CN109609734A - A kind of preparation method of cold rolling non-orientation silicon steel - Google Patents

A kind of preparation method of cold rolling non-orientation silicon steel Download PDF

Info

Publication number
CN109609734A
CN109609734A CN201910012540.4A CN201910012540A CN109609734A CN 109609734 A CN109609734 A CN 109609734A CN 201910012540 A CN201910012540 A CN 201910012540A CN 109609734 A CN109609734 A CN 109609734A
Authority
CN
China
Prior art keywords
cold rolling
als
silicon steel
orientation silicon
rolling 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.)
Granted
Application number
CN201910012540.4A
Other languages
Chinese (zh)
Other versions
CN109609734B (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

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Electromagnetism (AREA)
  • Manufacturing & Machinery (AREA)
  • Soft Magnetic Materials (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)

Abstract

A kind of preparation method of cold rolling non-orientation silicon steel, comprising steps of 1) smelt and be casting continuously to form slab: it is at being grouped as and weight percent content, C≤0.0030%, Si2.90%~3.50%, Mn0.15%~0.30%, Als0.80%~1.5%, P≤0.008%, S≤0.0020%, N≤0.0025%, Ti≤0.0020%, Nb≤0.0020%, V≤0.0020%；2) slab heats；3) hot rolling；4) it batches；5) normalizing；6) cold rolling；7) anneal: heating rate v meets 20+2.15 × (WSi+WAls)≤v≤80‑3.85×(WSi+WAls).The present invention can obtain iron loss P1.5/50≤ 2.40W/kg, magnetic strength B50>=1.68T, with a thickness of the cold rolling non-orientation silicon steel of the 0.50mm high trade mark.

