CN112647019B - Manufacturing method of steel with different strength grades and low yield ratio - Google Patents
Manufacturing method of steel with different strength grades and low yield ratio Download PDFInfo
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- CN112647019B CN112647019B CN202011433048.3A CN202011433048A CN112647019B CN 112647019 B CN112647019 B CN 112647019B CN 202011433048 A CN202011433048 A CN 202011433048A CN 112647019 B CN112647019 B CN 112647019B
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 55
- 239000010959 steel Substances 0.000 title claims abstract description 55
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 19
- 238000005096 rolling process Methods 0.000 claims abstract description 36
- 238000000034 method Methods 0.000 claims abstract description 20
- 238000001816 cooling Methods 0.000 claims abstract description 17
- 238000010791 quenching Methods 0.000 claims abstract description 15
- 230000000171 quenching effect Effects 0.000 claims abstract description 15
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 6
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 6
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 5
- 239000012535 impurity Substances 0.000 claims abstract description 4
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 4
- 229910000734 martensite Inorganic materials 0.000 claims description 32
- 229910000859 α-Fe Inorganic materials 0.000 claims description 16
- 238000010438 heat treatment Methods 0.000 claims description 11
- 229910001563 bainite Inorganic materials 0.000 claims description 8
- 238000003303 reheating Methods 0.000 claims description 7
- 238000009749 continuous casting Methods 0.000 claims description 3
- 229910001562 pearlite Inorganic materials 0.000 claims description 3
- 238000007670 refining Methods 0.000 claims description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 3
- 239000000463 material Substances 0.000 abstract description 2
- 238000001556 precipitation Methods 0.000 description 5
- 238000000635 electron micrograph Methods 0.000 description 4
- 239000010955 niobium Substances 0.000 description 4
- 239000010936 titanium Substances 0.000 description 4
- 239000013078 crystal Substances 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 229910052799 carbon Inorganic materials 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 229910001568 polygonal ferrite Inorganic materials 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 229910001275 Niobium-titanium Inorganic materials 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 230000004075 alteration Effects 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- BWDUFCSALZHSPQ-UHFFFAOYSA-N molybdenum niobium titanium Chemical compound [Ti][Nb][Mo] BWDUFCSALZHSPQ-UHFFFAOYSA-N 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- RJSRQTFBFAJJIL-UHFFFAOYSA-N niobium titanium Chemical compound [Ti].[Nb] RJSRQTFBFAJJIL-UHFFFAOYSA-N 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
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- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
The invention provides a method for manufacturing steel with different strength grades and low yield ratio, belonging to the technical field of steel material engineering. The steel plate manufactured by the manufacturing method comprises the following components in percentage by weight: c: 0.06-0.12%, Mn: 1.40-1.80%, Si: 0.10-0.20%, P is less than or equal to 0.015%, S is less than or equal to 0.005%, Alt: 0.020 to 0.040%, Nb: 0.020 to 0.050%, Ti: 0.080-0.120 percent, less than or equal to 0.0060 percent of N, and the balance of Fe and inevitable impurities. The steel plate adopts the processes of hot continuous rolling controlled cooling and quenching at different temperatures, and low yield ratio steel plates with different strength levels are realized. The steel plate has yield strength of 550-690MPa, tensile strength of 750-830MPa, yield ratio of not more than 0.83 and impact energy stability at-40 ℃ of more than 40J, and good process performance.
Description
Technical Field
The invention belongs to the technical field of steel material engineering, and particularly relates to a manufacturing method of steel with different strength grades and low yield ratio.
Background
The high-strength steel hot-rolled strip steel with the grade of more than 700MPa is widely produced by adopting the component design of low-carbon niobium-titanium microalloy or low-carbon niobium-titanium-molybdenum microalloy, and the thickness specification is generally 2-16 mm. The composite material is more used for engineering cranes, concrete pump trucks, automobile carriages, automobile girders and the like, and has the characteristic of low manufacturing cost. However, the yield ratio is high due to the production process, generally above 0.90, meanwhile, the precipitation degree of titanium and niobium is inconsistent due to the head-tail temperature difference of the strip steel and the uneven cooling of the steel coil, so that the intensity fluctuation is large, in addition, the different structures and the large performance difference of all parts of the strip steel are caused due to the uneven cooling in the production, for example, a super-cooled structure is easily formed in an area with too fast cooling, so that the plasticity is reduced, and the cracking is caused in the bending process.
In order to further improve the mechanical property and the service performance of the high-strength steel, the transverse cutting steel plate after the hot rolling coil is uncoiled is quenched, so that the problems of high yield ratio, large strength property fluctuation and poor processability are solved.
