CN102264922A - Non-oriented electrical steel sheets having high workability for client companies and manufacturing method thereof - Google Patents
Non-oriented electrical steel sheets having high workability for client companies and manufacturing method thereof Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- 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
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- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
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- 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
- C21D1/30—Stress-relieving
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- 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
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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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Abstract
The present invention relates to non-oriented electrical steel sheets that are magnetized by SRA treatment and a manufacturing method thereof. The technical essence of the invention lies in: the non-oriented electrical steel sheets having strong magnetism by SRA treatment and comprising Si: 0.2 ~ 1.0%, Al: 0.9 ~ 2.0%, Mn: 0.1 ~ 0.5%, P: 0.01 ~ 0.05, the remaining % Fe; and other inevitable impurities, wherein Si and Al satisfy equations of 1.4=Si + Al=2.4 and 1=Al/Si=5; and the manufacturing method thereof. The present invention improves workability for client companies by obtaining a low Vickers hardness through deriving optimal process conditions and adjusting elements of Al and Si to optimum levels, and results in magnetism with high magnetic density and reduces iron loss through enhancing grain growth and improving texture.
Description
Technical field
The present invention relates to a kind of preparation method who has non-oriented electromagnetic steel sheet He this steel plate of fine magnetic property at SRA (stress relief annealing) afterwards, more specifically, relate to a kind of preparation method who after suitably adjusting steel constituent and processing conditions, has non-oriented electromagnetic steel sheet and this steel plate of good workability and magnetic property.
Background technology
Recently, non-oriented electromagnetic steel sheet, it is a kind ofly in rotating equipment electric energy to be changed into the required vitals of mechanical energy, need have magnetic property, promptly low iron loss and high magneticflux-density are so that reduce energy expenditure.Particularly, iron loss is the energy that loses with form of heat in energy conversion process, therefore the low more efficient that then can improve rotating equipment more of iron loss, and magneticflux-density is as a kind of strength that produces power, and the efficient of the high more rotating equipment of magneticflux-density is also high more.Such non-oriented electromagnetic steel sheet is cut off into the shape of iron core, and after carrying out stamping-out (blanked), lamination (stacked), connection, copper cash is twined on it, thereby be used for power equipment.
For realizing low iron loss in the non-oriented electromagnetic steel sheet, should reduce hysteresis loss (hysteresis loss) and eddy losses (eddy current loss).Eddy losses is by adding Si, Al, Mn and increase resistivity or by the steel plate attenuation is improved, hysteresis loss being improved by improving texture, suppress impurity and increasing grain fineness number in steel plate.
In addition, the hysteresis loss proportion is 60～80% in the iron loss of non-oriented electromagnetic steel sheet because in preparation during steel plate, impurity with which, so its inhibition is difficult, and cost increases when suppressing.Therefore, preferably improve iron loss and magneticflux-density by the texture that increases grain fineness number or generation easy magnetization.
About described texture, if＜100---it is an easy magnetized direction in the normal direction (ND)---being positioned at the surface of steel plate, then is optimal.Shown in Fig. 2 (a), along with the aggregation degree (integration) of cube (cube) texture ({ 001}＜100 〉) increases, it is good that magnetic property becomes.Comparatively speaking, shown in Fig. 2 (b), alpha fibre (＜110〉//RD) and gamma fibers (＜111〉//ND) aggregation degree should be lower, orientation＜110 wherein or＜111〉(with＜100〉compare not easy magnetization) be more ubiquitous at surface of steel plate.Though the formation of this class texture can decide by alloy composition, the growth of itself and crystal grain is closely related.Usually, in non-oriented electromagnetic steel sheet, the branch rate of the orientation favourable to magnetic (for example cubic texture ({ 001}＜100 〉)) reduces when cold rolling and grain growing, and its value is reduced to below 3%.Therefore need that exploitation is a kind of to be increased the composition of the favourable cubic texture aggregation degree of magnetic and can improve processing conditions to the aggregation degree of the favourable texture of magnetic when grain growing is set.
Summary of the invention
Technical problem
Therefore, the inventor has carried out studying repeatedly and testing for solving the problems referred to above that run in the prior art, and made the present invention based on its result, a target of the present invention provides a kind ofly to be had good workability and has non-oriented electromagnetic steel sheet of low iron loss and high magnetic flux density and preparation method thereof client company.
