CN111979393A - Hot-rolled high-strength steel plate with excellent low-temperature toughness and preparation method thereof - Google Patents
Hot-rolled high-strength steel plate with excellent low-temperature toughness and preparation method thereof Download PDFInfo
- Publication number
- CN111979393A CN111979393A CN201910429655.3A CN201910429655A CN111979393A CN 111979393 A CN111979393 A CN 111979393A CN 201910429655 A CN201910429655 A CN 201910429655A CN 111979393 A CN111979393 A CN 111979393A
- Authority
- CN
- China
- Prior art keywords
- hot
- steel plate
- equal
- less
- strength steel
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
Images
Classifications
-
- 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
- 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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- 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
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention relates to a hot-rolled high-strength steel plate with excellent low-temperature toughness and a preparation method thereof, wherein the hot-rolled high-strength steel plate comprises the following chemical components, by weight, 0.05-0.10% of C, 0.03-0.20% of Si, 1.1-1.7% of Mn, less than or equal to 0.015% of P, less than or equal to 0.005% of S, 0.07-0.11% of Ti, 0.015-0.045% of Nb, less than or equal to 0.005% of N, 0.02-0.05% of Als, 15-25% of Mn/C, 2.0-3.5% of Ti/Nb, and the balance of Fe and impurities. The yield strength of the hot-rolled high-strength steel plate provided by the invention is greater than 590MPa, the tensile strength is greater than 650MPa, the impact energy is stable, the impact energy at minus 20 ℃ is greater than 130J, the impact energy at minus 40 ℃ is greater than 100J, the elongation A50 is greater than 17%, the cold bending property can reach d 2a, and 180 degrees are qualified.
Description
Technical Field
The invention relates to the technical field of ferrous metallurgy, in particular to a hot-rolled high-strength steel plate with excellent low-temperature toughness and a preparation method thereof.
Background
The low-alloy high-strength steel is high-strength steel added with micro-alloy elements such as Mo, Nb, V, Ti and the like on the basis of C-Mn steel, and is widely applied to the industries such as engineering machinery, coal mine machinery and the like. In recent years, in order to develop high-strength steel with low cost and high cost performance, titanium-containing steel is unprecedentedly developed under the background that the cost of titanium alloy is obviously lower than that of niobium-vanadium alloy. However, researches find that the low-temperature toughness of the high-titanium steel is greatly reduced along with the increase of the content of Ti, the fluctuation is large, the influence is more obvious when the thickness is thicker, the effective solution is difficult to solve all the time, and the further development of the hot-rolled high-titanium steel is limited.
The invention patent with publication number CN104264052A discloses a steel plate for engineering machinery and a production method thereof, wherein the steel plate comprises the following chemical components in percentage by mass: 0.05 to 0.09 percent of C, 0.05 to 0.30 percent of Si, 1.5 to 2.0 percent of Mn, less than or equal to 0.025 percent of P, less than or equal to 0.005 percent of S, 0 to 0.07 percent of Nb, 0.08 to 0.15 percent of Ti, 0.10 to 0.30 percent of Mo, 0.015 to 0.06 percent of Als, 0.0010 to 0.0030 percent of Ca, less than or equal to 0.006 percent of N and the balance of Fe, and q adopts a hot rolling and tempering process to provide a product with the thickness specification of 3 to 8.5mm, the impact energy at 20 ℃ is more than or equal to 80J, but the impact energy index at 40 ℃ below zero is not provided, the alloy and working procedure cost is higher due to the precious metal Mo and the subsequent treatment, and the steel plate with the thickness of more than 8.5mm cannot be stably produced.
The invention patent with publication number CN104532125A discloses a high-strength steel for engineering machinery and a preparation method thereof, wherein the preparation method comprises the following steps: smelting and refining in a converter, and then continuously casting to form a blank; heating the casting blank at 1150-1250 ℃; the initial rolling temperature of rough rolling is 1100-1150 ℃, the initial rolling temperature of finish rolling is 915-960 ℃, and the final rolling temperature is 820-880 ℃; after rolling, a two-stage cooling mode is adopted: the first section is cooled to 720-760 ℃ at the cooling speed of 3-6 ℃/s, and the second section is cooled to 560-600 ℃ at the cooling speed of 30-50 ℃/s; and air-cooling to room temperature after coiling. The first stage of the method in the patent has low cooling speed, cannot perform grain refinement, and has low toughness, and the method also has the problems of containing precious metals such as Mo and the like and not mentioning low-temperature toughness indexes.
