CN112813347B - Ferrite rolling production method of high-r-value low-carbon aluminum killed steel - Google Patents
Ferrite rolling production method of high-r-value low-carbon aluminum killed steel Download PDFInfo
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- CN112813347B CN112813347B CN202011604560.XA CN202011604560A CN112813347B CN 112813347 B CN112813347 B CN 112813347B CN 202011604560 A CN202011604560 A CN 202011604560A CN 112813347 B CN112813347 B CN 112813347B
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
Abstract
The invention provides a ferrite rolling production method of high r value low carbon aluminum killed steel, which comprises the following steps: continuous casting of a plate blank, heating of a hot-rolled plate blank, rough rolling, hot coiling, finish rolling, laminar flow, hot rolling and coiling, cold rolling and pickling, cold rolling, continuous annealing, leveling and recoiling; the low-carbon aluminum killed steel comprises the following chemical components in percentage by weight: c: 0.01-0.06 Wt%, Si: less than or equal to 0.06 Wt%, Mn: 0.1-0.25 Wt%, P: less than or equal to 0.020 Wt%, S: less than or equal to 0.015 Wt%, Alt: 0.020-0.0450 Wt%, and the balance of Fe and inevitable trace elements. The low-carbon aluminum killed steel ferrite hot-rolled cold-rolled coil with a high r value is produced on a continuous annealing production line, wherein the r value of DC01 is 1.5-1.8, the r value of SPCC is 1.2-1.4, and the r value basically reaches the r value level of a finished product of a conventional austenite rolling process, so that the use requirement of a user is completely met.
Description
Technical Field
The invention belongs to the field of steel production and manufacturing, and particularly relates to a ferrite rolling production method of high-r-value low-carbon aluminum killed steel.
Background
The ferritic Rolling process (also known as Warm Rolling) was developed by the research center for steel research in belgium at the end of the 20 th century 80 s, with the aim of producing a cheap, soft, non-aged hot rolled sheet that can be used directly or for subsequent cold Rolling production, which has attracted the general attention and research of the world's various scholars.
Compared with the traditional austenite rolling process, the ferrite rolling process has obvious advantages, the heating temperature is reduced, the energy cost is saved, the generation of iron scales and the abrasion of a roller are reduced, the yield is improved, the equipment load under the ferrite rolling process is lower than that of the austenite rolling process, and the rolling energy consumption is reduced.
Because the ferrite area range of ultra-low carbon aluminum killed steel, namely IF steel (the carbon content is less than 0.01 percent) is large and the temperature is high, the current ferrite rolling process is mainly applied to the production of IF steel. The final cold rolled product of the ferrite rolling of the ultra-low carbon aluminum killed steel has higher r (plastic strain ratio) value and better deep drawing property than the cold rolled annealed steel of the austenite rolling.
For low-carbon aluminum killed steel (with the carbon content of 0.01% -0.06%), when ferrite rolling is adopted, although the conventional performance is close to or superior to that of a traditional austenite rolled steel coil, the r value of the ferrite rolling is always in a lower level, even the r value is only 50% of that of the traditional austenite rolled steel coil, and under the condition of low-grade and high-use common in the current market, the ferrite rolling of the low-carbon aluminum killed steel (with the carbon content of 0.01% -0.06%) is difficult to popularize. However, for most steel mills, the IF steel occupies a very small yield ratio, and most of the products are low-carbon aluminum killed steel. On the basis of the existing process equipment and plate blank components, the development of the low-carbon aluminum killed steel ferrite rolling production method has great significance.
In addition, ferrite rolling is mostly applied to continuous casting and rolling production lines at present, rolling line transformation is often needed, and the problems of steel swinging before finish rolling, induction heating before coiling, difficult control of process temperature, low production efficiency, large investment and the like exist. How to perform accurate control on production rhythm and temperature stability based on a conventional hot continuous rolling production line is also a difficult problem which needs to be solved.
In summary, the following problems exist in the prior art: the rolling r value of finished products is too low when the conventional low-carbon aluminum killed steel (with the carbon content of 0.01-0.06%) is subjected to ferrite rolling.