Technical scheme
One aspect of the present invention provides a kind of non-oriented electromagnetic steel sheet that has fine magnetic property at SRA (Stress Relief Annealing) afterwards, described steel plate contains Si:0.2～1.0wt%, Al:0.9～2.0wt%, Mn:0.1～0.5wt%, P:0.01～0.05wt%, all the other are Fe and other unavoidable impurities, and wherein Si and Al satisfy 1.4≤Si+Al≤2.4 and 1≤Al/Si≤5.
In the non-oriented electromagnetic steel sheet of the present invention, after SRA, the cubic texture of section (cube texture) branch rate is compared increase before with SRA on the whole plane of described non-oriented electromagnetic steel sheet.
In the non-oriented electromagnetic steel sheet of the present invention, after SRA, the cubic texture of section (cube texture) branch rate is more than 5%.
Non-oriented electromagnetic steel sheet of the present invention can have the resistivity of 30～42 μ Ω cm.
In non-oriented electromagnetic steel sheet of the present invention, described unavoidable impurities can comprise below the C:0.003wt%, below the S:0.002wt%, below the N:0.002wt% and below the Ti:0.002wt%.
Non-oriented electromagnetic steel sheet of the present invention is in the Vickers' hardness that has before the SRA below the 130Hv.
Non-oriented electromagnetic steel sheet of the present invention can have above magneticflux-density (B50) of 1.74T and the following iron loss (W15/50) of 2.6w/kg.
Another aspect of the present invention provides a kind of preparation to have the method for the non-oriented electromagnetic steel sheet of fine magnetic property after SRA, this method comprises and reheating and hot-rolled steel ingot, this steel ingot contains Si:0.2～1.0wt%, Al:0.9～2.0wt%, Mn:0.1～0.5wt%, P:0.01～0.05wt%, all the other are Fe and other unavoidable impurities, wherein Si and Al satisfy 1.4≤Si+Al≤2.4 and 1≤Al/Si≤5, obtain hot-rolled steel sheet thus; Annealing and cold rolling hot-rolled steel sheet obtain cold-rolled steel sheet thus; Then with it 770～830 ℃ of annealing.
The present invention prepares in the method for non-oriented electromagnetic steel sheet, and the annealing of described cold-rolled steel sheet comprises and be heated to 850～950 ℃, then soaking 30sec～4min under 770～830 ℃ of temperature.
The present invention prepares in the method for non-oriented electromagnetic steel sheet, and the annealing of described hot-rolled steel sheet is to keep the mode of 2～4min time inside furnace to carry out under 800～1100 ℃ the temperature in smelting furnace.
The present invention prepares in the method for non-oriented electromagnetic steel sheet, and described unavoidable impurities can comprise below the C:0.003wt%, below the S:0.002wt%, below the N:0.002wt% and below the Ti:0.002wt%.
Beneficial effect
As mentioned above, the present invention make Al and Si component and cold rolling before and annealing conditions afterwards reach best, thereby produced a large amount of magnetized texture that helps, also increased grain fineness number, thereby the effect of a kind of non-oriented electromagnetic steel sheet that client company is had good workability and for example low iron loss of magnetic and high magnetic flux density and preparation method thereof effectively is provided.
Description of drawings
Fig. 1 is the figure that shows the relation between Al and the Si.
Fig. 2 is the structure iron that schematically shows texture.
Fig. 3 is that expression sample of the present invention and duplicate are before SRA and orientation distribution function afterwards (ODF).
Fig. 4 is the figure of the Φ 2=45 ° section (section) represented in order to understand ODF.
Embodiment
Hereinafter, describe the present invention with reference to accompanying drawing.
For solving the problems of the technologies described above, the element al that Xiang Gangzhong adds uses with different amounts with Si, magnetic property, texture such as assessment iron loss and magneticflux-density, and Vickers' hardness is intended to determine to show the scope of fine magnetic property with the variation of various compositions.
The reason that each component of the present invention is limited is described in detail.
Carbon (C) can be less amount use because it increases iron loss.If the amount of C surpasses 0.003%, then the sosoloid C in the steel is deposited as carbide, and increases iron loss thus used as iron core the time.Therefore, the amount of C preferably is limited to below 0.003%.
Silicon (Si) is useful, because it can increase resistance.Be intensity and the increase resistivity of guaranteeing material, the addition of Si can be more than 0.2%.But if the amount of Si surpasses 1.0%, then the hardness of steel plate increases, and has reduced stamping-out thus.Therefore, the amount with Si is limited to 0.2～1.0%.
