CN110449465B - Method for reducing cold-rolled edge fracture zone of high-hardenability cold-rolled high-strength steel - Google Patents
Method for reducing cold-rolled edge fracture zone of high-hardenability cold-rolled high-strength steel Download PDFInfo
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- CN110449465B CN110449465B CN201910599996.5A CN201910599996A CN110449465B CN 110449465 B CN110449465 B CN 110449465B CN 201910599996 A CN201910599996 A CN 201910599996A CN 110449465 B CN110449465 B CN 110449465B
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B15/00—Arrangements for performing additional metal-working operations specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
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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
- B21B37/28—Control of flatness or profile during rolling of strip, sheets or plates
- B21B37/44—Control of flatness or profile during rolling of strip, sheets or plates using heating, lubricating or water-spray cooling of the product
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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
- B21B37/76—Cooling control on the run-out table
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B45/00—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
- B21B45/02—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills for lubricating, cooling, or cleaning
- B21B45/0203—Cooling
- B21B45/0209—Cooling devices, e.g. using gaseous coolants
- B21B45/0215—Cooling devices, e.g. using gaseous coolants using liquid coolants, e.g. for sections, for tubes
- B21B45/0218—Cooling devices, e.g. using gaseous coolants using liquid coolants, e.g. for sections, for tubes for strips, sheets, or plates
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B15/00—Arrangements for performing additional metal-working operations specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
- B21B2015/0057—Coiling the rolled product
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Abstract
The invention relates to a method for reducing cold-rolled edge cracking strips of high-hardenability cold-rolled high-strength steel, which comprises the working procedures of high-strength steel smelting, heating by a heating furnace, rough rolling, descaling, 2250mm hot continuous rolling, laminar cooling and coiling, wherein the laminar cooling adopts a rear-section 1/2 cooling mode, and meanwhile, water spraying at the side of a fine adjustment area is closed. The invention can effectively solve the defect of cold-rolled edge fracture strip of high-hardenability high-strength steel without influencing normal production and product performance, and improve the yield and the instant yield of strip steel.
Description
Technical Field
The invention relates to a method for controlling a steel strip cold-rolled edge fracture strip, in particular to a method for reducing a high-hardenability cold-rolled high-strength steel cold-rolled edge fracture strip.
Background
As automobiles are being more and more lightweight, the proportion of high-strength steel in automobile steel is increasing. High-strength steel generally employs a high alloy system or a high carbon system in order to obtain high strength, and these component systems provide a steel sheet with high hardenability. Generally, with the increase of strength, the alloy content is higher, the hardenability is increased, martensite phase transformation easily occurs when the cooling speed of high-hardenability high-strength steel is too high, particularly, brittle tissues or stress cracking phenomena easily occur when laminar flow after hot rolling and the cooling speed of the edge part in the coiling process are faster, edge corrosion even occurs to heavy hot rolling raw materials, the edge plasticity of the strip steel is lower, and the edge cracking zone is higher in the cold rolling deformation process. The Chinese patent with the patent number of 201810882943.X discloses a method for preventing edge cracking and strip breakage of hot continuous rolled steel plates in cold rolling, and the Chinese metallurgy, 2018, stage 9, discloses 980 MPa-grade dual-phase steel edge cracking and strip breakage reason analysis, and the two disclosed technologies propose measures for putting a slow cooling pit and closing finish rolling side spraying for DP980 cold rolling edge cracking, but the scale generated on the surface layer of the strip steel in the implementation process is too thick, so that the pickling is difficult, the rolling difficulty is further increased, the rolling crack rate is higher, and meanwhile, corresponding measures are not proposed for the problem of high-hardenability high-strength steel edge cracking and strip breakage.
Disclosure of Invention
The invention aims to provide a method for reducing the cold rolling edge fracture zone of high-hardenability cold-rolled high-strength steel, reduce or even eliminate the edge fracture zone rate of the high-hardenability high-strength steel in the cold rolling process, improve the production stability and solve the defects of the background technology.
A method for reducing cold-rolled edge fracture strips of high-hardenability cold-rolled high-strength steel comprises the working procedures of 2250mm hot continuous rolling and laminar cooling of the hot continuous rolling, wherein the laminar cooling adopts a rear section 1/2 cooling mode, and water spraying at the side of a fine adjustment area is closed.
