CN112058910A - Production method for improving rolling stability of thick pipeline steel - Google Patents
Production method for improving rolling stability of thick pipeline steel Download PDFInfo
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- CN112058910A CN112058910A CN202010901118.7A CN202010901118A CN112058910A CN 112058910 A CN112058910 A CN 112058910A CN 202010901118 A CN202010901118 A CN 202010901118A CN 112058910 A CN112058910 A CN 112058910A
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
- B21B1/24—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process
- B21B1/26—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process by hot-rolling, e.g. Steckel hot mill
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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Abstract
The invention discloses a production method for improving rolling stability of thick pipeline steel, which comprises the steps of heating a plate blank, rough rolling, finish rolling, cooling after rolling and coiling, wherein in the step of heating the plate blank, the furnace time is 170-230min, and the heating temperature is 1190-1250 ℃; in the rough rolling step, the rough rolling biting temperature is 1070-; in the finish rolling step, the finish rolling inlet temperature is controlled at 960-1000 ℃, the finish rolling is performed by seven-stand hot continuous rolling dummy F2 and F5, and the accumulated reduction is more than or equal to 60 percent; the finishing temperature is 810 ℃ and 850 ℃; the acceleration is given to be 0.003-0.008m/s2 after threading; the post-rolling cooling is laminar cooling, a front-section cooling mode is selected, the cooling speed is 15-30 ℃/s, and the final cooling temperature is controlled at 500-550 ℃. Compared with the prior art, the rolling stability of the thick pipeline steel of the conventional hot continuous rolling production line can be obviously improved.
Description
Technical Field
The invention belongs to the technical field of pipeline steel preparation methods, and particularly relates to a rolling control method for thick-specification pipeline steel suitable for a conventional hot continuous rolling production line.
Background
The petroleum pipeline steel is mainly used for pipelines for transporting petroleum and natural gas, particularly the natural gas pipeline has high operating pressure and requires higher toughness. The pipeline construction is developing towards the direction of large wall thickness and high strength and toughness, so that the pipeline conveying pressure can be improved, and the natural gas conveying efficiency is greatly improved. However, as the thickness of the steel sheet increases, the difficulty of production thereof sharply increases.
The thick-specification pipeline steel (15-25mm) process requires low finish rolling temperature (810-:
firstly, the speed of strip steel is often lower (1.4-2.0m/s) at low finishing temperature, and when the speed of strip steel of a coiler is lower than 1.8m/s, the coiler is easy to slip, so that scrap steel is coiled;
secondly, when the coiling target temperature is lower than 550 ℃, the temperature fluctuation is large, and the temperature hit rate is low;
and thirdly, the large fluctuation of the coiling temperature easily causes the deformation of the strip steel in the laminar cooling process, and causes production accidents such as guard plate collision and the like.
Therefore, how to design a pipeline steel rolling method which can realize the uniformity of the structure and the performance of the thick pipeline steel, is suitable for the conventional hot continuous rolling production line, has simple operation, high effectiveness and strong stability, and becomes the important factor in the development of the thick pipeline steel.
Disclosure of Invention
The technical task of the invention is to provide a production method for improving rolling stability of thick pipeline steel aiming at the defects of the prior art, and solve the technical problems of mismatching, large speed variable, large temperature fluctuation and unstable performance of the prior production process.
The technical scheme for solving the technical problem is as follows: a production method for improving rolling stability of thick pipeline steel comprises the steps of slab heating, rough rolling, finish rolling, cooling after rolling and coiling, and is characterized in that: wherein, in the step of heating the plate blank, the furnace time is 170-230min, and the heating temperature is 1190-1250 ℃; in the rough rolling step, the rough rolling biting temperature is 1070-; in the finish rolling step, the finish rolling inlet temperature is controlled at 960-1000 ℃, the finish rolling is performed by seven-stand hot continuous rolling dummy F2 and F5, and the accumulated reduction is more than or equal to 60 percent; the finishing temperature is 810 ℃ and 850 ℃; the acceleration is given to be 0.003-0.008m/s2 after threading; the post-rolling cooling is laminar cooling, a front-section cooling mode is selected, the cooling speed is 15-30 ℃/s, and the final cooling temperature is controlled at 500-550 ℃.
In the slab heating step, the temperature difference of the surface of the strip steel is less than or equal to 30 ℃, and the heating time is more than or equal to 190 min.
And (3) descaling by high-pressure water before rough rolling.
And (3) descaling by high-pressure water before finish rolling.
