CN109609734B - Preparation method of cold-rolled non-oriented silicon steel - Google Patents

Preparation method of cold-rolled non-oriented silicon steel Download PDF

Info

Publication number
CN109609734B
CN109609734B CN201910012540.4A CN201910012540A CN109609734B CN 109609734 B CN109609734 B CN 109609734B CN 201910012540 A CN201910012540 A CN 201910012540A CN 109609734 B CN109609734 B CN 109609734B
Authority
CN
China
Prior art keywords
cold
als
oriented silicon
silicon steel
percent
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
Application number
CN201910012540.4A
Other languages
Chinese (zh)
Other versions
CN109609734A (en
Inventor
李准
陈圣林
万政武
王雄奎
杨朝
程迪夫
杨光
吕黎
詹东方
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Wuhan Iron and Steel Co Ltd
Original Assignee
Wuhan Iron and Steel Co Ltd
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Wuhan Iron and Steel Co Ltd filed Critical Wuhan Iron and Steel Co Ltd
Priority to CN201910012540.4A priority Critical patent/CN109609734B/en
Publication of CN109609734A publication Critical patent/CN109609734A/en
Application granted granted Critical
Publication of CN109609734B publication Critical patent/CN109609734B/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

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
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium

Abstract

A preparation method of cold-rolled non-oriented silicon steel comprises the following steps: 1) smelting and continuous casting to form a plate blank: the composition and weight percentage content of the alloy are less than or equal to 0.0030 percent of C, 2.90 to 3.50 percent of Si, 0.15 to 0.30 percent of Mn, 0.80 to 1.5 percent of Als, less than or equal to 0.008 percent of P, less than or equal to 0.0020 percent of S, less than or equal to 0.0025 percent of N, less than or equal to 0.0020 percent of Ti, less than or equal to 0.0020 percent of Nb, and less than or equal to 0.0020 percent of V; 2) heating a casting blank; 3) hot rolling; 4) coiling; 5) normalizing; 6) cold rolling; 7) annealing: the temperature raising rate v satisfies 20+2.15 × (W)Si+WAls)≤v≤80‑3.85×(WSi+WAls). The invention can obtain the iron loss P1.5/50Less than or equal to 2.40W/kg, magnetic induction B50The high-grade cold-rolled non-oriented silicon steel is not less than 1.68T and has the thickness of 0.50 mm.