The method for reducing the high-hardenability cold-rolled high-strength steel cold-rolled edge crack broken strip comprises the working procedures of high-strength steel smelting, heating by a heating furnace, rough rolling, descaling, 2250mm hot continuous rolling, laminar cooling and coiling, wherein a head-tail temperature U-shaped coiling process is adopted in the coiling process, the head-tail temperature is compensated by 30 ℃, the compensation length is 50m, the coiling temperature is controlled to be 610 ℃ or above, and the bainite transformation region is prevented from staying.
According to the method for reducing the high-hardenability cold-rolled high-strength steel cold-rolled edge fracture strip, the off-line hot coil is placed in an inverted stacking mode after being coiled, the hot coil is axially vertical to the ground, the lowermost and uppermost hot coils of the stack are replaced by other steel coils produced in the same batch, the temperature drop rate of the edge is reduced, and the temperature difference of the edge is avoided.
According to the method for reducing the cold rolling edge cracking and strip breakage of the high-hardenability cold-rolled high-strength steel, the hot-rolled steel coil is subjected to cold continuous rolling after being stacked and cooled, and the cold rolling reduction rate is controlled to be 45-50%; after cold rolling, entering a cold continuous rolling process, wherein the additional tension of a 4 th frame and a 5 th frame is controlled to be 10KN-30KN in the cold rolling process, and the tension between the frames is controlled to be 250KN-320 KN; and the edge cutting is carried out in the subsequent procedure, and the edge cutting is not carried out before rolling, so that the generation of edge microcracks and the expansion in the rolling process are reduced.
Compared with the prior art, the invention has the beneficial effects that:
according to the invention, by adjusting key control points such as a laminar cooling mode and a coiling mode and adopting the rear section 1/2 for cooling, transformation of matrix ferrite and pearlite can be promoted, water spraying at the side of a fine adjustment area is closed, the coiling temperature is controlled to be 610 ℃ or above, and the rapid temperature drop of the edge part and the generation of brittle tissues of the edge part in the coiling process are avoided; the traditional hot coil stacking mode is changed, the hot coil shafts are vertically arranged, so that the edge heat preservation and the over-fast temperature drop of the edge are facilitated, meanwhile, the temperature conduction among stacked coils is conducive to fully tempering the edge tissues, and the generation of edge fragile tissues is reduced; the cold rolling reduction rate is reduced, no trimming is adopted before rolling, and the tension between cold rolling frames is controlled, so that the side crack belt breakage accident caused by overlarge reduction rate and side crack expansion is avoided.
The method is simple and easy to implement, does not influence the production process of the original steel, and has high economic benefit; the invention can effectively solve the defect of cold-rolled edge fracture strip of high-hardenability high-strength steel without influencing normal production and product performance, and improve the yield and the instant yield of strip steel.
The method is simple and easy to implement. Especially, the effect on martensite cold-rolled steel and quenching distribution steel such as MS1500, QP1180 and the like with high hardenability is obvious.
Drawings
FIG. 1 is a schematic view of an end-of-line hot coil stacking;
FIG. 2 is a schematic diagram of a cold-rolled edge fractured strip of a QP1180 steel strip in the prior production process;
FIG. 3 is a metallographic structure diagram of a QP1180 steel strip 2mm away from an edge part in the prior art;
FIG. 4 is a metallographic structure of QP1180 steel strip produced in example 1 at 2mm from the edge;
FIG. 5 is a comparison of the strength of a QP1180 hot rolled steel strip in example 1 at different positions in the front and rear width directions using the present invention;
FIG. 6 is a comparison of the elongation at different positions in the front and rear width directions of a QP1180 hot rolled steel strip in example 1, according to the present invention;
FIG. 7 is a schematic diagram of cold rolled edge quality of a QP1180 steel strip produced in example 1;
FIG. 8 is a schematic diagram of a cold-rolled edge broken strip of MS1500 steel strip in a prior production process;
FIG. 9 is a metallographic structure diagram of an MS1500 steel strip 2mm away from an edge part in the prior art;
FIG. 10 is a metallographic structure of the MS1500 steel strip produced in example 2 at a distance of 2mm from the edge;
FIG. 11 is a comparison of the strength of the MS1500 hot rolled strip in example 2 at different positions in the width direction before and after the hot rolled strip is subjected to the hot rolling of the present invention;
FIG. 12 is a comparison of the elongation at different positions before and after the application of the present invention to the MS1500 hot rolled steel strip in example 2;
FIG. 13 is a cold rolling quality diagram of the MS1500 steel strip produced in example 2.