Compared with the prior art, the invention has the following outstanding beneficial effects:
1. the invention is suitable for the conventional hot continuous rolling production line, does not need technical transformation of the laminar cooling equipment, and has simple process and strong operability;
2. finish rolling is cancelled, a finish rolling temperature control closed loop is controlled, a constant acceleration rolling control model is adopted, appropriate acceleration is given, the uniform change of the rolling speed after threading is beneficial to the calculation of the layer cooling temperature, the opening frequency of a layer cooling water valve in the rolling process is greatly reduced, the cooling temperature stability is increased, the coiling temperature hit rate is improved, and the coiling temperature control Cpk is improved from 0.75 to 1.25;
3. the pipeline steel with the thickness of more than or equal to 15mm is stably produced, the product structure and the performance are uniform, the difference between the yield strength and the plate performance is reduced from more than 50MPa to within 30MPa, and the detection uniformity of the Charpy impact energy and the drop hammer shearing area is obviously improved, so that the material is ensured to have excellent comprehensive mechanical properties;
4. the difference of the structure and the performance of the pipeline steel is reduced, the rolling stability of the thick pipeline steel is obviously improved, the coiling qualification rate is improved to 99.8 percent, the quality of the material object is improved, and the market competitiveness of the pipeline steel is improved.
Detailed Description
The present invention will be further described with reference to the following embodiments.
The method comprises the following specific steps: heating a plate blank → rough rolling → finish rolling → cooling after rolling → coiling.
1. Heating the plate blank:
the continuous casting billet comprises the following components in percentage by weight: 0.07-0.08% of C, 0.20% of Si, 1.39-1.42% of Mn, Nb: 0.042-0.048%, Ti: 0.021-0.023 percent, and the balance of Fe and inevitable impurities.
The components are characterized by a Mn-Nb-Ti system, no Cr and low Nb configuration, replace noble metal alloys such as Cu, Ni, Mo, V and the like, can meet the requirements of higher strength and toughness of pipeline steel, and simultaneously reduce the production cost.
Heating the continuous casting slab with the thickness of 210-230mm for 230min at the temperature of 1190-1250 ℃ for 170-230min, ensuring that alloy elements are fully dissolved and effectively refining the grain size of the original structure. The temperature difference of the surface of the strip steel is less than or equal to 30 ℃, and the heating time is more than or equal to 190 min.
2. Rough rolling:
high-pressure water descaling before rough rolling, and descaling among rough rolling passes, so that the surface quality of the plate blank is ensured, and the temperature of the intermediate plate blank can be controlled.
Rolling in a recrystallization zone, and the rough rolling bite temperature 1070-.
The slab rough rolling adopts 5 passes, and the accumulated reduction rate is 60-80%, so that austenite recrystallization and austenite grain refinement are ensured. The specific reduction rate of each pass is 24%, 26%, 25% and 26%.
The thickness of the rough rolled blank (intermediate billet) is 48-55mm, when the thickness of the finished product is increased, the thickness of the intermediate billet is increased, the deformation of a non-recrystallization area in the finish rolling process can be increased, and ferrite grains are refined.
The final pass speed of the rough rolling is 4.0-4.3m/s, and the final rolling temperature of the rough rolling is controlled at 1000-.
3. Finish rolling:
the inlet temperature of the finish rolling is controlled to be 960-1000 ℃, and the surface of the steel is descaled by high-pressure water, and the start temperature of the finish rolling is close to the critical recrystallization temperature.
The finish rolling is seven-stand hot continuous rolling (F1-F7), namely F2 and F5, and the pass deformation of the finish rolling is increased, so that the accumulated deformation of a non-recrystallization area is increased. The accumulated rolling reduction is more than or equal to 60 percent, austenite becomes flat after deformation, and deformation bands and dislocation are formed in the crystal grains, so that the effective nucleation area of the ferrite crystal grains is increased, and the ferrite crystal grains are refined. Specifically, the reduction rate of each pass is 31%, 0%, 34%, 24%, 0%, 16% and 8%.
The finishing rolling temperature is 810-.
The constant acceleration control model developed automatically is adopted, the closed loop of the finish rolling temperature control is cancelled, and the acceleration is given to 0.003-0.008m/s after the strip is threaded2And the speed stability of the strip steel in the layer cooling process is ensured. The cooling stability in the process of laminar cooling is ensured by adjusting the speed of the strip steel, and the performance difference of the same plate is reduced.
4. Cooling after rolling:
after the finish rolling process is finished, laminar cooling is started, a front-section cooling mode is selected, the cooling speed is 15-30 ℃/s, and the final cooling temperature is controlled at 500-.