The invention patent with publication number CN103122435A discloses a hot-rolled titanium-containing high-strength steel plate with yield strength more than 700MPa and a manufacturing method thereof, wherein the steel plate comprises the following components in percentage by weight: 0.05 to 0.12 percent of C, 0.2 to 0.5 percent of Si, 1.0 to 1.6 percent of Mn, 0.16 to 0.20 percent of Ti, less than or equal to 0.010 percent of N, less than or equal to 0.02 percent of P and less than or equal to 0.010 percent of S; 0.001-0.0025% of optional component B; and the balance of Fe and impurities, smelting the steel plate in a vacuum induction furnace of 80kg in an experimental factory, specifically sequentially performing a heating process, a rolling process and a controlled cooling process, wherein the thickness specification is 3-8mm, the steel plate is always strengthened only by Ti precipitation, performance fluctuation is easy to cause, low-temperature toughness indexes are not mentioned, and in addition, the steel plate is produced in the experimental factory environment, the thickness specification is also limited, and a certain distance is reserved from industrial mass production.
The invention patent with publication number CN106319389A discloses a low-cost and high-machinability steel for engineering machinery and a manufacturing method thereof, and the steel comprises the following components in percentage by weight: 0.06-0.10% of C, 0.30-0.60% of Si, 1.00-1.60% of Mn, less than or equal to 0.015% of P, less than or equal to 0.0030% of S, 0.20-0.60% of Ni, 0.50-0.80% of Cr, 0.25-0.55% of Mo, 0.025-0.065% of V, 0.0008-0.0020% of B, 0.008-0.018% of Ti, 0.030-0.070% of Al, less than or equal to 0.0050% of N, 0.0010-0.0040% of Ca and the balance of Fe and inevitable impurities, wherein the preparation method adopts a combination mode of controlled rolling and two-phase region quenching and tempering processes, but the alloy contains high Cr, Ni, Mo and the like, the alloy cost is high, the process flow is long, the production cost is too high, and the popularization and application aspects have high difficulty.
The invention patent with publication number CN109161796A discloses a high-strength beam steel 800L with good low-temperature impact toughness and a production method thereof, and the components by weight percentage are as follows: 0.065-0.085% of C, 0.05-0.15% of Si, 1.30-1.60% of Mn, less than or equal to 0.014% of P, less than or equal to 0.003% of S, 0.045-0.065% of Nb, 0.10-0.12% of Ti, 0.015-0.035% of Als and less than or equal to 0.0050% of N, wherein the Nb-controlled cooling method is adopted for production, the laminar cooling speed is 23-50 ℃/S, although excellent mechanical properties can be ensured, the cooling speed is still not high, and sufficient water-substituted alloy effect cannot be achieved, and the Nb content is one of reasons that the Nb content is relatively high, if the cooling process is optimized, the alloy cost has further reduced space, and the market competitiveness can be further enhanced.
Disclosure of Invention
Aiming at the problems, the hot-rolled high-strength steel plate with excellent low-temperature toughness and the preparation method thereof are provided, aiming at adopting Nb and Ti micro-alloying and controlled rolling and controlled cooling technologies, fully playing the roles of grain refinement and precipitation strengthening and solving the problems of low-temperature toughness fluctuation, thickness limitation and the like of the high-strength steel.
The specific technical scheme is as follows:
the first aspect of the present invention is to provide a hot-rolled high-strength steel sheet excellent in low-temperature toughness, characterized in that the chemical composition of the high-strength steel sheet is, in terms of weight percentage, 0.05 to 0.10% of C, 0.03 to 0.20% of Si, 1.1 to 1.7% of Mn, 0.015% or less of P, 0.005% or less of S, 0.07 to 0.11% of Ti, 0.015% to 0.045% of Nb, 0.005% or less of N, 0.02 to 0.05% of Als, 15 to 25% of Mn/C, 2.0 to 3.5% of Ti/Nb, and the balance of Fe and unavoidable impurities.
The composition ranges in the hot-rolled high-strength steel sheet according to the present invention are set for the following reasons:
1) c is the cheapest element for improving the strength of the material, the hardness and the strength of the material are improved along with the increase of the carbon content, but the ductility and the toughness and the welding performance are reduced, and the weight percentage content of C is only 0.05-0.10 percent in comprehensive consideration.