Detailed Description
The invention is further illustrated by the following specific examples:
example 1
Producing a QP1180 steel strip, entering a 2250mm hot continuous rolling process after smelting, heating by a heating furnace, rough rolling, descaling and 2250mm continuous rolling by a continuous rolling machine, and then entering a laminar cooling section, wherein the laminar cooling section comprises a front section and a rear section, and each section comprises 10 groups of water spray beam groups; the hot-rolling laminar flow cooling section adopts a rear section 1/2 cooling mode, the rear section starts the 11 th-20 th groups to spray water for cooling, each group has 4 spray beams, and the 1/2 cooling mode selects 2 spray beams in each group to spray water for cooling; meanwhile, water spraying at the side of the fine adjustment area is closed, and the temperature drop of the edge part is improved; after laminar cooling, the laminar flow enters a coiling process, the coiling process adopts a U-shaped coiling process, the head and the tail are compensated by 30 ℃, the compensation length is 50m, and the coiling temperature is controlled at 630 +/-15 ℃;
after the coiling is finished, the lower coil hot coil is placed in an inverted stacking mode, as shown in figure 1, the hot coil is axially stacked vertically to the ground, the hot coils at the bottommost part and the topmost part of the stack are replaced by DP780 steel coils produced in the same batch, and after the coil is cooled, the edge tissues are shown in figure 4;
the cooled steel coil enters a cold continuous rolling process, the cold rolling reduction rate is 45%, and trimming is not performed before rolling so as to avoid the expansion of microcracks generated by trimming in the rolling process; in the cold rolling process, the additional tension between the 4 th frame and the 5 th frame is set to be 10KN, the tension between the frames is controlled to be 250KN-280KN, and the appearance of the lower-line cold-rolled edge part is shown in figure 7;
FIG. 4 is a metallographic structure of QP1180 steel strip produced in example 1 at 2mm from the edge; FIG. 3 is a metallographic structure diagram of a QP1180 steel strip 2mm away from an edge part in the prior art; as can be seen by comparing fig. 4 and fig. 3, the metallographic structure of the QP1180 steel strip produced by the process of the present invention, which is 2mm away from the edge portion, is ferrite and pearlite, and acicular ferrite and dispersed maoendo are significantly reduced; meanwhile, the comparison of the mechanical properties of different positions in the front and rear width directions implemented by the process shown in fig. 5 and 6 shows that the edge plasticity of the QP1180 produced by the method is obviously improved compared with that of the QP1180 produced by the prior art.
Fig. 7 is a picture of an edge quality object of QP1180 produced in example 1, fig. 2 is a schematic view of a QP1180 cold-rolled edge cracking strip produced by using the prior art, and it can be seen by comparing fig. 7 with fig. 2 that the cold-rolled edge cracking is completely eliminated by using the QP1180 produced by using the process of the present invention.