Aluminium (Al) can increase resistance with Si is the same, reduces eddy losses thus, thereby reduces iron loss.Compare with the Si of same amount, the degree that Al increases steel plate hardness is less, therefore increases workability and magnetic property simultaneously, so be important element.For increasing workability and magnetic property simultaneously, the consumption of Al is preferably more than 0.9%.But, if its amount surpasses 2.0%, then can make the formability variation, and when the preparation steel, the oxide compound inclusion compound of generation be increased, thereby reduce surface quality and increased manufacturing cost.Therefore, the consumption of Al is limited to 0.9～2.0%.
Manganese (Mn) can increase resistance and produce sulfide, and therefore preferred its consumption is more than 0.1%.If the amount of Mn surpasses 0.5%, then can make the formability variation and preparation cost is increased.Therefore, the amount of Mn is limited to 0.1～0.5%.
Phosphorus (P) is a kind of displaced type alloying element, has very big solid solution hardening effect, and has the effect that improves intra-face anisotropy and improve intensity.The consumption of P can be more than 0.01%, so that promote the formation of texture.But if the content of P surpasses 0.05%, then the increase of intensity is faster than the improvement degree of formability, and makes P at grain boundary segregation, and snappiness is sharply reduced, and for example can make material fragility occur.Therefore, the amount of P is necessary to be limited to 0.01～0.05%.
Sulphur (S) forms less MnS settling, makes the magnetic property variation thus, and it is the least possible therefore should to control its amount.If use excessive S, then S can be after being deposited as MnS and being residual, crystal boundary is become fragile, and can produce red brittleness thus.Therefore, the amount of S is limited to below 0.002%.
Nitrogen (N) can make the deposition of AlN increase when a large amount of the use.What is more, when the AlN chap, can reduce the growth property of crystal grain and increase iron loss.Therefore, the amount of N is limited to below 0.002%.
Titanium (Ti) forms less TiN, TiC settling, and the growth that not only suppresses crystal grain thus also promotes to be unfavorable for the texture of magnetic property, promptly gamma fibers (＜111〉//ND) formation, therefore should make its content less.In the present invention, the amount of Ti is limited to below 0.002%.
The value of Si+Al is preferably 1.4～2.4.Therefore Si and Al all can make resistance increase, and reduce iron loss thus, therefore should make the value of Si+Al more than 1.4.But, if the value of Si+Al surpasses 2.4, the then cold rolling difficulty that becomes.
For further improving magnetic property, the value of preferred Al/Si satisfies 1≤Al/Si≤5.If the value of Al/Si is less than 1, then cubic texture branch rate reduces after SRA.Comparatively speaking, if the value of Al/Si surpasses 5, then when the preparation steel owing to excessive Al produces a large amount of oxide compound inclusions, thereby make the surface quality variation.When the amount of any one element wherein was too high, the saturation magnetic flux density of steel plate reduced.Therefore, should take all factors into consideration these two kinds of elements and select suitable content.
Among the present invention, comprise the non-oriented electromagnetic steel sheet that a kind of cubic texture (cube texture) branch rate at section on the whole steel plate plane increases before than SRA after SRA, also comprise a kind of after SRA the cubic texture branch rate of section at the non-oriented electromagnetic steel sheet more than 5%.In addition, in the present invention, also comprising a kind of resistivity is the non-oriented electromagnetic steel sheet of 30～42 μ Ω cm.In addition, in the present invention, preferably below 130Hv, and preferred magneticflux-density (B50) is more than 1.74T (tesla) in the Vickers' hardness before the SRA, and iron loss (W15/50) is below the 2.6w/kg.
The invention provides a kind of method for preparing described steel plate, this method comprises, steel ingot is reheated and anneal, this steel ingot contains Si:0.2～1.0wt%, Al:0.9～2.0wt%, Mn:0.1～0.5wt%, P:0.01～0.05wt%, all the other are Fe and other unavoidable impurities, wherein Si and Al satisfy 1.4≤Si+Al≤2.4 and 1≤Al/Si≤5, obtain hot-rolled steel sheet thus; Annealing and cold rolling this hot-rolled steel sheet prepare cold-rolled steel sheet thus; Then with it 770～830 ℃ of annealing.Described unavoidable impurities comprises that C:0.003wt% is following, S:0.002wt% following, below the N:0.002wt% and below the Ti:0.002wt%.