Description

A kind of preparation method of cold rolling non-orientation silicon steel
Technical field
The present invention relates to the preparation technical fields of non-orientation silicon steel more particularly to a kind of with a thickness of the cold of the 0.50mm high trade mark Roll the preparation method of non-orientation silicon steel.
Background technique
Non-orientation silicon steel is used as always rotary motor iron core material because of its excellent magnetic property for a long time.With energy conservation The continuous improvement of environmental requirement, what the magnetic property for further increasing non-orientation silicon steel became that user and production firm face important asks Topic.
Measuring cold rolling non-orientation silicon steel magnetic property index mainly has magnetic strength and iron loss, for the cold rolling non-orientation silicon of 0.50mm Steel, with iron loss P1.5/50With magnetic strength B50Two indices measure its performance.High grade cold rolling non-oriented silicon steel in 0.50mm thickness at present Product iron loss P1.5/50It is even lower to have already decreased to 2.30~2.40W/kg, but magnetic strength B50It is only capable of reaching 1.62~1.66T, then It is relatively difficult to further increase magnetic strength, this also becomes one of problem to be solved.
Currently, the method for improving the magnetic property of cold rolling non-orientation silicon steel product is by changing in finished product crystal grain position to reduction Iron loss P1.5/50And the ratio by controlling the advantageous plane texture of finished product improves magnetic strength B50.As " rapid heating process is to high magnetic for document Feel the influence of orientation silicon steel texture and magnetic property, Wuhan Engineering Vocational College journal, 2009, in Vol.21No.1 ", pass through The quick heat treatment research before decarburizing annealing is carried out to high magnetic induction grain-oriented silicon steel cold rolled sheet quickly to heat to product magnetic property Influence, the results showed that the quick heating before decarburizing annealing primary recrystallization average grain size is influenced it is little, but to for the first time again Crystallization texture has an impact.Quickly after heat treatment, { 110 } crystallite dimension in sample reduces, and quantity increases, and is conducive to raising two The accuracy of secondary recrystallization overall orientation, effectively improves magnetic strength.For another example document " study, Wuhan work by the rapid heating process of steel band Journey Vocationl Technical College journal, 2010, in Vol.22No.2 ", by using induction rapid-heating device to 0.3~0.7mm thickness Steel band has carried out quick Heating Experiment, the results showed that and temperature rise period, steel band average heating speed can achieve 100 DEG C/s or more, Quick heating is achieved the effect that.For another example application No. is 201711430630.2 Chinese invention patent application, it discloses one The induction heating nitriding method of kind orientation silicon steel by smelting, heats simultaneously hot rolling, normalizing, cold rolling to slab after continuous casting and takes off Carbon process；Two-part nitriding is carried out in induction nitriding furnace, in dry type N2It is cooled to room temperature under atmosphere, separant coating, high temperature are net It is stand-by after annealing.The nitride that the invention obtains is more and uniform, and depth of penetration can arrive steel plate thickness centre, steel plate thickness Centre AlN particle reaches 1~1.5 on every square micron, and magnetic property is stablized；Ammonia consumption reduction simultaneously is not less than 40%, and it is easy to operate, it is easy to implement, it is easy to be mass produced.For another example document " Park J.T., Effect of Heating Rate on the Development of Annealing Texture in Nonoriented Electrical Steels, ISIJ International, Vol.43 (2003), studies have shown that being greater than 10 in No.10, pp.1611~1614 " DEG C/s speed heats up favorable texture component can be improved fastly, improve magnetic property.
Summary of the invention
In order to solve the above problem, the object of the present invention is to provide a kind of preparation methods of cold rolling non-orientation silicon steel, can obtain To iron loss P1.5/50≤ 2.40W/kg, magnetic strength B50>=1.68T, with a thickness of the cold rolling non-orientation silicon steel of the 0.50mm high trade mark.
To achieve the above object, the preparation method of the cold rolling non-orientation silicon steel designed by the present invention, comprising steps of
1) it smelts and is casting continuously to form slab
Cold rolling non-orientation silicon steel at being grouped as and weight percent content is, C≤0.0030%, Si:2.90%~ 3.50%, Mn:0.15%~0.30%, Als:0.80%~1.5%, P≤0.008%, S≤0.0020%, N≤ 0.0025%, Ti≤0.0020%, Nb≤0.0020%, V≤0.0020%, remaining is Fe and other inevitable remaining members Element；
2) slab heats
Slab is heated to 1050~1150 DEG C, soaking time is 60~180 minutes；
3) hot rolling
Finishing temperature is controlled at 800~900 DEG C；
4) it batches
Coiling temperature >=600 DEG C are controlled, the coil of strip after batching enters holding pit, slow cooling；
5) normalizing
Normalizing temperature is 880~940 DEG C, and the normalizing time is 50~140 seconds, and then steel band carries out conventional pickling；
6) cold rolling
It is 0.50mm that steel band, which is rolled to finished product thickness,；
7) it anneals
The heating rate v of steel band meets formula (1) in annealing process；
20+2.15×(WSi+WAls)≤v≤80-3.85×(WSi+WAls) formula (1)
In formula (1), v is steel band heating rate in annealing process, unit DEG C/s；
WSiFor Si content in ingredient, unit %wt；
WAlsFor Als content in ingredient, unit %wt.
