CN110184537B - Low-carbon cobalt-containing high-strength bridge cable steel and production method thereof - Google Patents
Low-carbon cobalt-containing high-strength bridge cable steel and production method thereof Download PDFInfo
- Publication number
- CN110184537B CN110184537B CN201910441764.7A CN201910441764A CN110184537B CN 110184537 B CN110184537 B CN 110184537B CN 201910441764 A CN201910441764 A CN 201910441764A CN 110184537 B CN110184537 B CN 110184537B
- Authority
- CN
- China
- Prior art keywords
- strength
- steel
- carbide
- bridge cable
- temperature
- 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.)
- Active
Links
Images
Classifications
-
- 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
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
-
- 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- 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
- C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
-
- 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
- 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
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Strip Materials And Filament Materials (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The low-carbon cobalt-containing high-strength bridge cable steel comprises the following chemical components in percentage by weight: c: 0.10 to 0.14 wt%, Si: 1.00-1.15 wt%, Mn: 1.6-1.8 wt%, Al: 1.55-1.95 wt%, P is less than or equal to 0.01 wt%, S is less than or equal to 0.01 wt%, Co: 0.21 to 0.28wt%, V: 0.45-0.55 wt%; the production process comprises the following steps: heating the hot-rolled wire rod under the condition that the vacuum degree is not more than 100Pa or under the protection atmosphere of argon gas; drawing; water cooling; air cooling and drawing the product with temperature according to the conventional drawing speed to phi 6.9 mm. According to the invention, the metallographic structure is adopted as carbide-free bainite on the bridge cable steel for the first time, the Co is added, the phase change process is accelerated, the formation of the carbide-free bainite structure is promoted, the self-repairing of microcracks can be realized through the phase change of a microstructure, the strength of the steel wire after being galvanized and stabilized can reach more than 2200MPa, and the requirement of twisting is met for more than 35 times.
Description
Technical Field
The invention relates to a wire rod and a production method thereof, belongs to a wire rod for a bridge cable and a production method thereof, and particularly relates to a low-carbon cobalt-containing high-strength wire rod for a bridge cable and a production method thereof.
Background
The bridge cable steel wire is a safe bearing part of modern bridges (cable-stayed bridges and suspension bridges) and is formed by cold drawing and hot galvanizing high-carbon steel wire rods. From the 90 s of the last century to the present, the strength of the steel wire of the bridge cable is continuously improved, and gradually develops from 1670MPa and 1770MPa to 1860MPa and 1960MPa, and the high strength means larger bridge span (meeting the requirements of crossing the river and the sea, reducing the influence on ecology and navigation), higher safety (reducing the dead weight of the bridge) and lower investment cost (reducing the steel consumption) and is a key index for measuring the level of bridge construction.
The data show that the corresponding weight loss of the cable is reduced by more than 10% when the strength of the cable steel wire used as the 'life line' of the modern bridge is improved by 10%. The improvement of material strength can enhance the spanning capability of the main cable, and the material consumption of a cable system can be reduced or the safety factor of the main cable can be improved when the spanning distance is fixed: the Italian Mexican strait bridge in the plan is a double-tower suspension bridge with a main span of 3300m, and after a 1860MPa galvanized steel wire main cable is adopted, the total weight of the main cable is about 166500 tons, which is reduced by nearly 10000 tons compared with a 1770MPa galvanized steel wire main cable. Therefore, with the increasing bridge span and the increasing requirements for bridge construction, the trend of cables to higher strength is inevitable.
