CN115584436A - Economical hydrogen conveying pipeline steel and production method thereof - Google Patents
Economical hydrogen conveying pipeline steel and production method thereof Download PDFInfo
- Publication number
- CN115584436A CN115584436A CN202211172545.1A CN202211172545A CN115584436A CN 115584436 A CN115584436 A CN 115584436A CN 202211172545 A CN202211172545 A CN 202211172545A CN 115584436 A CN115584436 A CN 115584436A
- Authority
- CN
- China
- Prior art keywords
- less
- equal
- percent
- controlling
- 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.)
- Granted
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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
-
- 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
- C22C38/04—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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
An economical hydrogen conveying pipeline steel comprises the following components in percentage by weight: c:0.03 to 0.08%, si: less than or equal to 0.15 percent, mn:0.53 to 1.19%, P: less than or equal to 0.012 percent, S: less than or equal to 0.0015 percent, ti: 0.010-0.080%, al:0.025 to 0.048%, N: less than or equal to 0.0045 percent, O: less than or equal to 0.002 percent, and the method comprises the following steps: after smelting, casting into a blank; heating a casting blank; rough rolling; fine rolling; cooling; and (4) coiling. The yield strength of the invention is 298-507 MPa, and heat treatment is not needed, thus shortening the production process and reducing the overall energy consumption.
Description
Technical Field
The invention relates to pipeline steel and a production method thereof, in particular to hydrogen conveying pipeline steel and a production method thereof.
Background
The hydrogen is taken as clean energy which is vigorously developed at present, the energy composition proportion is greatly improved in the future, and the total hydrogen energy consumption amount in China in 2050 is expected to reach 6000 million tons. However, as pipeline transportation is the most economical way for transporting hydrogen in long distance, the market for steel special for hydrogen transportation is in huge demand.
In order to solve the problem of long-distance safe hydrogen transportation, the material is required to have good hydrogen embrittlement resistance, and particularly, the material is required to have proper component design, good steel purity and segregation control level, low structure/residual stress and good performance uniformity in material design.
After retrieval:
the Chinese patent application No. 202111089004.8 discloses a production method of L360QS hydrogen transmission pipeline steel, and the chemical components of the steel comprise, by percentage, C = 0.07-0.10%, si = 0.20-0.30%, mn = 0.80-0.90%, P ≤ 0.008%, S ≤ 0.0015%, alt = 0.025-0.035%, nb = 0.010-0.020%, ti = 0.015-0.020%, cr = 0.10-0.15%, B ≤ 0.0005%, pcm = 0.16-0.19%, and the balance Fe and inevitable impurities. The normalizing L360QS steel produced according to the document has uniform and stable steel plate performance, and the same plate difference is within 40 MPa; yield strength: 380-420 MPa; tensile strength: 480 to 560MPa; elongation a50:45 to 70 percent; the yield ratio is less than or equal to 0.75; impact at-40 ℃ is 300-400J; -30 ℃ drop-weight shear area ratio: 85 to 100 percent. HIC resistance index under A solutionCLR, CTR and CSR are all 0, and under the experiment of the concentration of 10MPaH2, the reduction of area is more than 60 percent, and the elongation is more than 26 percent. But based on conventional anti-H 2 The design concept of the S corrosion steel adopts the design of low carbon, low manganese and low P, S components and the production by normalizing, quenching and tempering or quenching and tempering processes, so that the acid resistance requirement of low-steel-grade products is met, but the process cost is higher and the requirement of high-steel-grade products is not met.