Described hot-rolled steel sheet can be in smelting furnace keeps 2～4min time inside furnace to anneal under 800～1100 ℃ the temperature.If anneal being lower than under 800 ℃ the temperature, and time inside furnace is less than 2min, and then texture possibly can't be grown or growth fine, and the degree that magneticflux-density is increased diminishes.Comparatively speaking, if anneal being higher than under 1100 ℃ the temperature, and time inside furnace is greater than 4min, though texture can fully grow, energy waste for the improvement of magneticflux-density too much.
In addition, described cold-rolled steel sheet is annealed in 770～830 ℃ temperature range.If annealing temperature is lower than 770 ℃, then abundant recrystallization at first produces the texture that is unfavorable for magnetic property thus when SRA.Comparatively speaking, if annealing temperature is higher than 830 ℃, then crystal grain before SRA, greatly grow and be transformed into the gamma fibers that is unfavorable for magnetic property (＜111〉//ND).
In addition, the annealing of preferred described cold-rolled steel sheet is carried out the mode of the equal thermal treatment of 30sec～4min and is carried out to be heated to after 850～950 ℃ under 770～830 ℃ of temperature.Fully guarantee cubic texture even be heated to 850～950 ℃, when in the said temperature scope, carrying out equal thermal treatment, divide rate to produce influence unfriendly cubic texture.Therefore,, reduce temperature then and carry out equal thermal annealing, thereby keep higher cubic texture branch rate by described cold-rolled steel sheet is heated to the said temperature scope.
Therefore in addition,, have orientation＜111 that are unfavorable for magnetic property because being grown under the temperature that is lower than 850 ℃ of recrystallization grains is insufficient〉the amount of texture increase, cubic texture divides rate to reduce thus.Comparatively speaking, if temperature is higher than 950 ℃, then grain growing must be thicker, makes the magnetic property variation.Therefore, Heating temperature is limited to 850～950 ℃.In addition, if annealing time is less than 30sec, then the crystal grain of cold-rolled steel sheet can't recrystallize, divides rate to produce adverse influence to cubic texture.Comparatively speaking, if annealing time greater than 4min, then productivity reduces.Therefore, annealing time is limited to 30sec～4min.
Hereinafter, will be described in more detail the present invention by following examples.
[embodiment 1]
For keeping saturation magnetic flux density (Bs) to equal the saturation magnetic flux density (Bs) of Fe-Si base non-oriented electromagnetic steel sheet 50A700～50A470 (JIS standard), the scope of intrinsic resistance (ρ) is set to 30～42 μ Ω cm, and the relation between component (%) and the intrinsic resistance (ρ) is represented by following equation.
In following table 1, show, the Al/Si value less than 1 and the composition corresponding F12 of Fe-Si and Al/Si value greater than 1 and the composition corresponding F1 of Fe-Al.
Table 1
In the preparation method, steel ingot uses vacuum melting and makes, and is heated to 1150 ℃, and 870 ℃ of hot rollings, obtains hot-rolled steel sheet thus, and its thickness is 2.0mm.Described hot-rolled steel sheet at 1000 ℃ of annealing 4min, is cold-rolled to 0.5mm then, and the cold-rolled steel sheet with gained is heated to 900 ℃ thereafter, then at 770 ℃ of annealing 30sec.Subsequently, with this steel plate in nitrogen atmosphere in 750 ℃ of SRA 2 hours.For assessing the texture of two samples that obtain thus, the section (TD direction) before and after the SRA is observed with EBSD (Electron Back-Scattered Diffraction (Electron Back Scattered Diffraction)).The orientation distribution function as a result (ODF, Orientation Distribution Function) that obtains is shown among Fig. 3.The reason of being determined ODF by the texture data is, is intended to the texture that observes is carried out quantitative analysis.In addition, only to Φ among the ODF
2=45 ° section carries out graphic extension, be because its expression has all typical texture of the metal of body-centered cubic structure, for example, cubic texture ({ 001}＜100 〉), rotation cubic texture ({ 001}＜110 〉), alpha fibre (＜110〉//RD) and gamma fibers (＜111〉//ND).
Fig. 4 is illustrated in the position of the typical texture of the metal with body-centered cubic structure in the Φ 2=45 ° section among the ODF.The position of texture shown in Fig. 4 is the ideal position, uses level line to represent the intensity of texture usually.