Disclosure of Invention
The invention aims to provide a method for manufacturing low-yield-ratio steel with different strength grades, which utilizes a hot continuous rolling controlled cooling and quenching process to obtain a structure characterized by massive ferrite + short rod-shaped/granular martensite or a structure characterized by massive ferrite + granular martensite + lath martensite/bainite so as to obtain low-yield-ratio high-strength steel plates with different strength grades. The steel plate manufactured by the method has the tensile strength of more than 700MPa, the thickness specification of 2-16 mm, low yield ratio, stable strength performance and good processability.
In order to achieve the purpose, the invention adopts the technical scheme that:
a manufacturing method of steel with different strength grades and low yield ratio comprises the following components in percentage by weight: c: 0.06-0.12%, Mn: 1.40-1.60%, Si: 0.10-0.20%, S is less than or equal to 0.005%, P is less than or equal to 0.015%, Nb: 0.020 to 0.050%, Ti: 0.080-0.120%, Alt: 0.020-0.040%, N is less than or equal to 0.006%, and the balance of Fe and inevitable impurities.
Further, the manufacturing method includes the steps of: the method comprises the following working procedures of top-bottom combined blown converter, LF refining, slab continuous casting, slab heating, double-rack rough rolling, 7-rack hot continuous rolling finish rolling, plate strip laminar cooling, plate strip coiling, coil plate flattening, steel plate heating and quenching; wherein,
the slab heating process: the slab reheating temperature is 1200-1280 ℃, and the in-furnace time is 150-200 min;
the double-frame rough rolling process comprises the following steps: the rough rolling temperature is 1040-1100 ℃, and the total reduction rate of rough rolling is more than or equal to 70%;
7, hot continuous rolling and finish rolling process of the machine frame: the initial rolling temperature of finish rolling is 1020-1080 ℃, the total reduction rate of finish rolling is more than or equal to 70%, and the final rolling temperature of finish rolling is 820-900 ℃;
the plate strip laminar cooling and plate strip coiling process comprises the following steps: the laminar cooling speed is 20-45 ℃/s, and the coiling temperature is 550-650 ℃;
the working procedures of flattening the rolled plate, heating the steel plate and quenching are as follows: and after the rolled plate is flattened, reheating the steel plate at 710-930 ℃ for 3.25h, and performing water cooling quenching to room temperature after the steel plate is taken out of the furnace.
Further, the structure of the strip after the strip coiling process is characterized by ferrite plus pearlite, and the grain size of the ferrite is more than 11.5 grades.
Further, the steel plate structure after quenching to room temperature is characterized in that: the microstructure of the steel plate after the quenching treatment at the temperature of 710-820 ℃ is massive ferrite + short rod-shaped and/or granular martensite, and the microstructure of the steel plate after the quenching treatment at the temperature of 820-930 ℃ is a microstructure of massive ferrite + granular/massive martensite + lath martensite/bainite.
Compared with the prior art, the invention has the beneficial effects that:
1. the manufacturing method can manufacture high-strength steel plates with 750-830 MPa-level tensile strength and stable performance in different strengths, has a yield ratio of less than or equal to 0.83, and has good processability, and the impact energy at-40 ℃ is stable above 40J.
2. The yield strength of the steel plate manufactured by the manufacturing method is 550-690 MPa.
Drawings
FIG. 1 is an electron micrograph of a low yield ratio high strength steel plate according to an embodiment of the present invention after 720 ℃ quenching;
FIG. 2 is an electron micrograph of a low yield ratio high strength steel plate quenched at 780 ℃ according to an embodiment of the present invention;
FIG. 3 is an electron micrograph of a low yield ratio high strength steel plate quenched at 840 ℃ according to an embodiment of the present invention;
FIG. 4 is an electron micrograph of the low yield ratio high strength steel plate quenched at 900 ℃ according to the example of the present invention.
Detailed Description
The technical solutions and effects of the present invention will be further described with reference to the drawings and specific embodiments, but the scope of the present invention is not limited thereto.
Example 1
The manufacturing method of this example produced 8mm thick steel of different strength grades and low yield ratios.
The steel plate manufactured by the embodiment comprises the following components in percentage by weight: c: 0.08%, Mn: 1.48%, Si: 0.16%, S: 0.001%, P: 0.011%, Nb: 0.028%, Ti: 0.098%, Alt: 0.038%, N: 0.0045 percent, and the balance of Fe and inevitable impurities. C. Mn is mainly an element for improving the strength, Al, Nb and Ti play roles in refining grains and strengthening precipitation, low Si is mainly easy to remove oxide scales on the surface of the plate strip, and nitrogen control aims at inhibiting the precipitation of TiN.
