CN115058573B - Production method for high-grade non-oriented silicon steel after strip breakage during primary cold rolling - Google Patents
Production method for high-grade non-oriented silicon steel after strip breakage during primary cold rolling Download PDFInfo
- Publication number
- CN115058573B CN115058573B CN202210697862.9A CN202210697862A CN115058573B CN 115058573 B CN115058573 B CN 115058573B CN 202210697862 A CN202210697862 A CN 202210697862A CN 115058573 B CN115058573 B CN 115058573B
- Authority
- CN
- China
- Prior art keywords
- cold rolling
- annealing
- silicon steel
- oriented silicon
- grade non
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
- 238000005097 cold rolling Methods 0.000 title claims abstract description 84
- 229910000976 Electrical steel Inorganic materials 0.000 title claims abstract description 54
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 35
- 238000000137 annealing Methods 0.000 claims abstract description 105
- 238000000034 method Methods 0.000 claims abstract description 37
- 239000011248 coating agent Substances 0.000 claims abstract description 12
- 238000000576 coating method Methods 0.000 claims abstract description 12
- 238000004806 packaging method and process Methods 0.000 claims abstract description 8
- 238000002791 soaking Methods 0.000 claims description 24
- 238000004321 preservation Methods 0.000 claims description 18
- 229910052710 silicon Inorganic materials 0.000 claims description 9
- 238000005266 casting Methods 0.000 claims description 7
- 238000009749 continuous casting Methods 0.000 claims description 7
- 238000010438 heat treatment Methods 0.000 claims description 7
- 238000005098 hot rolling Methods 0.000 claims description 7
- 238000009628 steelmaking Methods 0.000 claims description 7
- 229910052739 hydrogen Inorganic materials 0.000 claims description 6
- 238000005554 pickling Methods 0.000 claims description 5
- 239000000047 product Substances 0.000 description 54
- 229910000831 Steel Inorganic materials 0.000 description 16
- 239000010959 steel Substances 0.000 description 16
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 14
- 230000006698 induction Effects 0.000 description 13
- 230000000052 comparative effect Effects 0.000 description 12
- 229910052742 iron Inorganic materials 0.000 description 7
- 239000007789 gas Substances 0.000 description 6
- 239000002253 acid Substances 0.000 description 4
- 229910045601 alloy Inorganic materials 0.000 description 4
- 239000000956 alloy Substances 0.000 description 4
- 239000002994 raw material Substances 0.000 description 4
- 238000005406 washing Methods 0.000 description 4
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 3
- 239000012467 final product Substances 0.000 description 3
- 239000001257 hydrogen Substances 0.000 description 3
- 239000002245 particle Substances 0.000 description 3
- 238000005096 rolling process Methods 0.000 description 3
- 230000009286 beneficial effect Effects 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 238000002360 preparation method Methods 0.000 description 2
- 229910052761 rare earth metal Inorganic materials 0.000 description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910000565 Non-oriented electrical steel Inorganic materials 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 238000010924 continuous production Methods 0.000 description 1
- 230000001627 detrimental effect Effects 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000005265 energy consumption Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 238000010304 firing Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 150000002910 rare earth metals Chemical class 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
- C21D8/1233—Cold rolling
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
-
- 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
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
-
- 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
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1277—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular surface treatment
- C21D8/1283—Application of a separating or insulating coating
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Physics & Mathematics (AREA)
- Metallurgy (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Organic Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Electromagnetism (AREA)
- Manufacturing Of Steel Electrode Plates (AREA)
- Soft Magnetic Materials (AREA)
Abstract
The invention discloses a production method of high-grade non-oriented silicon steel after strip breakage during one-time cold rolling, which comprises the following steps: primary cold rolling of a broken coil, intermediate annealing, secondary cold rolling, finished product annealing, coating and finishing packaging, wherein the thickness of the primary cold rolling of the broken coil is 0.80-1.00 mm, and the temperature of the intermediate annealing is 900-920 ℃; the method can ensure the smoothness of the secondary cold rolling of the primary cold rolling broken strip coil with the thickness of 0.80-1.00 mm, can maintain the magnetic property at a normal level, saves the direct scrapping of the high-grade non-oriented silicon steel after the cold rolling broken strip, and reduces the loss.
