CN104451379A - High-strength low-alloy niobium-vanadium structural steel and preparation method thereof - Google Patents
High-strength low-alloy niobium-vanadium structural steel and preparation method thereof Download PDFInfo
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Abstract
The present invention discloses high-strength low-alloy niobium-vanadium structural steel comprising the following components in percentage by weight: 0.12-0.20% of C, 0.15-0.35% of Si, 1.10-1.60% of Mn, not larger than 0.020% of P, not larger than 0.003% of S, 0.020-0.050% of Nb, 0.040-0.060% of V, 0.020-0.040% of Alt, 0.41-0.45% of Ceq, and the balance of Fe and unavoidable impurities. During rolling, a heating temperature of a continuous casting billet is 1150-1250 DEG C, a billet heating time is 300-400 minutes, a soaking time is not smaller than 50 minutes, and a tapping temperature is 1130-1230 DEG C; two-stage control rolling is adopted, the pressing amount in each rough rolling procedure is not smaller than 40mm, a final rolling temperature is 900-1050 DEG C, the billet is roughly rolled to an intermediate billet not smaller than 1.3 times of a finished product thickness, a start finish rolling temperature is not larger than 870 DEG C, the pressing rate in each procedure is not smaller than 10%, laminar cooling is adopted after rolling, a re-reddening temperature is 600-700 DEG C, a high temperature offline temperature is 250-500 DEG C, and a stack cooling time is 72 hours. The high-strength low-alloy niobium-vanadium structural steel disclosed by the invention is high in applicability, excellent in resistance to lamination crack, free of heat treatment and low in production cost.
Description
Technical field
The invention belongs to field of metallurgy, relate to a kind of low-alloy high-strength steel plate and preparation method thereof, especially a kind of 101.6mm thick A572Gr50 High-Strength Low-Alloy niobium vanadium structural steel and preparation method thereof,
Background technology
Super-thick steel plate is at some special occasions, as power station, chemical industry, water conservancy, warship, basin, Highrise buildings etc., there is the very large market requirement, the production of China's super-thick steel plate can not meet the demand in market, every year still need from external import, particularly the thick steel of some high performance spies, has very high value added.
Special heavy plate is applied to Super High, large-span steel building, security requirement is more and more higher, this just requires that > 100mm thick High-Strength Low-Alloy niobium vanadium structure iron A572Gr50 must have: 1. higher intensity and toughness, meet 4 DEG C, thickness of slab 1/4 place impact of collision merit >=27J; 2. the anti-lamellar tearing performance of good Z-direction; 3. good welding property; 4. high cleanliness, low S, P, inclusion and gas content.
At production thickness specification > 100mm, the A572Gr50 steel plate of more than yield strength 345MPa, domestic steel mill is subject to the condition restrictions such as continuous casting material size, deformation homogeneity, compression ratio, steel rolling rhythm, intensity, the toughness properties of steel plate are unstable, qualification rate is low, or simply can not be up to standard, internal soundness is difficult to meet especially.Main special heavy plate manufacturing enterprise generally adopts steel ingot to be raw material production super-thick steel plate, and lumber recovery is low, and production environment is severe, and the production cycle is slower.
Summary of the invention
For the defect that prior art exists, the object of this invention is to provide a kind of High-Strength Low-Alloy niobium vanadium structural steel and preparation method thereof, this product utilization 320mm blank is produced, under the prerequisite ensureing heavy thickness, intensity reaches more than 345MPa, with short production cycle, rhythm of production is fast, has great economic implications.
Object of the present invention is achieved through the following technical solutions:
A kind of High-Strength Low-Alloy niobium vanadium structure iron, it is characterized in that: the chemical component weight per-cent of this structure iron is C:0.12 ~ 0.20%, Si:0.15 ~ 0.35%, Mn:1.10 ~ 1.60%, P :≤0.020%, S :≤0.003%, Nb:0.020 ~ 0.050%, V:0.040 ~ 0.060%, Alt:0.020 ~ 0.040%, Ceq:0.41 ~ 0.45%, all the other are Fe and inevitable impurity.