2) In common solid solution elements, Si is only second to P and is dissolved in ferrite and austenite in a solid manner, so that the strength can be improved, the Si can reduce the diffusion speed of carbon in the ferrite, carbides precipitated during tempering are not easy to aggregate, the tempering stability is improved, but quenching cracks are easy to generate due to overhigh Si, and the crack tendency is larger under ultra-fast cooling; during the heating of the steel, Si combines with O to produce SiO2Then the iron olivine Fe and FeO are subjected to a series of complex solid-phase reactions to generate the iron olivine Fe2SiO4The surface quality is influenced, and the Si content is preferably 0.03-0.20% by weight in comprehensive consideration.
3) Mn can obviously reduce the Ar1 temperature of the steel and the decomposition speed of austenite, and can improve the strength with the infinite solid solution energy of Fe, but if the Mn content is too high, the tempering brittleness of the steel can be increased, so that the serious center segregation is caused, and the Mn content is preferably 1.1-1.7 percent by weight in comprehensive consideration; meanwhile, the Mn/C is controlled to be between 15 and 25, so that better toughness matching can be ensured.
4) Nb has strong affinity with C, N in steel, can form stable Nb (C, N) compounds with Nb, is induced to separate out in the controlled rolling process, is dispersed and distributed along austenite grain boundaries and is used as phase-change nucleation particles, can effectively prevent recrystallization and improve ferrite nucleation rate, has obvious effect on grain refinement, and is preferably 0.015-0.045% in weight percentage.
5) And the Ti and C, N elements form high-temperature resistant TiN and TiC particles to play a role in precipitation strengthening, the TiN and TiC particles are pinned at the original austenite crystal boundary to prevent austenite crystal grains from growing large, the TiN and TiC particles can obviously prevent grains in a heat affected zone from growing large during welding and improve welding performance, but when the Ti content is lower, the effects of precipitation strengthening and welding performance improvement are small, when the Ti content is too high, the plasticity is reduced, and performance fluctuation is easily caused, and the Ti content by weight is preferably 0.07-0.11 percent in comprehensive consideration.
6) The influence of N on the performance of steel is similar to that of C and P, the strength is obviously improved along with the increase of N content, the plasticity, particularly the toughness is obviously reduced, the weldability is deteriorated, the cold brittleness is aggravated, the aging tendency is increased, N and Ti have good affinity to form a thick TiN compound, the thick TiN compound is difficult to fully dissolve during heating to form inclusions, the inclusions become crack sources in the stretching and impacting processes, and the alloy waste can also be caused, so that the comprehensive consideration that N is less than or equal to 0.005 percent is favorable.
7) And Als can be deoxidized in the steel and can also play a role in refining grains, and the Als is preferably 0.02-0.05 percent in comprehensive consideration.
8) The crystal grains are refined by adopting Nb microalloying and a first section high cooling rate process together, the effect of replacing alloy with water at high cooling rate is exerted, the alloy cost is saved, and meanwhile, the (Nb, Ti) and (C, N) particles are also ensured to be uniformly distributed in steel to play a role in composite precipitation strengthening, and the Ti/Nb content is preferably 2.0-3.5 percent in comprehensive consideration.
9) P, S is a harmful impurity element in steel, P in the steel is easy to form segregation in the steel, the toughness and welding performance of the steel are reduced, S is easy to form plastic sulfide, the steel plate is layered, and the performance of the steel plate is deteriorated, so the lower the P, S content is, the better, the comprehensive consideration is that the P, S content of the steel is that P is less than or equal to 0.015 percent, and S is less than or equal to 0.005 percent.
A second aspect of the present invention provides a method for producing the above hot-rolled high-strength steel sheet, characterized by comprising the steps of:
1) smelting and casting to obtain a steel billet;
2) heating the steel billet, performing hot rolling consisting of rough rolling and finish rolling, cooling consisting of a first section of cooling and a second section of cooling, coiling, flattening and finishing to obtain a hot-rolled high-strength steel plate;
Wherein, the heating tapping temperature in the step 2) is 1240-1300 ℃, and the heating time is more than or equal to 150min, so as to ensure that alloy elements such as Nb, Ti and the like and carbon nitride are completely dissolved in solid, and prevent large particles from being precipitated and grown to form inclusions; the outlet temperature of rough rolling is 1040-; the first section cooling rate is 50-80 ℃/s, so that the finish rolling temperature of finish rolling is cooled to 610-650 ℃, the second section cooling rate is 5-15 ℃/s, the higher first section cooling rate is favorable for refining grains, and the (Nb, Ti) (C, N) can be inhibited from separating out and growing in the first section cooling process, so that a large amount of nano-scale precipitated phases can be dispersed and separated out in the coiling process, so that the strength of a thick steel plate is improved, meanwhile, the lower second section cooling rate is favorable for obtaining a more stable coiling temperature, and is particularly favorable for obtaining a thicker steel plate, so that the steel plate with uniform structure performance is favorably obtained; the coiling temperature was 550-590 ℃.