Description
Technical Field
The invention belongs to the technical field of non-oriented silicon steel preparation, and particularly relates to a production method for high-grade non-oriented silicon steel after strip breakage during one-time cold rolling.
Background
With the upgrading of national household appliance energy efficiency standards, the demand for high-grade non-oriented silicon steel is gradually increased, and steel enterprises which do not produce silicon steel originally put new production lines into production teams of non-oriented silicon steel. The method is influenced by the limit of the technical level and the capability of cold rolling equipment, the phenomenon of cold rolling breakage is unavoidable in the process of producing high-grade non-oriented silicon steel by partial enterprises, particularly civil enterprises, and the problem that the cold rolling breakage of about 1% of enterprises in the process of producing high-grade non-oriented silicon steel (Si content is more than or equal to 3.0%) cannot hit the thickness of a target finished product is reported.
After the strip breakage, the continuous production can not be carried out and only scrapped due to the work hardening and the brittleness of the silicon steel with high Si content, or the finished product can be cold rolled to the target thickness again after intermediate annealing, but the finished product magnetic property does not meet the national standard and only scrapped, and the loss is larger.
Chinese patent CN 102634729A-a preparation method of non-oriented silicon steel with low iron loss, high magnetic induction and high grade discloses a process of continuously annealing after cold rolling to 0.8mm thickness for 1-4 min at 840-900 ℃ for 3.0-3.4% of Si content and adding Sn component, thus preparing a target finished product with 0.35mm thickness.
Chinese patent CN111235461A- "high strength non-oriented electrical steel for high carbon new energy driving motor containing rare earth and its manufacturing method" discloses a process of continuously annealing at 720-760 ℃ for 20-40 min after cold rolling once to 0.70-0.75 mm thickness by adding rare earth element Ce and microalloy element Nb and Ti components and adding 2.0-3.0% Si/1.0-2.0% Als, thus preparing 0.35mm thickness target finished product.
Gu Chengyi et al studied the performance of high grade non-oriented silicon steel with 3.10% Si and 0.54Als as main components by adopting a secondary cold rolling method in journal electrical materials in 2010 in 4, wherein the primary cold rolling is carried out to a thickness of 0.78mm, and then intermediate annealing is carried out in a continuous annealing furnace at 850 ℃ for 160s, thus finally preparing the target product with a thickness of 0.35mm.
In the prior art, a secondary cold rolling process is generally adopted to produce high-grade non-oriented silicon steel, namely, cold rolling is firstly carried out to a certain specific intermediate thickness and then cold rolling is carried out to the thickness of a finished product, however, cold rolling strip breakage of partial enterprises at present occurs randomly, that is, the intermediate thickness is not specific, so that no prior art can be used for reference. According to the principle of materialism, the influence of different intermediate thicknesses and intermediate annealing processes on silicon steel tissues and textures is larger, and the magnetic performance of a final finished product is directly influenced, but a method for saving and reproducing the scrapped coil after the cold rolling and belt breakage is not carried out in the prior art.
Disclosure of Invention
In order to solve the technical problems, the invention provides a production method for the high-grade non-oriented silicon steel after strip breakage during primary cold rolling, which can ensure the smoothness of secondary cold rolling of a primary cold rolling broken strip coil with the thickness of 0.80-1.00 mm, maintain the magnetic performance at a normal level, save direct scrapping of the high-grade non-oriented silicon steel after the cold rolling broken strip and reduce loss.
In order to achieve the above purpose, the technical scheme adopted by the invention is as follows:
the production method after the strip breakage of the high-grade non-oriented silicon steel during one-time cold rolling comprises the following steps: primary cold rolling to break coil, intermediate annealing, secondary cold rolling, finished product annealing, coating and finishing packaging;
the thickness of the primary cold rolling broken coil is 0.80-1.00 mm;
the soaking temperature of the intermediate annealing is 900-920 ℃, and the intermediate annealing has the effects that the grain size of the steel strip is proper to ensure the smooth completion of secondary cold rolling and good texture components are ensured to meet the magnetic property requirement of a final product because the texture has stronger hereditary property, and when the soaking temperature of the annealing is too low, the {100} texture components and the {110} texture components are fewer and the {111} texture components are more, so that the magnetic property is unfavorable; when the annealing soaking temperature is too high, the grain size is larger, which is unfavorable for the smooth secondary cold rolling.