The manufacturing method of the embodiment specifically comprises the following steps: the blank for steel rolling is a continuous casting blank, and the thickness of the blank is 230 mm. Heating the billet at 1260 ℃ for 173 min; the rough rolling temperature of the double-frame rough rolling is 1075 ℃, and the rough rolling total reduction rate is 81 percent; 7, the initial rolling temperature of the fine rolling of the stand is 1055 ℃, the total reduction rate of the fine rolling is 84 percent, and the final rolling temperature is 845 ℃; the front laminar flow section is concentrated with a cooling layer, the cooling speed is 40 ℃/s, and the coiling temperature is 606 ℃; the structure of the rolled plate strip is ferrite plus pearlite, and the grain size of the ferrite is 12 grades.
Heating the steel plate at 720 deg.C, 780 deg.C, 840 deg.C, 900 deg.C for 40min, and water-cooling for quenching. The steel plate after the steel coil is uncoiled can be heated again to enable areas with insufficient precipitation of microalloy elements in the strip steel to be continuously precipitated so as to improve the strength, and finally the precipitation strengthening effect tends to be consistent. Then, by quenching processes at different temperatures, polygonal ferrite grains with different proportions and martensite structures with different forms and proportions are obtained, wherein the fine polygonal ferrite has better comprehensive mechanical property, and the martensite structures with different forms and proportions can obtain the low-yield-ratio high-strength steel with stable performance at different strength levels. The specific steel plate performance indexes after quenching are shown in table 1.
TABLE 1 mechanical Properties of the steel sheets produced in this example
| Thickness/mm | Reheating temperature/. degree.C | Yield strength Mpa | Tensile strength/Mpa | Elongation/percent | Yield ratio | -40 ℃ impact work/J |
| 8 | 720 | 623 | 813 | 18 | 0.77 | 43 52 48 |
| 8 | 780 | 580 | 772 | 20 | 0.75 | 90 86 90 |
| 8 | 840 | 581 | 774 | 20.5 | 0.75 | 128 126 130 |
| 8 | 900 | 689 | 828 | 17 | 0.83 | 138 144 128 |
After the steel is reheated and water-cooled and quenched at 720 ℃, the yield strength is 623MPa, the tensile strength is 813MPa, the elongation is 18%, the yield ratio is 0.77, the impact energy is 43J, 52J and 48J, the microstructure is ferrite, granular and short rod-shaped martensite and carbide, the size of the martensite crystal grain is basically less than 1 μm, the proportion of the martensite is about 13.5%, and carbide exists on the crystal boundary and the ferrite.
After reheating at 780 ℃ and water cooling quenching, the yield strength is 580MPa, the tensile strength is 772MPa, the elongation is 20%, the yield ratio is 0.75, the impact energy is 90J, 86J and 90J, the microstructure is ferrite and martensite, the martensite crystal grains are in a short rod shape, the size is 1-3 mu m, and the martensite proportion is about 15.3%.
After the steel is reheated and water-cooled and quenched at 840 ℃, the yield strength is 581MPa, the tensile strength is 774MPa, the elongation is 20.5%, the yield ratio is 0.75, the impact energy is 128J, 126J and 130J, the microstructure is polygonal and acicular ferrite, granular martensite and massive martensite, lath martensite and bainite, the proportion of the granular martensite to the massive martensite is about 7.1%, and the proportion of the lath martensite to the bainite is about 11.4%.
After the steel is reheated and water-cooled and quenched at 900 ℃, the yield strength is 689MPa, the tensile strength is 828MPa, the elongation is 17%, the yield ratio is 0.83, the impact energy is 138J, 144J and 128J, the microstructure is polygonal and acicular ferrite, granular martensite and massive martensite, lath martensite and bainite, the proportion of the granular martensite to the massive martensite is about 3%, and the proportion of the lath martensite to the bainite is about 22.5%.
The invention realizes that the low yield ratio high-strength steel with the thickness of 8mm can be produced by adopting one component and adopting the same component through reasonably designing components and adjusting key process parameters of each process section, wherein the strength levels of 770MPa, 810MPa, 820MPa and the like are different.
Although embodiments of the present invention have been shown and described, it will be appreciated by those skilled in the art that changes, modifications, substitutions and alterations can be made in these embodiments without departing from the principles and spirit of the invention, the scope of which is defined in the appended claims and their equivalents.