At present, all steel wires for bridge cables are formed by drawing and galvanizing hypereutectoid wire rods, and cable steel wires with different strength grades correspond to hot rolled wire rods with different brands, such as 82B (carbon content 0.82%) corresponding to steel wire strength 1770MPa, 87Mn (carbon content 0.87%) corresponding to steel wire strength 1860MPa, and 97Si (carbon content 0.97%) corresponding to steel wire strength 2000 MPa. Along with the improvement of the strength, the carbon content is increased, the control of segregation, organization and the like is increasingly difficult, and the windows of smelting and rolling processes are narrow; meanwhile, with the increase of the carbon content, the strength of the steel wire is increased, the brittleness is increased, and the toughness and the safety of the steel wire are obviously reduced. Therefore, the traditional hypereutectoid steel is gradually difficult to adapt to the performance requirements of ultrahigh strength and has a limited development prospect, and a novel ultrahigh-strength steel needs to be found urgently to meet the engineering construction requirements.
In recent years, the research and development of ultrahigh strength has seen a new highlight, and the most revolutionary discovery is the carbide-free bainite steel discovered by Bhadeshia et al in 2004, the structure of which consists of elongated bainite ferrite and film-like carbon-rich residual austenite which are alternately arranged, the ferrite in the bainite structure is in semi-coherent relation with the parent phase, and the fine crystal structure brought by low-temperature transformation and the fine structure and high-density dislocation in the ferrite determine the high strength of the steel; the residual austenite belongs to a face-centered cubic structure, has a plurality of sliding systems, can relieve stress concentration, belongs to a soft phase, and obviously improves the toughness of the carbide-free bainite steel.
The prior art searches and analyzes the situation:
currently, bridge wire steels are all pearlite structures (hypereutectoid steels) and are mainly aimed at the production of hot rolled wire rods for galvanized steel wires below 2000MPa, as retrieved:
the Chinese patent publication No. CN102181786A relates to a coil rod for a 1670MPa level bridge cable galvanized steel wire and a preparation method thereof; the document of Chinese patent publication No. CN101311288A relates to a wire rod for 1770MPa grade bridge stay cable galvanized steel wire and a manufacturing method thereof; the document of Chinese patent publication No. CN102634730A relates to a wire rod for 1860MPa bridge cable galvanized steel wire and a manufacturing method thereof; the document of Chinese patent publication No. CN105671443A relates to a hot-rolled wire rod for 1960MPa cable galvanized steel wires and a production method thereof. The strength of the steel wire produced by the four documents after drawing is less than 2000MPa, the steel wire is relatively low, and the engineering application of products with related or similar performance is internationally available, and the steel wire belongs to conventional or improved products.
The Chinese patent publication No. CN102936688A relates to a wire rod with tensile strength more than or equal to 2000MPa for bridge cables and a production method thereof, the actual strength of the steel wire in the document is less than 2100MPa, the C content is as high as 0.95-1.2%, and the N content is 0.01-0.03%. Although the high content of C, N ensures the strength of the steel wire, the production difficulty is large, and if the production control is improper, the large fluctuation of the torsion value is often accompanied, which is not favorable for the control of the steel wire quality and the safety of the bridge.
The Chinese patent publication No. CN 10339273 discloses a carbide-free bainite steel, which comprises the following chemical components in parts by weight: 0.3-0.4% of C, 1.0-2.0% of Si, 1.5-2.5% of Mn, 0.8-1.4% of Cr0.1-0.6% of Mo0.8-1.6% of Ni0.004-0.008% of B and 0.2-0.5% of Ti, and the balance of Fe and accompanying impurities, smelting the steel by adopting a medium-frequency induction furnace, preparing a casting in a die, wherein the tapping temperature is 1650-. The steel grade is added with a large amount of noble alloys such as Ni, Cr, Ti and the like, the tensile strength of steel only reaches 1500MPa, and the steel is suitable for toothed plates of steel bodies, not only is the strength of the steel wires manufactured, but also cannot exceed 2000 MPa. With the engineering application of 2000MPa grade galvanized steel wires and the increasingly harsh bridge construction environment, the research and development of higher grade steel for bridge cables are increasingly urgent.