The weight percentage of Si, mn, als in the high-grade non-oriented silicon steel is as follows: si is more than or equal to 3.0% and less than or equal to 3.2%, mn is more than or equal to 0.1% and less than or equal to 0.5%, als is more than or equal to 0.4% and less than or equal to 1.0%.
The primary cold rolling broken coil is obtained through steelmaking, continuous casting, casting blank heating, hot rolling, normalizing pickling and primary cold rolling, and broken coil occurs in the primary cold rolling process.
Before the primary cold rolling, the thickness of the hot rolled steel strip after pickling is 2.20mm, the grains are uniform recrystallized ferrite structures, the average grain size is 90-100 mu m, and the hot rolled steel strip has stronger Goss ({ 110} <001 >) texture, {112} <110> texture and gamma texture.
The intermediate annealing adopts a continuous annealing furnace for annealing, and H is adopted in the continuous annealing furnace 2 30-35% N by volume 2 And H 2 To prevent the surface shape of the steel strip during the intermediate annealingOxide-forming particles or nitride-forming particles, which promote preferential nucleation and growth of {111} orientation grains at the particles, which are detrimental to magnetic properties during product annealing, are responsible for the higher volume percentage of hydrogen during intermediate annealing than during product annealing.
The heat preservation time of the intermediate annealing is 100-120 s, the soaking time is adjusted by adjusting the running speed of the steel strip, the uniformity of the structure of the whole steel coil can be guaranteed in the heat preservation time, the performance consistency of a final finished product is improved, if the heat preservation time is too short, the uniformity of the steel coil is poor, the rolling mill vibrates during secondary cold rolling, fluctuation instability can occur in the magnetic performance of the final finished product, and the cost is increased due to the overlong heat preservation time.
And cold rolling for the second time until the thickness of the finished product is 0.35mm.
In the annealing step of the finished product, the annealing temperature is 970-990 ℃, the heat preservation time is 30-50 s, and H is adopted in the annealing process 2 10-15% N by volume 2 And H 2 Is used for protecting the mixed gas.
When the annealing temperature is too low, the grain size of the finished product is smaller, which is not beneficial to iron loss; when the annealing temperature is too high, mixed crystals may be caused by excessive firing, which increases energy consumption and deteriorates iron loss and magnetic induction. The annealing heat preservation time is too short, and the uneven crystal grains of the finished product are not beneficial to iron loss; the annealing heat preservation time is too long, the production efficiency is low, and the cost is increased. The hydrogen percentage is too low, the reducing atmosphere in the annealing furnace is insufficient, so that the surface of the silicon steel is subjected to weak oxidation to deteriorate the iron loss of the finished product, and the production cost is increased due to the too high hydrogen percentage.
The invention also provides the high-grade non-oriented silicon steel, which is produced by the production method, and the method can save the scrapped coil of the high-grade non-oriented silicon steel after cold rolling and belt breakage, reduce the direct scrapped loss and ensure that the magnetic property of the finished product meets P 1.5/50 ＝2.15～2.30W/kg、B 50 =1.66 to 1.68T, far exceeding the national standard requirements.
Compared with the prior art, the production method for the high-grade non-oriented silicon steel after strip breakage during one-time cold rolling has the following advantages:
(1) The invention can save the problem of scrapping the coil after the cold rolling and belt breaking of the high-grade non-oriented silicon steel at lower production cost, and reduce the direct scrapping loss;
(2) The magnetic property P of the high-grade non-oriented silicon steel product produced by the invention 1.5/50 ＝2.15～2.30W/kg、B 50 =1.66 to 1.68T, far exceeding national standard GB/T2521.1-2016 part 1 of full process cold rolled electrical steel: performance requirements in grain-unoriented steel belts (sheets).
Drawings
FIG. 1 is a diagram showing the structure of the non-oriented silicon steel produced in example 2;
FIG. 2 is a texture map of the non-oriented silicon steel produced in example 2;
FIG. 3 is a structure diagram of the non-oriented silicon steel produced in comparative example 8;
FIG. 4 is a texture map of the non-oriented silicon steel produced in comparative example 8.