Compared with prior art, in the preparation method of cold rolling non-orientation silicon steel of the invention first to steel grade chemical component into Row improves.Cold rolling non-orientation silicon steel chemical component of the present invention be will be explained in detail below to the relationship of cold rolling non-orientation silicon steel performance.
C element is harmful element, and can expand γ phase region when the constituent content is excessively high reduces phase transition temperature, when too high levels C is also taken off in annealing operation, while crystal grain being hindered to grow up, therefore it is required that its content≤0.0030%.
S element is harmful element, can form MnS with Mn and be mingled with, seriously crystal grain can be hindered to grow up, and then deteriorate magnetic property, It is required that its content≤0.0020%.
N element is harmful element, and whens too high levels can form AlN with Al element, seriously crystal grain can be hindered to grow up, while Nitration case in also easily being formed in annealing process, deteriorates finished product magnetic property, it is desirable that its content≤0.0025%.
P element, when steel grade Si, Als constituent content are high and carbon element content is lower, phosphorus element content is excessively high to increase greatly The brittleness for adding steel band brings difficulty, content requirement≤0.008% to production.
Ti, V, Nb element are harmful element, easily form Ti (N, C), V (N, C) and Nb (N, C) with C, N, strongly prevention crystal grain It grows up, iron loss is deteriorated seriously, therefore control Ti, Nb, V difference≤0.0020%.
Si element, is the effective element for reducing iron loss, it can increase resistivity, reduce iron loss；Si too high levels will be led It causes steel band to become fragile and then very big difficulty can be brought to cold working, especially when finished steel sheet thinner thickness；But Si content is too low, Iron loss reduces degree and weakens, and present invention is mainly applied to high grade non-oriented electrical steel productions, have certain want to finished product iron loss It asks, therefore and controls Si content 2.90%~3.50%.
Als element, it is similar to Si effect, improve resistivity, reduce iron loss, while can also make (100) component increase and (111) component reduces, and improves magnetic values；But it is wrapped in easily being blocked when Als too high levels, casting billet surface also easily scabs, and then causes Finished steel sheet surface defect increases, especially finished steel sheet thinner thickness when, therefore control Als content 0.80%~1.5%.
Mn element, improves hot rolling plasticity and hot rolled plate tissue promotes (100) and (110) component to reinforce, and (111) component subtracts It is weak, improve magnetic property；But Mn expands γ phase region, and reduction finished products temperature is unfavorable for crystal grain and grows up, and then influences iron loss.Cause This, Mn content should control 0.15%~0.30%.
Secondly, the present invention optimizes the preparation process of cold rolling non-orientation silicon steel, each step is carried out specifically below It is bright.
Slab heating temperature is controlled at 1050~1150 DEG C, is when being lower than 1050 DEG C due to heating temperature, steel billet temperature is low, In hot rolling, mill load is excessive, and pressure is difficult, and equipment easy to damage causes production difficulty to increase；If heating temperature is higher than 1150 DEG C, the precipitations such as AlN, MnS in slab can be made to be dissolved, tiny field trash is then precipitated in hot rolling, process is annealed after inhibition When crystal grain grow up, and then deteriorate magnetic.
Normalizing temperature keeps the temperature 50~140 seconds at 880~940 DEG C, makes hot rolled plate completion recrystallization and crystal grain is uniform；Have simultaneously Sharp texture (100), (110) component increase, and it is magnetic to improve product.It is being lower than 880 DEG C of when normalizing, since temperature is lower, crystal grain It is tiny to be not easy to grow up, it is unfavorable to final finished；When temperature is higher than 940 DEG C, crystallite dimension is relatively large, and steel plate is crisp when cold rolling Property become larger, be unfavorable for cold rolling and lead to plate, and increased costs.
In annealing operation, why the present invention limits the reason of heating rate v meets the requirement of formula (1) as No yield point The silicon steel trade mark and Si and Als member are known as larger relationship, and the content with the raising Si and Als element of the No yield point trade mark also increases, And the increase of the constituent content will lead to optimum grain size in finished product and change therewith, both elements influence finished product magnetic property It is larger, therefore the present invention is on the basis of many experiments, to heating rate v in annealing operation and (WSi+WAls) content intended It closes, obtains formula (1).
Preferably, the cold rolling non-orientation silicon steel at being grouped as and weight percent content is, C≤ 0.0030%, Si:3.1~3.23%, Mn:0.18~0.27%, Als:0.81~0.83%, P≤0.008%, S≤ 0.0020%, N≤0.0025%, Ti≤0.0020%, Nb≤0.0020%, V≤0.0020%, remaining for Fe and it is other can not The residual elements avoided.
The present invention has the advantages that compared with prior art, the present invention passes through Si in control cold rolling non-orientation silicon steel: 2.90%~3.50%, Mn:0.15%~0.30%, Als:0.80%~1.5%, and heating temperature is limited in annealing operation Degree meets formula (1) and improves favorable texture coefficient ratio Tp (formula in the present invention (2) are shown in definition) and then improve cold rolling non-orientation The magnetic property of silicon steel.
Specific embodiment
