CN103924154A - Production method of steel plate - Google Patents
Production method of steel plate Download PDFInfo
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- CN103924154A CN103924154A CN201310012625.5A CN201310012625A CN103924154A CN 103924154 A CN103924154 A CN 103924154A CN 201310012625 A CN201310012625 A CN 201310012625A CN 103924154 A CN103924154 A CN 103924154A
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Abstract
The invention discloses a production method of a steel plate. The production method comprises the steps: carrying out continuous casting of liquid steel to obtain a plate blank, and successively carrying out heating, rough rolling, finish rolling and cooling of the plate blank, wherein with the total weight of the plate blank as a benchmark, the plate blank comprises 0.16-0.18 wt% of carbon, 0.35-0.60 wt% of silicon, 1.30-1.60 wt% of manganese, 0.06-0.08 wt% of vanadium, 0.015-0.020 wt% of titanium, 0.012-0.016 wt% of nitrogen, and the balance Fe and unavoidable impurities. The production method of the steel plate has no need of adopting of an expensive niobium iron alloy, and the produced steel plate has relatively high strength, relatively high toughness and relatively low yield ratio.
Description
Technical field
The present invention relates to plastic working field, particularly, relate to a kind of production method of steel plate.
Background technology
High-intensity Structural Steel Plate has been widely used in some priority projects of China, at present, when the steel plate of production high intensity levels, it is one of main path that micro-alloyed steel adopts controlled rolling and Controlled cooling process, more commonly adopt niobium-vanadium composite micro-alloying or adopt separately Nb-microalloying, in existing market situation, the higher cost of niobium-vanadium composite micro-alloying and Nb-microalloying that causes of price of niobium is higher, and, in to the process of continuous casting of molten steel, strand easily produces transverse crack, and heat processing technique is very complicated.
Summary of the invention
The production method that the object of this invention is to provide a kind of steel plate, utilizes the method to produce steel plate, and without using expensive ferrocolumbium, and the steel plate of producing has higher intensity and toughness and lower yield tensile ratio.
To achieve these goals, the invention provides a kind of production method of steel plate, this production method comprises: continuous casting of molten steel is obtained to slab, to described slab heat successively, roughing, finish rolling and cooling, wherein, the gross weight of described slab of take is benchmark, in described slab, contain: the carbon of 0.16-0.18 % by weight, the silicon of 0.35-0.60 % by weight, the manganese of 1.30-1.60 % by weight, the vanadium of 0.06-0.08 % by weight, the titanium of 0.015-0.020 % by weight, the nitrogen of 0.012-0.016 % by weight, all the other are Fe and inevitable impurity.
Preferably, the start rolling temperature of described finish rolling is 850-920 ℃, and finishing temperature is 830-870 ℃.
Preferably, described cooling speed is 6-10 ℃/s.
Preferably, during to described heating of plate blank, make described heating of plate blank to 1170-1200 ℃.
Preferably, the start rolling temperature of described roughing is 1150-1180 ℃.
Preferably, the total reduction of described roughing is 60-65%.
Preferably, the thickness of described steel plate is 40-70mm.
Preferably, the metallographic structure of described steel plate is comprised of ferrite and pearlite.
Preferably, the yield strength of described steel plate is greater than or equal to 460MPa.
By technique scheme, adopt vanadium-nitrogen micro-alloying technology to produce high-strength steel, in steel, form carbon, nitrogen and the carboritride of vanadium, utilize dissolving and the precipitation mechanism of vanadium in matrix to suppress growing up and forming precipitation strength effect of matrix grain.Nitrogen element is not only cheap, and increase nitrogen is conducive to separating out of vanadium, in the situation that the intensity of steel plate is constant, by adding cheap nitrogen, can reduce the usage quantity of vanadium, and, in this production method, without using expensive ferrocolumbium, thereby, utilize this production method to reduce the production cost of high tensile steel plate.And, in this production method, by the chemical quality ratio of the various compositions of appropriate design, make the steel plate of producing there is good mechanical property, designing on the basis of molten steel chemical composition, adopt controlled rolling and control cooling technology, reaching and optimize the metallographic structure of steel plate and the object of mechanical property.
Other features and advantages of the present invention partly in detail are described the embodiment subsequently.
Embodiment
Below the specific embodiment of the present invention is elaborated.Should be understood that, embodiment described herein only, for description and interpretation the present invention, is not limited to the present invention.