The rolling process adopts a constant acceleration mode, the uniform change of the rolling speed is beneficial to the calculation of the layer cooling temperature, the opening frequency of a layer cooling water valve in the rolling process is greatly reduced, the cooling temperature stability is increased, and the coiling temperature Cpk can be increased to 1.25. The difference between the yield strength of the cooled steel plate and the performance of the cooled steel plate is reduced to be within 30MPa, and the qualification rate of the Charpy impact shearing area and the DWTT shearing area is obviously improved. The X60 and X65 grades are mixed type tissues which mainly comprise polygonal ferrite and pearlite, and the X70 grade is mixed type tissues which mainly comprise acicular ferrite and contain a small amount of pearlite and a small amount of polygonal ferrite, wherein the proportion of the polygonal ferrite is less than or equal to 25 percent. The structure and the performance are uniform, thereby ensuring that the material has excellent comprehensive mechanical properties.
5. Coiling:
because the pass deformation of finish rolling is increased, and the rolling speed system adopts a constant acceleration mode, the laminar cooling stability is high, and the mechanical uniformity is good, the coiling of the steel plate is easy to operate, and the appearance is excellent.
To better compare the technology of the present application with the prior art, comparative tests were carried out, the specific methods and parameters of the examples and comparative examples being as follows:
example 1:
1. 15.9mm X65M pipeline steel, the thickness of the plate blank is 227mm, the reheating temperature of the plate blank is controlled at 1190 ℃, the surface temperature difference of the strip steel is less than or equal to 30 ℃, and the heating time is 210 min. The continuous casting billet comprises the following components in percentage by weight: 0.07% of C, 0.20% of Si, 1.42% of Mn, Nb: 0.048%, Ti: 0.023 percent, and the balance of Fe and inevitable impurities.
2. The initial rolling temperature of rough rolling is 1070 ℃, 5-pass rolling is adopted, the reduction rate of each pass is 24%, 26%, 25%, 26%, the thickness of the intermediate billet is 52mm, the descaling and the full opening are realized, the final rolling temperature of rough rolling is controlled to be 1000 ℃, and the rolling speed is 4.0-4.2 m/s.
3. The initial rolling temperature of finish rolling is 960 ℃, the finish rolling is seven-stand hot continuous rolling, the rolling reduction rates of the respective passes are 31%, 0%, 34%, 24%, 0%, 16% and 8%, and the final rolling temperature is set to be 810 ℃. The closed loop of the final rolling temperature control is cancelled, a constant acceleration speed control model is adopted, the water between the frames is fully opened, the rolling speed range is 1.8-2.2m/s, the constant acceleration is given to be 0.006m/s2。
4. Laminar cooling, the front-stage cooling mode was selected, and the coiling temperature was 550 ℃.
Through detection, the finishing rolling temperature Cpk of the X65M pipeline steel produced by the embodiment is controlled to be 1.20, the coiling temperature Cpk is controlled to be 1.25, and the temperature is stably controlled at a higher level; mechanical properties Rt 0.5: 508/525/532MPa, Rm: 612/616/625MPa, the performance of the steel plate is less than or equal to 30MPa with the plate difference; the Charpy impact power value at 20 ℃ below zero is 167/175/198J, and the drop hammer shear area at 10 ℃ below zero is 100 percent; the structure is mainly polygonal ferrite and pearlite, and the grain size is 12.5-13.0 grade.
Example 2:
1. 19.1mm X60M pipeline steel, the thickness of the plate blank is 227mm, the reheating temperature of the plate blank is controlled at 1250 ℃, the surface temperature difference of the strip steel is less than or equal to 30 ℃, and the heating time is 190 min. The continuous casting billet comprises the following components in percentage by weight: 0.08% of C, 0.20% of Si, 1.39% of Mn, Nb: 0.042%, Ti: 0.021%, and the balance Fe and inevitable impurities.
2. The initial rolling temperature of rough rolling is 1110 ℃, 5-pass rolling is adopted, the reduction rate of each pass is 23%, 24%, 25%, 24% and 25%, the thickness of the intermediate billet is 55mm, the descaling and the full opening are realized, the final rolling temperature of the rough rolling is controlled to be 1040 ℃, and the rolling speed is 4.0-4.2 m/s.
