CN106702260A - High-magnetic-inductivity low-iron-loss non-oriented silicon steel and production method thereof - Google Patents

High-magnetic-inductivity low-iron-loss non-oriented silicon steel and production method thereof Download PDF

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CN106702260A
CN106702260A CN201611096926.0A CN201611096926A CN106702260A CN 106702260 A CN106702260 A CN 106702260A CN 201611096926 A CN201611096926 A CN 201611096926A CN 106702260 A CN106702260 A CN 106702260A
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silicon steel
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CN106702260B (en
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李准
郑泽林
黎世德
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Wuhan Iron and Steel Co Ltd
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C21D8/1222—Hot 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
    • 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
    • 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
    • C21D8/1244—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
    • C21D8/1255—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 with diffusion of elements, e.g. decarburising, nitriding
    • 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
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • 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
    • 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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

Abstract

The invention discloses high-magnetic-inductivity low-iron-loss non-oriented silicon steel. The high-magnetic-inductivity low-iron-loss non-oriented silicon steel comprises, by weight, 0.015%-0.070% of C, 2.0%-3.0% of Si, 0.15%-0.50% of Mn, 0-0.02% of P, 0-0.0020% of S, 0-0.0025% of N, 0-0.01% of Als (not including 0.01%), 0.03%-0.20% of Sn or Sb or (Sn/2+Sb), 0-0.001% of Ti, 0-0.0020% of Nb and 0-0.0020% of V. A production method of the high-magnetic-inductivity low-iron-loss non-oriented silicon steel includes the steps that smelting and continuous casting are performed so that a slab can be formed; the slab is heated; hot rolling is conducted; coiling is performed; normalizing is carried out; one-step cold rolling is adopted after acid pickling, so that the slab is rolled to be in a finished product thickness; decarburization annealing is carried out; continuous annealing is executed; and conventional cooling, coating and finishing are performed for standby application. According to the high-magnetic-inductivity low-iron-loss non-oriented silicon steel and the production method thereof, a one-step cold rolling method is adopted for rolling, the finished product thickness is 0.35 mm, the iron loss P1.5/50 is smaller than or equal to 2.1 W/kg, and B5000 is larger than or equal to 1.74 T; and moreover, production efficiency is high and economic efficiency is achieved.