Description

Preparation method of cold-rolled non-oriented silicon steel
Technical Field
The invention relates to the technical field of preparation of non-oriented silicon steel, in particular to a preparation method of high-grade cold-rolled non-oriented silicon steel with the thickness of 0.50 mm.
Background
Non-oriented silicon steel has long been used as a material for an iron core of a rotating electrical machine due to its excellent magnetic properties. With the continuous improvement of the requirements on energy conservation and environmental protection, further improving the magnetic performance of the non-oriented silicon steel becomes an important problem for users and manufacturers.
The magnetic performance index of the cold-rolled non-oriented silicon steel mainly has magnetic induction and iron loss, and for the cold-rolled non-oriented silicon steel with the thickness of 0.50mm, the iron loss P is used1.5/50And magnetic induction B50Two metrics measure its performance. Iron loss P of current 0.50mm thick medium-high grade cold-rolled non-oriented silicon steel product1.5/50Has been reduced to 2.30-2.40W/kg or even lower, but has magnetic induction B50The magnetic induction can only reach 1.62-1.66T, and further improvement of the magnetic induction is difficult, which is one of the problems to be solved.
At present, the method for improving the magnetic property of the cold-rolled non-oriented silicon steel product is to reduce the iron loss P by changing the grain orientation in the finished product1.5/50And increasing the magnetic induction B by controlling the proportion of the favorable surface texture of the finished product50. For example, in the literature, "the influence of the rapid heating process on the texture and the magnetic performance of the high-magnetic-induction oriented silicon steel, which is reported by the institute of the occupational technology of Wuhan engineering, 2009, Vol.21No.1", the influence of the rapid heating on the magnetic performance of a product is researched through the rapid heating treatment before the decarburization annealing of the high-magnetic-induction oriented silicon steel cold rolled sheet, and the result shows that the rapid heating before the decarburization annealing has little influence on the average grain size of primary recrystallization, but has influence on the texture of the primary recrystallization. After rapid heating treatment, the {110} crystal grain size in the sample is reduced, the number is increased, the accuracy of secondary recrystallization overall orientation is favorably improved, and the magnetic induction is effectively improved. As shown in the document "fast heating process research of steel strip, proceedings of Wuhan institute of engineering and occupational technology academy, 2010, Vol.22No. 2", an induction fast heating device is used to perform a fast heating experiment on a steel strip with a thickness of 0.3-0.7 mm, and the result shows that in the temperature rise stage, the average temperature rise speed of the steel strip can reach more than 100 ℃/s, so that the fast heating effect is achieved. Further, as the chinese patent application with application No. 201711430630.2, it discloses an induction heating nitriding method of oriented silicon steel, which comprises the processes of smelting, continuous casting, heating and hot rolling, normalizing, cold rolling and decarburization of a casting blank; two-stage nitriding in an induction nitriding furnaceIn the dry type N2Cooling to room temperature in the atmosphere, coating a separant, and carrying out high-temperature purification annealing for later use. The nitride obtained by the method is more and uniform, the depth of a infiltrated layer can reach the central part of the thickness of the steel plate, AlN particles at the central part of the thickness of the steel plate are 1-1.5 per square micron, and the magnetic property is stable; meanwhile, the consumption of ammonia gas is reduced by not less than 40%, and the method is simple and convenient to operate, easy to implement and easy for large-scale production. Further, as shown in the literature "Park J.T., effective of heating rate on the Development of inorganic electronic devices, ISIJ International, Vol.43(2003), No.10, pp.1611-1614", it is shown that rapid temperature rise at a rate of more than 10 ℃/s increases the Texture components and improves the magnetic properties.
Disclosure of Invention
In order to solve the above problems, an object of the present invention is to provide a method for manufacturing cold-rolled non-oriented silicon steel capable of obtaining iron loss P1.5/50Less than or equal to 2.40W/kg, magnetic induction B50The high-grade cold-rolled non-oriented silicon steel is not less than 1.68T and has the thickness of 0.50 mm.
In order to achieve the purpose, the preparation method of the cold-rolled non-oriented silicon steel comprises the following steps:
1) smelting and continuous casting into plate blank
The cold-rolled non-oriented silicon steel comprises, by weight, not more than 0.0030% of C, 2.90-3.50% of Si, 0.15-0.30% of Mn, 0.80-1.5% of Als, not more than 0.008% of P, not more than 0.0020% of S, not more than 0.0025% of N, not more than 0.0020% of Ti, not more than 0.0020% of Nb, not more than 0.0020% of V, and the balance of Fe and other unavoidable residual elements;
2) heating of casting blanks
Heating the casting blank to 1050-1150 ℃, and keeping the temperature for 60-180 minutes;
3) hot rolling
Controlling the finishing temperature to be 800-900 ℃;
4) coiling
Controlling the coiling temperature to be more than or equal to 600 ℃, feeding the coiled steel coil into a heat preservation pit, and slowly cooling;
5) normalizing
Normalizing at 880-940 ℃ for 50-140 seconds, and then carrying out conventional pickling on the steel strip;
6) cold rolling
Rolling the steel strip to the thickness of 0.50 mm;
7) annealing
The temperature rise speed v of the steel strip in the annealing process meets the formula (1);
20+2.15×(WSi+WAls)≤v≤80-3.85×(WSi+WAls) Formula (1)
In the formula (1), v is the temperature rise speed of the steel strip in the annealing process, and the unit ℃/s;
WSiis the Si content in the component, the unit is wt%;
WAlsis the Als content in the component, unit% wt.