3. The initial rolling temperature of finish rolling is 1000 ℃, the finish rolling is seven-stand hot continuous rolling, the rolling reduction rates of the passes are 27%, 0%, 25%, 20%, 0%, 15% and 9%, and the final rolling temperature is set to be 830 ℃. The closed loop of the final rolling temperature control is cancelled, a constant acceleration speed control model is adopted, the water between the frames is fully opened, the rolling speed range is 1.6-2.0m/s, and the acceleration is given to be 0.005m/s after threading2。
4. Laminar cooling, the front section cooling mode was selected, and the coiling temperature was 500 ℃.
When the X60M pipeline steel produced in the embodiment 2 of the invention is used, the final rolling temperature control Cpk is 1.15, the coiling temperature control Cpk is 1.18, and the temperature is stably controlled at a higher level; mechanical properties Rt 0.5: 485/507/505MPa, Rm: 588/604/600MPa, the performance of the steel plate is less than or equal to 30MPa with the plate difference; -20 ℃ charpy impact value 148/167/150J, -10 ℃ drop shear area 95/100/100%; the structure is mainly polygonal ferrite and pearlite, and the grain size is 12.0-13.0 grade.
Comparative example 1:
1. 15.9mm X65M pipeline steel, the slab thickness is 227mm, the slab reheating temperature is 1215 ℃, the strip steel surface temperature difference is less than or equal to 30 ℃, and the heating time is 190 min. The continuous casting billet comprises the following components in percentage by weight: 0.07% of C, 0.20% of Si, 1.42% of Mn, Nb: 0.048%, Ti: 0.023 percent, and the balance of Fe and inevitable impurities.
2. The initial rolling temperature of rough rolling is 1087 ℃, 5-pass rolling is adopted, the reduction rate of each pass is 24%, 26%, 25%, 26% and 25%, the thickness of the intermediate billet is 52mm, the descaling and the full rolling are performed, the final rolling temperature of the rough rolling is controlled to 1032 ℃, and the rolling speed is 4.1-4.3 m/s.
3. The initial rolling temperature of finish rolling is 992 ℃, the finish rolling is seven-stand hot continuous rolling, namely F2 and F5, the reduction rate of each pass is 32%, 0%, 33%, 24%, 0%, 15% and 8%, and the final rolling temperature is set to be 840 ℃. And a closed-loop speed control model for controlling the finish rolling temperature is adopted, the water between the racks is fully opened, and the rolling speed range is 1.8-2.4 m/s.
4. Laminar cooling, the front-stage cooling mode was selected, and the coiling temperature was 550 ℃.
Through detection, the finishing rolling temperature control Cpk of the X65M pipeline steel produced in the comparative example 1 is 1.18, the coiling temperature control Cpk is only 0.88, and the coiling temperature fluctuation is large; mechanical properties Rt 0.5: 482/535/500MPa, Rm: 603/618/612MPa, and the difference between the yield strength and the plate is more than 50 MPa; -20 ℃ charpy impact value 125/195/180J, -10 ℃ drop shear area 75/100/95%; the structure is mainly polygonal ferrite and pearlite, and the grain size is 11.5-13.0 grade.
Comparative example 2:
1. 19.1mm X60M pipeline steel, the thickness of the plate blank is 227mm, the reheating temperature of the plate blank is 1230 ℃, the surface temperature difference of the strip steel is less than or equal to 30 ℃, and the heating time is more than or equal to 190 min. The continuous casting billet comprises the following components in percentage by weight: 0.08% of C, 0.20% of Si, 1.39% of Mn, Nb: 0.042%, Ti: 0.021%, and the balance Fe and inevitable impurities.
2. The initial rolling temperature of rough rolling is 1082 ℃, 5-pass rolling is adopted, the reduction rate of each pass is 16%, 23%, 24%, 28% and 28%, the thickness of the intermediate billet is 55mm, the rolling is descaled and fully opened, and the rolling speed is 4.0-4.1 m/s.
3. The finish rolling is carried out at a nip temperature of 1070 ℃, the finish rolling is carried out by seven-stand hot continuous rolling, namely F6, the reduction rate of each pass is 23%, 24%, 18%, 12%, 10%, 0% and 7%, and the finish rolling temperature is set to be 810 ℃. The constant acceleration control is adopted, and the constant acceleration is given to be 0.005m/s2. Water container between framesThe rolling speed is in the range of 1.6-2.1 m/s.
4. Laminar cooling, the front section cooling mode is selected, the cooling speed is 15 ℃/s, and the coiling temperature is set to 520 ℃.
Through detection, the finishing rolling temperature control Cpk of the X60M pipeline steel produced in the comparative example 2 is 1.16, the coiling temperature control Cpk is only 0.75, and the coiling temperature fluctuation is large; mechanical properties Rt 0.5: 485/455/512MPa, Rm: 596/585/602/MPa, the difference between the yield strength and the plate is more than 50 MPa; -20 ℃ charpy impact value 155/136/170J, -10 ℃ drop shear area 90/65/100%; the structure is mainly polygonal ferrite plus pearlite, and the grain size is 11.0-12.5 grade.