For a better understanding of the invention, invention is described in detail below with reference to specific example.
To solve the problems, such as that magnetic property present in the thick high grade cold rolling non-oriented silicon steel product of existing 0.50mm is bad, this Invention provides a kind of preparation method of cold rolling non-orientation silicon steel, specifically, the present invention passes through optimization cold rolling non-orientation silicon steel Chemical component and technique are to improve favorable texture coefficient ratio Tp and then improve the magnetic property of cold rolling non-orientation silicon steel, more specifically Say, the present invention control cold rolling non-orientation silicon steel in Si:2.90%~3.50%, Mn:0.15%~0.30%, Als:0.80%~ 1.5%, and limit warming temperature in annealing operation and meet formula (1).It below will be by specific embodiment come to this hair The preferred embodiment of the preparation method of bright cold rolling non-orientation silicon steel is described in detail.
Examples 1 to 6
A kind of preparation method of cold rolling non-orientation silicon steel, comprising steps of
1) it smelts and is casting continuously to form slab
Cold rolling non-orientation silicon steel at being grouped as and weight percent content is, C≤0.0030%, Si:2.90%~ 3.50%, Mn:0.15%~0.30%, Als:0.80%~1.5%, P≤0.008%, S≤0.0020%, N≤ 0.0025%, Ti≤0.0020%, Nb≤0.0020%, V≤0.0020%, remaining is Fe and other inevitable remaining members Element；
2) slab heats
Slab is heated to 1050~1150 DEG C, soaking time is 60~180 minutes；
3) hot rolling
Finishing temperature is controlled at 800~900 DEG C；
4) it batches
Coiling temperature >=600 DEG C are controlled, the coil of strip after batching enters holding pit, slow cooling；
5) normalizing
Normalizing temperature is 880~940 DEG C, and the normalizing time is 50~140 seconds, and then steel band carries out conventional pickling；
6) cold rolling
It is 0.50mm that steel band, which is rolled to finished product thickness,；
7) it anneals
Heating rate v meets formula (1) in annealing process；
20+2.15×(WSi+WAls)≤v≤80-3.85×(WSi+WAls) formula (1)
In formula (3), v is steel band heating rate in annealing process, unit DEG C/s；
WSiFor Si content in ingredient, unit %wt；
WAlsFor Als content in ingredient, unit %wt.
Table 1 is 1~3 the composition value list of the embodiment of the present invention 1~6 and comparative example
Table 1
Table 2 is the main technologic parameters of the embodiment of the present invention and comparative example
Table 2
3 embodiment of the present invention of table and comparative example obtain the performance of cold rolling non-orientation silicon steel
Table 3
Being described as follows about formula (2) and formula (3) in table 3:
Tp=-63.39+0.041 × v+6.31 × P1.5/50+28.61×B50Formula (3)
Formula (2) is the definition of favorable texture coefficient in the present invention, is chosen to magnetic property favorable texture component in inverse pole figure The sum of interior density value and the ratio to magnetic unfavorable texture component the sum of density value in inverse pole figure, are knitted using this ratio to measure Structure group ratio；Formula (3) is heating rate, finished product iron loss in favorable texture coefficient T p defined in formula (2) and annealing operation P1.5/50With magnetic strength B50Between relationship, favorable texture coefficient T p and magnetic values are in close relations, and favorable texture ratio is higher in finished product Shi Chengpin has excellent magnetic characteristics, and can quickly calculate favorable texture coefficient in finished product using formula (3), saves a large amount of detection works Make.
In conjunction with table 3 as can be seen that when heating speed of steel band during finished products is unsatisfactory for public affairs in comparative example 1~3 When formula (1) requires, favorable texture coefficient is lower, finished product magnetic difference.The reason for this is that because in annealing process heating rate it is slow, crystal grain obtains To abundant Recovery and recrystallization, crystallite dimension is larger, deteriorates finished product magnetic property；Heating rate is higher than public affairs during strip anneal When the speed of formula (1), because steel band heating speed is too fast, crystal grain has little time to reply and grow up, favorable texture (100) in finished product, (110) etc. component ratios are reduced, and favorable texture coefficient T p is lower, deteriorate magnetic property.Annealing operation is using full in Examples 1 to 6 Formula (1) in the foot present invention, the last magnetic property of sample is preferable, finished product iron loss P in embodiment1.5/50≤ 2.40W/kg, magnetic strength B50 ≥1.68T；Actual measurement Tp value and theoretical calculation Tp value numerical value are close, and trend is identical, and work as the steel band in annealing process and add When thermal velocity meets formula (1) in the present invention, Tp value and magnetic property P in finished product1.5/50And B50Preferably, steel band heats in comparative example Speed is unsatisfactory for that the present invention claims, penalties, at the same also because of annealing speed not outside the scope of the present invention, the calculating of Tp value has generated Relatively large deviation.
The embodiments described above only express several embodiments of the present invention, and the description thereof is more specific and detailed, but simultaneously Limitations on the scope of the patent of the present invention therefore cannot be interpreted as.It should be pointed out that for those of ordinary skill in the art For, without departing from the inventive concept of the premise, various modifications and improvements can be made, these belong to guarantor of the invention Protect range.Therefore, the scope of protection of the patent of the invention shall be subject to the appended claims.