Compared with the prior art, the preparation method of the cold-rolled non-oriented silicon steel firstly improves the chemical components of the steel grade. The relationship between the chemical components of the cold-rolled non-oriented silicon steel of the present invention and the properties of the cold-rolled non-oriented silicon steel will be described in detail below.
The C element is a harmful element, and when the content of the element is too high, the gamma phase region can be enlarged to reduce the phase transition temperature, and when the content is too high, the C is also removed in the annealing process, and the crystal grain growth is inhibited, so that the content is required to be less than or equal to 0.0030 percent.
The S element is a harmful element and can form MnS inclusion with Mn, which can seriously hinder the growth of crystal grains and further deteriorate the magnetic property, and the content of the S element is required to be less than or equal to 0.0020 percent.
N is a harmful element, can form AlN with Al when the content is too high, can seriously hinder the grain growth, and can easily form an inner nitriding layer in the annealing process to deteriorate the magnetic property of a finished product, and the content is required to be less than or equal to 0.0025 percent.
When the contents of Si and Als elements in steel grades are high and the content of carbon element is low, the brittleness of the steel strip can be greatly increased due to the over-high content of phosphorus element, the production difficulty is brought, and the content requirement is less than or equal to 0.008 percent.
Ti, V and Nb are harmful elements, and are easy to form Ti (N, C), V (N, C) and Nb (N, C) with C, N, so that the growth of crystal grains is strongly prevented, and the iron loss is seriously deteriorated, therefore, Ti, Nb and V are respectively controlled to be less than or equal to 0.0020 percent.
Si element, which is an effective element for reducing iron loss, can increase resistivity and reduce iron loss; too high Si content will cause the strip to become brittle and thus cause great difficulty in cold working, especially when the finished strip is thin; but the Si content is too low, the iron loss reduction degree is weakened, the invention is mainly applied to the production of high-grade non-oriented electrical steel, and has certain requirements on the iron loss of finished products, so that the Si content is controlled to be 2.90-3.50%.
Als element, similar to Si, increases resistivity, reduces iron loss, increases (100) component and reduces (111) component, and improves magnetic value; however, when the content of Als is too high, the tundish is easy to block, the surface of the casting blank is easy to scar, and further the surface defects of the finished steel strip product are increased, especially when the thickness of the finished steel strip product is thinner, so that the content of Als is controlled to be 0.80-1.5%.
Mn element, which improves hot rolling plasticity and hot rolled plate structure to promote the strengthening of (100) and (110) components, and (111) component weakening to improve magnetic performance; however, Mn expands a gamma phase region, and reduces the annealing temperature of a finished product, so that the growth of crystal grains is not facilitated, and further the iron loss is influenced. Therefore, the Mn content should be controlled to 0.15% -0.30%.
Next, the present invention optimizes the process for producing cold-rolled non-oriented silicon steel, and the following steps will be described in detail.
The heating temperature of the casting blank is controlled to be 1050-1150 ℃, because when the heating temperature is lower than 1050 ℃, the temperature of the steel blank is low, the load of a rolling mill is overlarge during hot rolling, the reduction is difficult, equipment is easy to damage, and the production difficulty is increased; when the heating temperature is higher than 1150 ℃, AlN, MnS, etc. in the slab are precipitated and dissolved, and then fine inclusions are precipitated at the time of hot rolling, thereby suppressing grain growth at the time of post-process annealing, and further deteriorating magnetic properties.
Keeping the temperature of the normalizing temperature at 880-940 ℃ for 50-140 seconds to ensure that the hot rolled plate is recrystallized and the crystal grains are uniform; meanwhile, the texture (100) and texture (110) components are increased, and the magnetism of the product is improved. The melting is frequent at a temperature lower than 880 ℃, and because the temperature is lower, crystal grains are fine and are not easy to grow, so that the final product performance is not good; when the temperature is higher than 940 ℃, the grain size is relatively large, the brittleness of the steel plate during cold rolling is increased, the cold rolling property is not favorable, and the cost is increased.
In the annealing process, the reason why the temperature rise speed v is limited to meet the requirement of the formula (1) in the invention is that the mark of the non-oriented silicon steel has a larger relationship with Si and Als elements, the content of the Si and Als elements is increased along with the increase of the non-oriented mark, the increase of the content of the elements can cause the change of the optimal grain size in a finished product, and the two elements have larger influence on the magnetic performance of the finished product, so the invention has great experiment bases on the temperature rise speeds v and (W) in the annealing processSi+WAls) The contents were fitted to obtain formula (1).
Preferably, the cold-rolled non-oriented silicon steel comprises, by weight, not more than 0.0030% of C, 3.1-3.23% of Si, 0.18-0.27% of Mn, 0.81-0.83% of Als, not more than 0.008% of P, not more than 0.0020% of S, not more than 0.0025% of N, not more than 0.0020% of Ti, not more than 0.0020% of Nb, not more than 0.0020% of V, and the balance Fe and other unavoidable residual elements.
The invention has the advantages that: compared with the prior art, the method improves the magnetic performance of the cold-rolled non-oriented silicon steel by controlling 2.90-3.50% of Si, 0.15-0.30% of Mn and 0.80-1.5% of Als in the cold-rolled non-oriented silicon steel and limiting the temperature rise in the annealing process to meet the requirement of a formula (1) to improve the favorable texture coefficient ratio Tp (defined as the formula (2) in the invention).
Detailed Description
For a better understanding of the present invention, reference will now be made in detail to the present invention, which is illustrated in the accompanying drawings.