The Chinese patent application No. 202210304498.5 discloses an L245S hydrogen transmission pipeline steel and a production method thereof, wherein the chemical component content of the steel is C =0.03% -0.05%, si =0.20% -0.28%, mn =0.70% -1.0%, P is less than or equal to 0.010%, S is less than or equal to 0.0015%, alt =0.020% -0.040%, nb =0.020% -0.030%, ca is less than or equal to 0.006%, B is less than or equal to 0.0005%, pcm =0.08% -0.12%, and the balance is Fe and inevitable impurities. The document adopts an online quenching and offline tempering process to produce the L245S, omits a reheating process of offline quenching, has low process cost, short production period, low alloy content of steel, uniform and stable steel plate performance, and has good HIC (hydrogen induced cracking), SSCC (sulfide stress cracking) and hydrogen embrittlement resistance: in a hydrogen environment with the pressure of 6MPa, the yield strength is 350-420 MPa, the tensile strength is 440-500 MPa, the reduction of area is more than 50 percent, and the elongation is more than 25 percent; under the impact test at the temperature of minus 20 ℃, the impact toughness is 300 to 400J; under a drop weight test at the temperature of minus 20 ℃, the drop weight shear area ratio is more than 88 percent. But it is also based on conventional anti-H 2 The design concept of the S corrosion steel adopts the design of low carbon, low manganese and low P, S components and the production by normalizing, quenching and tempering or quenching and tempering processes, so that the acid resistance requirement of low-grade steel products is met, the process cost is high, and the requirement of high-grade steel products is not met.
Disclosure of Invention
The invention provides an economical hydrogen conveying pipeline steel with yield strength of 298-507 MPa and without subsequent heat treatment and a production method thereof, aiming at the requirement of a high-pressure-resistant hydrogen conveying medium pipeline.
The measures for realizing the aim are as follows:
an economical hydrogen conveying pipeline steel comprises the following components in percentage by weight: c:0.03 to 0.08%, si: less than or equal to 0.15 percent, mn:0.53 to 1.19%, P: less than or equal to 0.012%, S: less than or equal to 0.0015 percent, ti: 0.010-0.080%, al:0.025 to 0.048%, N: less than or equal to 0.0045%, O: less than or equal to 0.002 percent, and the balance of Fe and inevitable impurities.
Preferably: the weight percentage content of Ti is 0.019-0.073%.
Preferably: the weight percentage content of S is less than or equal to 0.0012 percent.
Preferably: the weight percentage content of N is less than or equal to 0.0041 percent.
Further: adding: cr is less than or equal to 0.30 percent, mo is less than or equal to 0.20 percent, nb is less than or equal to 0.04 percent, or the composition of two or more of Cr and Mo is more than or equal to 0.20 percent.
The production method of the economical hydrogen conveying pipeline steel comprises the following steps:
1) Casting into a blank after smelting, and controlling to finish component fine adjustment in an LF refining stage;
2) Heating the casting blank, wherein: controlling the charging temperature of the surface of the casting blank to be not lower than 650 ℃, the average temperature of the casting blank to be not lower than 700 ℃, and controlling the phase transformation rate to be not higher than 8%; or after cutting, stacking, slowly cooling to below 500 ℃, and then charging, wherein the phase change rate is controlled to exceed 92%; the heating temperature is controlled to be 1200-1280 ℃. But preferably, high-temperature charging is adopted to reduce heating energy consumption.
3) Carrying out rough rolling, wherein the total reduction rate of the rough rolling is controlled to be not less than 80%, and the secondary reduction rate of the last two steps of the rough rolling is not less than 23%;
4) Carrying out finish rolling: controlling the total reduction rate of finish rolling to be 60-85%, and the reduction rates of the last two passes are less than or equal to 10%; controlling the finishing temperature to be 860-920 ℃;
5) Cooling to the coiling temperature at the cooling speed of 10-40 ℃/s;
6) Coiling is carried out, and the coiling temperature is controlled to be 550-700 ℃.
Further: the phase transformation ratio of the cast slab when the cast slab is charged into the furnace is preferably controlled not to exceed 5%.
The action and mechanism of each component and main process in the invention
C: mainly has the solid solution strengthening effect and improves the strength of the steel. However, C belongs to easily segregated elements, and easily causes the formation of pearlite bands or M/A bands; meanwhile, C belongs to a strong hardenability element, and when C is too high, the phase change of the structure in the plate thickness direction is easy to be uneven in the cooling control process; all of the above results lead to unfavorable hydrogen resistance. The C content is suitably 0.03 to 0.08%. When Ti is 0.04-0.08%, its consumption on C improves its segregation effect, and its content can be raised to 0.05-0.08%.
