CN106609335A - Tensile strength 700 MPa-grade high broaching hot-rolled steel plate and manufacturing method thereof - Google Patents
Tensile strength 700 MPa-grade high broaching hot-rolled steel plate and manufacturing method thereof Download PDFInfo
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Abstract
The invention relates to a tensile strength 700 MPa-grade high broaching hot-rolled steel plate and a manufacturing method thereof, and solves the technical problems of weak broaching and flanging performance of a traditional tensile strength 700 MPa-grade high broaching hot-rolled steel plate. The tensile strength 700 MPa-grade high broaching hot-rolled steel plate comprises the following chemical components in percentage by weight: 0.05-0.09% of C, 0.15-0.35% of Si, 1.20-1.80% of Mn, P not more than 0.015%, S not more than 0.008%, 0.015-0.050% of Al, 0.08-0.13% of Ti, 0.035-0.065% of V, and the balance of iron and inevitable impurities. The hot-rolled steel plate can be used for manufacturing vehicle structural parts.
Description
Technical field
The present invention relates to high-chambering steel plate, the high reaming hot rolled steel plate of more particularly to a kind of tensile strength 700MPa level and its manufacture method.
Background technology
With the development of auto industry, to lightweight, safety, reduces cost, the requirement more and more higher of reduction fuel consumption, " high-strength thinning " is the inexorable trend of automobile steel to automobile industry.Many vehicle body parts, such as automobile power swing arm, wheel etc., put forward higher requirement to the intensity of steel.But in application process find, this high-strength material make some have the parts of larger reaming amount and flange amount when be very easy to it is cracking, so these parts intensity height on the premise of require steel with good reaming performance, stretch flangeability is good.
Prior art produces the line and staff control that high reaming steel mainly obtains single-phase ferrite or ferrite+bainite by alloying element and cooling controlling and rolling controlling process in steel, obtains good reaming performance.But in existing disclosed technology, the line and staff control of ferrite or ferrite+bainite is difficult to obtain higher intensity, single-phase ferritic structure intensity is not enough, if bainite too high levels in ferrite+bainite structure, the intensity of steel plate rises, but the consequence brought is the drastically decline of reaming performance.
The patent of Chinese patent application CN 201510049822.3 is disclosed " the hot rolling acid-cleaning strip and its production method with high reaming performance ", by the control and rolling to chemical composition, the control of acid cleaning process parameter, so that the strip microscopic metallographic structure come into output is ferrite+bainite, volume ratio 10～20% wherein shared by bainite structure, strip tensile strength >=the 540MPa, hole expansibility λ >=100%.But its limited strength, it is impossible to meet needs of the automobile industry to the high reaming performance steel plate of higher intensity.
" a kind of tensile strength 780MPa disclosed in the patent of Chinese patent application CN 201310628170.X
A kind of level high-chambering steel plate and its manufacture method ", there is provided the high reaming steel of high intensity, the main precipitation strength using Ti and C is acted on; cause its reaming performance not high; 50%≤λ≤70%, it is impossible to which for making, shaping is complicated, the part high to reaming and flange performance requirement.
Therefore, there is problems with about the technical scheme of the high reaming performance SPHC of high intensity and its manufacture method disclosed in prior art：The feature of high intensity and high reaming performance can not be provided simultaneously with, it is impossible to for both requiring to intensity, shaping is complicated, and the application scenario high to reaming and flange performance requirement, it is impossible to meet needs of the automobile industry to " high-strength thinning " reduction energy resource consumption.
The content of the invention
It is an object of the invention to provide a kind of high reaming hot rolled steel plate of tensile strength 700MPa level and its manufacture method, solve the technical problem of existing tensile strength 700MPa level high reaming hot rolled steel plate reaming and flange processing poor performance.
The technical solution used in the present invention is：
A kind of high reaming hot rolled steel plate of tensile strength 700MPa level, the percentage by weight of its chemical composition is：C:0.05%～0.09%, Si：0.15%～0.35%, Mn:1.20%～1.80%, P≤0.015%, S≤0.008%, Al:0.015%～0.050%, Ti:0.08%～0.13%, V：0.035%～0.065%, balance of iron and inevitably it is mingled with.