The examples and comparative examples are compared in process control values as shown in the following table:
the properties of the steel coils of the examples and comparative examples are compared in the following table:
the results show that the rolling stability of the thick pipeline steel can be obviously improved by using the process, the coiling temperature Cpk is improved to 1.25 from 0.75, and meanwhile, the finishing temperature still keeps a higher control level; the difference between the yield strength and the plate performance is reduced to be within 30MPa from more than 50MPa, and the detection uniformity of the Charpy impact energy and the drop hammer shear area is obviously improved, so that the excellent comprehensive mechanical property of the material is ensured. And the comparative example 1 under the same chemical composition design adopts a finish rolling temperature control closed-loop speed control model, and the comparative example 2 adopts constant acceleration control, but due to different rolling reduction control designs, stable coiling temperature can not be realized after subsequent relatively slow cooling, so that the performance difference of the yield strength and the plate is still more than 50MPa, and the quality is unstable.
It should be noted that while the invention has been described in detail with respect to specific embodiments thereof, it will be apparent to those skilled in the art that various obvious changes can be made therein without departing from the spirit and scope of the invention.
Claims (4)
1. A production method for improving rolling stability of thick pipeline steel comprises the steps of slab heating, rough rolling, finish rolling, cooling after rolling and coiling, and is characterized in that: wherein, in the step of heating the plate blank, the furnace time is 170-230min, and the heating temperature is 1190-1250 ℃; in the rough rolling step, the rough rolling biting temperature is 1070-; in the finish rolling step, the finish rolling inlet temperature is controlled at 960-1000 ℃, the finish rolling is performed by seven-stand hot continuous rolling dummy F2 and F5, and the accumulated reduction is more than or equal to 60 percent; the finishing temperature is 810 ℃ and 850 ℃; the acceleration is given to be 0.003-0.008m/s2 after threading; the post-rolling cooling is laminar cooling, a front-section cooling mode is selected, the cooling speed is 15-30 ℃/s, and the final cooling temperature is controlled at 500-550 ℃.
2. The production method for improving rolling stability of thick gauge pipeline steel according to claim 1, wherein: in the slab heating step, the temperature difference of the surface of the strip steel is less than or equal to 30 ℃, and the heating time is more than or equal to 190 min.
3. The production method for improving rolling stability of thick gauge pipeline steel according to claim 1, wherein: and descaling by high-pressure water before rough rolling.
4. The production method for improving rolling stability of thick gauge pipeline steel according to claim 1, wherein: and removing scale by high-pressure water before finish rolling.
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN113857264A (en) * | 2021-09-27 | 2021-12-31 | 日照宝华新材料有限公司 | SPA-H hot-rolled coil shape control method |
| CN115889455A (en) * | 2022-10-28 | 2023-04-04 | 江苏沙钢集团有限公司 | Efficient rolling method for thin-specification pipeline steel |
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| CN105132807A (en) * | 2015-10-10 | 2015-12-09 | 武汉钢铁(集团)公司 | Pipeline steel excellent in acid corrosion resistance on seabed and production method |
| CN107177784A (en) * | 2016-03-11 | 2017-09-19 | 内蒙古包钢钢联股份有限公司 | The milling method of 22mm think gauge X80 heavy-caliber pipeline steel |
| CN105734236A (en) * | 2016-03-16 | 2016-07-06 | 攀钢集团攀枝花钢铁研究院有限公司 | Method for improving falling performance of thick-gauge pipeline steel |
| CN106048181A (en) * | 2016-07-27 | 2016-10-26 | 武汉钢铁股份有限公司 | Low-temperature thick-specification pipeline steel preparing method suitable for hot continuous rolling production line |
| CN106119715A (en) * | 2016-09-05 | 2016-11-16 | 攀钢集团攀枝花钢铁研究院有限公司 | Think gauge X60 pipe line steel and production method thereof |
| CN106244925A (en) * | 2016-09-05 | 2016-12-21 | 攀钢集团攀枝花钢铁研究院有限公司 | Think gauge X42 pipe line steel and production method thereof |
| CN110656228A (en) * | 2019-10-31 | 2020-01-07 | 攀钢集团攀枝花钢铁研究院有限公司 | Production method of thick X80 pipeline steel |
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| CN115889455A (en) * | 2022-10-28 | 2023-04-04 | 江苏沙钢集团有限公司 | Efficient rolling method for thin-specification pipeline steel |
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Application publication date: 20201211 |