Si: in the invention, the catalyst mainly plays a role in solid solution strengthening and can assist in desulfurization. However, when the Si content is too high, tiger skin line defects are easily formed on the surface of the steel strip, and the difference of cooling efficiency of the surface of the steel strip caused by the tiger skin line defects can cause uneven phase change of the surface structure of the steel strip and unfavorable hydrogen resistance, so that the Si content is controlled to be less than or equal to 0.15 percent.
Mn: in the present invention, it mainly acts to solid solution strengthen and improve the hardenability of steel, but Mn is a strong segregation element, and its segregation easily causes a decrease in local transformation temperature and an increase in C segregation, so the Mn addition should be controlled as much as possible, so the Mn content is controlled to 0.53 to 1.19%.
Ti: in the invention, the Ti is a strong carbide element, and the precipitation of TiC can consume C in steel, so that the control of C segregation is facilitated; meanwhile, dispersed and precipitated particles of Ti are good hydrogen traps, and the hydrogen resistance can be improved. Preferably, the Ti content is 0.010-0.080%, preferably, the Ti content is 0.019-0.073% by weight.
Al: in the invention, the main deoxidizing element reduces the O content of the steel grade and plays a role in fixing N, but when the deoxidizing element is excessive, the size and the content of inclusions in the steel grade are increased easily, and the fluidity of molten steel is reduced. The proper addition amount is 0.025-0.048%.
P, S, N, O: in the invention, the elements are all limited elements, P is easy to be subjected to center segregation, S is easy to form strip-shaped inclusions with Mn, N is easy to be combined with Ti to form oversized TiN inclusions, and O is easy to increase the size and the number of the inclusions, which are not beneficial to the hydrogen resistance.
Cr, mo: if the Cr content is increased, the addition amount of Mn should be reduced; mo is suitable for addition with a low segregation degree, but the addition amount is not too high, so that the formation of a large amount of M/A hard phase structure is avoided.
Nb: generally, the Ti is precipitated together to play the roles of fine grain strengthening and precipitation strengthening.
The invention controls the charging temperature of the surface of the casting blank to be not lower than 650 ℃, the average temperature of the casting blank to be not lower than 700 ℃ and the phase change rate to be not more than 8 percent; controlling the heating temperature to be 1200-1280 ℃; because the phase change can occur in the cooling process after the plate blank is cut, the temperature gradient exists in the thickness direction of the plate blank, the phase change time and the proportion in the thickness direction of the plate blank are different, and the phase change process is accompanied with the nonuniformity of the structure; when the integral phase change proportion is controlled not to exceed 8 percent, the integral structure is relatively uniform, and the influence on the tissue heredity in the subsequent steel rolling and cooling control processes is small; when the transformation ratio is between 8 and 92 percent, the integral transformation and the nonuniformity of the structure are inherited to the subsequent rolling and cooling control processes, so that the final structure is nonuniform, and the hydrogen resistance is further influenced; when the transformation ratio exceeds 92%, the whole structure is basically completely transformed, and is relatively homogenized again, so that the structure is not seriously influenced in the subsequent steel rolling and cooling processes, and the energy consumption in the reheating process is increased.
The invention controls the total reduction rate of rough rolling to be not less than 80 percent, and the secondary reduction rate of the last two rough rolling to be not less than 23 percent, and utilizes the large deformation of the last two rough rolling to lead the structure to accumulate a large amount of deformation, fully generates static recrystallization on crystal grains in the subsequent transmission process of the intermediate billet, and leads the crystal grains to be homogenized, thereby being beneficial to the subsequent finish rolling and the homogenization of the controlled cooling structure.