The invention provides a kind of production method of steel plate, this production method comprises: continuous casting of molten steel is obtained to slab, to described slab heat successively, roughing, finish rolling and cooling, wherein, the gross weight of described slab of take is benchmark, in described slab, contain: the carbon of 0.16-0.18 % by weight, the silicon of 0.35-0.60 % by weight, the manganese of 1.30-1.60 % by weight, the vanadium of 0.06-0.08 % by weight, the titanium of 0.015-0.020 % by weight, the nitrogen of 0.012-0.016 % by weight, all the other are Fe and inevitable impurity.
In above-mentioned production method, adopt vanadium-nitrogen micro-alloying technology to produce high-strength steel, in steel, form carbon, nitrogen and the carboritride of vanadium, utilize dissolving and the precipitation mechanism of vanadium in matrix to suppress growing up and producing precipitation strength effect of matrix grain.Nitrogen element is not only cheap, and than VC, the stability of VN is higher, VN has lower free energy, increase nitrogen and be conducive to separating out of vanadium, in the situation that the intensity of steel plate is constant, by adding cheap nitrogen, can reduce the usage quantity of vanadium, and, in this production method, without using expensive ferrocolumbium, thereby, utilize this production method to reduce the production cost of high tensile steel plate.
And, in this production method, by chemical quality ratio, the especially vanadium of the various compositions of appropriate design and the ratio of nitrogen, make the steel plate of producing there is good mechanical property.Designing on the basis of molten steel chemical composition, adopting for example controlled rolling and the control cooling technology of TMCP, reaching and optimize the metallographic structure of steel plate and the object of mechanical property.
In the present embodiment, the molten steel first having refined is for example, without the direct continuous casting of vacuum-treat (adopt secondary cooling water control continuous casting), and can to strand, impose light pressure to prevent dendritic segregation in the lower end of crystallizer.
Then, the slab that continuous casting is formed heats in process furnace, during to heating of plate blank, makes heating of plate blank to 1170-1200 ℃.The temperature that slab is heated to need to be considered the degree of uniformity of original austenite grains and the solid solution degree of alloying element etc., can guarantee, at the lower temperature of alloying element solid solution, slab is carried out to the thermal treatment of suitable duration, thereby guarantee that alloying element solid solution prevents AUSTENITE GRAIN COARSENING simultaneously.
In present embodiment, adopt two-stage control rolling, i.e. roughing Wei austenite recrystallization district's rolling, finish rolling are in not crystallizing field rolling of austenite.
When roughing (rolling of austenite recrystallization district), by austenite repeatedly recrystallize make Austenite Grain Refinement, the ferrite crystal grain being generated by austenite phase transformation so also will be refinement, thereby improves the toughness of steel plate.During finish rolling, along with the accumulation of deformation quantity forms the deformation austenite being elongated in a large number, in crystal grain, produce a large amount of slip band and dislocation, increased effective grain boundary area, increased ferrite nucleation site and nucleation rate, VN separates out, vanadium suppresses recrystallize, extend the time that recrystallize starts, reduce the temperature of Austenite Dynamic Recrystallization simultaneously, rolling Reng austenite recrystallization district is carried out, and, deformation inductdion VN, V(C, N) (carboritride of vanadium) and VC separate out in austenite, VN, V(C, N) and VC provide forming core core for the ferrite transformation in austenite crystal, and the VN separating out, V(C, N) and the VC austenite that suppresses recrystallize by pinning effect grow up, thereby also increased the length of effective crystal boundary, make to obtain austenitic intracrystalline and crystal boundary all provides a large amount of ferrite nucleation sites, ferrite crystal grain after refinement phase transformation, thereby make the steel plate of producing there is higher intensity and toughness.
In the present embodiment, the start rolling temperature of roughing is preferably 1150-1180 ℃, corresponding with the temperature arriving in process furnace with slab.In order to guarantee that steel plate is along the uniform crystal particles of whole thickness direction, and guarantee also can have enough large total reduction in follow-up finishing stands, thereby can not cause coarse grains, thereby the total reduction of roughing is preferably 60-65%.
Finish rolling is not carried out within the scope of the Precipitation Temperature in crystallizing field and at VN at austenite, preferably, in order to make the power that finish rolling can separate out at vanadium in austenite maximum, make in the short period, to separate out in austenite more VN, thereby the start rolling temperature of finish rolling is 850-920 ℃.Finishing temperature not only exerts an influence to speed of cooling, and, finishing temperature is too high causes final tissue can not obtain refinement fully, make steel plate toughness variation, the too low ferrite that can make of finishing temperature is subject to processing distortion, causes equally microstructure coarsening, toughness variation, therefore, preferably, finishing temperature is 830-870 ℃.Rolling condition based on other, the total reduction of finish rolling can be set to 40-70%, so that ferritic crystal grain is enough tiny, the good mechanical performance of the steel plate of producing.