Description

A kind of high-magnetic induction, low-iron loss non-orientation silicon steel and its production method
Technical field
The present invention relates to non-orientation silicon steel and its production method, a kind of high-magnetic induction, low-iron loss non-orientation silicon steel is specifically belonged to And its production method.
Background technology
Non-orientation silicon steel is the important magnetic material for manufacturing various electric machine iron cores, is played in electric power, electronics, mechanical industry Important effect.In recent years, with energy growing tension, and the need for energy-conserving and environment-protective, the requirement to silicon steel performance is also got over Come higher.In addition, the high efficiency in order to reach motor, to the high performance requirements of the silicon steel sheet as core material also increasingly It is high, it is desirable to obtain magnetic strength high while the low electric steel plate of iron loss.
In through the retrieval both at home and abroad patent document published, be related to produce high-magnetic induction, low-iron loss non-orientation silicon steel into Point, the relevant report of technique and performance.
China Patent Publication No. is the document of CN101463448A, is disclosed《A kind of high-magnetic strength non-oriented electrical steel and its Production method》.Its main chemical compositions is：C≤0.010%、Si：0.8%~2.0%, Mn：0.2%~1.2%, P≤0.03%, S≤ 0.01%th, Als≤0.002%, N≤0.003%, remaining is Fe.Its production method is：Smelt（By carbon control in ＜ 0.010%, adopt Use silicon deoxidation）→ continuous casting and slow cooling（To 900 DEG C of ＜）→ hot rolling（Heating-up temperature is 1200~1270 DEG C, soaking temperature ＜ 1200 DEG C, steel billet temperature is 1100~1150 DEG C, start rolling temperature >=1000 DEG C, oiler temperature control >=700 DEG C）→ cold rolling（It is once cold Roll or with Intermediate Gray fire two is cold rolling）→ finished products → painting insulating barrier → be made finished product.Though the document is without to hot rolled plate Carry out normalizing operation, it is possible to decrease production cost, but it is relatively low to there is finished product magnetic property, such as P1.5/50 onlyIt is 4.32~4.83W/kg, B5000It is 1.700~1.735T, and hot rolling heating-up temperature is higher, causes production energy cost to increase.
China Patent Publication No. is the document of CN102634729A, it discloses《A kind of low-iron loss high-magnetic strength trade mark high without The preparation of orientation silicon steel》, its main chemical compositions is C≤0.005%, Si：3.0~3.4%, Mn：0.25~0.40%, S≤ 0.003%, N≤0.004%, Al：0.5~0.8%, Sn：0.05~0.09%, Ca：0.001~0.003%, remaining composition be Fe and Inevitable impurity.The strand that obtains of casting is hot rolled, normalizing（Temperature is 850~890 DEG C, and soaking time is 4.5~5.5 Minute）, once cold rolling to 0.80mm, intermediate annealing process be 850~870 DEG C, then carry out secondary cold-rolling to 0.35mm, finally Finished products are simultaneously coated with insulating coating, are made finished product.Obtained finished product steel belt, its magnetic property P in this way1.5/50It is 2.221 ~2.242W/kg, B5000It is 1.708~1.712T, it is same relatively low, and using cold-rolling practice twice.
The content of the invention
It is not enough present in above-mentioned document it is an object of the invention to overcome, there is provided one kind is by once cold rolling method, finished product Thickness is in 0.35mm, iron loss P1.5/50≤ 2.1W/kg, B5000The high-magnetic induction, low-iron loss non-orientation silicon steel and its producer of >=1.74T Method.
Realize the measure of above-mentioned purpose：
A kind of high-magnetic induction, low-iron loss non-orientation silicon steel, it is into being grouped into and weight percent content is：C：0.015~0.070%, Si：2.0~3.0%, Mn：0.15%~0.50%, P≤0.02%, S≤0.0020%, N≤0.0025%, Als：＜ 0.01%, Sn or Sb or (Sn/2+Sb)：0.03~0.20%, Ti≤0.001%, Nb≤0.0020%, V≤0.0020%, remaining be Fe and other not Evitable residual elements.
Produce a kind of method of high-magnetic induction, low-iron loss non-orientation silicon steel, its step：
1）Smelt and be casting continuously to form slab；
2）By heating strand to 1050~1150 DEG C, and it is incubated 60~120min；
3）Hot rolling is carried out, control finish rolling finishing temperature is at 800~900 DEG C；
4）Batched, control coiling temperature is not less than 600 DEG C, and coil of strip is inserted into holding pit after batching carries out slow cooling；
5）Normalizing is carried out, normalizing temperature control is carried out in Ac3 point temperatures above interval；
6）Finished product thickness 0.35mm, and rolling temperature control are rolling at 150 DEG C~300 DEG C using once cold rolling after pickling；
7）Carry out decarburizing annealing：, at 800~860 DEG C, at 1~10 minute, dew point is 20~80 for annealing time for control annealing temperature ℃；Atmosphere is the H of wet type2With N2Mixed atmosphere, wherein H2It is 20~50% to account for volume ratio；
8）Continuous annealing is carried out, control annealing temperature is incubated 20~180s at 950~1050 DEG C, and its atmosphere is dry type hydrogen With nitrogen mixture, H2 ratios are 25%~50%；
9）Conventional chilling, coating and finishing, and it is stand-by.
The effect of each element of the present invention and main technique control parameter.
Traditional view thinks that C content is more few better in steel, it is therefore an objective to the not decarburization in annealing, prevents from forming internal oxidation layer With interior nitration case.But warp experimental studies have found that, in steel contain a certain amount of C when, to improve finished product magnetic strength it is favourable.C expands γ phase regions, Undergo phase transition, crystal grain thinning.Enter austenitic area in more than Ac3 in normalizing operation control normalizing temperature, nitrogen is in austenite Solubility is much larger than it in ferrite.C content increases can increase the solid solution capacity of nitrogen in this stage, suppress the analysis of AlN particles Go out.And the excessive C of content reduces content when final finished is annealed in the way of de- C.During C content ＜ 0.015%, because of its content It is less, the effect for improving magnetic strength is not had, as content ＞ 0.070%, decarburization can be caused difficult.Therefore its content range exists 0.015~0.070%.