The invention controls the total reduction rate of finish rolling to be 60-85%, and the reduction rates of the last two passes are all less than or equal to 10%; controlling the finishing temperature to be 860-920 ℃; the high finishing rolling temperature and the limitation of the last two rolling reduction rates are to avoid the phase change in the rolling process and the formation of local hard phase belts on the surface, thereby reducing the risk of hydrogen bulge.
The reason why the present invention cools to the coiling temperature at a cooling rate of 10-40 ℃/s is that an excessively high cooling rate causes unevenness in the sheet thickness structure performance, which is disadvantageous in hydrogen resistance, and also causes local hardening of the sheet surface, which increases the risk of hydrogen bubbling.
The coiling temperature is controlled to be 550-700 ℃ because the coiling is carried out at relatively high temperature, the steel coil generates self-ignition in the slow cooling process in the air, the structure phase change stress is further eliminated, and the hydrogen resistance is improved.
Compared with the prior art, the invention has the yield strength of 298-507 MPa, does not need heat treatment, shortens the production and manufacturing process and reduces the overall energy consumption.
Drawings
FIG. 1 is a metallographic structure diagram according to the invention.
Detailed Description
The present invention is described in detail below:
table 1 is a list of chemical compositions for each example of the present invention and comparative example;
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 listing the properties of each example of the invention and comparative example.
The examples of the invention were produced as follows
1) Casting into a blank after smelting, and controlling to finish component fine adjustment in an LF refining stage;
2) Heating the cast slab, wherein: controlling the charging temperature of the surface of the casting blank to be not lower than 650 ℃, the average temperature of the casting blank to be not lower than 700 ℃, and controlling the phase transformation rate to be not higher than 8%; controlling the heating temperature to be 1200-1280 ℃;
3) Carrying out rough rolling, wherein the total reduction rate of the rough rolling is controlled to be not less than 80%, and the secondary reduction rate of the last two steps of the rough rolling is not less than 23%;
4) Carrying out finish rolling: controlling the total reduction rate of finish rolling to be 60-85%, and the reduction rates of the last two passes are less than or equal to 10%; controlling the finishing temperature to be 860-920 ℃;
5) Cooling to the coiling temperature at the cooling speed of 10-40 ℃/s;
6) Coiling is carried out, and the coiling temperature is controlled to be 550-700 ℃.
TABLE 1 tabulated values (wt%) of the ingredients of the examples and comparative examples of the invention
Table 2 list of main process parameters of various embodiments of the present invention
TABLE 3 List of the properties of the inventive and comparative examples
As can be seen from Table 3, the designed product does not adopt an off-line heat treatment process with high energy consumption, and has good toughness and hydrogen resistance, and the elongation rate in a hydrogen environment reaches over 96 percent in a conventional environment.
The present embodiments are merely preferred examples, and are not intended to limit the scope of the present invention.
Claims (7)
1. The economical hydrogen conveying pipeline steel comprises the following components in percentage by weight:
c:0.03 to 0.08%, si: less than or equal to 0.15%, mn:0.53 to 1.19%, P: less than or equal to 0.012 percent, S: less than or equal to 0.0015 percent, ti: 0.010-0.080%, al:0.025 to 0.048%, N: less than or equal to 0.0045 percent, O: less than or equal to 0.002 percent, and the balance of Fe and inevitable impurities.
2. An economical steel for hydrogen transportation pipelines according to claim 1, characterized in that: the weight percentage content of Ti is 0.019-0.073%.
3. An economical steel for hydrogen transportation pipelines according to claim 1, characterized in that: the weight percentage content of S is less than or equal to 0.0012 percent.
4. An economical steel for hydrogen transportation pipelines according to claim 1, characterized in that: the weight percentage content of N is less than or equal to 0.0041 percent.
5. An economical steel for hydrogen transportation pipelines according to claim 1, characterized in that: adding: cr is less than or equal to 0.30 percent, mo is less than or equal to 0.20 percent, nb is less than or equal to 0.04 percent, or the composition of two or more of the Cr and the Mo is more than or equal to 0.04 percent.