After rolling, control coolingly to control the austenite crystal state after thermal distortion, do not reduce steel plate toughness and further optimize the intensity of steel plate.First for what guarantee steel plate, finally organize ferrite+perlite, there will not be other tissue; Secondly, owing to having V(C, N in the process of cooling after rolling) separate out, although cooling speed is crossed when slow, can make V(C, N) amount of separating out increases, is conducive to improve precipitating reinforcing effect, but can make ferrite crystal grain grow up and cause intensity and toughness deterioration; Cooling excessive velocities can cause the tissue odds of steel plate even, and cannot ensure time enough and make V(C, N) can separate out fully, thereby preferably, described cooling speed is 6-10 ℃/s.
In present embodiment, cooling temperature in (temperature when hot-rolled sheet enters cooling section) is 760-800 ℃, and coolant outlet temperature (temperature when hot-rolled sheet leaves cooling section) is 650-680 ℃.
The metallographic structure of the steel plate of producing by production method of the present invention is comprised of ferrite and pearlite, and wherein, the ratio that ferrite proportion is higher, perlite is shared is lower.
The steel plate below thickness 70mm is produced in the applicable hot rolling of production method of steel plate of the present invention, for example, the thickness of described steel plate can be 40-70mm, and, utilize the production method of steel plate of the present invention can produce the steel plate that yield strength is greater than or equal to 460MPa.
More than describe the preferred embodiment of the present invention in detail; but the present invention is not limited to the detail in above-mentioned embodiment, within the scope of technical conceive of the present invention; can carry out multiple simple variant to technical scheme of the present invention, these simple variant all belong to protection scope of the present invention.
It should be noted that in addition, each concrete technical characterictic described in above-mentioned embodiment, in reconcilable situation, can combine by any suitable mode, for fear of unnecessary repetition, the present invention is to the explanation no longer separately of various possible array modes.
In addition, between various embodiment of the present invention, also can carry out arbitrary combination, as long as it is without prejudice to thought of the present invention, it should be considered as content disclosed in this invention equally.
The present invention is further detailed explanation by the following examples.
Embodiment 1-10
The present embodiment is for illustrating the production method of steel plate provided by the invention.
Respectively molten iron is smelted, obtained forming molten steel as shown in table 1, afterwards this continuous casting of molten steel (adopting two water-cool control) is become to slab; The slab that continuous casting is obtained heats respectively successively, roughing, finish rolling and cooling, and finally makes steel plate.Wherein, adopt gas heating furnace to heating of plate blank, adopting TMCP technology to carry out controlled rolling to slab obtains hot-rolled sheet and adopts the laminar flow type of cooling to control the cooling final steel plate that obtains to described hot-rolled sheet, in process furnace by heating of plate blank temperature (slab heating temperature) extremely, the start rolling temperature of roughing, the start rolling temperature of finish rolling, finishing temperature, cooling speed, cooling temperature in and coolant outlet temperature are as shown in table 2 respectively, the total reduction of roughing, the thickness of the slab that continuous casting obtains, the thickness of the intermediate blank that roughing obtains and the thickness of finished steel plate are as shown in table 3 respectively.
Table 1
Table 2
Table 3
Performance test
On the finished steel plate making at above embodiment 1-10, sample, and detect yield strength (ReL), tensile strength (Rm) and elongation (A%) according to the method for GB/T228 regulation, method according to GB/T229-2007 regulation detects 0 ℃ of impact of collision merit, and detected result is shown in Table 4.
After the processing such as the sample of obtaining on the finished steel plate that above embodiment 1-10 is made is polished, polishing and etch, utilize opticmicroscope to metallographic structure observation analysis, and according to the method for GB6394-2002 regulation, mean grain size is measured, measurement result is shown in Table 4.Above-mentioned sample is carried out after metallographic structure microscopic examination is analyzed finding, utilize in the above-mentioned sample that production method of the present invention makes, whole thickness direction homogeneous microstructure along sample, microtexture no significant difference in the center of surface, 1/4 thickness place and the through-thickness of sample, and the mean grain size recording is below 7.5 μ m; And the metallographic structure of above-mentioned sample is ferrite+perlite, wherein, ferritic volume ratio is larger, and pearlitic volume ratio is less.
Table 4
From the data of above-mentioned table 4, can find out, adopt more than the yield strength of the steel plate making in the embodiment 1-10 of production method provided by the invention reaches 470MPa, more than tensile strength reaches 600MPa, elongation reaches more than 23.0%, and 0 ℃ of impact of collision merit surpasses 150J.