Detailed Description
The production method after the strip breakage of the high-grade non-oriented silicon steel during one-time cold rolling comprises the following steps: primary cold rolling to break coil, intermediate annealing, secondary cold rolling, finished product annealing, coating and finishing packaging;
the weight percentage of Si, mn, als in the high-grade non-oriented silicon steel is as follows: si is more than or equal to 3.0% and less than or equal to 3.2%, mn is more than or equal to 0.1% and less than or equal to 0.5%, als is more than or equal to 0.4% and less than or equal to 1.0%;
the primary cold-rolled broken strip is obtained through steelmaking, continuous casting, casting blank heating, hot rolling, normalizing pickling and primary cold rolling, and broken strip occurs in the primary cold rolling process; the thickness of the primary cold rolling broken coil is 0.80-1.00 mm;
before the primary cold rolling, the thickness of the hot rolled steel strip after pickling is 2.20mm, the grains are uniform recrystallized ferrite structures, the average grain size is 90-100 mu m, and the hot rolled steel strip has stronger Goss ({ 110} <001 >) texture, {112} <110> texture and gamma texture.
The intermediate annealing adopts a continuous annealing furnace for annealing, and H is adopted in the continuous annealing furnace 2 The volume percentage is 30-35%N of (2) 2 And H 2 The soaking temperature of the intermediate annealing is 900-920 ℃, and the soaking time is adjusted to 100-120 s by adjusting the running speed of the steel belt;
secondary cold rolling to a thickness of 0.35mm;
in the annealing step of the finished product, the annealing temperature is 970-990 ℃, the heat preservation time is 30-50 s, and H is adopted in the annealing process 2 10-15% N by volume 2 And H 2 Is used for protecting the mixed gas.
The present invention will be described in detail with reference to examples.
Example 1
A production method for high-grade non-oriented silicon steel after strip breakage during primary cold rolling comprises the following steps: the method comprises the steps of primary cold rolling coil breakage, intermediate annealing, secondary cold rolling, finished product annealing, coating, finishing and packaging, and specifically comprises the following steps:
the raw material with the thickness of 2.20mm is obtained by adopting a conventional process (steelmaking, continuous casting, casting blank heating, hot rolling and normalized acid washing), and the weight percentage of the main alloy components is 3.0 percent of Si, 0.5 percent of Mn and 1.0 percent of Als. The cold rolling process is unable to continue production due to strip breakage, the thickness of the broken strip coil is 0.80mm, the cold rolled broken strip coil is subjected to intermediate annealing in a high-grade non-oriented silicon steel horizontal continuous annealing production line, the soaking temperature of the intermediate annealing is 900 ℃, the heat preservation is 100s, and H is adopted 2 Volume fraction of 30% (N) 2 +H 2 ) Atmosphere protection; cold rolling the steel coil subjected to intermediate annealing again to a finished product thickness of 0.35mm, and then performing finished product annealing coating, wherein in the finished product annealing process, the annealing temperature is 970 ℃, the heat preservation time is 30s, and H is adopted in the annealing process 2 10% by volume of (N) 2 +H 2 ) And (5) protecting the mixed gas.
By adopting the production method, the problem of scrapped rolls after cold rolling and belt breakage of high-grade non-oriented silicon steel can be saved, the direct scrapped loss is reduced, and the magnetic property P of the finished product is ensured 1.5/50 ＝2.30W/kg、B 50 =1.66T, far exceeding the national standard requirements.