In non-oriented electromagnetic steel sheet, comprise cubic texture ({ 001}＜100 〉) and rotation cubic texture ({ 001}＜110 〉)＜100 //the branch rate of ND is many more, and is favourable more to magnetic property.Particularly, the branch rate of cubic texture ({ 001}＜100 〉) is important for magnetic property.But, alpha fibre (＜110〉//RD) and gamma fibers (＜111〉//ND) have and be difficult for magnetized magnetic beach axle (magnetic hard axis), so its minute rate more little just favourable to magnetic property more.
As shown in Figure 3, no matter whether implement SRA, the maximum strength (f (g) max) of Fe-Al base F1 texture all is higher than the maximum strength of Fe-Si base F12 texture.Think that this is because formed Fe-Al base F1 texture is more firm.For Fe-Al base F1, the specific tenacity mutually of (F (g) max=5.3) is higher before its cubic texture after SRA (F (g) max=6.4) and the SRA.
The branch rate of texture is determined by comprising the value that meets less than the crystal grain of 15 ° of low angle crystal boundaries.By relatively before the SRA of reality and cubic texture afterwards divide rate, cubic texture branch rate increases to 6% after the SRA by 5% before the SRA among the Fe-Al, and cubic texture branch rate is decreased to 2% after the SRA by 3% before the SRA among the Fe-Si.
Therefore, when grain growing, compare with Fe-Si, Fe-Al has the texture that more helps magnetic property, particularly cubic texture.To the observed result of this texture as can be known, under the situation of sample of the present invention, the intensity of cubic texture and branch rate all increase after SRA in the whole steel plate plane, obtain good magnetic property thus.
[embodiment 2]
Table 2
Composition shown in the table 2 is carried out vacuum melting, prepare steel ingot thus, steel ingot is heated to 1150 ℃ then, and 870 ℃ of hot rollings, make the hot-rolled steel sheet of thickness thus with 2.0mm, thereafter with hot-rolled steel sheet 1000 ℃ annealing 4min, pickling, being cold-rolled to thickness then is 0.5mm, under the condition cold-rolled steel sheet is being annealed separately afterwards.Then, in nitrogen atmosphere, implemented SRA 2 hours in 750 ℃.Use the sample obtain thus, annealing temperature by EBSD evaluation cold-rolled steel sheet and cubic texture divide the relation between the rate.
As can be seen from Table 2, when Fe-Al base cold-rolled steel sheet during, SRA after, help the branch rate increase of the cubic texture of magnetic property 770～830 ℃ of annealing.After SRA, in common Fe-Si, cubic texture divides rate below 3%, and in sample of the present invention, cubic texture divides rate more than 6%, and it is more than the twice of cubic texture branch rate among the Fe-Si.And as can be known in the present composition Al/Si greater than 1 and in each processing conditions the annealing temperature of cold-rolled steel sheet be under 770～830 ℃ the situation, after SRA, can mainly be formed with the texture that is beneficial to magnetic property.
[embodiment 3]
Table 3
Composition carries out vacuum melting shown in the his-and-hers watches 3, make steel ingot thus, then this steel ingot is heated to 1150 ℃, and, makes the hot-rolled steel sheet of thickness thus with 2.0mm 870 ℃ of hot rollings, afterwards, with hot-rolled steel sheet 1000 ℃ annealing 4min, pickling, being cold-rolled to steel plate thickness is 0.5mm, implement annealing then by being heated to 900 ℃, and 800 ℃ of equal thermal treatments of carrying out 30sec.Gained the results are shown under the title of " before the SRA " in the table 3 thus, and will be at 750 ℃ in nitrogen atmosphere under the title that the results are shown in " after the SRA " in the table 3 after the SRA 2 hours.With composition therefor in the present embodiment as the function of Al and Si and be plotted among Fig. 1.
The amount of Vickers' hardness and Al is closely related.Greater than 1 sample of the present invention, before SRA, it is extremely low to record Vickers' hardness for Al/Si, below 130Hv, and further reduces after SRA.In the present invention, compare before with SRA, magneticflux-density increases to more than the 1.74T after SRA.Compare before with SRA, the magneticflux-density of duplicate reduces after SRA.For sample of the present invention, iron loss significantly is decreased to below the 2.6w/kg, and for duplicate, iron loss is more much bigger than 2.6w/kg.Compare before with SRA, cubic texture branch rate increases to more than 6% after SRA in the sample of the present invention, but cubic texture divides rate to reduce in duplicate.