The reasons why chemical composition of the high reaming hot rolled steel plate of tensile strength 700MPa level of the present invention is limited within the above range is as follows：
Carbon：Carbon improves in the present invention intensity and obtains the important element of intended tissue.Solid solution in the base carbon improve material quenching degree, reduce transformation temperature, be conducive to obtain bainite and martensite tissue.Other carbon and Ti and V combines to form the carboritride of Ti and V, and alternate precipitation is formed in ferrite, with reinforced ferrite, reduces the intensity difference effect between ferrite and martensite.Carbon content is too high, and the ratio of martensite of acquisition is high, is unfavorable for obtaining high reaming performance, and carbon content is too low, it is impossible to obtain enough intensity, the C content that the present invention sets is as 0.05%～0.09%.
Silicon：Silicon is solid-solubilized in steel matrix significantly reinforcing effect, and also there is Si in the present invention promotion C to spread to austenite, suppress the effect of perlitic transformation.Pearlite has serious deterioration effect to reaming performance.In the present invention, as Si contents are too low, pearlite is occurred in microscopic structure, reduces reaming performance, Si too high levels can form the serious Fe for being difficult to remove in hot rolling plate surface2O3, affect product appearance and sequent surface to process.The present invention limits Si contents as 0.15%～0.35%.
Manganese：On the one hand manganese can play a part of solution strengthening in the present invention, while γ areas can be expanded, reduce γ → α transition temperatures, expand rolling mill practice scope, be conducive to obtaining bainite+martensitic structure.But Mn contents are high, can accordingly increase the cost of steel, can also increase carbon equivalent, be unfavorable for welding.The present invention limits Mn content ranges as 1.20%～1.80%.
Titanium：Titanium is important alloying element in the present invention, and titanium forms the effective fining austenite grains of TiN precipitated phases in high temperature rolling.In low temperature, Ti and C-shaped form important alternate precipitate in ferrite transformation into TiC particles, improve ferritic intensity, so as to reduce the intensity difference between ferrite and martensite, harmony during deformation is improved, there is high reaming performance while obtaining high intensity.Ti is too high to cause the toughness of steel plate to decline.The present invention limits Ti contents as 0.08%～0.13%.
Vanadium：Vanadium is in the present invention the important alloying element that alternate precipitation is obtained in ferrite transformation.Because there is alternate precipitation uniform precipitation, disperse, size to be nano level feature, invigoration effect substantially, and can keep material to have certain toughness.The present invention limits the content of V as V：0.035%～0.065%.
Sulphur and phosphorus：Sulphur forms sulphide inculsion in steel so as to which ductility and toughness are reduced.During steel rolling, because MnS is mingled with as rolling direction extends, the anisotropy for making steel increases, and Laminated steel is caused when serious.Simultaneously sulfur content is high unfavorable to the weldability of steel.The high cold brittleness for increasing steel of phosphorus, the brittle transition temperature for making steel rises, and the impact flexibility for making steel is remarkably decreased.But in view of actual process control ability, the present invention limits S≤0.008%, P≤0.015%.
Aluminium：Aluminium effect in the present invention is to play a part of deoxidation, and aluminium is strong oxidizing property formation element, and oxygen forms Al in steel2O3Remove in steel-making.Aluminium is too high to form excessive Al2O3It is mingled with, and continuous casting is easily to block sprue gate.The present invention limits Al content as 0.015%～0.050%.
A kind of manufacture method of the high reaming hot rolled steel plate of tensile strength 700MPa level, the method includes：
Molten steel carries out continuous casting Jing after Fruit storage and obtains continuous casting steel billet, wherein the percentage by weight of the molten steel composition is：C:0.05%～0.09%, Si：0.15%～0.35%, Mn:1.20%～1.80%, P≤0.015%, S≤0.008%, Al:0.015%～0.050%, Ti:0.08%～0.13%, V：0.035%～0.065%, balance of iron and inevitably it is mingled with.
Continuous casting steel billet carries out hot rolling in 1220 DEG C～1260 DEG C after 200～280min of heating, described hot rolling is two-part rolling mill practice, and roughing is 6 passage tandem rollings, is rolled more than austenite recrystallization temperature, and roughing end temp is 1020～1070 DEG C；Finish rolling is 7 passage tandem rollings, and in the non-recrystallization temperature area rolling of austenite, finish rolling end temp is 820 DEG C～860 DEG C, finish rolling reduction ratio is more than 75%, section cooling takes the three-stage type of cooling, first paragraph to adopt water-cooled after finish rolling, and cooling velocity is 20-50 DEG C/s, first paragraph final cooling temperature is 600-700 DEG C/s, second segment adopts air cooling, and air cooling time is 4-15s, and the 3rd section is water-cooled, cooling velocity is 30-60 DEG C/s, and coiling temperature is 200 DEG C～300 DEG C.