The above production method is also characterized in that the thickness of the steel sheet is controlled to be 3 to 16mm when the steel sheet is rolled in the step 2).
The beneficial effect of above-mentioned scheme is:
1) the steel plate provided by the invention does not contain noble metals such as Ni, Cr, Mo and the like, only contains a small amount of Nb and higher Ti, does not need heat treatment, and has low process cost and high production efficiency;
2) the yield strength of the steel plate provided by the invention is greater than 590MPa, the tensile strength is greater than 650MPa, the impact energy is stable, the impact energy at minus 20 ℃ is greater than 130J, the impact energy at minus 40 ℃ is greater than 100J, the elongation A50 is greater than 17%, the cold bending property can reach d 2a, and 180 degrees are qualified;
3) the steel plate provided by the invention can reach more than 10mm, can cover part of the specification of a medium plate, and has strong market competitiveness.
Drawings
FIG. 1 is a metallographic structure diagram of a steel sheet prepared in example 1 of the present invention.
Detailed Description
The technical solutions in the embodiments of the present invention will be clearly and completely described below with reference to the drawings in the embodiments of the present invention, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all of the embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
It should be noted that the embodiments and features of the embodiments may be combined with each other without conflict.
The invention is further described with reference to the following drawings and specific examples, which are not intended to be limiting.
The invention provides a hot-rolled high-strength steel plate with excellent low-temperature toughness, which comprises the following chemical components, by weight, 0.05-0.10% of C, 0.03-0.20% of Si, 1.1-1.7% of Mn, less than or equal to 0.015% of P, less than or equal to 0.005% of S, 0.07-0.11% of Ti, 0.015-0.045% of Nb, less than or equal to 0.005% of N, 0.02-0.05% of Als, 15-25% of Mn/C, 2.0-3.5% of Ti/Nb, and the balance of Fe and inevitable impurities.
The preparation method of the hot-rolled high-strength steel plate comprises the following steps:
1) smelting and casting to obtain a steel billet;
2) heating the steel billet, performing hot rolling consisting of rough rolling and finish rolling, cooling consisting of a first section of cooling and a second section of cooling, coiling, flattening and finishing to obtain a hot-rolled high-strength steel plate;
3) cooling and coiling;
wherein, the heating tapping temperature in the step 2) is 1240-1300 ℃, and the heating time is more than or equal to 150 min; the outlet temperature of the rough rolling is 1040-; the first section cooling rate is 50-80 ℃/s, so that the finish rolling temperature of finish rolling is cooled to 610-650 ℃, and the second section cooling rate is 5-15 ℃/s; the coiling temperature is 550-590 ℃, and the thickness of the steel plate is controlled to be 3-16mm during coiling.
Specifically, in examples 1 to 4 and comparative examples 1 and 2 of the present invention, steel slabs were smelted and cast according to the following compositions:
specifically, the corresponding preparation process parameters in examples 1 to 4 of the present invention and comparative examples 1 and 2 are shown in the following table:
as shown in fig. 1, examples of the present invention provide a steel sheet having a fine and uniform structure therein, which is advantageous for obtaining an excellent low temperature toughness product.
The steel sheets prepared in examples 1 to 4 of the present invention and comparative examples 1 and 2 were tested for their properties according to national standards of GB/T228 and GB/T231 as shown in the following table:
from the above table, in the hot-rolled high-strength steel prepared by the preparation method provided by the invention, under the condition that chemical components are free of Cr and Mo, the yield strength is above 628MPa, the tensile strength is above 685-810MPa, the A50 is above 18%, the low-temperature toughness at minus 20 ℃ and minus 40 ℃ is excellent and stable, the cold bending property can meet the requirement that D is 2a, and 180 ℃ is qualified, the alloy content in the comparative example is higher, but the low-temperature toughness average value is lower, and for the thick specification, the low-temperature toughness fluctuates, which shows that the invention has more excellent mechanical properties such as low-temperature toughness on the premise of lower alloy content.