Claims (1)
1. The manufacturing method of the 8mm thick 800MPa grade low yield ratio steel is characterized in that the steel plate manufactured by the manufacturing method comprises the following components in percentage by weight: c: 0.08%, Mn: 1.48%, Si: 0.16%, S: 0.001%, P: 0.011%, Nb: 0.028%, Ti: 0.098%, Alt: 0.038%, N: 0.0045 percent, and the balance of Fe and inevitable impurities;
the manufacturing method comprises the following steps: the method comprises the following working procedures of top-bottom combined blown converter, LF refining, slab continuous casting, slab heating, double-rack rough rolling, 7-rack hot continuous rolling finish rolling, plate strip laminar cooling, plate strip coiling, coil plate flattening, steel plate heating and quenching; wherein,
the slab heating process: the slab reheating temperature is 1260 ℃, and the furnace time is 173 min;
the double-frame rough rolling process comprises the following steps: the rough rolling temperature is 1075 ℃, and the rough rolling total reduction rate is 81 percent;
7, hot continuous rolling and finish rolling process of the machine frame: the initial rolling temperature of finish rolling is 1055 ℃, the total reduction rate of finish rolling is 84%, and the finish rolling temperature of finish rolling is 845 ℃;
the plate strip laminar cooling and plate strip coiling process comprises the following steps: the laminar cooling speed is 40 ℃/s, and the coiling temperature is 606 ℃;
the working procedures of flattening the rolled plate, heating the steel plate and quenching are as follows: after the rolled plate is flattened, the reheating temperature of the steel plate is 900 ℃, the heating time is 40min, and the steel plate is water-cooled and quenched to room temperature after being taken out of the furnace;
the structure of the plate strip after the plate strip coiling process is characterized by ferrite and pearlite, and the grain size of the ferrite is more than 11.5 grade;
after the steel is quenched by water cooling at the reheating temperature of 900 ℃, the yield strength is 689MPa, the tensile strength is 828MPa, the elongation is 17 percent, the yield ratio is 0.83, the impact energy is 138J, 144J and 128J at the temperature of-40 ℃, the microstructure is polygonal and acicular ferrite, granular martensite and massive martensite, lath martensite and bainite, the proportion of the granular martensite to the massive martensite accounts for 3 percent, and the proportion of the lath martensite to the bainite accounts for 22.5 percent.
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| CN102719743A (en) * | 2012-06-27 | 2012-10-10 | 山西太钢不锈钢股份有限公司 | Hot-rolled coil plate for oil casing and manufacturing method thereof |
| CN103589954A (en) * | 2013-11-29 | 2014-02-19 | 东北大学 | Hot rolling steel plate with characteristic of multiple grades in one steel, and manufacturing method thereof |
| CN110629114A (en) * | 2019-10-17 | 2019-12-31 | 山东钢铁集团日照有限公司 | Low-cost high-strength high-toughness bridge steel and preparation method thereof |
| CN111549288A (en) * | 2020-05-22 | 2020-08-18 | 包头钢铁（集团）有限责任公司 | Automobile girder steel with thickness of 12.0-16.0 mm and high toughness of 700MPa and production method thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN102851615A (en) * | 2011-06-28 | 2013-01-02 | 鞍钢股份有限公司 | Tensile strength 800 MPa-grade low-yield-ratio structural steel plate and manufacturing method thereof |
| CN103060715B (en) * | 2013-01-22 | 2015-08-26 | 宝山钢铁股份有限公司 | A kind of ultra-high strength and toughness steel plate and manufacture method thereof with low yielding ratio |
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Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102277539A (en) * | 2011-08-01 | 2011-12-14 | 南京钢铁股份有限公司 | High-strength steel with low yield ratio, high plasticity and ultrafine grain and preparation method thereof |
| CN102719743A (en) * | 2012-06-27 | 2012-10-10 | 山西太钢不锈钢股份有限公司 | Hot-rolled coil plate for oil casing and manufacturing method thereof |
| CN103589954A (en) * | 2013-11-29 | 2014-02-19 | 东北大学 | Hot rolling steel plate with characteristic of multiple grades in one steel, and manufacturing method thereof |
| CN110629114A (en) * | 2019-10-17 | 2019-12-31 | 山东钢铁集团日照有限公司 | Low-cost high-strength high-toughness bridge steel and preparation method thereof |
| CN111549288A (en) * | 2020-05-22 | 2020-08-18 | 包头钢铁（集团）有限责任公司 | Automobile girder steel with thickness of 12.0-16.0 mm and high toughness of 700MPa and production method thereof |
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