Example 2
A production method for high-grade non-oriented silicon steel after strip breakage during primary cold rolling comprises the following steps: the method comprises the steps of primary cold rolling coil breakage, intermediate annealing, secondary cold rolling, finished product annealing, coating, finishing and packaging, and specifically comprises the following steps:
the raw material with the thickness of 2.20mm is obtained by adopting a conventional process (steelmaking, continuous casting, casting blank heating, hot rolling and normalized acid washing), and the weight percentage of the main alloy components is 3.0 percent of Si, 0.5 percent of Mn and 1.0 percent of Als. The cold rolling process is unable to continue production due to strip breakage, the thickness of the broken strip coil is 0.80mm, the cold rolled broken strip coil is subjected to intermediate annealing in a high-grade non-oriented silicon steel horizontal continuous annealing production line, the soaking temperature of the intermediate annealing is 920 ℃, the heat preservation is 120s, and H is adopted 2 Volume fraction of 35% (N) 2 +H 2 ) Atmosphere protection; cold rolling the steel coil subjected to intermediate annealing again to a finished product thickness of 0.35mm, and then performing finished product annealing coating, wherein in the finished product annealing process, the annealing temperature is 990 ℃, the heat preservation time is 50s, and H is adopted in the annealing process 2 10% by volume of (N) 2 +H 2 ) And (5) protecting the mixed gas.
By adopting the production method, the problem of scrapped rolls after cold rolling and belt breakage of high-grade non-oriented silicon steel can be saved, the direct scrapped loss is reduced, and the magnetic property P of the finished product is ensured 1.5/50 ＝2.15W/kg、B 50 =1.68t, far exceeding the national standard requirements.
Example 3
A production method for high-grade non-oriented silicon steel after strip breakage during primary cold rolling comprises the following steps: the method comprises the steps of primary cold rolling coil breakage, intermediate annealing, secondary cold rolling, finished product annealing, coating, finishing and packaging, and specifically comprises the following steps:
the raw material with the thickness of 2.20mm is obtained by adopting a conventional process (steelmaking, continuous casting, casting blank heating, hot rolling and normalized acid washing), and the weight percentage of the main alloy components is 3.2 percent of Si, 0.1 percent of Mn and 0.4 percent of Als. The cold rolling process is unable to continue production due to strip breakage, the thickness of the broken strip coil is 1.00mm, the cold rolled broken strip coil is subjected to intermediate annealing in a high-grade non-oriented silicon steel horizontal continuous annealing production line, the soaking temperature of the intermediate annealing is 900 ℃, the heat preservation is carried out for 120s, and H is adopted 2 A volume fraction of 30%N 2 And H 2 Is protected by the mixed atmosphere; cold rolling the steel coil subjected to intermediate annealing again to a finished product thickness of 0.35mm, and then performing finished product annealing coating, wherein in the finished product annealing process, the annealing temperature is 990 ℃, the heat preservation time is 30s, and H is adopted in the annealing process 2 10% by volume of N 2 And H 2 Is used for protecting the mixed gas.
By adopting the production method, the problem of scrapped rolls after cold rolling and belt breakage of high-grade non-oriented silicon steel can be saved, the direct scrapped loss is reduced, and the magnetic property P of the finished product is ensured 1.5/50 ＝2.29W/kg、B 50 =1.67T, far exceeding the national standard requirements.
Example 4
A production method for high-grade non-oriented silicon steel after strip breakage during primary cold rolling comprises the following steps: the method comprises the steps of primary cold rolling coil breakage, intermediate annealing, secondary cold rolling, finished product annealing, coating, finishing and packaging, and specifically comprises the following steps:
the raw material with the thickness of 2.20mm is obtained by adopting a conventional process (steelmaking, continuous casting, casting blank heating, hot rolling and normalized acid washing), and the weight percentage of the main alloy components is 3.2 percent of Si, 0.1 percent of Mn and 0.4 percent of Als. The cold rolling process is unable to continue production due to strip breakage, the thickness of the broken strip coil is 1.00mm, the cold rolled broken strip coil is subjected to intermediate annealing in a high-grade non-oriented silicon steel horizontal continuous annealing production line, the soaking temperature of the intermediate annealing is 920 ℃, the heat preservation is 120s, and H is adopted 2 N with volume fraction of 35% 2 And H 2 And mixed atmosphere protection; cold rolling the steel coil subjected to intermediate annealing again to a finished product thickness of 0.35mm, and then performing finished product annealing coating, wherein in the finished product annealing process, the annealing temperature is 970 ℃, the heat preservation time is 50s, and H is adopted in the annealing process 2 10% by volume of N 2 And H 2 Is used for protecting the mixed gas.