In the present invention, High-Strength Low-Alloy niobium vanadium structure iron is a kind of 101.6mm thick A572Gr50 High-Strength Low-Alloy niobium vanadium structure iron.The Rolled From Continuous Casting Slab that this structure iron is 320mm by thickness becomes thickness to be the steel plate of 101.6mm, and compression is only than being 3.15:1.
The present invention comparatively preferably comprises following component by weight percentage: C:0.16%, Si:0.20%, Mn:1.55%, P :≤0.013%, S :≤0.002%, Nb:0.03%, V:0.05%, Alt:0.030%, all the other are Fe and inevitable impurity.
A preparation method for High-Strength Low-Alloy niobium vanadium structure iron, it is characterized in that, the method comprises following operation: desulfurizing iron pre-treatment → converter smelting → LF refining → RH refining → continuous casting → strand heating → de-scaling → rolling → cooling → finished product warehouse-in; Specific requirement is as follows:
After desulfurizing iron pre-treatment, sulphur content controls at S≤0.005%, converter control P content≤0.013%, desulfating and deoxidation and alloying constituent adjustment are carried out in LF refining, vacuumize during RH refining process under condition of high vacuum degree≤5.0mbar condition hold-time >=20 minutes, continuous casting controls tundish temperature liquidus line+8 ~ 22 DEG C, continuously cast bloom stacking slow cooling more than 72 hours;
Rolling technology: adopt Controlled Rolling And Controlled Cooling, continuous blank heating temperature is 1150 DEG C ~ 1250 DEG C, adopt austenite recrystallization district and Unhydrated cement two-phase control rolling, roughing adopts the broken austenite crystal of passage heavy reduction, reduction in pass >=40mm, roughing finishing temperature control is at 900 ~ 1050 DEG C, and finish rolling start rolling temperature is≤870 DEG C; Roll rear controlled cooling model, red temperature is 600 ~ 700 DEG C, air cooling subsequently.
Chemical composition is one of key factor affecting continuously cast bloom internal soundness and special heavy plate performance, and the present invention obtains excellent over-all properties to make described steel, and limit the chemical composition of described steel, reason is:
C: carbon is the one of the chief elements affecting high-strength steel mechanical property, improved the intensity of steel by gap solid solution, during too high levels, toughness and weldability will be deteriorated, and carbon content control of the present invention is 0.12 ~ 0.20%.
Si: silicon is the deoxidant element that steel-making is necessary, has certain solution strengthening effect; Silicone content is too high, is unfavorable for plate surface quality and toughness, and silicone content of the present invention controls 0.15 ~ 0.35%.
Mn: manganese has thinning microstructure, improves the effect of intensity and low-temperature flexibility, and with low cost.When Fe content is too high, easily cause continuous casting slab segregation.Fe content of the present invention controls 1.10 ~ 1.60%.
P: phosphorus is harmful impurity element, and phosphorus has very strong solution strengthening effect, it makes the intensity of steel, hardness significantly improves, but reduces the toughness of steel tempestuously, and especially low-temperature flexibility is called cold short, and phosphorus content of the present invention controls≤0.02%.
S: sulphur is the harmful element in steel, sulphur and iron generate FeS in grain boundaries segregation, melt during hot-work, cause the cracking of steel, are called hot-short, and sulphur content of the present invention controls≤0.003%.
Nb: trace niobium has pinning effect to austenite grain boundary, suppresses the recrystallize of deformed austeaite, and forms precipitate when cooling, and improves intensity and toughness.DeGrain when niobium addition level is less than 0.02%, when being greater than 0.05%, toughness reduces, and causes continuously cast bloom surface crack to produce, and also has deterioration effect in addition to welding property.Content of niobium of the present invention controls 0.02 ~ 0.05%.