In order to meet the continuously improved engineering construction requirements, the invention innovatively develops the low-carbon cobalt-containing high-strength carbide-free bainite bridge cable steel. The method has the advantages that the metallographic structure is adopted as carbide-free bainite on the bridge cable steel for the first time, the Co element is added, the phase change process is accelerated, and the formation of the carbide-free bainite structure is promoted, so that a brand-new solution is provided for the upgrading and updating of the bridge cable steel, a wire rod with the diameter of phi 14mm is drawn into a steel wire with the diameter of phi 6.9mm, the strength can reach over 2200MPa after the steel wire rod is subjected to galvanizing and stabilizing treatment, and the requirement of twisting for more than 35 times is met; in addition, in carbide-free bainite, residual austenite serving as a soft phase can generate a TRIP effect under the action of stress to form martensite so as to reduce the generation of cracks, namely, the microstructure can realize self-repair of microcracks through phase transformation, so that the safety of the bridge cable steel wire is improved while the ultrahigh strength of the steel wire is realized.
Disclosure of Invention
The invention aims to solve the technical bottleneck of the traditional hypereutectoid bridge cable steel, meet the requirements of large-span and light-weight construction of bridges, and provide the low-carbon cobalt-containing high-strength bridge cable steel and the production method thereof, wherein the metallographic structure is adopted as carbide-free bainite on the bridge cable steel for the first time, the Co element is added, the phase change process is accelerated, the formation of the carbide-free bainite structure is promoted, the self-repair of microcracks can be realized through the phase change of the microstructure, the wire rod with the diameter of 14mm is drawn into a steel wire with the diameter of 6.9mm, the strength can reach over 2200MPa after the galvanization and the stabilization treatment, and the requirements of more than 35 times of torsion are met.
The measures for realizing the aim are as follows:
the low-carbon cobalt-containing high-strength bridge cable steel comprises the following chemical components in percentage by weight: c: 0.10 to 0.14 wt%, Si: 1.00-1.15 wt%, Mn: 1.6-1.8 wt%, Al: 1.55-1.95 wt%, P is less than or equal to 0.01 wt%, S is less than or equal to 0.01 wt%, Co: 0.21 to 0.28wt%, V: 0.45-0.55 wt%, and the balance of Fe and inevitable impurities; the metallographic structure is carbide-free bainite; the strength is more than or equal to 2200MPa, and the twisting times are more than 35 times.
Preferably: the content of Co is 0.21-0.26 wt%.
Preferably: the content of V is 0.51-0.55 wt%.
The method for producing the low-carbon cobalt-containing high-strength bridge cable steel comprises the following steps:
1) heating the hot-rolled wire rod to 770-870 ℃ at the heating speed of 15-20 ℃/s under the condition that the vacuum degree is not more than 100Pa or under the argon gas protective atmosphere, and preserving heat for 20-30 min at the temperature;
2) drawing: the deformation rate in drawing is 7-10S-1Drawing the wire rod from phi 14mm to phi 11.3mm at 650-770 deg.c;
3) performing water cooling to the temperature of 400-460 ℃, and preserving heat for 30-45 min at the temperature;
4) air cooling and drawing the product with the temperature of phi 6.9mm at the conventional drawing speed, wherein the drawing temperature is 200-400 ℃.
The action and mechanism of each element and main process of the invention
C: carbon is the most important constituent element in steel, has the most obvious influence on the strength and the plasticity of the wire rod, and the strength is continuously improved and the plasticity is rapidly reduced after drawing along with the increase of the carbon content. The bridge cable steel wire has higher requirements on strength and also has strict requirements on the torsion value for measuring the comprehensive toughness of the material. The reduced carbon content can obviously improve the torsion value and accelerate the formation of the non-carbide bainite steel, so that in order to balance the requirements of the torsion value and the non-carbide bainite steel, the invention is different from the prior art, creatively adopts a medium-low carbon component system, and changes the current situation that the traditional bridge cable steel mainly depends on the carbon content to improve the strength. The carbon content of the invention is 0.10-0.14 wt%.