In order to solve the problem of poor magnetic performance of the existing 0.50mm thick high-grade cold-rolled non-oriented silicon steel product, the invention provides a preparation method of cold-rolled non-oriented silicon steel, and particularly, the invention improves the magnetic performance of the cold-rolled non-oriented silicon steel by improving the favorable texture coefficient ratio Tp by optimizing the chemical components and the process of the cold-rolled non-oriented silicon steel, and more particularly, the invention controls 2.90-3.50% of Si, 0.15-0.30% of Mn and 0.80-1.5% of Als in the cold-rolled non-oriented silicon steel, and limits the temperature rise in the annealing process to meet the formula (1). Hereinafter, preferred embodiments of the method for manufacturing cold rolled non-oriented silicon steel according to the present invention will be described in detail with reference to specific examples.
Examples 1 to 6
A preparation method of cold-rolled non-oriented silicon steel comprises the following steps:
1) smelting and continuous casting into plate blank
The cold-rolled non-oriented silicon steel comprises, by weight, not more than 0.0030% of C, 2.90-3.50% of Si, 0.15-0.30% of Mn, 0.80-1.5% of Als, not more than 0.008% of P, not more than 0.0020% of S, not more than 0.0025% of N, not more than 0.0020% of Ti, not more than 0.0020% of Nb, not more than 0.0020% of V, and the balance of Fe and other unavoidable residual elements;
2) heating of casting blanks
Heating the casting blank to 1050-1150 ℃, and keeping the temperature for 60-180 minutes;
3) hot rolling
Controlling the finishing temperature to be 800-900 ℃;
4) coiling
Controlling the coiling temperature to be more than or equal to 600 ℃, feeding the coiled steel coil into a heat preservation pit, and slowly cooling;
5) normalizing
Normalizing at 880-940 ℃ for 50-140 seconds, and then carrying out conventional pickling on the steel strip;
6) cold rolling
Rolling the steel strip to the thickness of 0.50 mm;
7) annealing
The temperature-rising speed v in the annealing process meets the formula (1);
20+2.15×(WSi+WAls)≤v≤80-3.85×(WSi+WAls) Formula (1)
In the formula (3), v is the temperature rise speed of the steel strip in the annealing process, and the unit ℃/s;
WSiis the Si content in the component, the unit is wt%;
WAlsis the Als content in the component, unit% wt.
Table 1 shows the value lists of the components of examples 1 to 6 and comparative examples 1 to 3 of the present invention
TABLE 1
Figure BDA0001937881020000061
Figure BDA0001937881020000071
Table 2 shows the main process parameters of the inventive and comparative examples
TABLE 2
Figure BDA0001937881020000072
TABLE 3 Properties of Cold-rolled non-oriented silicon Steel obtained in examples of the present invention and comparative examples
TABLE 3
Figure BDA0001937881020000073
Figure BDA0001937881020000081
The explanations in table 3 regarding equations (2) and (3) are as follows:
Figure BDA0001937881020000082
Tp＝-63.39+0.041×v+6.31×P1.5/50+28.61×B50formula (3)
The formula (2) is the definition of the texture coefficient which is beneficial to the magnetic property, the ratio of the sum of the density values of the texture components which are beneficial to the magnetic property in the inverse pole figure to the sum of the density values of the texture components which are not beneficial to the magnetic property in the inverse pole figure is selected, and the ratio is used for measuring the proportion of the texture components; the formula (3) is the favorable texture coefficient Tp defined in the formula (2) and the temperature rise speed and the finished product iron loss P in the annealing process1.5/50And magnetic induction B50The favorable texture coefficient Tp has close relation with the magnetic value, the finished product has excellent magnetic property when the favorable texture proportion in the finished product is higher, and the favorable texture coefficient in the finished product can be quickly calculated by using the formula (3)And a large amount of detection work is saved.
It can be seen from table 3 that, in comparative examples 1 to 3, when the heating speed of the steel strip in the annealing process of the finished product does not meet the requirement of the formula (1), the texture coefficient is favorably low, and the magnetism of the finished product is poor. The reason is that because the temperature rise speed is slow in the annealing process, crystal grains are fully recovered and recrystallized, the size of the crystal grains is large, and the magnetic performance of a finished product is deteriorated; when the heating speed in the annealing process of the steel strip is higher than the speed of the formula (1), the crystal grains cannot recover and grow up in time due to the overhigh heating speed of the steel strip, the proportion of components such as favorable textures (100) and (110) in a finished product is reduced, the favorable texture coefficient Tp is lower, and the magnetic performance is deteriorated. In the annealing process in the embodiments 1-6, the final magnetic property of the sample is better by adopting the formula (1) in the invention, and the iron loss P of the finished product in the embodiments1.5/50Less than or equal to 2.40W/kg, magnetic induction B50Not less than 1.68T; the actual measured Tp value is close to the theoretical calculated Tp value, the trend is the same, and when the heating speed of the steel strip in the annealing process meets the formula (1) of the invention, the Tp value and the magnetic property P in the finished product1.5/50And B50Preferably, in the comparative example, the heating rate of the steel strip does not satisfy the requirements of the present invention, the properties are deteriorated, and since the annealing rate is not out of the range of the present invention, the calculation of Tp value has been largely deviated.
The above-mentioned embodiments only express several embodiments of the present invention, and the description thereof is more specific and detailed, but not construed as limiting the scope of the present invention. It should be noted that, for a person skilled in the art, several variations and modifications can be made without departing from the inventive concept, which falls within the scope of the present invention. Therefore, the protection scope of the present patent shall be subject to the appended claims.