By adopting the production method, the problem of scrapped rolls after cold rolling and belt breakage of high-grade non-oriented silicon steel can be saved, the direct scrapped loss is reduced, and the magnetic property P of the finished product is ensured 1.5/50 ＝2.26W/kg、B 50 =1.68t, far exceeding the national standard requirements.
Comparative example 1
The difference from example 1 is H at the time of intermediate annealing 2 Volume fraction of 25%, and magnetic property P of the final product 1.5/50 ＝2.40W/kg、B 50 =1.62t, both core loss and magnetic induction worsen.
Comparative example 2
The difference from example 1 is that the soaking temperature in the intermediate annealing is 870 ℃ and the magnetic properties P of the finished product are 1.5/50 ＝2.51W/kg、B 50 =1.60T, both the core loss and the magnetic induction are poor (especially the magnetic induction), the magnetic induction does not meet the national standard requirement B 50 ≥1.62T。
Comparative example 3
The difference from example 2 is that the soaking temperature in the intermediate annealing is 960℃and the magnetic properties P of the finished product are 1.5/50 ＝2.31W/kg、B 50 =1.65t, but the grains are coarse due to the excessively high soaking temperature in the intermediate annealing, and breakage occurs in the secondary cold rolling.
Comparative example 4
The difference from example 1 is that the soaking time in the intermediate annealing is 80s, and the magnetic property of the finished product is the best value of P 1.5/50 ＝2.39W/kg、B 50 The iron loss and the magnetic induction are both poor, and the grains are uneven due to short soaking time in the intermediate annealing, the rolling mill vibrates during the secondary cold rolling, and the finished product magnetic property fluctuates and the stability is poor.
Comparative example 5
The difference from example 4 is that the soaking time in the intermediate annealing is 80s, and the magnetic property of the finished product is the best value of P 1.5/50 ＝2.35W/kg、B 50 The iron loss and the magnetic induction are both poor, and the grains are uneven due to short soaking time in the intermediate annealing, the rolling mill vibrates during the secondary cold rolling, and the finished product magnetic property fluctuates and the stability is poor.
Comparative example 6
The difference from example 4 is that the soaking temperature at the time of annealing of the finished product is 1020 ℃ and the magnetic property of the finished product is P 1.5/50 ＝2.32W/kg、B 50 =1.65t, both core loss and magnetic induction worsen.
Comparative example 7
As in example 4The difference is that the soaking temperature is 950 ℃ when the finished product is annealed, and the magnetic property of the finished product is P 1.5/50 ＝2.41W/kg、B 50 =1.65t, both core loss and magnetic induction worsen.
Comparative example 8
The difference from example 3 is that the soaking temperature of the intermediate annealing is 870 ℃, the soaking time of the intermediate annealing is 100s, the soaking temperature of the final annealing is 950 ℃, the soaking time of the final annealing is 50s, and the magnetic properties of the final product are P 1.5/50 ＝2.50W/kg、B 50 =1.61T, both the core loss and the magnetic induction become worse (in particular, the magnetic induction), B, the magnetic induction does not meet the national standard requirement 50 ≥1.62T。
The texture patterns and the texture patterns of the non-oriented silicon steel produced in the example 2 and the comparative example 8 are shown in fig. 1-4; 1-2, the grain of the finished non-oriented silicon steel product produced in example 1 is uniform, the average grain size reaches 110 μm, and Goss texture with certain strength and favorable magnetic performance appears; as can be seen from fig. 3 to 4, the grain size uniformity of the non-oriented silicon steel product produced in comparative example 2 was poor, the average grain size was 90 μm, and the gamma texture channels, which were disadvantageous to the magnetic properties, had not completely disappeared.
The above detailed description of a production method of high grade non-oriented silicon steel after strip breakage at one cold rolling with reference to the examples is illustrative and not restrictive, and several examples can be listed according to the defined scope, thus variations and modifications without departing from the general inventive concept shall fall within the scope of protection of the present invention.