Disclosure of Invention
The invention aims to solve the problem that the r value of a finished product coil is too low when the conventional low-carbon aluminum killed steel (with the carbon content of 0.01-0.06%) is subjected to ferrite rolling.
In order to solve the problems, the invention provides a method for rolling low-carbon aluminum killed steel ferrite, in particular a method for rolling low-carbon aluminum killed steel ferrite with a high r value, which comprises the following steps:
continuous casting of a plate blank, heating of a hot-rolled plate blank, rough rolling, feeding into a hot coil box, finish rolling, laminar flow, hot rolling and coiling, cold rolling and pickling, cold rolling, continuous annealing, leveling and recoiling; the low-carbon aluminum killed steel comprises the following chemical components in percentage by weight: c: 0.01-0.06 Wt%, Si: less than or equal to 0.06 Wt%, Mn: 0.1-0.25 Wt%, P: less than or equal to 0.020 Wt%, S: less than or equal to 0.015 Wt%, Alt: 0.020-0.0450 Wt%, and the balance of Fe and inevitable trace elements.
Specifically, the plate blank is heated, the heating time is 150min-180min, and the tapping temperature is 1050 ℃ -1100 ℃.
Specifically, the plate blank after the heating process enters a rough rolling unit to be subjected to 5-pass or 7-pass rough rolling, and the final pass temperature of the rough rolling is a low-temperature austenite temperature region of 820-860 ℃.
Specifically, rough rolling descaling water is sprayed among all passes of rough rolling.
Specifically, the inlet temperature of the finish rolling is 800-850 ℃.
Specifically, the finish rolling temperature is 720-750 ℃.
Specifically, the finish rolling and steel throwing are set at 6-10m/s, laminar cooling water is not opened, and the laminar temperature is controlled at 630-660 ℃.
Specifically, the cooling water of the spraying machine frame at the front section of finish rolling and the side water spraying are fully opened, and the reduction rate of the last two machine frames at the outlet is 10-20%.
Specifically, in the cold rolling process, the total rolling reduction rate of cold rolling is more than or equal to 75%.
Specifically, the steel after the cold rolling process adopts a continuous annealing production mode, and the heating temperature of the continuous annealing is 770-830 ℃.
The invention adopts the existing conventional hot continuous rolling production line, can complete the hot rolling production of the ferrite area without modifying related equipment, has the production rhythm control close to the traditional austenite rolling rhythm, and solves the problems that the conventional hot continuous rolling production line has slow production rhythm of the ferrite area hot rolling and is difficult to match the final rolling and laminar temperature. The purposes of reducing energy cost, reducing the generation of iron scales and the abrasion of a roller, improving the yield and reducing the rolling energy consumption are achieved.
The invention relates to a high r-value low-carbon aluminum killed steel ferrite rolling production method, which is characterized in that a high r-value low-carbon aluminum killed steel ferrite hot-rolled cold-rolled coil is produced in a continuous annealing production line through the control of hot-rolling and cold-rolling system processes, wherein the r-value of DC01 is 1.5-1.8, the r-value of SPCC is 1.2-1.4, and the r-value basically reaches the r-value level of a finished product of a conventional austenite rolling process, in addition, the yield strength of the whole product is about 20-30MPa lower than that of a conventional austenite rolling product, and other performance values are basically consistent, so that the use requirements of users are completely met.
Drawings
FIG. 1 is a photograph of a metallographic structure of example 1 of the present invention magnified 500 times;
FIG. 2 is a photograph of metallographic structure of example 2 of the present invention magnified 500 times;
FIG. 3 is a photograph of metallographic structure of example 3 of the present invention magnified 500 times;
FIG. 4 is a photograph of metallographic structure of example 4 of the present invention magnified 500 times.