While the invention has been described with reference to a preferred embodiment, it will be understood by those skilled in the art that various changes in form and detail may be made therein without departing from the spirit and scope of the invention.
Claims (3)
1. The hot-rolled high-strength steel plate with excellent low-temperature toughness is characterized by comprising the chemical components of, by weight, 0.05-0.10% of C, 0.03-0.20% of Si, 1.1-1.7% of Mn, less than or equal to 0.015% of P, less than or equal to 0.005% of S, 0.07-0.11% of Ti, 0.015-0.045% of Nb, less than or equal to 0.005% of N, 0.02-0.05% of Als, 15-25% of Mn/C, 2.0-3.5% of Ti/Nb and the balance of Fe and inevitable impurities.
2. A method of manufacturing a hot-rolled high-strength steel sheet according to claim 1, comprising the steps of:
1) smelting and casting to obtain a steel billet;
2) heating the steel billet, performing hot rolling consisting of rough rolling and finish rolling, cooling consisting of a first section of cooling and a second section of cooling, coiling, flattening and finishing to obtain a hot-rolled high-strength steel plate;
wherein, the heating tapping temperature in the step 2) is 1240-1300 ℃, and the heating time is more than or equal to 150 min; the outlet temperature of the rough rolling is 1040-; the first section cooling rate is 50-80 ℃/s, so that the finish rolling temperature of finish rolling is cooled to 610-.
3. The manufacturing method according to claim 1, wherein the thickness of the steel sheet is controlled to be 3 to 16mm when rolled in the step 2).
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201910429655.3A CN111979393A (en) | 2019-05-22 | 2019-05-22 | Hot-rolled high-strength steel plate with excellent low-temperature toughness and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201910429655.3A CN111979393A (en) | 2019-05-22 | 2019-05-22 | Hot-rolled high-strength steel plate with excellent low-temperature toughness and preparation method thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN111979393A true CN111979393A (en) | 2020-11-24 |
Family
ID=73436333
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201910429655.3A Pending CN111979393A (en) | 2019-05-22 | 2019-05-22 | Hot-rolled high-strength steel plate with excellent low-temperature toughness and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN111979393A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113462974A (en) * | 2021-06-29 | 2021-10-01 | 莱芜钢铁集团银山型钢有限公司 | 10-60 mm thickness specification high-strength high-toughness forklift steel and preparation method thereof |
| CN115558864A (en) * | 2022-10-19 | 2023-01-03 | 湖南华菱涟源钢铁有限公司 | High-strength steel plate and preparation method thereof |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH05222484A (en) * | 1992-02-10 | 1993-08-31 | Kawasaki Steel Corp | Hot rolled steel strip with low yield ratio for construction use excellent in refractoriness and toughness and its production |
| CN101565794A (en) * | 2008-04-22 | 2009-10-28 | 宝山钢铁股份有限公司 | High-strength hot rolling automotive frame steel plate and manufacturing method thereof |
| CN102424933A (en) * | 2011-12-02 | 2012-04-25 | 山西太钢不锈钢股份有限公司 | Hot-rolled high-strength strip steel and manufacturing method thereof |
| CN102899561A (en) * | 2012-10-23 | 2013-01-30 | 鞍钢股份有限公司 | High-strength cold forming steel sheet and manufacturing method thereof |
| 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 |
| CN106636907A (en) * | 2016-12-29 | 2017-05-10 | 内蒙古包钢钢联股份有限公司 | Thin gauge carriage body steel belt with yield strength of 600MPa, and manufacturing method of thin gauge carriage body steel belt |
| CN109161796A (en) * | 2018-08-31 | 2019-01-08 | 邯郸钢铁集团有限责任公司 | With favorable low-temperature impact toughness high-strength crossbeam steel 800L and its production method |
-
2019
- 2019-05-22 CN CN201910429655.3A patent/CN111979393A/en active Pending
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH05222484A (en) * | 1992-02-10 | 1993-08-31 | Kawasaki Steel Corp | Hot rolled steel strip with low yield ratio for construction use excellent in refractoriness and toughness and its production |
| CN101565794A (en) * | 2008-04-22 | 2009-10-28 | 宝山钢铁股份有限公司 | High-strength hot rolling automotive frame steel plate and manufacturing method thereof |
| CN102424933A (en) * | 2011-12-02 | 2012-04-25 | 山西太钢不锈钢股份有限公司 | Hot-rolled high-strength strip steel and manufacturing method thereof |