Claims (2)

1. a kind of preparation method of cold rolling non-orientation silicon steel, which is characterized in that comprising steps of
1) it smelts and is casting continuously to form slab
Cold rolling non-orientation silicon steel at being grouped as and weight percent content is, C≤0.0030%, Si:2.90%~3.50%, Mn:0.15%~0.30%, Als:0.80%~1.5%, P≤0.008%, S≤0.0020%, N≤0.0025%, Ti≤ 0.0020%, Nb≤0.0020%, V≤0.0020%, remaining is Fe and other inevitable residual elements；
2) slab heats
Slab is heated to 1050~1150 DEG C, soaking time is 60~160 minutes；
3) hot rolling
Finishing temperature is controlled at 800~900 DEG C；
4) it batches
Coiling temperature >=600 DEG C are controlled, the coil of strip after batching enters holding pit, slow cooling；
5) normalizing
Normalizing temperature is 880~940 DEG C, and the normalizing time is 50~140 seconds, and then coil of strip carries out conventional pickling；
6) cold rolling
It is 0.50mm that steel band, which is rolled to finished product thickness,；
7) it anneals
Heating rate v meets formula (1) in annealing process；
20+2.15×(WSi+WAls)≤v≤80-3.85×(WSi+WAls) formula (1)
In formula (1), v is steel band heating rate in annealing process, unit DEG C/s；
WSiFor Si content in ingredient, unit %wt；
WAlsFor Als content in ingredient, unit %wt.
2. the preparation method of cold rolling non-orientation silicon steel according to claim 1, which is characterized in that the cold rolling non-orientation silicon Steel at being grouped as and weight percent content is, C≤0.0030%, Si:3.1~3.23%, Mn:0.18~0.27%, Als:0.81~0.83%, P≤0.008%, S≤0.0020%, N≤0.0025%, Ti≤0.0020%, Nb≤ 0.0020%, V≤0.0020%, remaining is Fe and other inevitable residual elements.
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 true CN109609734A (en) 2019-04-12
CN109609734B 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)

Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN110241362A (en) * 2019-07-09 2019-09-17 鞍钢股份有限公司 A kind of driving motor non-orientation silicon steel and its production method
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
CN110629120A (en) * 2019-10-31 2019-12-31 武汉钢铁有限公司 Cold-rolled non-oriented silicon steel with excellent magnetic property and production method thereof
CN112176250A (en) * 2020-09-19 2021-01-05 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
CN113403455A (en) * 2021-06-17 2021-09-17 张家港扬子江冷轧板有限公司 Production method of non-oriented silicon steel
CN114045433A (en) * 2021-11-10 2022-02-15 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

Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN1850431A (en) * 2006-05-18 2006-10-25 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

Patent Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN1850431A (en) * 2006-05-18 2006-10-25 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

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
JONG-TAE PARK: "Effect of Heating Rate on the Development of Annealing Texture", 《METALS AND MATERIALS ENGINEERING》 *

Cited By (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN110241362A (en) * 2019-07-09 2019-09-17 鞍钢股份有限公司 A kind of driving motor non-orientation silicon steel and its production method
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
CN110629120A (en) * 2019-10-31 2019-12-31 武汉钢铁有限公司 Cold-rolled non-oriented silicon steel with excellent magnetic property and production method thereof
CN112176250A (en) * 2020-09-19 2021-01-05 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
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
CN113403455A (en) * 2021-06-17 2021-09-17 张家港扬子江冷轧板有限公司 Production method of non-oriented silicon steel
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
CN114045433A (en) * 2021-11-10 2022-02-15 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

Also Published As

Publication number Publication date
CN109609734B (en) 2020-11-03

Similar Documents

Publication Publication Date Title
CN109609734A (en) A kind of preparation method of cold rolling non-orientation silicon steel
CN102453837B (en) Method for preparing non-oriented silicon steel with high magnetic induction
KR101070064B1 (en) Process for producing grain-oriented magnetic steel sheet with high magnetic flux density
CN103228801B (en) Method for producing directional electromagnetic steel sheet
CN104220607B (en) The manufacture method of orientation electromagnetic steel plate
CN106702260B (en) A kind of high-magnetic induction, low-iron loss non-orientation silicon steel and its production method
CN103205548B (en) Manufacturing method of low-coercive force electromagnetic pure ion cold-rolled sheet
KR101389248B1 (en) Manufacturing method for grain-oriented electromagnetic steel sheet
JP5265835B2 (en) Method for producing non-oriented electrical steel sheet
CN103667879A (en) Non-oriented electrical sheet with superior magnetic and mechanical properties, and production method of non-oriented electrical sheet
CN104911322B (en) Method for preparing oriented high silicon steel thin plate by using rolling
CN109136503A (en) The preparation method of low temperature high magnetic induction grain-oriented silicon steel
CN110468352A (en) A kind of non-orientation silicon steel and its production method
CN105886932A (en) Non-oriented silicon steel for high-power-factor motor and production method
CN109055861A (en) A kind of low-iron loss high-magnetic strength orientation silicon steel thin belt and preparation method thereof
CN100457385C (en) Method for manufacturing electromagnetic pure iron cold-rolled sheet material with low coercive force and high magnetoconductivity
JP6079580B2 (en) Method for producing grain-oriented electrical steel sheet
JPH055126A (en) Production of nonoriented silicon steel sheet
CN110157976A (en) A kind of preparation method of the Fe-6.9%Si strip containing rare earth Nd
CN109825760A (en) A kind of boracic non-oriented electrical steel and its production method of endless rolling
CN112921164B (en) Low-iron-loss high-permeability non-oriented electrical steel and production method thereof
JPH08143960A (en) Production of nonoriented silicon steel sheet having high magnetic flux density and reduced in iron loss
JPH0273919A (en) Manufacture of nonoriented electrical steel sheet having excellent magnetic characteristics
JP4320793B2 (en) Method for producing electrical steel sheet with excellent punchability and magnetic properties in the rolling direction
JP2784661B2 (en) Manufacturing method of high magnetic flux density thin unidirectional magnetic steel sheet

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