Si, is the effective element for reducing iron loss, and it can increase resistivity, reduce iron loss；Si contents more than 3.0% when in Ac3 Point difficulty annealed above, and steel band can be caused to become fragile and then very big difficulty can be brought to cold working；When its content is less than 2.0%, Finished product iron loss is higher, therefore control Si contents are below 2.0%~3.0%.
Als, can form tiny AlN, be unfavorable for that crystal grain is grown up, to make to reduce AlN as far as possible, it is desirable to Als ＜ 0.01%.
Mn, advantageously forms thick MnS, and promote hot rolled plate tissue（100）With（110）Component is strengthened,（111）Component subtracts It is weak, improve magnetic property；Simultaneously to improve red brittleness, its content should be little more than 0.50% improvement result more than 0.15%, therefore Mn contents should control 0.15%~0.50%.
Sn or Sb, is to form favorable texture to have element, can be increased（100）With（110）Position can suppress to texture （111）Texture is formed, so as to improve magnetic strength, improves magnetic property.Its content Sn or Sb contents or（Sn/2+Sb）If being less than 0.03%, then do not reach raising magnetic strength and use, but during more than 0.20%, the cold rolling crackle that is also easy to produce causes rolling difficult.Therefore Sn or Sb or（Sn/2+Sb）Should control 0.03%~0.20%.
P, when Si contents are high, P can make plate fragility become big, be unfavorable for cold-rolling workability, therefore the control of control P content≤ 0.01%。
S, is harmful element, and tiny MnS is formed with Mn, and crystal grain is grown up when can strongly prevent finished products, therefore control exists ≤0.0020%。
N, is harmful element, easily forms immature AlN particles with Al, suppresses crystal grain and grows up, thus control≤ 0.0025%。
Why the present invention controls temperature requirement of the hot rolled plate during normalizing more than Ac3 points, is now hot rolling Plate annealing enters austenitic area, and as γ → α changes during cooling, the meltage reduction of C can separate out tiny cementite, and then The texture favourable to magnetic strength is formed, improves the final magnetic property of finished product.If normalizing temperature is less than Ac3 points, can in ferrite or Ferrite and austenite two-phase section normalizing, the crystallite dimension after normalizing are smaller and uneven, and generation is difficult to greatly in crystal grain when cold rolling The Zona transformans of amount, can form a large amount of texture for deteriorating magnetic property during final annealing.Therefore Hot Rolled Plate Normalizing requirement temperature is in Ac3 points More than.
The present invention why control 150 DEG C~300 DEG C it is cold rolling roll, and once cold rolling is to 0.35mm finished product thicknesses Magnetic strength can be increased substantially when rolling temperature is more than 150 DEG C, improve almost not acting on during less than 150 DEG C to magnetic strength.It is higher than Also there is improvement result at 300 DEG C to magnetic strength, but temperature is too high, and production cost increases, and equipment attrition degree is also increased, therefore cold Temperature upper limit is rolled for 300 DEG C.
Compared with prior art, using once cold rolling method, finished product thickness is in 0.35mm, iron loss P for the present invention1.5/50≤2.1W/ Kg, B5000>=1.74T, and production efficiency is high, economy.
Specific embodiment
The present invention is described in detail below：
Table 1 is the comparative example of various embodiments of the present invention and comparative example；
Table 2 is the main technologic parameters and capabilities list of various embodiments of the present invention and comparative example.
Various embodiments of the present invention are produced according to following steps：
1）Smelt and be casting continuously to form slab；
2）By heating strand to 1050~1150 DEG C, and it is incubated 60~120min；
3）Hot rolling is carried out, control finish rolling finishing temperature is at 800~900 DEG C；
4）Batched, control coiling temperature is not less than 600 DEG C, and coil of strip is inserted into holding pit after batching carries out slow cooling；
5）Normalizing is carried out, normalizing temperature control is carried out in Ac3 point temperatures above interval；
6）Finished product thickness 0.35mm, and rolling temperature control are rolling at 150 DEG C~300 DEG C using once cold rolling after pickling；
7）Carry out decarburizing annealing：, at 800~860 DEG C, at 1~10 minute, dew point is 20~80 for annealing time for control annealing temperature ℃；Atmosphere is the H of wet type2With N2Mixed atmosphere, wherein H2It is 20~50% to account for volume ratio；
8）Continuous annealing is carried out, control annealing temperature is incubated 20~180s at 950~1050 DEG C, and its atmosphere is dry type hydrogen With nitrogen mixture, H2 ratios are 25%~50%；
9）Conventional chilling, coating and finishing, and it is stand-by.
Table 1 is various embodiments of the present invention and comparative example the composition value list（wt%）
The various embodiments of the present invention of table 2 and comparative example technological parameter value and capabilities list
Explanation：In table 1, Sn or Sb, finished product magnetic property P are not added with the composition of comparative example 1~31.5/50And B5000Fail to reach this hair Bright level；C, finished product magnetic property P are not added with the composition of comparative example 7~91.5/50And B5000Fail to reach level of the present invention.Comparative example 10~11 are rolled in cold rolling process using normal temperature, finished product magnetic property P1.5/50And B5000Fail to reach level of the present invention.
In table 2, the normalizing temperature of comparative example 13 is less than composition Ac3 point temperature, finished product magnetic property P1.5/50And B5000Fail to reach To level of the present invention；Als, finished product iron loss P are added in the composition of comparative example 141.5/50It is higher, magnetic strength B5000Also it is relatively low, fail to reach Level of the present invention.
From table 2 it can be seen that iron loss P can be obtained under the conditions of the technology of the present invention is met1.5/50≤ 2.1W/kg, and magnetic strength B5000The non-orientation silicon steel of >=1.74T.And ought not meet C simultaneously：0.015~0.070%, Sn/Sb or Sn+Sb：0.03~ 0.20%, normalizing requirement temperature is cold rolling in 150 DEG C~300 DEG C of temperature ranges, it is impossible to obtain iron loss P more than Ac3 points1.5/50 ≤ 2.1W/kg, and magnetic strength B5000The non-orientation silicon steel of >=1.74T.
Above-described embodiment is only most preferably to enumerate, and is not the restriction to embodiments of the present invention.