Si: silicon is an element that strengthens the steel and inhibits the formation of carbides, promoting the formation of carbide-free bainite, but excessive silicon increases the brittleness of the steel and deteriorates the hot dip galvanizing effect of the steel wire. The Si content of the invention is controlled to be 1.00-1.15 wt%.
Mn: proper amount of manganese can improve the strength and hardenability, and lath bainite with small size can be obtained; in addition, manganese and sulfur are combined to generate MnS, so that the harm of sulfur is reduced, but the overhigh manganese can increase the overheating sensitivity of steel, so that crystal grains are easy to grow during heat treatment. The Mn content of the invention is controlled to be 1.6-1.8 wt%.
Al: the aluminum plays a main role in inhibiting the formation of carbides and promoting the formation of carbide-free bainite, is a key element in a component system, can obviously shorten the bainite phase transition time, and shortens the conventional phase transition process which needs several hours or even several days to meet the requirements of industrial production, but the overhigh aluminum pair causes difficulty in smelting and continuous casting. The invention Al: 1.55 to 1.95 wt%.
P, S: phosphorus and sulfur are harmful elements in the steel, phosphorus is easy to produce cold brittleness, sulfur is easy to produce hot brittleness, and further the processing conditions of steel wire drawing and heat treatment are deteriorated, so the content of the phosphorus and the sulfur needs to be reduced as much as possible. The invention has P less than or equal to 0.01 wt% and S less than or equal to 0.01 wt%.
Co: the cobalt has the similar effect as Al, mainly plays the roles of accelerating the phase transition process and promoting the formation of a carbide-free bainite structure, but belongs to precious and rare metals, so the cobalt provided by the invention has the following comprehensive consideration: 0.21-0.28 wt%, preferably Co content is 0.21-0.26 wt%.
V: vanadium has a promoting effect on carbide-free bainite transformation, and can significantly refine grains in a hot rolling dynamic recrystallization process, but excessive vanadium can cause coarse VCN grains, lose the effect of refining grains and be harmful to the performance of steel. The invention V: 0.45 to 0.55 wt%, preferably the content of V is 0.51 to 0.55 wt%.
The invention controls the hot rolled wire rod to be heated to 770-870 ℃ at the heating speed of 15-20 ℃/s under the condition that the vacuum degree is not more than 100Pa or under the argon gas protective atmosphere, and keeps the temperature for 20-30 min, because the austenite grains of the wire rod are uniform and fine in the process, enough nucleation points are provided for the subsequent phase transformation of the non-carbide bainite steel, and the phase transformation rate and degree of the non-carbide bainite steel are improved.
The present invention controls the deformation rate of drawing to 7 to 10S-1Because the nucleation point of the carbide-free bainite structure can be improved under the rate deformation, and the transformation degree is provided; and drawing the wire rod from phi 14mm to phi 11.3mm at 650-770 ℃ to refine austenite grain size.
The cooling temperature of the wire rod is controlled to be 400-460 ℃, and the heat preservation is carried out for 30-45 min at the temperature, because of the sufficient heat preservation time and the proper heat preservation temperature, the phase change rate and the degree of the carbide-free bainite steel are improved.
The invention controls the drawing temperature of the wire rod from phi 11.3mm to phi 6.9mm to be 200-400 ℃ in order to accelerate the formation of carbide-free bainite structure and shorten the transformation time.
Compared with the prior art, the invention adopts the metallographic structure as carbide-free bainite on the bridge cable steel for the first time, and by adding Co element, the phase change process is accelerated, the formation of the carbide-free bainite structure is promoted, the self-repair of microcracks can be realized through the phase change of the microstructure, the wire rod with the diameter of 14mm is drawn into the steel wire with the diameter of 6.9mm, the strength can reach over 2200MPa after the galvanization and the stabilization treatment, and the requirement of twisting is met for more than 35 times.
Drawings
FIG. 1 is a diagram of a carbide-free bainite structure according to the present invention.