6. The method for producing an economical steel for hydrogen transportation lines according to claim 1, characterized by comprising the steps of:
1) Casting into a blank after smelting, and controlling to finish component fine adjustment in an LF refining stage;
2) Heating the casting blank, wherein: controlling the charging temperature of the surface of the casting blank to be not lower than 650 ℃, the average temperature of the casting blank to be not lower than 700 ℃, controlling the phase transformation rate not to exceed 8%, or stacking and slowly cooling the casting blank to be below 500 ℃ after cutting, and then charging the casting blank, controlling the phase transformation rate to exceed 92%; controlling the heating temperature to be 1200-1280 ℃;
3) Carrying out rough rolling, wherein the total reduction rate of the rough rolling is controlled to be not less than 80%, and the secondary reduction rate of the last two steps of the rough rolling is not less than 23%;
4) Carrying out finish rolling: controlling the total reduction rate of finish rolling to be 60-85%, and the reduction rates of the last two passes are less than or equal to 10%; controlling the finishing temperature to be 860-920 ℃;
5) Cooling to the coiling temperature at the cooling speed of 10-40 ℃/s;
6) Coiling is carried out, and the coiling temperature is controlled to be 550-700 ℃.
7. The method for producing an economical steel for hydrogen transportation pipelines according to claim 7, wherein: controlling the phase transformation rate of the casting blank when the casting blank is fed into the furnace not to exceed 5 percent.
Priority Applications (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202211172545.1A CN115584436B (en) | 2022-09-26 | 2022-09-26 | Economical hydrogen conveying pipeline steel and production method thereof |
| PCT/CN2023/117276 WO2024066987A1 (en) | 2022-09-26 | 2023-09-06 | Economical hydrogen gas conveying pipeline steel, and production method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202211172545.1A CN115584436B (en) | 2022-09-26 | 2022-09-26 | Economical hydrogen conveying pipeline steel and production method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN115584436A true CN115584436A (en) | 2023-01-10 |
| CN115584436B CN115584436B (en) | 2023-06-23 |
Family
ID=84772808
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202211172545.1A Active CN115584436B (en) | 2022-09-26 | 2022-09-26 | Economical hydrogen conveying pipeline steel and production method thereof |
Country Status (2)
| Country | Link |
|---|---|
| CN (1) | CN115584436B (en) |
| WO (1) | WO2024066987A1 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN117444552A (en) * | 2023-12-25 | 2024-01-26 | 中北大学 | Method for improving hydrogen embrittlement resistance of 316L stainless steel hydrogen conveying pipe |
| WO2024066987A1 (en) * | 2022-09-26 | 2024-04-04 | 武汉钢铁有限公司 | Economical hydrogen gas conveying pipeline steel, and production method |
Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH09287027A (en) * | 1996-04-19 | 1997-11-04 | Sumitomo Metal Ind Ltd | Production of high strength, high toughness and seamless steel pipe |
| WO2013044640A1 (en) * | 2011-09-26 | 2013-04-04 | 宝山钢铁股份有限公司 | Steel plate with low yield ratio high toughness and manufacturing method thereof |
| CN106811700A (en) * | 2015-12-02 | 2017-06-09 | 鞍钢股份有限公司 | A kind of think gauge acid-resisting X60MS hot-rolled coils and its manufacture method |
| CN107190203A (en) * | 2017-05-31 | 2017-09-22 | 武汉钢铁有限公司 | With the yield strength >=800MPa SPHCs and production method of sheet billet Direct Rolling |
| CN107988547A (en) * | 2016-10-27 | 2018-05-04 | 鞍钢股份有限公司 | A kind of effective X52MS hot-rolled coils of high-frequency resistance welding (HFRW) and its manufacture method |