In the prior art in the production method of the steel plate of common employing niobium-vanadium composite micro-alloying or Nb-microalloying, for example, to chemical composition and content, be: the carbon of 0.17 % by weight, the silicon of 0.45 % by weight, the manganese of 1.50 % by weight, the niobium of 0.055 % by weight, the titanium of 0.020 % by weight, the vanadium of 0.050 % by weight and the inevitably slab of impurity heat respectively successively, roughing, finish rolling and cooling, and finally make steel plate, wherein, in process furnace by heating of plate blank to 1250 ℃, 1180 ℃ of the start rolling temperatures of roughing, 940 ℃ of the start rolling temperatures of finish rolling, 850 ℃ of finishing temperatures, cooling 8 ℃/s of speed, the total reduction 65% of roughing, the thickness of finished steel plate is 40mm, the yield strength of measuring the steel plate making after the finished steel plate of producing detects is 510MPa, tensile strength is 640MPa, elongation 21%, 0 ℃ of ballistic work 158J, thereby, relatively can obtain, the mechanical property of the steel plate that the production method of steel plate of the present invention is produced can reach the mechanical property of the steel plate that the production method of steel plate of the expensive ferrocolumbium of employing of prior art produces, but, the production method of steel plate of the present invention is owing to not using expensive ferrocolumbium, and cheap nitrogen also helps separating out of vanadium, thereby cost is reduced greatly.
Claims (9)
1. the production method of a steel plate, this production method comprises: continuous casting of molten steel is obtained to slab, to described slab heat successively, roughing, finish rolling and cooling, it is characterized in that, the gross weight of described slab of take is benchmark, in described slab, contain: the carbon of 0.16-0.18 % by weight, the silicon of 0.35-0.60 % by weight, the manganese of 1.30-1.60 % by weight, the vanadium of 0.06-0.08 % by weight, the titanium of 0.015-0.020 % by weight, the nitrogen of 0.012-0.016 % by weight, all the other are Fe and inevitable impurity.
2. the production method of steel plate according to claim 1, wherein, the start rolling temperature of described finish rolling is 850-920 ℃, finishing temperature is 830-870 ℃.
3. the production method of steel plate according to claim 1 and 2, wherein, described cooling speed is 6-10 ℃/s.
4. the production method of steel plate according to claim 1, wherein, during to described heating of plate blank, makes described heating of plate blank to 1170-1200 ℃.
5. according to the production method of the steel plate described in claim 1 or 4, wherein, the start rolling temperature of described roughing is 1150-1180 ℃.
6. the production method of steel plate according to claim 1, wherein, the total reduction of described roughing is 60-65%.
7. the production method of steel plate according to claim 1, wherein, the thickness of described steel plate is 40-70mm.
8. the production method of steel plate according to claim 1, wherein, the metallographic structure of described steel plate is comprised of ferrite and pearlite.
9. the production method of steel plate according to claim 1, wherein, the yield strength of described steel plate is greater than or equal to 460MPa.
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Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH02153042A (en) * | 1988-12-06 | 1990-06-12 | Kobe Steel Ltd | High strength and high toughness non-heat treated steel for hot forging |
| JPH10102182A (en) * | 1996-10-01 | 1998-04-21 | Kawasaki Steel Corp | High toughness steel for welded structure, excellent in resistance to galvanizing crack, and its production |
| JPH10219390A (en) * | 1996-12-05 | 1998-08-18 | Nippon Steel Corp | 80kg steel with high productivity, and its production |
| CN102703813A (en) * | 2012-06-27 | 2012-10-03 | 攀枝花钢城集团有限公司 | Vanadium and titanium compound microalloyed steel bar and production method thereof |
-
2013
- 2013-01-14 CN CN201310012625.5A patent/CN103924154A/en active Pending
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH02153042A (en) * | 1988-12-06 | 1990-06-12 | Kobe Steel Ltd | High strength and high toughness non-heat treated steel for hot forging |
| JPH10102182A (en) * | 1996-10-01 | 1998-04-21 | Kawasaki Steel Corp | High toughness steel for welded structure, excellent in resistance to galvanizing crack, and its production |
| JPH10219390A (en) * | 1996-12-05 | 1998-08-18 | Nippon Steel Corp | 80kg steel with high productivity, and its production |
| CN102703813A (en) * | 2012-06-27 | 2012-10-03 | 攀枝花钢城集团有限公司 | Vanadium and titanium compound microalloyed steel bar and production method thereof |
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Application publication date: 20140716 |