Detailed Description
The technical solutions in the embodiments of the present invention will be clearly and completely described below with reference to the drawings in the embodiments of the present invention, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all of the embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
In an embodiment of the invention, a ferrite rolling production method of a high r value low carbon aluminum killed steel is provided, which comprises the following steps: continuous casting of a plate blank, heating of a hot-rolled plate blank, rough rolling, hot coiling, finish rolling, laminar flow, primary coiling, cold rolling and acid pickling, cold rolling, continuous annealing, leveling and secondary coiling; the low-carbon aluminum killed steel comprises the following chemical components in percentage by weight: c: 0.01-0.06 Wt%, Si: less than or equal to 0.06 Wt%, Mn: 0.1-0.25 Wt%, P: less than or equal to 0.020 Wt%, S: less than or equal to 0.015 Wt%, Alt: 0.020-0.0450 Wt%, and the balance of Fe and inevitable trace elements.
The production line provided by the invention comprises the following process flows: the method comprises the steps of slab continuous casting, hot rolling slab heating, rough rolling, hot coiling box, finish rolling, laminar flow, hot rolling coiling, cold rolling pickling, cold rolling, continuous annealing, leveling and recoiling. The hot rolling specification of the high r value low carbon aluminum killed steel produced by the ferrite rolling process is 2.0-5.5mm, and the cold rolling specification is 0.3-2.0 mm.
Slab continuous casting: the components and smelting continuous casting process of the plate blank are completely consistent with those of the traditional austenite rolling plate blank.
Heating: the heating time of the slab is 150-. Compared with the traditional ferrite rolling process, the tapping temperature is about 150 ℃, the low heating temperature can reduce energy consumption, reduce oxidation burning loss and improve the yield, and simultaneously can also reduce the temperature waiting time of subsequent rolling and improve the rolling rhythm of ferrite area rolling.
Rough rolling: and (3) feeding the steel into a rough rolling unit to perform rough rolling for 5 or 7 times, wherein the temperature of the last pass of the rough rolling is controlled in a low-temperature austenite temperature region of 820-860 ℃. In order to improve the rolling rhythm, reduce the time for waiting for temperature and avoid improving the middle roller way to improve the air cooling capacity, the invention transfers the common ferrite rolling air cooling process to be synchronous with the rough rolling process, namely, the aim of accurately controlling the temperature and improving the rolling rhythm is achieved by controlling the water spraying pass of rough rolling descaling water during each pass of rough rolling.
A hot rolling box: the hot rolling box can reduce the temperature difference between the head and the tail, break the iron scale, improve the temperature uniformity and the surface quality of the intermediate billet, and simultaneously achieve the aim of further reducing the temperature of the intermediate billet on the premise of not influencing the production rhythm.
Finish rolling and laminar flow: in order to improve the rolling rhythm, the front section of stand for rolling and finish rolling in the ferrite region can roll in an austenite and ferrite two-phase region, the temperature of a steel plate can be reduced by spraying cooling water of the stand, spraying water on the side and the like in the front section of stand for finish rolling, but the stand at the rear section of stand for finish rolling is required to be in a complete ferrite region when rolling, and the set finish rolling temperature needs to be less than 750 ℃. In order to obtain a more uniform structure, the reduction rate of the last two frames of the finish rolling outlet needs to be controlled to be 10-20%. In addition, in order to realize the recovery and growth of ferrite after coiling by utilizing the waste heat after rolling, the condition that a continuous annealing mode is required to be adopted in combination with the cold rolling and annealing process of the ferrite rolling of the low-carbon aluminum killed steel with a high r value is adopted, the coiling temperature needs to be controlled at a higher level, the high coiling temperature is favorable for the growth of ferrite grains of a hot-rolled coil, the aggregation and coarsening of carbides and the further precipitation and growth of aluminum nitride, and the coiling temperature of the traditional austenite rolling continuous annealing hot-rolled substrate is 750 ℃ plus 680 ℃.