Therefore, can confirm after SRA, make the best composition ratio of magnetic property increase can be 1.4≤Si+Al≤2.4 and 1≤Al/Si≤5 owing to hanging down iron loss and high magnetic flux density.Described optimum range is corresponding to the scope in the thick line among Fig. 1.
Claims (10)
1. non-oriented electromagnetic steel sheet that after stress relief annealing SRA, has fine magnetic property, this steel plate comprises Si:0.2～1.0wt%, Al:0.9～2.0wt%, Mn:0.1～0.5wt%, P:0.01～0.05wt%, all the other are Fe and other unavoidable impurities, and wherein Si and Al satisfy 1.4≤Si+Al≤2.4 and 1≤Al/Si≤5.
2. the non-oriented electromagnetic steel sheet of claim 1 wherein after SRA, was compared increase before the cubic texture branch rate of section on the whole plane of described non-oriented electromagnetic steel sheet and SRA.
3. the non-oriented electromagnetic steel sheet of claim 1, wherein after SRA, the cubic texture of section divides rate more than 5%.
4. each non-oriented electromagnetic steel sheet among the claim 1-3, wherein said non-oriented electromagnetic steel sheet has the resistivity of 30～42 μ Ω cm.
5. each non-oriented electromagnetic steel sheet among the claim 1-3, wherein said unavoidable impurities comprise that C:0.003wt% is following, S:0.002wt% is following, below the N:0.002wt% and below the Ti:0.002wt%.
6. each non-oriented electromagnetic steel sheet among the claim 1-3, wherein said non-oriented electromagnetic steel sheet is in the Vickers' hardness that has before the SRA below the 130Hv.
7. each non-oriented electromagnetic steel sheet among the claim 1-3, wherein said non-oriented electromagnetic steel sheet have above magneticflux-density (B50) of 1.74T and the iron loss (W15/50) below the 2.6w/kg.
8. method for preparing the non-oriented electromagnetic steel sheet that after SRA, has fine magnetic property, this method comprises, steel ingot is reheated and hot rolling, described steel ingot contains Si:0.2～1.0wt%, Al:0.9～2.0wt%, Mn:0.1～0.5wt%, P:0.01～0.05wt%, all the other are Fe and other unavoidable impurities, wherein Si and Al satisfy 1.4≤Si+Al≤2.4 and 1≤Al/Si≤5, obtain hot-rolled steel sheet thus; Annealing and cold rolling this hot-rolled steel sheet obtain cold-rolled steel sheet thus; Cold-rolled steel sheet is annealed, and described annealing comprises and is heated to 850～950 ℃, then equal thermal treatment 30sec～4min under 770～830 ℃ of temperature.
9. the method for claim 8, the annealing of wherein said hot-rolled steel sheet is to keep the mode of 2～4min to anneal under 800～1100 ℃ the temperature in smelting furnace.
10. the method for claim 8, wherein said unavoidable impurities comprise that C:0.003wt% is following, S:0.002wt% is following, below the N:0.002wt% and below the Ti:0.002wt%.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| KR1020080134595A KR101110253B1 (en) | 2008-12-26 | 2008-12-26 | Non-oriented magnetic steel sheet with superior workability and manufacturing method thereof |
| KR10-2008-0134595 | 2008-12-26 | ||
| PCT/KR2009/007500 WO2010074447A2 (en) | 2008-12-26 | 2009-12-15 | Non-oriented electrical steel sheets having high workability for client companies and manufacturing method thereof |
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| Publication Number | Publication Date |
|---|---|
| CN102264922A true CN102264922A (en) | 2011-11-30 |
| CN102264922B CN102264922B (en) | 2013-11-13 |
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| CN200980152838XA Active CN102264922B (en) | 2008-12-26 | 2009-12-15 | Non-oriented electrical steel sheets having high workability for client companies and manufacturing method thereof |
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| Country | Link |
|---|---|
| JP (1) | JP5707333B2 (en) |
| KR (1) | KR101110253B1 (en) |
| CN (1) | CN102264922B (en) |
| WO (1) | WO2010074447A2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102869795A (en) * | 2010-02-26 | 2013-01-09 | 国立大学法人横滨国立大学 | Metallic material which is solid solution of body-centered cubic (bcc) structure having controlled crystal axis <001> orientation, and process for producing same |