| CN108018488A (en) * | 2017-12-13 | 2018-05-11 | 武汉钢铁有限公司 | A kind of CT110 grades of connecting pipes hot rolled strip and production method |
| CN114107807A (en) * | 2021-11-03 | 2022-03-01 | 邯郸钢铁集团有限责任公司 | Low-cost light steel 650DB for suspension arm of truck-mounted crane and production method thereof |
| WO2022148492A1 (en) * | 2021-01-05 | 2022-07-14 | 江阴兴澄特种钢铁有限公司 | Steel for cold forging universal joint fork of passenger vehicle, and manufacturing method therefor |
Family Cites Families (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP4585483B2 (en) * | 2006-05-11 | 2010-11-24 | 新日本製鐵株式会社 | High strength steel pipe with excellent weld toughness and deformability and method for producing high strength steel plate |
| CN109457179B (en) * | 2018-11-19 | 2020-12-29 | 包头钢铁（集团）有限责任公司 | Hot-rolled steel strip for hydrogen sulfide corrosion resistant welded pipe and manufacturing method thereof |
| CN109402510A (en) * | 2018-11-19 | 2019-03-01 | 包头钢铁（集团）有限责任公司 | A kind of resistance to anti-H that extremely trembles with fear2S corrodes welded tube hot rolled strip and its manufacturing method |
| CN109402511B (en) * | 2018-11-19 | 2020-12-29 | 包头钢铁（集团）有限责任公司 | Hot-rolled steel strip for hydrogen sulfide corrosion resistant welded pipe and manufacturing method thereof |
| CN112226676B (en) * | 2020-09-03 | 2021-12-21 | 包头钢铁（集团）有限责任公司 | Low-cost L320MS/X46MS hot-rolled steel strip for hydrogen sulfide corrosion resistant welded pipe and manufacturing method thereof |
| CN113832399B (en) * | 2021-09-23 | 2022-10-11 | 马鞍山钢铁股份有限公司 | Economical pipeline steel resistant to hydrogen sulfide corrosion and production method thereof |
| CN114959468B (en) * | 2022-05-18 | 2023-05-26 | 包头钢铁（集团）有限责任公司 | Nickel-free L360MSX52MS H-resistant thick-specification extreme cold-resistant 2 S-corrosion hot-rolled coil and preparation method thereof |
| CN115584436B (en) * | 2022-09-26 | 2023-06-23 | 武汉钢铁有限公司 | Economical hydrogen conveying pipeline steel and production method thereof |
-
2022
- 2022-09-26 CN CN202211172545.1A patent/CN115584436B/en active Active
-
2023
- 2023-09-06 WO PCT/CN2023/117276 patent/WO2024066987A1/en unknown
Patent Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH09287027A (en) * | 1996-04-19 | 1997-11-04 | Sumitomo Metal Ind Ltd | Production of high strength, high toughness and seamless steel pipe |
| WO2013044640A1 (en) * | 2011-09-26 | 2013-04-04 | 宝山钢铁股份有限公司 | Steel plate with low yield ratio high toughness and manufacturing method thereof |
| CN106811700A (en) * | 2015-12-02 | 2017-06-09 | 鞍钢股份有限公司 | A kind of think gauge acid-resisting X60MS hot-rolled coils and its manufacture method |
| CN107988547A (en) * | 2016-10-27 | 2018-05-04 | 鞍钢股份有限公司 | A kind of effective X52MS hot-rolled coils of high-frequency resistance welding (HFRW) and its manufacture method |
| CN107190203A (en) * | 2017-05-31 | 2017-09-22 | 武汉钢铁有限公司 | With the yield strength >=800MPa SPHCs and production method of sheet billet Direct Rolling |
| CN108018488A (en) * | 2017-12-13 | 2018-05-11 | 武汉钢铁有限公司 | A kind of CT110 grades of connecting pipes hot rolled strip and production method |
| WO2022148492A1 (en) * | 2021-01-05 | 2022-07-14 | 江阴兴澄特种钢铁有限公司 | Steel for cold forging universal joint fork of passenger vehicle, and manufacturing method therefor |
| CN114107807A (en) * | 2021-11-03 | 2022-03-01 | 邯郸钢铁集团有限责任公司 | Low-cost light steel 650DB for suspension arm of truck-mounted crane and production method thereof |
Non-Patent Citations (1)
| Title |
|---|
| 张岩 等: "炼钢生产知识", 冶金工业出版社, pages: 178 - 179 * |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2024066987A1 (en) * | 2022-09-26 | 2024-04-04 | 武汉钢铁有限公司 | Economical hydrogen gas conveying pipeline steel, and production method |