The reasons why hot rolling technology system that the present invention takes, is as follows：
1st, the setting of continuous casting steel billet heating-up temperature and heat time
The dissolving for being set at the TiC particles for ensureing thick in continuous casting billet of continuous casting steel billet acid extraction，Technical solution of the present invention Ti content is higher，TiC particles can be separated out in continuous casting steel billet cooling procedure，The TiC particles for now separating out are thick，Without invigoration effect，Need in the heating of plate blank before hot rolling，Thick TiC particles are fully dissolved，So could be by the Ti of compound state、V element solid solution enters in austenite，Alternate precipitation is formed in subsequent hot rolling and the phase transformation of cooling procedure，Reinforced ferrite，This is extremely important for technical solution of the present invention，Temperature is too low and the heat time is too short，Original thick TiC particles can not fully dissolve in continuous casting steel billet，Temperature is too high，Heat time is long，Steel slab surface oxidation and decarbonization is serious，It is unfavorable for steel plate final performance and surface quality，Also consume the energy simultaneously.Therefore the present invention sets continuous casting steel billet heating-up temperature as 1220 DEG C～1260 DEG C, and the heat time is 200min～280min.
2nd, roughing end temp setting
Rolling process of rough rolling controls to be rolled more than austenite recrystallization temperature, it is ensured that austenite obtains uniform tiny austenite crystal through repeated deformation and recrystallization.Therefore the present invention sets roughing end temp as 1020 DEG C～1070 DEG C.
3rd, finish rolling end temp setting
The final rolling temperature of the present invention is acted on of both being set with, on the one hand rolled by austenite Unhydrated cement, obtaining inside has the flat austenite crystal of Zona transformans, and tiny ferrite crystal grain is transformed in subsequent laminar cooling process, plays the effect of refined crystalline strengthening.Crystal grain refinement of the present invention is critically important, and ferrite crystal grain roughening can reduce the reaming performance of product.Can also cause the crystal grain of final martensite also can be thick if roughing temperature is too high, so thick ferrite adds thick martensite, and when being deformed, martensite and ferritic boundary are easy for forming micropore material, serious reduction reaming performance.But final rolling temperature can not be too low, too low final rolling temperature easily induces austenitic states of the TiC in the operation of rolling and separates out, and causes, without enough precipitates in follow-up phase transition process, to affect precipitating reinforcing effect.Finish rolling end temp is set as 820 DEG C～860 DEG C.
3rd, section cooling speed and time set after finish rolling
Section cooling takes the three-stage type of cooling after finish rolling, first paragraph cooling adopts water-cooled, first paragraph cooling purpose after finish rolling is that austenite in material of the present invention is subcooled to into uniform temperature, as cooling velocity is too low, the ferrite crystal grain that obtain material phase transformation is thick, is unfavorable for the plasticity and reaming performance of steel plate；As cooling velocity is too high, then phase point temperature can be reduced, be unfavorable for obtaining the ferritic phase ratio of proper ratio in second segment cooling procedure；Final cooling temperature is too high, and the ferrite crystal grain after phase transformation is easily grown up, and final cooling temperature is too low, cannot get the ferrite content of enough ratios, then the plasticity of final material and reaming performance are too low.Consider, present invention setting, first paragraph cooling adopts water-cooled, cooling velocity is 20-50 DEG C/s, and first paragraph final cooling temperature is 600-700 DEG C/s.
Second segment cooling adopts air cooling, and second segment cooling is that austenite is changed into the part ferritic stage in material of the present invention, and such as air cooling time is too short, then cannot get the ferrite content of enough ratios, air cooling time is long, obtains excessive ferrite, then finally cannot get the martensite of proper ratio.Consider, second segment air cooling time is set as 4-15s.
Three-stage cooling adopts water-cooled, remaining austenite in material of the present invention is changed into martensite by three-stage cooling, and such as cooling velocity is too low and coiling temperature is too high, cannot get complete martensitic structure, part pearlitic structrure can be obtained, then seriously reduces the reaming performance of material；As cooling velocity is excessive, coiling temperature is too low, then the distorting stress in martensite is excessive, is also unfavorable for the plasticity and reaming performance of material.Consider, present invention setting, three-stage cooling is water-cooled, and cooling velocity is
30-60℃/s。
4th, the setting of hot-rolling coiling temperature
Hot-rolling coiling temperature mainly affects materials microstructure, performance.Consider, the present invention sets hot rolling reeling as 200 DEG C～300 DEG C.