Detailed Description
The present invention is described in detail below:
table 1 is a list of values for each example and comparative example of the present invention;
table 2 is a table of the main process parameters of each example of the present invention and comparative example;
table 3 is a table of the performance test of each example and comparative example of the present invention.
The preparation method comprises the following steps:
1) heating the hot-rolled wire rod to 770-870 ℃ at the heating speed of 15-20 ℃/s under the condition that the vacuum degree is not more than 100Pa or under the argon gas protective atmosphere, and preserving heat for 20-30 min at the temperature;
2) drawing: the deformation rate in drawing is 7-10S-1Drawing the wire rod from phi 14mm to phi 11.3mm at 650-770 deg.c;
3) performing water cooling to the temperature of 400-460 ℃, and preserving heat for 30-45 min at the temperature;
4) air cooling and drawing the product with the temperature of phi 6.9mm at the conventional drawing speed, wherein the drawing temperature is 200-400 ℃.
TABLE 1 tabulated values (wt%) of the ingredients of the examples and comparative examples of the invention
TABLE 2 controlled Rolling and Cooling Process for examples of the invention and comparative examples
TABLE 3 test List of the Performance of inventive and comparative examples
The results in table 3 show that the strength of the bridge cable steel wire can reach 2200MPa or more, and simultaneously meets the requirement of twisting for 35 times or more, and compared with the prior art, the bridge cable steel wire has remarkable technical advantages; in addition, the microstructure of the steel is carbide-free bainite, and residual austenite serving as a soft phase in the microstructure can generate a TRIP effect to form martensite under the action of stress so as to reduce the generation of cracks, namely the microstructure can realize self-repair of microcracks through phase transformation, so that the safety of the bridge cable steel wire is improved while the ultrahigh strength of the steel wire is realized.
The present embodiments are merely preferred examples, and are not intended to limit the scope of the present invention.
Claims (1)
1. The method for producing the low-carbon cobalt-containing high-strength bridge cable steel comprises the following steps:
1) heating the hot-rolled wire rod to 770-870 ℃ at the heating speed of 15-20 ℃/s under the condition that the vacuum degree is not more than 100Pa or under the argon gas protective atmosphere, and preserving heat for 20-30 min at the temperature;
2) drawing: the deformation rate in drawing is 7-10S-1Drawing the wire rod from phi 14mm to phi 11.3mm at 650-770 deg.c;
3) performing water cooling to the temperature of 400-460 ℃, and preserving heat for 30-45 min at the temperature;
4) air cooling and drawing the product with the temperature of phi 6.9mm at the conventional drawing speed at the drawing temperature of 200-400 ℃;
the low-carbon cobalt-containing high-strength bridge cable steel comprises the following chemical components in percentage by weight: c: 0.10 to 0.14 wt%, Si: 1.00-1.15 wt%, Mn: 1.6-1.8 wt%, Al: 1.55-1.95 wt%, P is less than or equal to 0.01 wt%, S is less than or equal to 0.01 wt%, Co: 0.21 to 0.28wt%, V: 0.51-0.55 wt%, the balance being Fe and unavoidable impurities; the metallographic structure is carbide-free bainite; the strength is more than or equal to 2200MPa, and the twisting times are more than 35 times.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201910441764.7A CN110184537B (en) | 2019-05-24 | 2019-05-24 | Low-carbon cobalt-containing high-strength bridge cable steel and production method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201910441764.7A CN110184537B (en) | 2019-05-24 | 2019-05-24 | Low-carbon cobalt-containing high-strength bridge cable steel and production method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN110184537A CN110184537A (en) | 2019-08-30 |