In the hot rolling process, the heating time of the plate blank is 150-180min, and the tapping temperature is 1050-1100 ℃. And the rough rolling unit performs 7-pass rough rolling, and the temperature of the last pass of the rough rolling is controlled in a low-temperature austenite temperature region of 820-860 ℃. The finish rolling process is set to a finish rolling inlet of 800-850 ℃, a finish rolling final temperature of 720-750 ℃, cooling water and side water spray between racks at the front section of finish rolling are fully opened, the reduction rate of the two racks at the end of an outlet is controlled to be 10-20%, finish rolling cast steel is set to be 6-10m/s, all cooling water of laminar flow is not opened, and the laminar flow temperature is controlled to be 630-660 ℃.
In the hot rolling process, the production rhythm control means comprises the following steps of firstly, adopting low heating temperature; secondly, the common ferrite rolling air cooling process is transferred to be synchronous with the rough rolling process, and the purposes of accurately controlling the temperature and improving the rolling rhythm are achieved by controlling the water spraying pass of rough rolling descaling water during each pass of rough rolling; thirdly, putting the hot coil box into use; and fourthly, reducing the temperature of the steel plate by spraying cooling water of the frame, laterally spraying water and the like on the front-stage frame in the finish rolling.
However, in the conventional hot continuous rolling production line, the laminar cooling section is often very long, and even under the condition that the laminar cooling section does not open cooling water at all, the temperature drop of the steel plate is about 100 ℃, so the rolling temperature of ferrite rolling cannot reach the coiling temperature of the conventional austenite rolling continuous annealing hot rolling substrate. Under the condition of not reforming a laminar flow area, compared with the traditional austenite rolling process, the method properly improves the finish rolling and steel throwing speed, can be beneficial to reducing laminar temperature drop and gives consideration to the control of the final rolling temperature and the coiling temperature of ferrite rolling.
The requirements of finish rolling and laminar flow are comprehensively considered, the finish rolling process of ferrite rolling of the low-carbon aluminum killed steel with the high r value is set to be a finish rolling inlet of 800-.
Cold rolling: the ferrite rolling base roll cold rolling process is basically consistent with the traditional austenite rolling process, according to the comparative analysis of tests, the larger total cold rolling reduction rate is beneficial to obtaining the high r value of the final product, and in addition, the ferrite rolling base roll strength is about 60MPa lower than that of the traditional austenite rolling base roll, thereby being beneficial to realizing the large reduction rate. The total rolling reduction rate of cold rolling is set to be more than or equal to 75 percent.
Annealing: AlN is precipitated in advance during the ferrite hot rolling of the low-carbon aluminum killed steel, a large amount of deformation zones exist in the rolling direction, the uniformity of crystal grains is poor, the unfavorable textures such as a {001} surface texture and a {110} surface texture are strong, and the like, and a higher r value cannot be obtained during the cover annealing. The conventional coiling temperature of the continuously annealed hot rolled substrate is 680-750 ℃, which is in accordance with the requirement that the ferrite rolling needs to utilize the waste heat to recover and grow the crystal grains, and the continuous annealing is beneficial to obtaining the high r value of the final product due to the heating temperature higher than that of the cover. Therefore, the heating temperature of the cold rolling continuous annealing is set to 770-830 ℃, and other processes are basically consistent with the traditional austenite rolling continuous annealing process.
The invention adopts the existing conventional hot continuous rolling production line, can complete the hot rolling production of the ferrite area without modifying related equipment, has the production rhythm control close to the traditional austenite rolling rhythm, and solves the problems that the conventional hot continuous rolling production line has slow production rhythm of the ferrite area hot rolling and is difficult to match the final rolling and laminar temperature. The purposes of reducing energy cost, reducing the generation of iron scales and the abrasion of a roller, improving the yield and reducing the rolling energy consumption are achieved.
According to the high r-value low-carbon aluminum killed steel ferrite rolling production method, through the control of hot rolling and cold rolling system processes, a high r-value low-carbon aluminum killed steel ferrite hot-rolled cold-rolled coil is produced in a continuous annealing production line, r or r90 is a plastic strain ratio, wherein the r value of DC01 is 1.5-1.8, the r value of SPCC is 1.2-1.4, the r value basically reaches the r value level of a finished product of a conventional austenite rolling process, in addition, the overall yield strength is about 20-30MPa lower than that of a conventional austenite rolling product, and other performance values are basically consistent, so that the use requirements of users are completely met.