The microscopic structure of the high reaming hot rolled steel plate of tensile strength 700MPa level that the present invention is obtained is fine grain granular ferrite+acicular ferrite+martensite, wherein the ratio of martensite is 5%-15%, there is the carbonitride of the Ti and V of uniform precipitation on ferrite matrix, ferritic grain size is 10-13 levels；Its 2～6mm thickness hot rolled steel plate yield strengths >=550MPa, tensile strength >=700MPa, elongation after fracture >=18%, reaming performance
≥120%。
The present invention meets needs of the automobile industry to " high-strength thinning " reduction energy resource consumption by the way that using the design of suitable microscopic structure, composition design and hot rolling technology design, steel plate still has high reaming performance while with high intensity.
The present invention has compared to existing technology following good effect：
1. the present invention is designed by suitable composition design and hot rolling technology, has obtained a kind of high reaming hot rolled steel plate of tensile strength 700MPa level, has high reaming performance, reaming performance while with high intensity≥120%；Can be applied to both require intensity, shaping is complicated, and the application scenario high to reaming and flange performance requirement.
2. present component is designed with low C, high Mn, high Ti, the component system containing V, it is obtained in that fine grain granular ferrite+acicular ferrite+martensite, and the carbonitride that alternate pick-up behavior obtains the Ti and V of uniform precipitation on ferrite matrix can be passed through, ensure the yield strength >=550MPa for obtaining steel plate, tensile strength >=700MPa, elongation after fracture >=18%.
3. hot rolling technique of the present invention by suitable slab heating temperature, hot rolling finishing temperature, roll rear sub-sectional cooling technique, obtain the martensitic structure of proper ratio, and enhance ferrite by obtaining the carbonitride of the uniform Ti for separating out and V on ferrite matrix, the intensity difference between ferrite and martensite is reduced, high reaming performance is obtained while high intensity.The high reaming performance hot rolled steel sheet of high intensity for obtaining, has high reaming performance while with high intensity.
4. the present invention disclosure satisfy that the needs for meeting automobile industry to " high-strength thinning " reduction energy resource consumption.
Description of the drawings
Fig. 1 is the microscopic structure metallograph of the hot rolled steel plate of the embodiment of the present invention 1；
Fig. 2 is the carbonitride transmission electron microscope photo of Ti and V on ferrite matrix in the hot rolled steel plate of the embodiment of the present invention 1 tissue.
Specific embodiment
With reference to embodiment 1～4, the present invention will be further described.
Table 1 is the chemical composition of embodiment of the present invention steel（By weight percentage）Aa, balance of Fe and inevitable impurity.
The chemical composition of the embodiment of the present invention steel of table 1, unit：Percentage by weight
According to the requirement that material composition of the present invention is designed; using molten iron pre-desulfurization; converter top bottom blowing; blow Ar stations (or LF stoves) and ensure that bottom blowing Ar mixings time are more than 5 minutes; RH stoves carry out trimming, vacuum circulation degassing process, it is ensured that the pure degassing times of RH are more than 15 minutes, while feeding appropriate iron-calcium line; whole process blows Ar protective castings, is cast into continuous casting steel billet.
After the heated stove of continuous casting steel billet is reheated, roll on continuous hot tandem rolling mill, hot rolling technology control parameter is shown in Table 2, after roughing milling train and finish rolling Continuous mill train controlled rolling, is controlled cooling, then batched.
The embodiment of the present invention hot rolling technology control parameter of table 2
The high reaming hot rolled steel plate of a kind of tensile strength 700MPa level that the present invention obtained using said method is obtained, referring to accompanying drawing 1,2, the microscopic structure of hot rolled steel plate is fine grain granular ferrite+acicular ferrite+martensite（Fig. 1）, the wherein ratio of martensite is 5%-15%, the carbonitride for having the Ti and V of uniform precipitation on ferrite matrix（Fig. 2）, ferritic grain size is 10-13 levels.
The hot rolled steel plate that the present invention is obtained according to《GB/T228.1-2010 metal material stretching test part 1s：Room temperature test method》Tension test is carried out, according to《GB/T
24524-2009 metal sheets and strip hole expansion test method》Hole expansion test is carried out, its mechanical property is shown in Table 3.