| CN110184537B true CN110184537B (en) | 2020-10-30 |
Family
ID=67717744
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201910441764.7A Active CN110184537B (en) | 2019-05-24 | 2019-05-24 | Low-carbon cobalt-containing high-strength bridge cable steel and production method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN110184537B (en) |
Citations (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0218167A1 (en) * | 1985-09-30 | 1987-04-15 | Nippon Steel Corporation | High tensile strength drawn steel wire with improved ductility |
| CN1175980A (en) * | 1995-01-20 | 1998-03-11 | 英国钢铁公司 | Improvements in and relating to cartide-free bainitic steels and method of producing such steels |
| JPH10110216A (en) * | 1996-10-04 | 1998-04-28 | Nippon Steel Corp | High strength steel wire for acsr, reduced in iron loss in medium and low magnetic field |
| JP2000080443A (en) * | 1998-07-06 | 2000-03-21 | Sumitomo Metal Ind Ltd | High cleanliness steel |
| CN102936688A (en) * | 2012-11-21 | 2013-02-20 | 武汉钢铁(集团)公司 | Wire with tensile strength>=2000MPa for bridge cable and production method |
| CN104451408A (en) * | 2014-12-04 | 2015-03-25 | 北京科技大学 | Medium-carbon ultrahigh strength bainite steel and preparation method thereof |
| CN107354380A (en) * | 2017-08-30 | 2017-11-17 | 武汉钢铁有限公司 | A kind of tensile strength >=2300MPa bridge cables steel and production method |
| WO2018124157A1 (en) * | 2016-12-27 | 2018-07-05 | Ｊｆｅスチール株式会社 | High-strength galvanized steel sheet and method for manufacturing same |
| CN108603264A (en) * | 2016-01-29 | 2018-09-28 | 杰富意钢铁株式会社 | The manufacturing method of high strength galvanized steel plate, high-strength parts and high strength galvanized steel plate |
| WO2018203126A1 (en) * | 2017-05-05 | 2018-11-08 | Arcelormittal | A method for the manufacturing of liquid metal embrittlement resistant galvannealed steel sheet |
| CN109280853A (en) * | 2018-11-19 | 2019-01-29 | 潍坊科技学院 | A kind of high tough bridge cable zinc-coated wire and preparation method thereof |
| JP2019044217A (en) * | 2017-08-31 | 2019-03-22 | 新日鐵住金株式会社 | Hot rolled steel sheet, spline shaft bearing and manufacturing method therefor |
| CN109628837A (en) * | 2019-01-02 | 2019-04-16 | 北京科技大学 | A kind of ultra-fine bainite type bridge cable steel and preparation method thereof |
-
2019
- 2019-05-24 CN CN201910441764.7A patent/CN110184537B/en active Active
Patent Citations (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0218167A1 (en) * | 1985-09-30 | 1987-04-15 | Nippon Steel Corporation | High tensile strength drawn steel wire with improved ductility |
| CN1175980A (en) * | 1995-01-20 | 1998-03-11 | 英国钢铁公司 | Improvements in and relating to cartide-free bainitic steels and method of producing such steels |
| JPH10110216A (en) * | 1996-10-04 | 1998-04-28 | Nippon Steel Corp | High strength steel wire for acsr, reduced in iron loss in medium and low magnetic field |
| JP2000080443A (en) * | 1998-07-06 | 2000-03-21 | Sumitomo Metal Ind Ltd | High cleanliness steel |
| CN102936688A (en) * | 2012-11-21 | 2013-02-20 | 武汉钢铁(集团)公司 | Wire with tensile strength>=2000MPa for bridge cable and production method |
| CN104451408A (en) * | 2014-12-04 | 2015-03-25 | 北京科技大学 | Medium-carbon ultrahigh strength bainite steel and preparation method thereof |
| CN108603264A (en) * | 2016-01-29 | 2018-09-28 | 杰富意钢铁株式会社 | The manufacturing method of high strength galvanized steel plate, high-strength parts and high strength galvanized steel plate |
| WO2018124157A1 (en) * | 2016-12-27 | 2018-07-05 | Ｊｆｅスチール株式会社 | High-strength galvanized steel sheet and method for manufacturing same |
| WO2018203126A1 (en) * | 2017-05-05 | 2018-11-08 | Arcelormittal | A method for the manufacturing of liquid metal embrittlement resistant galvannealed steel sheet |
