method for the steel of anti-lamellar tearing, it is characterized in that described steel comprise by weight 0.16% C, 0.48% Si, 1.47% Mn, 0.004% S, 0.012% P, 0.050% Nb, 0.021% Ti, 0.052% V, 0.18% Ni, 0.032% Als, be no more than 40 × 10
-6n, be no more than 40 × 10
-6o and be no more than 2 × 10
-6h, surplus is Fe and inevitable impurity, wherein Als represents dissolved aluminum, described method comprise carry out successively hot metal pretreatment, top and bottom combined blown converter smelting, LF refining, RH refining, sheet billet continuous casting, strand slow cooling, 4300mm Plate rolling, finished product slow cooling
Wherein, in hot metal pretreatment, to desulfurizing iron, strict implement technological process, the sulphur in molten iron controls 0.008%, and temperature is 1250 DEG C, the complete slag scratching clean molten iron surface of desulfurization;
Pretreated molten iron enters converter, and nickel plate adds converter with steel scrap bucket, and slag material adds in terminal for first 3 minutes, and finishing slag basicity controls at R=4.0, and the terminal pressure rifle time is 69 seconds, adopts the deoxidation of aluminium manganese titanium, adds aluminium manganese titanium 2.5kg/t
steel, during tapping, add sweetening agent 2.9kg/t along steel stream
steel, add and start when putting steel 1/2 opportunity to add when being added to 3/4, molten steel go out to 1/4 time, add ferromanganese, ferrosilicon, ferro-niobium and vanadium iron in batches, molten steel go out to 3/4 time add, wherein, sweetening agent is a kind of desulfurization slag charge containing CaO 83% ~ 95%;
Molten steel after converter smelting enters LF refining furnace, adds lime carry out slag making according to practical situation, and yellowish-white slag or white slag hold-time are 13 minutes, adopt omnidistance Bottom Argon Stirring, soft blow argon gas 5 minutes, and finishing slag basicity is 3.9, and aluminum steel add-on is 0.45kg/t
steel, titanium wire add-on is 0.96kg/t
steel;
Molten steel after LF refining enters RH refining furnace, and RH refining adopts present treatment pattern, avoids chemical heating, guarantee that pure degassing time is 5 minutes, soft blow argon gas 10 minutes, add CaFe line 1.10kg/t before soft blow argon during RH process
steel, smelting cycle controls at 50 minutes;
Employing whole process protection is poured into a mould, and covering slag adopts peritectic steel covering slag, and secondary cooling water adopts weak cold pattern, continuously cast bloom specification is: 300mm × 1800mm, setting pulling rate stationary phase is 0.85m/min, specific water 0.40L/kg, requires that the steel billet stacking slow cooling of flaw detection is sent for 48 hours more later and rolls;
Rolling temperature control, ensures to be rolled in the temperature range of regulation, steel billet tapping temperature 1150-1200 DEG C, roughing start rolling temperature is 1140 DEG C, finishing temperature is 1070 DEG C, roughing overall compression ratio > 50%, and workpiece thickness is 140mm, trimmed size 68mm, finish rolling start rolling temperature is 860 DEG C, and final cooling temperature is 650 DEG C, and speed of cooling is 10 DEG C/s, roll rear steel plate slow cooling 36 hours
The performance of described steel plate is as follows: lower yield strength is 475MPa, and tensile strength is 600MPa, and yield tensile ratio is 0.79, and elongation after fracture is that 23%, 180 degree of clod wash d=3a are qualified, and-40 DEG C of longitudinal AKv are 191J, and Z-direction relative reduction in area is 60%.
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