Claims (1)

1. A preparation method of cold-rolled non-oriented silicon steel is characterized by comprising the following steps:
1) smelting and continuous casting into plate blank
The cold-rolled non-oriented silicon steel comprises, by weight, not more than 0.0030% of C, 3.1-3.23% of Si, 0.18-0.27% of Mn, 0.81-0.83% of Als, not more than 0.008% of P, not more than 0.0020% of S, not more than 0.0025% of N, not more than 0.0020% of Ti, not more than 0.0020% of Nb, not more than 0.0020% of V, and the balance of Fe and other unavoidable residual elements;
2) heating of casting blanks
Heating the casting blank to 1050-1150 ℃, and keeping the temperature for 60-160 minutes;
3) hot rolling
Controlling the finishing temperature to be 800-900 ℃;
4) coiling
Controlling the coiling temperature to be more than or equal to 600 ℃, feeding the coiled steel coil into a heat preservation pit, and slowly cooling;
5) normalizing
Normalizing at 880-940 ℃ for 50-140 seconds, and then carrying out conventional pickling on the steel coil;
6) cold rolling
Rolling the steel strip to the thickness of 0.50 mm;
7) annealing
The temperature-rising speed v in the annealing process meets the formula (1);
20+2.15×(WSi+WAls)≤v≤80-3.85×(WSi+WAls) In the formula (1) and the formula (1), v is the temperature rise speed of the steel strip in the annealing process, and the unit ℃/s;
WSiis the Si content in the component, the unit is wt%;
WAlsis the Als content in the component, unit% wt.
CN201910012540.4A 2019-01-07 2019-01-07 Preparation method of cold-rolled non-oriented silicon steel Active CN109609734B (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
CN201910012540.4A CN109609734B (en) 2019-01-07 2019-01-07 Preparation method of cold-rolled non-oriented silicon steel

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
CN201910012540.4A CN109609734B (en) 2019-01-07 2019-01-07 Preparation method of cold-rolled non-oriented silicon steel

Publications (2)

Publication Number Publication Date
CN109609734A CN109609734A (en) 2019-04-12
CN109609734B true CN109609734B (en) 2020-11-03

Family

ID=66015644

Family Applications (1)

Application Number Title Priority Date Filing Date
CN201910012540.4A Active CN109609734B (en) 2019-01-07 2019-01-07 Preparation method of cold-rolled non-oriented silicon steel

Country Status (1)