The hot rolled steel plate that the present invention is obtained has the advantages that high intensity, high hole expandability, its 2～6mm thickness hot rolled steel plate yield strengths >=550MPa, tensile strength >=700MPa, elongation after fracture A >=18%, reaming performance≥120%。
The mechanical property of the embodiment of the present invention hot rolled steel plate of table 3
In addition to the implementation, the present invention can also have other embodiment.The technical scheme that all employing equivalents or equivalent transformation are formed, all falls within the protection domain of application claims.
Claims (5)
1. the high reaming hot rolled steel plate of a kind of tensile strength 700MPa level, the percentage by weight of its chemical composition is：C:0.05%～0.09%, Si：0.15%～0.35%, Mn:1.20%～1.80%, P≤0.015%, S≤0.008%, Al:0.015%～0.050%, Ti:0.08%～0.13%, V：0.035%～0.065%, balance of iron and inevitably it is mingled with.
2. the high reaming hot rolled steel plate of tensile strength 700MPa level as claimed in claim 1, it is organized as fine grain granular ferrite+acicular ferrite+martensite, wherein the ratio of martensite is 5%-15%, there is the carbonitride of the Ti and V of uniform precipitation on ferrite matrix, the ferritic grain size is 10-13 levels.
3. the high reaming hot rolled steel plate of tensile strength 700MPa level as claimed in claim 1 or 2, its 2～6mm thickness hot rolled steel plate yield strengths >=550MPa, tensile strength >=700MPa, elongation after fracture >=18%, reaming performance
≥120%。
4. the manufacture method of the high reaming hot rolled steel plate of tensile strength 700MPa level as described in claim 1-3 is arbitrary, including：
Molten steel carries out continuous casting Jing after Fruit storage and obtains continuous casting steel billet；Continuous casting steel billet carries out hot rolling in 1220 DEG C～1260 DEG C after 200～280min of heating, described hot rolling is two-part rolling mill practice, and roughing is 6 passage tandem rollings, is rolled more than austenite recrystallization temperature, and roughing end temp is 1020～1070 DEG C；Finish rolling is 7 passage tandem rollings, and in the non-recrystallization temperature area rolling of austenite, finish rolling end temp is 820 DEG C～860 DEG C, finish rolling reduction ratio is more than 75%, section cooling takes the three-stage type of cooling, first paragraph to adopt water-cooled after finish rolling, and cooling velocity is 20-50 DEG C/s, first paragraph final cooling temperature is 600-700 DEG C/s, second segment adopts air cooling, and air cooling time is 4-15s, and the 3rd section is water-cooled, cooling velocity is 30-60 DEG C/s, and coiling temperature is 200 DEG C～300 DEG C.
5. the manufacture method of the high reaming hot rolled steel plate of tensile strength 700MPa level as claimed in claim 4, it is characterised in that after finish rolling, controls steel plate finished product thickness for 2～6mm.
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Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107099739A (en) * | 2017-06-14 | 2017-08-29 | 唐山钢铁集团有限责任公司 | The inexpensive high-chambering steel plate of 600MPa grades of tensile strength and its production method |
| CN109112417A (en) * | 2017-06-26 | 2019-01-01 | 上海梅山钢铁股份有限公司 | A kind of tensile strength 590MPa grades of hot rolled steel plates used for automobile wheels |
| CN109487153A (en) * | 2017-09-11 | 2019-03-19 | 上海梅山钢铁股份有限公司 | A kind of tensile strength 440MPa grades high reaming hot rolling acid-cleaning steel plate |
| CN110578043A (en) * | 2019-10-23 | 2019-12-17 | 攀钢集团攀枝花钢铁研究院有限公司 | Method for cooling high-strength hot-rolled steel sheet |
| CN110592495A (en) * | 2019-10-25 | 2019-12-20 | 攀钢集团攀枝花钢铁研究院有限公司 | 600 MPa-grade vanadium-containing hot-rolled dual-phase steel |
| CN110656292A (en) * | 2018-06-28 | 2020-01-07 | 上海梅山钢铁股份有限公司 | 440 MPa-level tensile strength low-yield-ratio high-hole-expansibility hot-rolled steel plate |