Example 2
Producing an MS1500 steel strip, entering a 2250mm hot continuous rolling process after smelting, heating by a heating furnace, rough rolling, descaling and 2250mm continuous rolling by a continuous rolling mill, and then entering a laminar cooling section, wherein the laminar cooling section comprises a front section and a rear section, and each section comprises 10 groups of water spray beam groups; the hot-rolling laminar flow cooling section adopts a rear section 1/2 cooling mode, the rear section starts the 11 th-20 th groups to spray water for cooling, each group has 4 spray beams, and the 1/2 cooling mode selects 2 spray beams in each group to spray water for cooling; meanwhile, water spraying at the side of the fine adjustment area is closed, and the temperature drop of the edge part is improved; after laminar cooling, the laminar flow enters a coiling procedure, the head and tail compensation of the U-shaped coiling process is adopted in the coiling procedure for 30 ℃, the compensation length is 50m, and the coiling temperature is controlled to be 635 +/-15 ℃;
after the coiling is finished, the lower coil hot coil is placed in an inverted stacking mode, as shown in figure 1, the hot coil is axially stacked vertically to the ground, the bottommost and the topmost hot coils of the stack are replaced by other steel DP600 steel coils produced in the same batch, and after cooling, the edge structure is shown in figure 10;
the cooled steel coil enters a cold continuous rolling process, the cold rolling reduction rate is 50%, and trimming is not performed before rolling so as to avoid the expansion of microcracks generated by trimming in the rolling process; in the cold rolling process, the additional tension between the 4 th frame and the 5 th frame is set to be 30KN, the tension between the frames is controlled to be 280-320 KN, and the appearance of the lower-line cold-rolled edge part is shown in FIG. 13;
FIG. 10 is a metallographic structure of the MS1500 steel strip produced in example 2 at a distance of 2mm from the edge; FIG. 9 is a metallographic structure diagram of an MS1500 steel strip 2mm away from an edge part in the prior art; as can be seen by comparing the graphs in FIGS. 9 and 10, the metallographic structure of the MS1500 steel strip produced by the process of the invention, which is 2mm away from the edge, is ferrite, pearlite and a small amount of bainite, and the acicular martensite brittle structure obviously disappears; meanwhile, the comparison of the mechanical properties of different positions in the front and rear width directions of the MS1500 in the images of the images 11 and 12 shows that the edge plasticity of the MS1500 produced by the invention is obviously improved compared with the edge plasticity of the MS1500 produced by the prior art;
fig. 13 is a physical diagram of MS1500 edge quality produced in example 2, fig. 8 is a schematic diagram of an MS1500 cold-rolled edge break strip produced by the prior art, and it can be seen by comparing fig. 13 and fig. 8 that the MS1500 produced by the process of the present invention has completely eliminated the cold-rolled edge break.
The steel grades of the above embodiments are detected to have no edge crack phenomenon.
Claims (2)
1. A method for reducing cold rolling edge cracking strips of high-hardenability cold-rolled high-strength steel comprises 2250mm hot continuous rolling and laminar cooling processes, and is characterized in that: the laminar cooling adopts a rear section 1/2 cooling mode, and meanwhile, water spraying at the side of the fine adjustment area is closed; a coiling process, wherein the coiling temperature is controlled to be 610 ℃ or above;
the lower coil hot coil is placed in an inverted stacking mode after being coiled, so that the hot coil is axially vertical to the ground, and the lowermost and uppermost hot coils of the stack are replaced by other steel coils produced in the same batch, so that the temperature drop rate of the edge part is reduced, and the temperature difference of the edge part is avoided;
after the hot rolled steel coil is stacked and cooled, cold continuous rolling is carried out, and the cold rolling reduction rate is controlled to be 45-50%; after cold rolling, entering a cold continuous rolling process, wherein the additional tension of a 4 th frame and a 5 th frame is controlled to be 10KN-30KN in the cold rolling process, and the tension between the frames is controlled to be 250KN-320 KN; and the edge cutting is carried out in the subsequent procedure, and the edge cutting is not carried out before rolling, so that the generation of edge microcracks and the expansion in the rolling process are reduced.
2. The method for reducing the cold rolled edge cracking zone of the high hardenability cold rolled high strength steel according to claim 1, comprising the steps of high strength steel smelting, heating by a heating furnace, rough rolling, descaling, 2250mm hot continuous rolling, laminar cooling and coiling, wherein the steps of: the coiling process adopts a head-tail temperature U-shaped coiling process, the head-tail temperature is compensated for 30 ℃, the compensation length is 50m, and the bainite transformation region is prevented from staying.