Country Link
CN (1) CN109609734B (en)

Families Citing this family (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN110241362B (en) * 2019-07-09 2021-05-28 鞍钢股份有限公司 Non-oriented silicon steel for driving motor and production method thereof
CN110616370A (en) * 2019-08-30 2019-12-27 武汉钢铁有限公司 Production method of cold-rolled non-oriented silicon steel with excellent iron loss performance under low field
CN110629120B (en) * 2019-10-31 2021-04-30 武汉钢铁有限公司 Cold-rolled non-oriented silicon steel with excellent magnetic property and production method thereof
CN112176250B (en) * 2020-09-19 2021-11-26 张家港扬子江冷轧板有限公司 Non-oriented silicon steel for high-speed drive motor and manufacturing method thereof
CN113403455B (en) * 2021-06-17 2024-03-19 张家港扬子江冷轧板有限公司 Production method of unoriented silicon steel
CN114045433B (en) * 2021-11-10 2022-10-21 张家港扬子江冷轧板有限公司 Ultra-low iron loss non-oriented silicon steel and production method thereof
CN115255707A (en) * 2022-08-09 2022-11-01 首钢智新迁安电磁材料有限公司 Processing method of non-oriented electrical steel stator core

Family Cites Families (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN100418697C (en) * 2006-05-18 2008-09-17 武汉科技大学 High magentic induction oriented electrical steel sheet and its manufacturing method
CN105238996A (en) * 2015-11-20 2016-01-13 武汉钢铁(集团)公司 Cold-rolled thin strip non-oriented silicon steel with thickness of 0.2 and production method thereof

Also Published As

Publication number Publication date
CN109609734A (en) 2019-04-12

Similar Documents

Publication Publication Date Title
CN109609734B (en) Preparation method of cold-rolled non-oriented silicon steel
CN102453837B (en) Method for preparing non-oriented silicon steel with high magnetic induction
JP5675950B2 (en) Method for producing highly efficient non-oriented silicon steel with excellent magnetic properties
CN102925793B (en) Non-oriented electrical steel with magnetic induction greater than or equal to 1.8 T and production method thereof
RU2723121C1 (en) Non-oriented electrical steel with excellent magnetic properties and method of production thereof
CN106702260B (en) A kind of high-magnetic induction, low-iron loss non-orientation silicon steel and its production method
CN103361544B (en) Non orientating silicon steel and manufacture method thereof
CN103695791B (en) A kind of high magnetic induction grain-oriented silicon steel and production method
CN104404396B (en) High-magnetic-strength no-orientation silicon steel free from normalizing and production method of sheet billets
CN103014503B (en) Normalization-free high-magnetic induction low-iron loss acid etching-resistant non-oriented silicon steel and production method thereof
CN103667879A (en) Non-oriented electrical sheet with superior magnetic and mechanical properties, and production method of non-oriented electrical sheet
KR20150043504A (en) Manufacturing method of common grain-oriented silicon steel with high magnetic induction
CN105886932B (en) A kind of High Power Factor Non-oriented silicon steel for motors and production method
CN103305748A (en) Non-oriented electrical steel plate and manufacturing method thereof
CN105238996A (en) Cold-rolled thin strip non-oriented silicon steel with thickness of 0.2 and production method thereof
CN104152800A (en) Low-magnetic-anisotropy non-oriented silicon steel plate and preparation technology thereof
CN109055861A (en) A kind of low-iron loss high-magnetic strength orientation silicon steel thin belt and preparation method thereof
KR100779579B1 (en) Manufacturing method for non-oriented electrical steel sheet having low core loss and high magnetic flux density
CN112430780B (en) Cu-containing high-cleanliness non-oriented electrical steel plate and manufacturing method thereof
CN111270123A (en) Method for optimizing electromagnetic performance of non-oriented silicon steel and non-oriented silicon steel
CN110640104B (en) Non-oriented electrical steel plate with excellent magnetic property and manufacturing method thereof
JP5920387B2 (en) Method for producing grain-oriented electrical steel sheet
CN111663081B (en) Niobium-containing oriented silicon steel adopting low-temperature heating plate blank and production method
CN112143866A (en) Non-oriented silicon steel plate for servo motor and production method thereof
CN109825760A (en) A kind of boracic non-oriented electrical steel and its production method of endless rolling

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