| CN107354380A (en) * | 2017-08-30 | 2017-11-17 | 武汉钢铁有限公司 | A kind of tensile strength >=2300MPa bridge cables steel and production method |
| JP2019044217A (en) * | 2017-08-31 | 2019-03-22 | 新日鐵住金株式会社 | Hot rolled steel sheet, spline shaft bearing and manufacturing method therefor |
| CN109280853A (en) * | 2018-11-19 | 2019-01-29 | 潍坊科技学院 | A kind of high tough bridge cable zinc-coated wire and preparation method thereof |
| CN109628837A (en) * | 2019-01-02 | 2019-04-16 | 北京科技大学 | A kind of ultra-fine bainite type bridge cable steel and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN110184537A (en) | 2019-08-30 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN108893675B (en) | Thick-specification hot-rolled H-shaped steel with yield strength of 500MPa and preparation method thereof | |
| CN105624564A (en) | High-carbon steel wire with good fine steel cord drawing machining performance and manufacturing method of high-carbon steel wire | |
| CN111455269A (en) | Yield strength 960MPa grade very high strength marine steel plate and manufacturing method thereof | |
| WO2020238851A1 (en) | Steel, wire rod and manufacturing method of wire rod | |
| CN111748739B (en) | Heat-resistant spring steel with tensile strength of more than 2100MPa and production method thereof | |
| CN105112782A (en) | Low-temperature ferrite LT-FH40 steel plate applied to hot-rolled ships and production method thereof | |
| CN115181916B (en) | 1280 MPa-level low-carbon low-alloy ultrahigh-strength hot dip galvanized dual-phase steel and rapid heat treatment hot dip galvanizing manufacturing method | |
| CA3180467A1 (en) | Ultrahigh-strength dual-phase steel and manufacturing method therefor | |
| CN108660377A (en) | The preparation method of seamless steel pipe and seamless steel pipe | |
| CN111910134B (en) | High-strength high-toughness spring steel used under high-temperature and high-pressure conditions and production method thereof | |
| CN110055392B (en) | High-toughness bridge cable steel with tensile strength of more than or equal to 2500Mpa and preparation method thereof | |
| CN111321354B (en) | X70M hot-rolled steel strip and manufacturing method thereof | |
| KR102298180B1 (en) | Method for producing flat steel products comprising manganese-containing flat steel and such flat steel products | |
| CN105102659A (en) | Steel sheet for nitriding and production method therefor | |
| CN113416902B (en) | Low-cost thermal-forming axle housing steel plate with yield strength of 460MPa and preparation method thereof | |
| JP2018528323A (en) | Hot-dip galvanized steel sheet excellent in aging resistance and bake hardenability, alloyed hot-dip galvanized steel sheet, and method for producing the same | |
| CN108866443B (en) | Normalizing type low-yield-ratio high-strength steel plate and preparation method thereof | |
| CN110184537B (en) | Low-carbon cobalt-containing high-strength bridge cable steel and production method thereof | |
| CN114107824B (en) | Corrosion-resistant low-temperature-resistant spring steel for railway fastener and production method and heat treatment method thereof | |
| US20240167138A1 (en) | Dual-phase steel and hot-dip galvanized dual-phase steel having tensile strength greater than or equal to 980mpa and method for manufacturing same by means of rapid heat treatment | |
| CN110129683B (en) | Manufacturing method of high-strength bridge cable steel | |
| CN110257699B (en) | Carbide-free bainite bridge cable steel and manufacturing method thereof | |
| CN115181894B (en) | 590 MPa-level high-formability hot dip galvanized dual phase steel and rapid heat treatment hot dip galvanizing manufacturing method | |
| CN111647803B (en) | Copper-containing high-strength steel and preparation method thereof | |
| CN110144521B (en) | High-strength and high-toughness bridge cable steel and preparation method thereof |
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 | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |