CN102041446A - Method for manufacturing Q390E-Z35 low-alloy and high-strength thick plate - Google Patents
Method for manufacturing Q390E-Z35 low-alloy and high-strength thick plate Download PDFInfo
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Abstract
The invention provides a method for manufacturing a Q390E-Z35 low-alloy and high-strength thick plate. The thick plate comprises the following chemical components in percentage by weight: 0.15-0.18% of C, 1.30-1.50% of Mn, 0.18-0.25% of Si, less than or equal to 0.015% of P, less than or equal to 0.005% of S, 0.020-0.035% of Nb, 0.020-0.050% of V, 0.020-0.035% of Al, and the balance Fe and inevitable impurities. The manufacturing method comprises the following steps: carrying out controlled rolling and controlled cooling on a continuous casting to obtain the thick steel plate; heating to the normalizing temperature of 870-900 DEG C; and preserving the temperature for about 2 hours and then carrying out air cooling on a cooling bed. The manufacturing method provided by the invention is used to carry out normalizing treatment on the steel plate produced by the controlled rolling and controlled cooling process, thus being capable of improving tissues of the steel plate, and improving properties of the steel plate. In the manufacturing method for manufacturing the Q390E-Z35 thick plate, the requirement on the rolling mill capacity is not high, so the manufacturing method is suitable for most of medium and thick plate plants. The steel plate manufactured by the manufacturing method has the advantages of good comprehensive mechanical properties, and good resistance to lamellar tearing.
Description
Technical field
The invention belongs to the Plate Steel production field, specifically a kind of manufacture method of Q390E-Z35 low-alloy high-strength slab.
Background technology
In recent years, because the continuous increase of superelevation layer, large-span steel construction project, industries such as the energy, traffic, building, shipbuilding, machinofacture are increasing with slab, special heavy plate market demand.At present, though building structure is in the great majority with Q345 rank slab in the slab market, high-level structure is also improving constantly with the demand of slab.These steel plates not only require to have higher intensity and plasticity, also require to have lower yield tensile ratio, good low-temperature flexibility, good anti-lamellar tearing performance and welding property.
Plate Steel is subjected to condition restriction such as continuous casting material size, deformation homogeneity, compression ratio, steel rolling rhythm, and the intensity of steel plate, toughness properties instability, qualification rate are often lower.At present, domestic have only minority producer to have the ability of producing Plate Steel, and all be the stronger wide and heavy plate mill of employing ability, very high to equipment requirements.If can realize to have very important significance in the poor slightly steel mill of mill capacity with continuously cast bloom production intensity and the higher Plate Steel of toughness rank.
Summary of the invention
In order to overcome the problem that existing conventional mill can not be produced Plate Steel, the object of the present invention is to provide a kind of manufacture method of thick Q390E-Z35 low-alloy high-strength slab, this manufacture method is utilized continuously cast bloom, and the production technique that adopts controlled rolling and controlled cooling to add normalizing on middle plate mill produces and satisfies the Q390E-Z35 slab that GB requires.
Purpose of the present invention is achieved through the following technical solutions:
A kind of manufacture method of Q390E-Z35 low-alloy high-strength slab is characterized in that this manufacture method adopts cooling controlling and rolling controlling process to add normalizing process production, comprises following technology:
(1) blank is selected: the chemical ingredients of continuous casting material is: C:0.15～0.18%, Mn:1.30～1.50%, Si:0.18～0.25%, P :≤0.015%, S :≤0.005%, Nb:0.020～0.035%, V:0.020～0.050%, Al:0.020～0.035%, surplus are Fe and unavoidable impurities;
(2) rolling technology: select above-mentioned continuous casting material, Heating temperature is 1200～1250 ℃, and soaking time is 240～270min, and tapping temperature is 1180～1230 ℃; Rolling method adopts austenite recrystallization district and the two stages controlled rolling of austenite non-recrystallization district, every time draft 10～20% of roughing, and 1020～1050 ℃ of finishing temperatures, roughing becomes the intermediate blank of 1.7～2.0 times of finished product thicknesses; The finish rolling start rolling temperature is 850～870 ℃, and every time draft is 8～12%;
(3) roll postcooling technology: adopt the laminar flow cooling, 650～700 ℃ of final cooling temperatures, 5～10 ℃/s of rate of cooling;
(4) adopt the high temperature retarded cooling process that rolls off the production line: steel plate heat is rectified and is placed on the cold bed cooling, 430～450 ℃ of the temperature that rolls off the production line, and cooling in heap, 60 ~ 72 hours cooling in heap time are adopted in the steel plate back of rolling off the production line;
(5) normalizing process: 870 ~ 900 ℃ of steel plate normalizing temperatures, be incubated and go up the cold bed air cooling after 1～3 hour, obtain Q390E-Z35 low-alloy high-strength slab.
It is that the continuous casting material of 260mm is made the thick Q390E-Z35 low-alloy high-strength of 75mm slab that the present invention is specially adapted to adopt thickness.
The chemical ingredients of continuous casting material is preferably: C:0.16～0.17%, Mn:1.36～1.40%, Si:0.20～0.24%, P :≤0.012%, S :≤0.002%, Nb:0.025～0.030%, V:0.038～0.042%, Al:0.020～0.035%, surplus is Fe and unavoidable impurities.
Design of chemical composition of the present invention is according to being:
1, carbon content is controlled at 0.15 ~ 0.18%, for when guaranteeing armor plate strength, avoids the harm of C element to steel plasticity, toughness and weldability
2, manganese can be postponed austenite to ferritic transformation in described steel, enlarged the scope of austenite non-recrystallization, thereby can make full use of the controlled rolling of austenite non-recrystallization more and roll the back controlled chilling and come grain-size, improve the intensity and the toughness of steel the refinement steel plate.When the content of manganese was lower than 1.20%, above-mentioned effect was not remarkable, made intensity and toughness on the low side.When the content of manganese is higher than 1.60%,, cause the joint area lamellar tearing easily at continuously cast bloom with roll serious banded segregation and the banded pearlitic structure of formation in the attitude Plate Steel.Consider the factor of plate property and composition, the manganese content of light plate of the present invention should be controlled in 1.30～1.50% the scope.
3, the Si element gathers easily partially in crystal boundary, reduces the crystal boundary surface energy, and steel is produced along brilliant fracture.In addition, the Si element generates sharp brilliant peridotites (Fe at the interface at matrix and iron scale easily when continuously cast bloom heats
2SiO
4), when temperature is higher than 1175 ℃, Fe
2SiO
4Can become liquid phase from solid phase, fused Fe
2SiO
4Can assemble change greatly by significant promotes oxidn iron sheet pore, this will quicken the oxidation on steel surface.Fe
2SiO
4Can form a kind of eutectoid thing with FeO, this eutectoid thing is difficult in thick dephosphorization and removes, and is pressed into steel plate sometimes and causes surface imperfection in course of hot rolling subsequently, and therefore, the content of silicon should not be higher than 0.25%; But because silicon is when steel-making one of the most effective deoxidant element, when silicone content was lower than 0.10%, molten steel was easily oxidized.Therefore, silicone content should be controlled in 0.18～0.25% the scope as far as possible.
4, the low-temperature flexibility in the nearly seam of sulphur and the described steel of phosphorus grievous injury and welding district.Therefore, sulphur, phosphorus content should be controlled at respectively≤0.005% and≤below 0.015%.
5, the solute effect of dragging of trace niobium and Nb (C, N) to the pinning effect of austenite grain boundary, all suppress the austenitic recrystallize of deformation, in conjunction with TMCP, can the refinement ferrite crystal grain, but too high niobium, promote continuously cast bloom to produce surface crack, and promote the nearly seam of welding district to form thick M-A island, therefore, content of niobium should be controlled in 0.02～0.035% the scope.Vanadium combines formation VN particle with nitrogen in described steel, the VN particle returns in the red process at steel plate laminar flow refrigerative and separates out, and can improve the intensity of steel.When the content of vanadium was lower than 0.010%, above-mentioned effect was not remarkable.But along with the increase of content of vanadium, M-A island fragility has the trend that increases mutually in the nearly seam of the welding district, reduces welding property.Therefore, content of vanadium should be controlled at 0.02～0.05%.
The present invention has following advantage:
1, by the present invention, when adopting continuously cast bloom to produce, can on the lower middle plate mill of mill capacity, produce Q390E-Z35 low-alloy high-strength slab, not high to equipment requirements, be fit to apply, and production technique is easy,
The plate property steady quality.Be particularly suitable for adopting the thick continuously cast bloom of 260mm to produce the thick Q390E-Z35 low-alloy high-strength of 75mm slab.
2, its over-all properties of Q390E-Z35 low-alloy high-strength slab of obtaining of the present invention is: yield strength R
EL385 ~ 425MPa, tensile strength R
m570 ~ 630MPa, elongation after fracture δ
5〉=30%, relative reduction in area 〉=55% ,-40 ℃ of ballistic work Akv 〉=70J, cold-bending property is qualified.
The present invention carries out normalizing treatment by the steel plate to cooling controlling and rolling controlling process production, can improve the steel plate tissue, improves plate property.Utilize this explained hereafter Q390E-Z35 slab less demanding to mill capacity, be suitable for most Heavy Plate Plant, the steel plate comprehensive mechanical property is good, has good anti-lamellar tearing ability.
Description of drawings
Fig. 1 is the surperficial metallograph of 75mm Q390E-Z35 low-alloy high-strength slab of the present invention.
Fig. 2 is 1/4th place's metallographs of 75mm Q390E-Z35 low-alloy high-strength slab of the present invention.
Fig. 3 is the heart portion metallograph of 75mm Q390E-Z35 low-alloy high-strength slab of the present invention.
Embodiment
The present invention is described in further detail below in conjunction with specific embodiment.
The thick Q390E-Z35 low-alloy high-strength of a kind of 75mm slab manufacture method, continuous casting material thickness is 260mm.
By the method for the invention, manufactured experimently 5 stoves test steel as embodiment.Technical process is: converter smelting → LF refining → RH vacuum-treat → continuous-casting of steel billet → steel billet examination → surface-conditioning → steel billet heating → high-pressure water descaling → roughing mill is rolling → intermediate blank treat temperature → finishing mill rolling → ACC → aligning → high temperature slow cooling → normalizing → cold bed slow cooling → inspection → warehouse-in that rolls off the production line.
(1) continuous casting material thickness is 260mm, and blank chemical component sees Table 1.
The chemical ingredients of table 1 embodiment of the invention (wt, %)
| Test piece number (Test pc No.) | C | Mn | P | S | Si | Nb | V |
| 1 | 0.16 | 1.38 | 0.009 | 0.002 | 0.21 | 0.025 | 0.039 |
| 2 | 0.17 | 1.37 | 0.011 | 0.001 | 0.22 | 0.030 | 0.038 |
| 3 | 0.16 | 1.36 | 0.009 | 0.002 | 0.20 | 0.027 | 0.040 |
| 4 | 0.17 | 1.40 | 0.012 | 0.001 | 0.23 | 0.026 | 0.041 |
| 5 | 0.16 | 1.39 | 0.010 | 0.002 | 0.24 | 0.028 | 0.042 |
As can be seen from Table 1, according to the 5 stoves test steel of the present invention's preparation, chemical ingredients all meets requirement of the present invention.
Steel billet adopts cooling controlling and rolling controlling process to produce the Q390E-Z35 low-alloy high-strength thick steel plate of thickness 75mm by described method, and the main technique main points are as follows:
(2) rolling technology: blank heating temperature is 1200～1250 ℃, and soaking time is 240～270min, and tapping temperature is 1180～1230 ℃; Rolling method adopts austenite recrystallization district and the two stages controlled rolling of austenite non-recrystallization district.Every time draft 10～20% of roughing, 1020～1050 ℃ of finishing temperatures, roughing becomes the intermediate blank of 1.7～2.0 times of finished product thicknesses, and the finish rolling start rolling temperature is 850～870 ℃, and every time draft is 8～12%.
(3) roll postcooling technology: adopt the laminar flow cooling, 650～700 ℃ of final cooling temperatures, 5～10 ℃/s of rate of cooling.
(4) the high temperature retarded cooling process that rolls off the production line: steel plate heat is rectified and is placed on cold bed cooling, 430～450 ℃ of the temperature that rolls off the production line, 60 ~ 72 hours cooling in heap time.
(5) normalizing process: 870 ~ 900 ℃ of steel plate normalizing temperatures are incubated about 2 hours backs and go up the cold bed air cooling.
Each embodiment is tested steel plate and comparative steel sampling, according to GB/T 13239-2006 standard, adopt MTS NEW810 type tensile testing machine, stretch with 3mm/min constant chuck rate travel, test cross directional stretch performance, sampling point is 1/4 place of thickness of slab, and test-results is got the mean value of 2 samples.According to GB/T 229-2007 standard, adopt NCS series 500J instrumentation Charpy impact machine tester, test-40 ℃ of charpy impact merits, sampling point is 1/4 place of thickness of slab, test-results is got the mean value of 3 samples.The steel plate Mechanics Performance Testing the results are shown in Table 2.
The object performance of table 2 embodiment of the invention
| Specimen coding | R eL/MPa | R m/MPa | A/% | Relative reduction in area/% | Akv (40 ℃ vertically)/J | Clod wash |
| 1 | 400 | 600 | 30 | 55 | 90 | Qualified |
| 2 | 405 | 605 | 32 | 60 | 80 | Qualified |
| 3 | 405 | 595 | 32 | 60 | 85 | Qualified |
| 4 | 425 | 630 | 30 | 65 | 70 | Qualified |
| 5 | 385 | 570 | 31 | 70 | 90 | Qualified |
As can be seen, according to the test steel of explained hereafter of the present invention, the steel plate yield strength all reaches the Q390 level, and Z all satisfies the requirement of Z35 rank to performance, and-40 ℃ of ballistic works are all more than 70J.
Utilize explained hereafter Q390E-Z35 slab of the present invention less demanding to mill capacity, be suitable for most Heavy Plate Plant, the steel plate comprehensive mechanical property is good, has good anti-lamellar tearing ability.
Claims (3)
1. the manufacture method of a Q390E-Z35 low-alloy high-strength slab is characterized in that this manufacture method adopts cooling controlling and rolling controlling process to add normalizing process production, comprises following technology:
(1) blank is selected: the chemical ingredients of continuous casting material is: C:0.15～0.18%, Mn:1.30～1.50%, Si:0.18～0.25%, P :≤0.015%, S :≤0.005%, Nb:0.020～0.035%, V:0.020～0.050%, Al:0.020～0.035%, surplus are Fe and unavoidable impurities;
(2) rolling technology: select above-mentioned continuous casting material, Heating temperature is 1200～1250 ℃, and soaking time is 240～270min, and tapping temperature is 1180～1230 ℃; Rolling method adopts austenite recrystallization district and the two stages controlled rolling of austenite non-recrystallization district, every time draft 10～20% of roughing, and 1020～1050 ℃ of finishing temperatures, roughing becomes the intermediate blank of 1.7～2.0 times of finished product thicknesses; The finish rolling start rolling temperature is 850～870 ℃, and every time draft is 8～12%;
(3) roll postcooling technology: adopt the laminar flow cooling, 650～700 ℃ of final cooling temperatures, 5～10 ℃/s of rate of cooling;
(4) adopt the high temperature retarded cooling process that rolls off the production line: steel plate heat is rectified and is placed on the cold bed cooling, 430～450 ℃ of the temperature that rolls off the production line, and cooling in heap, 60 ~ 72 hours cooling in heap time are adopted in the steel plate back of rolling off the production line;
(5) normalizing process: 870 ~ 900 ℃ of steel plate normalizing temperatures, be incubated and go up the cold bed air cooling after 1～3 hour, obtain Q390E-Z35 low-alloy high-strength slab.
2. the manufacture method of Q390E-Z35 low-alloy high-strength slab according to claim 1 is characterized in that: adopting thickness is the continuous casting material of 260mm, obtains the thick Q390E-Z35 low-alloy high-strength of 75mm slab.
3. the manufacture method of Q390E-Z35 low-alloy high-strength slab according to claim 1, it is characterized in that: the chemical ingredients of continuous casting material is: C:0.16～0.17%, Mn:1.36～1.40%, Si:0.20～0.24%, P :≤0.012%, S :≤0.002%, Nb:0.025～0.030%, V:0.038～0.042%, Al:0.020～0.035%, surplus is Fe and unavoidable impurities.
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| CN102605245A (en) * | 2011-12-30 | 2012-07-25 | 内蒙古包钢钢联股份有限公司 | Ni-free normalized type Q370R pressure vessel steel plate and manufacturing method thereof |
| CN102912221A (en) * | 2012-10-12 | 2013-02-06 | 舞阳钢铁有限责任公司 | Large-thickness structural steel plate for high-rise building and production method thereof |
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| CN102605245A (en) * | 2011-12-30 | 2012-07-25 | 内蒙古包钢钢联股份有限公司 | Ni-free normalized type Q370R pressure vessel steel plate and manufacturing method thereof |
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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 |
| CN106756514A (en) * | 2017-01-24 | 2017-05-31 | 舞阳钢铁有限责任公司 | A kind of special thickness steel plate for building structure of high intensity normalizing type and its production method |
| CN107099746A (en) * | 2017-04-21 | 2017-08-29 | 舞阳钢铁有限责任公司 | A kind of normalizing type pressure vessel Aldecor plate and its production method |
| CN107130180A (en) * | 2017-06-13 | 2017-09-05 | 唐山钢铁集团有限责任公司 | A kind of inexpensive Q390 medium-thick plates and its production method |
| CN108149135A (en) * | 2017-12-08 | 2018-06-12 | 南阳汉冶特钢有限公司 | A kind of Q390E grades of molding steel plates of 420mm thickness low-temperature impact and its production method |
| CN108149135B (en) * | 2017-12-08 | 2019-12-03 | 南阳汉冶特钢有限公司 | A kind of Q390E grades of molding steel plates of 420mm thickness low-temperature impact and its production method |
| 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 |
| CN114892087A (en) * | 2022-05-11 | 2022-08-12 | 河北普阳钢铁有限公司 | Low-cost Q390GJC-N normalized high-construction steel and preparation method thereof |
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Application publication date: 20110504 |