Claims (4)
1. The production method for the high-grade non-oriented silicon steel after strip breakage during one-time cold rolling is characterized by comprising the following steps of: primary cold rolling to break coil, intermediate annealing, secondary cold rolling, finished product annealing, coating and finishing packaging;
the thickness of the primary cold rolling broken coil is 0.80-1.00 mm;
the soaking temperature of the intermediate annealing is 900-920 ℃;
the intermediate annealing adopts a continuous annealing furnace for annealing, and H is adopted in the continuous annealing furnace 2 30-35% of N by volume 2 And H 2 Is protected by the mixed gas;
the heat preservation time of the intermediate annealing is 100-120 s;
secondary cold rolling to a thickness of 0.35mm;
in the annealing step of the finished product, the annealing temperature is 970-990 ℃, the heat preservation time is 30-50 s, and H is adopted in the annealing process 2 10-15% by volume of N 2 And H 2 Is protected by the mixed gas;
the weight percentage of Si, mn, als in the high-grade non-oriented silicon steel is as follows: si is more than or equal to 3.0% and less than or equal to 3.2%, mn is more than or equal to 0.1% and less than or equal to 0.5%, als is more than or equal to 0.4% and less than or equal to 1.0%.
2. The production method according to claim 1, wherein the primary cold-rolled strip coil is obtained by steelmaking, continuous casting, casting blank heating, hot rolling, normalizing pickling, primary cold rolling, and strip breakage occurs during the primary cold rolling.
3. A high grade non-oriented silicon steel, characterized in that it is produced by the production method of claim 1 or 2.
4. The high grade non-oriented silicon steel as claimed in claim 3, wherein the high grade non-oriented silicon steel has a P 1.5/50 =2.15~2.30W/kg、B 50 =1.66~1.68T。
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210697862.9A CN115058573B (en) | 2022-06-20 | 2022-06-20 | Production method for high-grade non-oriented silicon steel after strip breakage during primary cold rolling |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210697862.9A CN115058573B (en) | 2022-06-20 | 2022-06-20 | Production method for high-grade non-oriented silicon steel after strip breakage during primary cold rolling |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN115058573A CN115058573A (en) | 2022-09-16 |
| CN115058573B true CN115058573B (en) | 2024-01-16 |
Family
ID=83202387
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202210697862.9A Active CN115058573B (en) | 2022-06-20 | 2022-06-20 | Production method for high-grade non-oriented silicon steel after strip breakage during primary cold rolling |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN115058573B (en) |
Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102418034A (en) * | 2011-12-14 | 2012-04-18 | 武汉钢铁(集团)公司 | Production method for high-grade non-oriented silicon steel |
| CN102634729A (en) * | 2012-04-01 | 2012-08-15 | 首钢总公司 | Preparation method for low-iron-loss, high-induction and high-mark non-oriented silicon steel |
| CN108823499A (en) * | 2018-07-24 | 2018-11-16 | 唐山钢铁集团有限责任公司 | A kind of cold rolled annealed unimach of thin gauge and its production method |
| CN110369500A (en) * | 2019-07-09 | 2019-10-25 | 鞍钢股份有限公司 | A kind of disconnected band control method of oriented silicon steel cold-rolled |
| CN110724808A (en) * | 2019-10-09 | 2020-01-24 | 马鞍山钢铁股份有限公司 | Method for producing electrical steel by cold rolling of 3.01 ~ 4.5.5 mm hot rolled coil |
| CN112538592A (en) * | 2020-09-17 | 2021-03-23 | 武汉钢铁有限公司 | Non-oriented silicon steel for high-speed motor with frequency of more than or equal to 10000Hz and production method |
| WO2021239057A1 (en) * | 2020-05-28 | 2021-12-02 | 宝山钢铁股份有限公司 | Thin-gauge oriented silicon steel plate having excellent manufacturability, and manufacturing method therefor |
| CN114250420A (en) * | 2021-12-30 | 2022-03-29 | 本钢板材股份有限公司 | Production method of cover type intermediate annealing high-grade non-oriented silicon steel 50BW350 |
-
2022
- 2022-06-20 CN CN202210697862.9A patent/CN115058573B/en active Active
Patent Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102418034A (en) * | 2011-12-14 | 2012-04-18 | 武汉钢铁(集团)公司 | Production method for high-grade non-oriented silicon steel |