The invention provides a ferrite rolling production method of high r value low carbon aluminum killed steel, which adopts the following component proportion and specific process. Wherein, Table 1 shows the compositions (in weight%) of the steels of the respective examples. Tables 2 and 3 show the hot rolling and cold rolling process parameters corresponding to the example steels shown in table 1. Table 4 shows the properties of the steel compositions corresponding to the examples of Table 1. FIG. 1 is a photograph of a metallographic structure of example 1 of the present invention magnified 500 times, the structure being F (ferrite) + a small amount of P (pearlite), the grain size being on the order of 8.0; FIG. 2 is a 500-fold magnified metallographic structure photograph of example 2 of the present invention, wherein the microstructure is F + a small amount of P, and the grain size is grade 9.0; FIG. 3 is a 500-fold magnified metallographic structure photograph of example 3 of the present invention, wherein the microstructure is F + few carbides, and the grain size is 7.0 grade; FIG. 4 is a 500-fold magnified metallographic structure photograph of example 4 of the present invention, wherein the microstructure is F + few carbides and the grain size is 7.5 grade. In addition, in combination with texture detection, the strength of favorable textures such as {111} <110> and {111} <112> is relatively uniform and is obviously converged on the gamma orientation line, and the strength of unfavorable textures such as {001} <100>, {001} <210>, {001} <110> is obviously reduced.
TABLE 1 product chemistry (Wt%)
TABLE 2 Hot Rolling Process parameters specified for the examples
TABLE 3 specific cold rolling and continuous annealing process parameters for each example
SF plate temperature is soaking temperature of the continuous annealing furnace, SCS plate temperature is slow cooling temperature of the continuous annealing furnace, FC plate temperature is fast cooling temperature of the continuous annealing furnace, OAS1 plate temperature is overaging 1 temperature of the continuous annealing furnace, OAS2 plate temperature is overaging 2 temperature of the continuous annealing furnace
TABLE 4 combination of properties of the cold rolled steels obtained in the examples
n 90: is strain hardening index
The above description is only an exemplary embodiment of the present invention, and is not intended to limit the scope of the present invention. In order that the components of the present invention may be combined without conflict, it is within the scope of the present invention that any person skilled in the art may make equivalent changes and modifications without departing from the spirit and principle of the present invention.
Claims (6)
1. A ferrite rolling production method of a high r value low carbon aluminum killed steel is characterized by comprising the following steps in sequence:
continuous casting of a plate blank, heating of a hot-rolled plate blank, rough rolling, feeding into a hot coil box, finish rolling, laminar flow, hot rolling and coiling, cold rolling and pickling, cold rolling, continuous annealing, leveling and recoiling;
the low-carbon aluminum killed steel comprises the following chemical components in percentage by weight: c: 0.0498-0.06 Wt%, Si: less than or equal to 0.06 Wt%, Mn: 0.1-0.25 Wt%, P: less than or equal to 0.020 Wt%, S: less than or equal to 0.015 Wt%, Alt: 0.020-0.0450 Wt%, and the balance of Fe and inevitable trace elements;
the reduction rate of the last two frames of the finish rolling outlet is controlled to be 10-20%;
heating the plate blank for 150-180min, and tapping at 1050-1100 deg.C;
the inlet temperature of the finish rolling is 800-850 ℃;
the finish rolling temperature is 720-750 ℃;
fine rolling and steel polishing are set at 6-10m/s, and the laminar flow temperature is controlled at 630-660 ℃;
the structure is ferrite plus a small amount of pearlite, and the grain size is 8.0 grade or 9.0 grade;
the advantageous texture strength of the {111} <110> and the {111} <112> is relatively uniform and is obviously converged on the gamma orientation line, and the disadvantageous texture strength of the {001} <100>, {001} <210>, {001} <110> is obviously reduced.