| CN117444552A (en) * | 2023-12-25 | 2024-01-26 | 中北大学 | Method for improving hydrogen embrittlement resistance of 316L stainless steel hydrogen conveying pipe |
| CN117444552B (en) * | 2023-12-25 | 2024-03-12 | 中北大学 | Method for improving hydrogen embrittlement resistance of 316L stainless steel hydrogen conveying pipe |
Also Published As
| Publication number | Publication date |
|---|---|
| WO2024066987A1 (en) | 2024-04-04 |
| CN115584436B (en) | 2023-06-23 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN110079740B (en) | High-toughness hot-rolled 530 MPa-grade automobile cold-stamped axle housing steel plate and manufacturing method thereof | |
| CN111378896B (en) | High-strength weather-resistant steel plate for building bridge and manufacturing method thereof | |
| CN115584436B (en) | Economical hydrogen conveying pipeline steel and production method thereof | |
| CN108929986B (en) | High-strength wear-resistant hot rolled steel plate for automobile braking and production process thereof | |
| CN111455269A (en) | Yield strength 960MPa grade very high strength marine steel plate and manufacturing method thereof | |
| CN110863135B (en) | High-nickel steel for low-temperature container and manufacturing method thereof | |
| CN112226673A (en) | Hot rolled steel plate with 650 MPa-grade tensile strength and manufacturing method thereof | |
| CN114934231B (en) | High-manganese low-magnetism high-strength austenitic steel and manufacturing method thereof | |
| CN112251670A (en) | 690 MPa-grade steel plate with good extensibility and manufacturing method thereof | |
| CN114686762B (en) | Production method of high-strength high-toughness hot continuous rolling thin steel plate with Brinell hardness of 500HBW | |
| CN113737108A (en) | Delay cracking resistant electro-galvanized super-strong dual-phase steel and manufacturing method thereof | |
| CN115261746B (en) | Super-thick Q420qE bridge steel plate and production method thereof | |
| CN114990432B (en) | Hot rolled strip steel with tensile strength not lower than 1500MPa produced by TSR production line and method | |
| CN115572901A (en) | 630 MPa-grade high-hardening-tempering-stability low-carbon low-alloy steel plate and manufacturing method thereof | |
| CN115161440A (en) | Hot-rolled heavy H-shaped steel with yield strength of 560MPa and production method thereof | |
| CN115491593A (en) | Hot-rolled thin strip steel with tensile strength of more than or equal to 1800MPa produced by TSR production line and method | |
| CN114959504A (en) | Acid-washing-free cord steel wire rod and production method thereof | |
| CN114480960A (en) | Low-yield-ratio low-temperature-toughness 800 MPa-grade high-strength steel and production process thereof | |
| CN114000068A (en) | Low-nitrogen ultrahigh-strength hot-rolled steel strip with thickness of 4-10mm and production method thereof | |
| CN115369307B (en) | Manufacturing method for producing hot-rolled 510L automobile girder steel based on CSP flow | |
| CN115852266B (en) | Production method for improving low-temperature impact toughness and high-temperature performance of ultra-thick hydrogen-bonded steel plate | |
| CN114836683B (en) | High-strength high-toughness low-yield-ratio pipeline steel plate suitable for wet hydrogen sulfide environment and manufacturing method thereof | |
| CN117210758B (en) | Steel for battery shell and preparation method thereof | |
| CN116837274A (en) | High reaming hot rolled steel sheet of economic tensile strength 750MPa | |
| CN116607078A (en) | S355-grade large-strain aging wind power steel and manufacturing 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 |