V: vanadium is the excellent reductor of steel.Adding vanadium in steel can thinning microstructure crystal grain, improves intensity and toughness.Form carbide during cooling after welding, be conducive to gaining in strength.DeGrain when addition is less than 0.04%, when being greater than 0.06%, the toughness of steel and weldability reduce.Therefore, content of vanadium should control in the scope of 0.04 ~ 0.06%.
Al: aluminium is a kind of important deoxidant element, adds the aluminium of trace, effectively can reduce the inclusion content in steel in molten steel, and crystal grain thinning.But too much aluminium, can promote that continuously cast bloom produces surface crack and reduces slab quality, Holo-Al content should control 0.020 ~ 0.040%.
Present component is reasonable, and through converter smelting, LF and RH refining, adopt the large pressure rolling of high temperature low speed, the tissue of steel plate is mainly uniform ferrite and adds perlite.Steel plate comprehensive mechanical property is good, and be embodied in: tensile strength is 480 ~ 520MPa, yield strength is 600 ~ 650MPa, unit elongation is 20 ~ 25%, 4 DEG C of impact property >=100J, has excellent anti-lamellar tearing ability, without the need to thermal treatment, production cost is lower.
The invention has the beneficial effects as follows:
1, the present invention is designed by Rational Composition, low-phosphorous sulphur smelting technology, coordinates the alloying elements such as Nb, V, enhances the toughness and tenacity of low alloy steel.Adopt Controlled Rolling And Controlled Cooling, ensure that steel plate Microstructure and properties is even, the large pressure rolling of high temperature low speed, develop yield strength > 345MPa rank 101.6mm thick High-Strength Low-Alloy niobium vanadium structural steel be only the prerequisite of 3.15:1 at compression ratio under, suitability is strong.
2, the present invention adopts TMCP combine with technique high temperature low speed large pressure Rolling Production special heavy plate, without the need to thermal treatment, reduces cost, and production process is stablized.
Accompanying drawing explanation
Fig. 1 is one embodiment of the invention 101.6mm thick A572Gr50 High-Strength Low-Alloy niobium vanadium structural steel As rolled sample tissue shape appearance figure, is organized as ferrite+perlite, homogeneous microstructure in figure, intensity and toughness good.
Embodiment
Embodiment 1 ~ 3 is the manufacture method of a kind of 101.6mm thick A572Gr50 High-Strength Low-Alloy niobium vanadium structural steel, and in employing, low-phosphorous, the sulfur hot metal smelting technique of carbon, adds micro-Nb, V, adopt Controlled Rolling And Controlled Cooling simultaneously.
The main chemical compositions of embodiment 1 ~ 3 is as shown in table 1:
The main chemical compositions (wt%) of table 1 embodiment of the present invention
| Embodiment | C | Si | Mn | P | S | Nb | V | Ti | Ceq |
| Embodiment 1 | 0.18 | 0.20 | 1.20 | 0.012 | 0.0016 | 0.025 | 0.049 | 0.0051 | 0.43 |
| Embodiment 2 | 0.14 | 0.22 | 1.60 | 0.010 | 0.0018 | 0.025 | 0.045 | 0.0045 | 0.43 |
| Embodiment 3 | 0.16 | 0.20 | 1.53 | 0.014 | 0.0015 | 0.024 | 0.046 | 0.0042 | 0.44 |
As can be seen from Table 1, the 3 stove test steel prepared according to the present invention, chemical composition all meets requirement of the present invention.
The rolling process for cooling parameter of each embodiment is as shown in table 2:
Table 2 rolling process for cooling parameter
| Embodiment | Thickness mm | Roughing finishing temperature DEG C | Finish rolling start rolling temperature DEG C | Finishing temperature DEG C | Red temperature DEG C |
| Embodiment 1 | 101.6 | 1081 | 835 | 826 | 675 |
| Embodiment 2 | 101.6 | 1073 | 848 | 843 | 650 |
| Embodiment 3 | 101.6 | 1053 | 827 | 833 | 655 |
Steel billet is by described method, and adopt cooling controlling and rolling controlling process to produce the A572Gr50 low-alloy high-strength thick steel plate of thickness 101.6mm, main technique main points are as follows:
(1) rolling technology: blank heating temperature is 1150 ~ 1250 DEG C, heat-up time is 300 ~ 400min, and tapping temperature is 1130 ~ 1230 DEG C; Rolling method adopts austenite recrystallization district and the rolling of austenite Unhydrated cement two-stage control.Roughing adopts the broken austenite crystal of passage heavy reduction, and draught per pass >=40mm, start rolling temperature >=1050 DEG C, the intermediate blank of roughing one-tenth >=1.3h times finished product thickness, finish rolling start rolling temperature is 780 ~ 880 DEG C, and every time draft is 10 ~ 15%.
In the present embodiment 1-3, Heating temperature is 1220 DEG C, and soaking time is 140min, and tapping temperature is 1200 DEG C; Roughing draught per pass 40mm, roughing becomes the intermediate blank of 1.57 times of finished product thicknesses; Finish rolling start rolling temperature is 820 ~ 850 DEG C, every time draft > 10%.
(2) roller repairing technique: adopt section cooling, red temperature 600 ~ 700 DEG C.
In the present embodiment 1-3, final cooling temperature 650 ~ 680 DEG C.
(3) high temperature rolls off the production line retarded cooling process: steel plate hot is rectified and is placed on cold bed cooling, the temperature that rolls off the production line 250 ~ 500 DEG C, and heap cool time 72 hours, obtains the A572Gr50 low-alloy high-strength thick steel plate of 101.6mm.
In the present embodiment 1-3, the temperature that rolls off the production line 440 DEG C, adopts cooling in heap after steel plate rolls off the production line, heap cool time 72 hours.
Mechanical property of steel plate is as shown in table 3 implemented according to the invention.Embodiment of the present invention steel plate comprehensive mechanical property is good, and tensile strength is 480 ~ 520MPa, and yield strength is 600 ~ 650MPa, unit elongation is 20 ~ 25%, 4 DEG C of impact property >=100J, meets the regulation of ASTM A572/A572M standard, there is stable processing technique, the features such as production cost is low.
The object performance of table 3 embodiment of the present invention
| Specimen coding | R eL/MPa | R m/MPa | A/％ | Akv (4 DEG C of longitudinal directions)/J | Clod wash |
| 1 | 505 | 635 | 21 | 110 | Qualified |
| 2 | 494 | 615 | 23 | 120 | Qualified |
| 3 | 480 | 600 | 22 | 115 | Qualified |
。
Claims (5)
1. a High-Strength Low-Alloy niobium vanadium structure iron, it is characterized in that: the chemical component weight per-cent of this structure iron is C:0.12 ~ 0.20%, Si:0.15 ~ 0.35%, Mn:1.10 ~ 1.60%, P :≤0.020%, S :≤0.003%, Nb:0.020 ~ 0.050%, V:0.040 ~ 0.060%, Alt:0.020 ~ 0.040%, Ceq:0.41 ~ 0.45%, all the other are Fe and inevitable impurity.
2. High-Strength Low-Alloy niobium vanadium structure iron according to claim 1, is characterized in that: the Rolled From Continuous Casting Slab that this structure iron is 320mm by thickness becomes thickness to be the steel plate of 101.6mm, and compression is only than being 3.15:1.
3. High-Strength Low-Alloy niobium vanadium structure iron according to claim 1, it is characterized in that: the chemical component weight per-cent of this structure iron is: C:0.16%, Si:0.20%, Mn:1.55%, P :≤0.013%, S :≤0.002%, Nb:0.03%, V:0.05%, Alt:0.030%, all the other are Fe and inevitable impurity.
4. the preparation method of a High-Strength Low-Alloy niobium vanadium structure iron according to claim 1, it is characterized in that, the method comprises following operation: desulfurizing iron pre-treatment → converter smelting → LF refining → RH refining → continuous casting → strand heating → de-scaling → rolling → cooling → finished product warehouse-in; Specific requirement is as follows:
After desulfurizing iron pre-treatment, sulphur content controls at S≤0.005%, converter control P content≤0.013%, desulfating and deoxidation and alloying constituent adjustment are carried out in LF refining, vacuumize during RH refining process under condition of high vacuum degree≤5.0mbar condition hold-time >=20 minutes, continuous casting controls tundish temperature liquidus line+8 ~ 22 DEG C, continuously cast bloom stacking slow cooling more than 72 hours.
5. rolling technology: adopt Controlled Rolling And Controlled Cooling, continuous blank heating temperature is 1150 DEG C ~ 1250 DEG C, adopt austenite recrystallization district and Unhydrated cement two-phase control rolling, roughing adopts the broken austenite crystal of passage heavy reduction, reduction in pass >=40mm, roughing finishing temperature control is at 900 ~ 1050 DEG C, and finish rolling start rolling temperature is≤870 DEG C; Roll rear controlled cooling model, red temperature is 600 ~ 700 DEG C, air cooling subsequently.
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Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN104988390A (en) * | 2015-06-29 | 2015-10-21 | 舞阳钢铁有限责任公司 | E-level extra-thick high-intensity steel plate produced by using continuous casting billet and production method thereof |
| CN105483526A (en) * | 2015-12-31 | 2016-04-13 | 江西理工大学 | Low-alloy high-strength steel with yttrium-based rare earth and manufacturing method thereof |
| CN106048408A (en) * | 2016-06-23 | 2016-10-26 | 山东钢铁股份有限公司 | Extremely-simple component steel plate for high-strength structures and manufacture method thereof |
| CN108220778A (en) * | 2018-01-19 | 2018-06-29 | 河钢股份有限公司承德分公司 | A kind of high-strength vehicle bridge steel of niobium vanadium complex intensifying and its production method |
| CN108588550A (en) * | 2018-01-19 | 2018-09-28 | 河钢股份有限公司承德分公司 | A kind of hot rolling press axle housing steel plate and its production method |
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| CN109825766A (en) * | 2019-02-28 | 2019-05-31 | 邯郸钢铁集团有限责任公司 | A kind of 460MPa high-strength steel reducing lobe defect and its production method |
| CN110629002A (en) * | 2019-10-17 | 2019-12-31 | 山东钢铁集团日照有限公司 | Method for producing low-compression-ratio lamellar tearing-resistant extra-thick plate based on TMCP (thermal mechanical control processing) |
| CN116200672A (en) * | 2022-11-25 | 2023-06-02 | 重庆钢铁股份有限公司 | Low-cost high-strength structural steel plate Q460D and manufacturing method |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN104988390A (en) * | 2015-06-29 | 2015-10-21 | 舞阳钢铁有限责任公司 | E-level extra-thick high-intensity steel plate produced by using continuous casting billet and production method thereof |
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| CN109825766A (en) * | 2019-02-28 | 2019-05-31 | 邯郸钢铁集团有限责任公司 | A kind of 460MPa high-strength steel reducing lobe defect and its production method |
| CN110629002A (en) * | 2019-10-17 | 2019-12-31 | 山东钢铁集团日照有限公司 | Method for producing low-compression-ratio lamellar tearing-resistant extra-thick plate based on TMCP (thermal mechanical control processing) |
| CN116200672A (en) * | 2022-11-25 | 2023-06-02 | 重庆钢铁股份有限公司 | Low-cost high-strength structural steel plate Q460D and manufacturing method |
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Application publication date: 20150325 |