2. The ferritic rolling production method of the high r-value low carbon aluminum killed steel as claimed in claim 1 is characterized in that the slab after the heating process enters a rough rolling mill set to carry out rough rolling for 5 or 7 times, and the final temperature of the rough rolling is in a low-temperature austenite temperature region of 820 ℃ to 860 ℃.
3. The ferritic rolling production method of a high r-value low carbon aluminum killed steel as claimed in claim 1 wherein, the rough rolling descaling water is sprayed between each pass of rough rolling.
4. The ferritic rolling production method of a high r-value low carbon aluminum killed steel as claimed in claim 1 wherein the finish rolling front section is sprayed with frame cooling water, the side spray is fully open, and the laminar cooling water is not open.
5. The ferritic rolling production method of the high r-value low-carbon aluminum killed steel as claimed in claim 1 is characterized in that the total rolling reduction rate of cold rolling in the cold rolling process is not less than 75%.
6. The ferritic rolling production method of the high r-value low-carbon aluminum killed steel as claimed in claim 1 is characterized in that the steel after the cold rolling process adopts a continuous annealing production mode, and the heating temperature of the continuous annealing is 770-830 ℃.
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| CN114196878A (en) * | 2021-11-19 | 2022-03-18 | 广西钢铁集团有限公司 | Production method for producing low-cost flexible low-carbon aluminum killed steel with three different yield strength grades on same production line |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4576656A (en) * | 1982-10-08 | 1986-03-18 | Kawasaki Steel Corporation | Method of producing cold rolled steel sheets for deep drawing |
| JPS63119907A (en) * | 1986-11-07 | 1988-05-24 | Kawasaki Steel Corp | Warm rolling method for steel strip |
| CN101921951A (en) * | 2009-06-16 | 2010-12-22 | 上海梅山钢铁股份有限公司 | Low-aluminum-content and high-aging-resistance hot-rolling thin steel plate for cold formation and manufacturing method thereof |
| CN102174683A (en) * | 2011-01-30 | 2011-09-07 | 首钢总公司 | Method for producing cold-rolling low-carbon aluminum killed steel with uniform through plate mechanical property |
| CN104745931A (en) * | 2015-03-26 | 2015-07-01 | 攀钢集团西昌钢钒有限公司 | Low-cost cold-rolled steel plate production method |
| CN107537857A (en) * | 2017-07-10 | 2018-01-05 | 首钢京唐钢铁联合有限责任公司 | A kind of ferrite rolling method |
| CN111167858A (en) * | 2020-01-03 | 2020-05-19 | 北京科技大学 | Method for headless rolling of ferrite area of ultrathin strip steel |
-
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- 2020-12-30 CN CN202011604560.XA patent/CN112813347B/en active Active
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4576656A (en) * | 1982-10-08 | 1986-03-18 | Kawasaki Steel Corporation | Method of producing cold rolled steel sheets for deep drawing |
| JPS63119907A (en) * | 1986-11-07 | 1988-05-24 | Kawasaki Steel Corp | Warm rolling method for steel strip |
| CN101921951A (en) * | 2009-06-16 | 2010-12-22 | 上海梅山钢铁股份有限公司 | Low-aluminum-content and high-aging-resistance hot-rolling thin steel plate for cold formation and manufacturing method thereof |
| CN102174683A (en) * | 2011-01-30 | 2011-09-07 | 首钢总公司 | Method for producing cold-rolling low-carbon aluminum killed steel with uniform through plate mechanical property |
| CN104745931A (en) * | 2015-03-26 | 2015-07-01 | 攀钢集团西昌钢钒有限公司 | Low-cost cold-rolled steel plate production method |
| CN107537857A (en) * | 2017-07-10 | 2018-01-05 | 首钢京唐钢铁联合有限责任公司 | A kind of ferrite rolling method |
| CN111167858A (en) * | 2020-01-03 | 2020-05-19 | 北京科技大学 | Method for headless rolling of ferrite area of ultrathin strip steel |
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