Claims (2)

1. a kind of high-magnetic induction, low-iron loss non-orientation silicon steel, it is into being grouped into and weight percent content is：C：0.015~ 0.070%, Si：2.0~3.0%, Mn：0.15%~0.50%, P≤0.02%, S≤0.0020%, N≤0.0025%, Als：＜ 0.01%, Sn or Sb or (Sn/2+Sb)：0.03~0.20%, Ti≤0.001%, Nb≤0.0020%, V≤0.0020%, remaining is Fe and other inevitable residual elements.
2. the method for producing a kind of high-magnetic induction, low-iron loss non-orientation silicon steel described in claim 1, its step：
1）Smelt and be casting continuously to form slab；
2）By heating strand to 1050~1150 DEG C, and it is incubated 60~120min；
3）Hot rolling is carried out, control finish rolling finishing temperature is at 800~900 DEG C；
4）Batched, control coiling temperature is not less than 600 DEG C, and coil of strip is inserted into holding pit after batching carries out slow cooling；
5）Normalizing is carried out, normalizing temperature control is carried out in Ac3 point temperatures above interval；
6）Finished product thickness 0.35mm, and rolling temperature control are rolling at 150 DEG C~300 DEG C using once cold rolling after pickling；
7）Carry out decarburizing annealing：, at 800~860 DEG C, at 1~10 minute, dew point is 20~80 for annealing time for control annealing temperature ℃；Atmosphere is the H of wet type2With N2Mixed atmosphere, wherein H2It is 20~50% to account for volume ratio；
8）Continuous annealing is carried out, control annealing temperature is incubated 20~180s at 950~1050 DEG C, and its atmosphere is dry type hydrogen With nitrogen mixture, H2 ratios are 25%~50%；
9）Conventional chilling, coating and finishing, and it is stand-by.
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CN107723591A (en) * 2017-09-28 2018-02-23 马钢(集团)控股有限公司 A kind of new-energy automobile motor cold rolling non-oriented electrical steel and its production method
CN108425003A (en) * 2018-06-07 2018-08-21 宁波革创新材料科技有限公司 A kind of household electrical appliances non-orientation silicon steel board fabrication method
CN108754106A (en) * 2018-06-07 2018-11-06 宁波革创新材料科技有限公司 A kind of heat treatment process of automobile micro machine non-orientation silicon steel
CN111206192A (en) * 2020-03-04 2020-05-29 马鞍山钢铁股份有限公司 High-magnetic-induction cold-rolled non-oriented silicon steel strip for electric automobile driving motor and manufacturing method thereof
CN111690870A (en) * 2019-03-11 2020-09-22 江苏集萃冶金技术研究院有限公司 Method for producing high-magnetic-induction thin-specification non-oriented silicon steel by cold continuous rolling
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
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CN113737089A (en) * 2020-05-29 2021-12-03 宝山钢铁股份有限公司 Low-cost and extremely-low-aluminum non-oriented electrical steel plate and manufacturing method thereof
CN116240471A (en) * 2023-02-21 2023-06-09 包头钢铁（集团）有限责任公司 Sb-containing non-oriented silicon steel 50W600 and preparation method thereof

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