| CN102634729A (en) * | 2012-04-01 | 2012-08-15 | 首钢总公司 | Preparation method for low-iron-loss, high-induction and high-mark non-oriented silicon steel |
| CN108823499A (en) * | 2018-07-24 | 2018-11-16 | 唐山钢铁集团有限责任公司 | A kind of cold rolled annealed unimach of thin gauge and its production method |
| CN110369500A (en) * | 2019-07-09 | 2019-10-25 | 鞍钢股份有限公司 | A kind of disconnected band control method of oriented silicon steel cold-rolled |
| CN110724808A (en) * | 2019-10-09 | 2020-01-24 | 马鞍山钢铁股份有限公司 | Method for producing electrical steel by cold rolling of 3.01 ~ 4.5.5 mm hot rolled coil |
| WO2021239057A1 (en) * | 2020-05-28 | 2021-12-02 | 宝山钢铁股份有限公司 | Thin-gauge oriented silicon steel plate having excellent manufacturability, and manufacturing method therefor |
| CN112538592A (en) * | 2020-09-17 | 2021-03-23 | 武汉钢铁有限公司 | Non-oriented silicon steel for high-speed motor with frequency of more than or equal to 10000Hz and production method |
| CN114250420A (en) * | 2021-12-30 | 2022-03-29 | 本钢板材股份有限公司 | Production method of cover type intermediate annealing high-grade non-oriented silicon steel 50BW350 |
Also Published As
| Publication number | Publication date |
|---|---|
| CN115058573A (en) | 2022-09-16 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| EP2821511B1 (en) | Manufacturing process of non-oriented silicon steel | |
| KR20170117568A (en) | A non-oriented electrical steel sheet having a high magnetic flux density and a low iron loss with good surface condition and a method for manufacturing the same | |
| CN102747291B (en) | High-frequency low-iron-loss excellent-magnetic-property non-orientated silicon steel strip and production method thereof | |
| US20130224064A1 (en) | Non-oriented electrical steel plate without corrugated fault and production method thereof | |
| CN109609734B (en) | Preparation method of cold-rolled non-oriented silicon steel | |
| EP3719160B1 (en) | Non-oriented electrical steel sheet with excellent magnetism and manufacturing method therefor | |
| WO2021027797A1 (en) | High-magnetic-induction oriented silicon steel and manufacturing mathod therefor | |
| CN107964631B (en) | Non-oriented silicon steel with yield strength of more than or equal to 500MPa for high-speed motor rotor and production method | |
| WO2014027452A1 (en) | Method for manufacturing non-oriented electromagnetic steel sheet | |
| CN109822070B (en) | Non-oriented electrical steel for electric driving of thin slab full-endless rolling and preparation method thereof | |
| CN112030059B (en) | Short-process production method of non-oriented silicon steel | |
| CN105238996A (en) | Cold-rolled thin strip non-oriented silicon steel with thickness of 0.2 and production method thereof | |
| CN114891978B (en) | Production method for high-grade non-oriented silicon steel after primary cold rolling strip breakage | |
| CN112143964A (en) | Non-oriented electrical steel plate with extremely low iron loss and continuous annealing process thereof | |
| CN115058573B (en) | Production method for high-grade non-oriented silicon steel after strip breakage during primary cold rolling | |
| CN110640104B (en) | Non-oriented electrical steel plate with excellent magnetic property and manufacturing method thereof | |
| JP2003096548A (en) | Non-oriented silicon steel sheet, and production method therefor | |
| JP5920387B2 (en) | Method for producing grain-oriented electrical steel sheet | |
| CN110643891B (en) | Non-oriented electrical steel plate with excellent magnetic property and manufacturing method thereof | |
| CN113846265B (en) | Non-oriented silicon steel suitable for cold continuous rolling and used for high-efficiency variable frequency compressor and production method | |
| CN114737129B (en) | High-performance non-oriented silicon steel for wound motor iron core and production method thereof | |
| CN114293100A (en) | Ultra-low iron loss non-oriented silicon steel thin strip and preparation method thereof | |
| CN113897543A (en) | Non-oriented electrical steel and method of manufacture | |
| CN112921164B (en) | Low-iron-loss high-permeability non-oriented electrical steel and production method thereof | |
| KR100321035B1 (en) | Method for manufacturing non-oriented electrical steel sheet with superior magnetic properties after heat treatment |
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 |