| CN102899561A (en) * | 2012-10-23 | 2013-01-30 | 鞍钢股份有限公司 | High-strength cold forming steel sheet and manufacturing method thereof |
| 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 |
| CN106636907A (en) * | 2016-12-29 | 2017-05-10 | 内蒙古包钢钢联股份有限公司 | Thin gauge carriage body steel belt with yield strength of 600MPa, and manufacturing method of thin gauge carriage body steel belt |
| CN109161796A (en) * | 2018-08-31 | 2019-01-08 | 邯郸钢铁集团有限责任公司 | With favorable low-temperature impact toughness high-strength crossbeam steel 800L and its production method |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113462974A (en) * | 2021-06-29 | 2021-10-01 | 莱芜钢铁集团银山型钢有限公司 | 10-60 mm thickness specification high-strength high-toughness forklift steel and preparation method thereof |
| CN115558864A (en) * | 2022-10-19 | 2023-01-03 | 湖南华菱涟源钢铁有限公司 | High-strength steel plate and preparation method thereof |
| CN115558864B (en) * | 2022-10-19 | 2023-10-24 | 湖南华菱涟源钢铁有限公司 | High-strength steel plate and preparation method thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN101768698B (en) | Low cost yield strength 700MPA level non-tempering processing high strength steel plate and manufacturing method thereof | |
| WO2016095721A1 (en) | Quenched-tempered high-strength steel with yield strength of 900 mpa to 1000 mpa grade, and manufacturing method therefor | |
| CN109536846B (en) | High-toughness hot-rolled steel plate with yield strength of 700MPa and manufacturing method thereof | |
| CN109778069B (en) | One-steel multi-stage cold-rolled low-alloy high-strength steel with yield strength covering 240-270 Mpa and manufacturing method thereof | |
| CN104357742B (en) | 420MPa high-thickness hot-rolled steel sheet for ocean engineering and production method thereof | |
| JP2022508292A (en) | 980MPa class cold rolled steel sheet with high hole expansion rate and high elongation rate and its manufacturing method | |
| CN111304531B (en) | Hot-rolled H-shaped steel with yield strength of 550MPa and production method thereof | |
| JP2023153941A (en) | Cold-rolled steel sheet with excellent formability, galvanized steel sheet, and manufacturing method thereof | |
| CN103526111A (en) | Hot-rolled plate band steel with yield strength being 900MPa and preparation method thereof | |
| CN104928602A (en) | Pipeline steel, wide and thick plate, resistant to H2S corrosion, and production method thereof | |
| CN113416889B (en) | Ultrahigh-strength hot-galvanized DH1470 steel with good welding performance and preparation method thereof | |
| CN109811267B (en) | One-steel multi-stage cold-rolled low-alloy high-strength steel with yield strength covering 300-340 Mpa grade and manufacturing method thereof | |
| CN114525452B (en) | Hot-dip galvanized low-alloy high-strength steel with yield strength of 700Mpa level and preparation method thereof | |
| CN106319355A (en) | Rare earth-contained high-manganese cold-rolled steel plate and manufacturing method thereof | |
| AU2022392619A1 (en) | High-strength steel with good weather resistance and manufacturing method therefor | |
| CN110592491B (en) | High-wear-resistance martensite/austenite dual-phase wear-resistant steel plate and manufacturing method thereof | |
| CN108728728B (en) | High manganese steel with extremely low yield ratio and manufacturing method thereof | |
| JP6684353B2 (en) | Thick plate steel excellent in low temperature toughness and hydrogen induced cracking resistance, and method of manufacturing the same | |
| CN111979393A (en) | Hot-rolled high-strength steel plate with excellent low-temperature toughness and preparation method thereof | |
| CN111748737B (en) | Easily-welded ultrahigh-strength steel with cold crack sensitivity coefficient less than or equal to 0.25 and production method thereof | |
| CN110066966B (en) | Low-internal-stress titanium-containing high-strength steel and production method thereof | |
| JP2023071938A (en) | High strength steel sheet having excellent ductility and workability, and method for manufacturing the same | |
| CN111979474B (en) | Hot continuous rolling fine grain bainite steel plate and preparation method thereof | |
| CN111218616B (en) | Low-temperature-resistant high-toughness high-strength low-alloy round steel and preparation method thereof | |
| JP2002363685A (en) | Low yield ratio high strength cold rolled steel sheet |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20201124 |
|
| RJ01 | Rejection of invention patent application after publication |