| CN110863136A (en) * | 2018-08-27 | 2020-03-06 | 上海梅山钢铁股份有限公司 | High-hole-expansion-performance hot rolled steel plate for enamel liner of water heater and manufacturing method thereof |
| CN110872676A (en) * | 2018-08-29 | 2020-03-10 | 上海梅山钢铁股份有限公司 | Production method of hot-dip aluminum-zinc steel plate |
| CN111321340A (en) * | 2018-12-17 | 2020-06-23 | 上海梅山钢铁股份有限公司 | Hot rolled steel plate with yield strength of 450MPa and manufacturing method thereof |
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Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1732281A (en) * | 2002-12-26 | 2006-02-08 | 新日本制铁株式会社 | High strength thin steel sheet excellent in hole expansibility, ductility and chemical treatment characteristics, and method for production thereof |
| CN103732779A (en) * | 2011-08-17 | 2014-04-16 | 株式会社神户制钢所 | High-strength hot-rolled steel plate |
| CN103930582A (en) * | 2011-11-08 | 2014-07-16 | 杰富意钢铁株式会社 | High-tensile-strength hot-rolled steel sheet and method for producing same |
| CN104694822A (en) * | 2013-12-06 | 2015-06-10 | 上海梅山钢铁股份有限公司 | High-strength hot rolled steel plate with 700 MPa grade yield strength and manufacturing method thereof |
-
2015
- 2015-10-23 CN CN201510691107.XA patent/CN106609335B/en active Active
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1732281A (en) * | 2002-12-26 | 2006-02-08 | 新日本制铁株式会社 | High strength thin steel sheet excellent in hole expansibility, ductility and chemical treatment characteristics, and method for production thereof |
| CN103732779A (en) * | 2011-08-17 | 2014-04-16 | 株式会社神户制钢所 | High-strength hot-rolled steel plate |
| CN103930582A (en) * | 2011-11-08 | 2014-07-16 | 杰富意钢铁株式会社 | High-tensile-strength hot-rolled steel sheet and method for producing same |
| CN104694822A (en) * | 2013-12-06 | 2015-06-10 | 上海梅山钢铁股份有限公司 | High-strength hot rolled steel plate with 700 MPa grade yield strength and manufacturing method thereof |
Cited By (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107099739A (en) * | 2017-06-14 | 2017-08-29 | 唐山钢铁集团有限责任公司 | The inexpensive high-chambering steel plate of 600MPa grades of tensile strength and its production method |
| CN109112417A (en) * | 2017-06-26 | 2019-01-01 | 上海梅山钢铁股份有限公司 | A kind of tensile strength 590MPa grades of hot rolled steel plates used for automobile wheels |
| CN109487153A (en) * | 2017-09-11 | 2019-03-19 | 上海梅山钢铁股份有限公司 | A kind of tensile strength 440MPa grades high reaming hot rolling acid-cleaning steel plate |
| CN110656292A (en) * | 2018-06-28 | 2020-01-07 | 上海梅山钢铁股份有限公司 | 440 MPa-level tensile strength low-yield-ratio high-hole-expansibility hot-rolled steel plate |
| CN110863136A (en) * | 2018-08-27 | 2020-03-06 | 上海梅山钢铁股份有限公司 | High-hole-expansion-performance hot rolled steel plate for enamel liner of water heater and manufacturing method thereof |
| CN110872676A (en) * | 2018-08-29 | 2020-03-10 | 上海梅山钢铁股份有限公司 | Production method of hot-dip aluminum-zinc steel plate |
| CN110872676B (en) * | 2018-08-29 | 2022-01-14 | 上海梅山钢铁股份有限公司 | Production method of hot-dip aluminum-zinc steel plate |
| CN111321340A (en) * | 2018-12-17 | 2020-06-23 | 上海梅山钢铁股份有限公司 | Hot rolled steel plate with yield strength of 450MPa and manufacturing method thereof |
| CN110578043A (en) * | 2019-10-23 | 2019-12-17 | 攀钢集团攀枝花钢铁研究院有限公司 | Method for cooling high-strength hot-rolled steel sheet |
| CN110592495A (en) * | 2019-10-25 | 2019-12-20 | 攀钢集团攀枝花钢铁研究院有限公司 | 600 MPa-grade vanadium-containing hot-rolled dual-phase steel |
| CN116234935A (en) * | 2020-09-29 | 2023-06-06 | 日本制铁株式会社 | Hot rolled steel sheet |
| CN114480951A (en) * | 2020-11-12 | 2022-05-13 | 上海梅山钢铁股份有限公司 | Hot-rolled dual-phase steel plate with tensile strength of 700MPa and manufacturing method thereof |
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| CN106609335B (en) | 2019-02-05 |
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