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| CN112605156B (en) * | 2021-01-15 | 2023-03-10 | 安阳钢铁股份有限公司 | Method for improving flatness of hot continuous rolling thin-specification checkered plate |
| CN113059003B (en) * | 2021-03-01 | 2023-07-21 | 首钢京唐钢铁联合有限责任公司 | Method for controlling cold-rolled high-strength steel acid edging crack |
| CN113245366A (en) * | 2021-04-16 | 2021-08-13 | 首钢集团有限公司 | Method for reducing non-welding-seam strip breakage rate in 590Mpa high-strength steel cold rolling |
Citations (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1483528A (en) * | 2002-09-19 | 2004-03-24 | 鞍钢集团新钢铁有限责任公司 | Three section laminar flow cooling technology for hot rolling band steel |
| CN101941024A (en) * | 2010-07-22 | 2011-01-12 | 河北省首钢迁安钢铁有限责任公司 | Method for eliminating peeling of IF steel edge in hot continuous rolling process |
| CN102101124A (en) * | 2009-12-22 | 2011-06-22 | 鞍钢股份有限公司 | Production method for eliminating edge defects of hot-rolled strip steel |
| CN102179407A (en) * | 2011-03-17 | 2011-09-14 | 宁波钢铁有限公司 | Method for preparing hot rolling strip steel capable of preventing edge crack of extremely thin rolled strip steel |
| CN103290311A (en) * | 2013-05-30 | 2013-09-11 | 宁波钢铁有限公司 | Method for manufacturing civil high-grade anti-theft door plank |
| CN104141093A (en) * | 2013-05-10 | 2014-11-12 | 河北钢铁股份有限公司承德分公司 | Automobile compartment body band steel with yield strength reaching 700MPa, and rolling method thereof |
| CN105734235A (en) * | 2014-12-10 | 2016-07-06 | 上海梅山钢铁股份有限公司 | Intensive cooling control method for hot continuous rolling strip steel |
| DE102016114404A1 (en) * | 2015-09-08 | 2017-03-09 | Hitachi, Ltd. | Reel temperature control device and reel temperature control method |
| CN107983771A (en) * | 2017-11-23 | 2018-05-04 | 攀钢集团攀枝花钢铁研究院有限公司 | The high-strength chill volume hot-rolling method of building concrete fixing piece |
| CN109465295A (en) * | 2018-08-06 | 2019-03-15 | 首钢集团有限公司 | Method for preventing edge cracking and strip breakage of hot continuous rolled steel plate in cold rolling |
-
2019
- 2019-07-04 CN CN201910599996.5A patent/CN110449465B/en active Active
Patent Citations (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1483528A (en) * | 2002-09-19 | 2004-03-24 | 鞍钢集团新钢铁有限责任公司 | Three section laminar flow cooling technology for hot rolling band steel |
| CN102101124A (en) * | 2009-12-22 | 2011-06-22 | 鞍钢股份有限公司 | Production method for eliminating edge defects of hot-rolled strip steel |
| CN101941024A (en) * | 2010-07-22 | 2011-01-12 | 河北省首钢迁安钢铁有限责任公司 | Method for eliminating peeling of IF steel edge in hot continuous rolling process |
| CN102179407A (en) * | 2011-03-17 | 2011-09-14 | 宁波钢铁有限公司 | Method for preparing hot rolling strip steel capable of preventing edge crack of extremely thin rolled strip steel |
| CN104141093A (en) * | 2013-05-10 | 2014-11-12 | 河北钢铁股份有限公司承德分公司 | Automobile compartment body band steel with yield strength reaching 700MPa, and rolling method thereof |
| CN103290311A (en) * | 2013-05-30 | 2013-09-11 | 宁波钢铁有限公司 | Method for manufacturing civil high-grade anti-theft door plank |
| CN105734235A (en) * | 2014-12-10 | 2016-07-06 | 上海梅山钢铁股份有限公司 | Intensive cooling control method for hot continuous rolling strip steel |
| DE102016114404A1 (en) * | 2015-09-08 | 2017-03-09 | Hitachi, Ltd. | Reel temperature control device and reel temperature control method |
| CN107983771A (en) * | 2017-11-23 | 2018-05-04 | 攀钢集团攀枝花钢铁研究院有限公司 | The high-strength chill volume hot-rolling method of building concrete fixing piece |
| CN109465295A (en) * | 2018-08-06 | 2019-03-15 | 首钢集团有限公司 | Method for preventing edge cracking and strip breakage of hot continuous rolled steel plate in cold rolling |
Non-Patent Citations (2)
| Title |
|---|
| 影响高强双相钢冷轧边部缺陷;张亮亮;《金属材料与冶金工程》;20181231;第46卷(第5期);第13-39页 * |
| 连铸连轧产品缺陷分析及控制措施;高菊;《钢铁钒钛》;20160229;第37卷(第1期);第131-136页 * |
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