| CN103534366A (en) * | 2011-12-19 | 2014-01-22 | Posco公司 | Grain-oriented electrical steel sheet having low core loss and high magnetic flux density, and method for manufacturing same |
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| KR102120276B1 (en) * | 2018-09-27 | 2020-06-08 | 주식회사 포스코 | Non-oriented electrical steel sheet and method for manufacturing the same |
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| JPH0757888B2 (en) * | 1989-05-26 | 1995-06-21 | 株式会社神戸製鋼所 | Manufacturing method of non-oriented electrical steel sheet with high magnetic flux density |
| JPH086135B2 (en) * | 1991-04-25 | 1996-01-24 | 新日本製鐵株式会社 | Manufacturing method of non-oriented electrical steel sheet with excellent magnetic properties |
| JP3603385B2 (en) * | 1995-04-21 | 2004-12-22 | Ｊｆｅスチール株式会社 | Non-oriented electrical steel sheet for compressor motors with excellent magnetic properties and coating adhesion |
| KR100268848B1 (en) * | 1996-10-08 | 2000-10-16 | 이구택 | Non oriented electric steel sheet with low hysterisis after stress removing annealing |
| JP3430830B2 (en) * | 1996-12-20 | 2003-07-28 | Ｊｆｅスチール株式会社 | Manufacturing method of non-oriented electrical steel sheet with excellent magnetic properties |
| JPH10183311A (en) | 1996-12-20 | 1998-07-14 | Kawasaki Steel Corp | Non-oriented silicon steel sheet excellent in blanking workability and magnetic characteristic |
| JP2001181806A (en) * | 1999-10-13 | 2001-07-03 | Nippon Steel Corp | Nonriented silicon steel sheet excellent in magnetic permeability, hot rolled sheet thereof and method for producing the same |
| JP2001192788A (en) * | 2000-01-12 | 2001-07-17 | Sumitomo Metal Ind Ltd | Nonoriented silicon steel sheet excellent in workability, and its manufacturing method |
| JP4707162B2 (en) * | 2000-02-28 | 2011-06-22 | 住友金属工業株式会社 | High strength non-oriented electrical steel sheet with excellent fatigue resistance and its manufacturing method |
| JP2003105508A (en) * | 2001-09-27 | 2003-04-09 | Nippon Steel Corp | Nonoriented silicon steel sheet having excellent workability, and production method therefor |
| JP4828095B2 (en) * | 2003-09-10 | 2011-11-30 | 新日本製鐵株式会社 | Non-oriented electrical steel sheet |
| CN1888112A (en) * | 2005-06-30 | 2007-01-03 | 宝山钢铁股份有限公司 | High magnetic induction and high grad non-orientation electrical steel and its making process |
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2008
- 2008-12-26 KR KR1020080134595A patent/KR101110253B1/en active IP Right Grant
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- 2009-12-15 WO PCT/KR2009/007500 patent/WO2010074447A2/en active Application Filing
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102869795A (en) * | 2010-02-26 | 2013-01-09 | 国立大学法人横滨国立大学 | Metallic material which is solid solution of body-centered cubic (bcc) structure having controlled crystal axis <001> orientation, and process for producing same |
| CN102869795B (en) * | 2010-02-26 | 2015-07-08 | 国立大学法人横滨国立大学 | Metallic material which is solid solution of body-centered cubic (bcc) structure having controlled crystal axis <001> orientation, and process for producing same |
| CN103534366A (en) * | 2011-12-19 | 2014-01-22 | Posco公司 | Grain-oriented electrical steel sheet having low core loss and high magnetic flux density, and method for manufacturing same |
| CN103534366B (en) * | 2011-12-19 | 2015-03-25 | Posco公司 | Grain-oriented electrical steel sheet having low core loss and high magnetic flux density, and method for manufacturing same |
Also Published As
| Publication number | Publication date |
|---|---|
| KR20100076518A (en) | 2010-07-06 |
| WO2010074447A2 (en) | 2010-07-01 |
| CN102264922B (en) | 2013-11-13 |
| JP2012512961A (en) | 2012-06-07 |
| KR101110253B1 (en) | 2012-03-13 |
| JP5707333B2 (en) | 2015-04-30 |
| WO2010074447A3 (en) | 2010-09-30 |
| WO2010074447A9 (en) | 2010-08-12 |
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