CN102264922B - 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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- CN102264922B CN102264922B CN200980152838XA CN200980152838A CN102264922B CN 102264922 B CN102264922 B CN 102264922B CN 200980152838X A CN200980152838X A CN 200980152838XA CN 200980152838 A CN200980152838 A CN 200980152838A CN 102264922 B CN102264922 B CN 102264922B
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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
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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
- 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
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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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- 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
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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 afterwards non-oriented electromagnetic steel sheet He this steel plate of fine magnetic property at SRA (stress relief annealing), more specifically, relate to a kind of preparation method who has non-oriented electromagnetic steel sheet and this steel plate of good workability and magnetic property after suitably adjusting steel constituent and processing conditions.
Background technology
Recently, non-oriented electromagnetic steel sheet, it is a kind of required vitals of mechanical energy that in rotating equipment, electric energy conversion become, and need to have magnetic property, i.e. low iron loss and high magneticflux-density, so that energy saving.Particularly, iron loss is the energy that loses with form of heat in energy conversion process, therefore the lower efficiency that more can improve rotating equipment of iron loss, and magneticflux-density is as a kind of strength that produces power, and the efficiency of the higher rotating equipment of magneticflux-density is also higher.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 wound on it, thus be used for power equipment.
, for realizing iron loss low in 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, inhibition of impurities and increase grain fineness number in steel plate.
In addition, in the iron loss of non-oriented electromagnetic steel sheet, the hysteresis loss proportion is 60～80%, and due to when preparing steel plate, with which, so its inhibition is difficult to impurity, and cost increases while suppressing.Therefore, preferably by the texture that increases grain fineness number or generation easy magnetization, improve iron loss and magneticflux-density.
About described texture, if＜100---it is easy magnetized direction in normal direction (ND)---being positioned at the surface of steel plate, is optimal.As 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, as 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) at surface of steel plate, be more ubiquitous.Although 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, minute rate of the orientation favourable to magnetic (for example cubic texture ({ 001}＜100 〉)), reduce when cold rolling and grain growing, and its value is reduced to below 3%.Therefore need a kind of composition that can increase the favourable cubic texture aggregation degree of magnetic of exploitation, and can improve the 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 repeatedly studying and testing for solving the problems referred to above that run in prior art, and based on its result, made the present invention, a target of the present invention is to provide 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 afterwards fine magnetic property at SRA (Stress Relief Annealing), 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 inevitable impurity, and wherein Si and Al meet 1.4≤Si+Al≤2.4 and 1≤Al/Si≤5.
In non-oriented electromagnetic steel sheet of the present invention, after SRA, the cubic texture of section (cube texture) minute rate is compared increase before with SRA on the whole plane of described non-oriented electromagnetic steel sheet.
In non-oriented electromagnetic steel sheet of the present invention, after SRA, the cubic texture of section (cube texture) minute 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 inevitable impurity can comprise below C:0.003wt%, below S:0.002wt%, and below N:0.002wt%, and below Ti:0.002wt%.
Non-oriented electromagnetic steel sheet of the present invention is in the Vickers' hardness that has before SRA below 130Hv.
Non-oriented electromagnetic steel sheet of the present invention can have the 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 method for preparing the non-oriented electromagnetic steel sheet that has fine magnetic property after SRA, the 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 inevitable impurity, wherein Si and Al meet 1.4≤Si+Al≤2.4 and 1≤Al/Si≤5, obtain thus hot-rolled steel sheet; 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 at 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 at the temperature of 800～1100 ℃ in smelting furnace.
The present invention prepares in the method for non-oriented electromagnetic steel sheet, and described inevitable impurity can comprise below C:0.003wt%, below S:0.002wt%, and below N:0.002wt%, and below 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 is conducive to, also increase grain fineness number, thereby effectively provide a kind of, client company has been had for example effect of the non-oriented electromagnetic steel sheet and preparation method thereof of low iron loss and high magnetic flux density of good workability and magnetic.
Description of drawings
Fig. 1 is the figure that shows the relation between Al and Si.
Fig. 2 is the structure iron that schematically shows texture.
Fig. 3 meaned sample of the present invention and duplicate before SRA and orientation distribution function afterwards (ODF).
Fig. 4 understands ODF and the figure of the Φ 2=45 ° section (section) that represents.
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 and Si use with different amounts, magnetic property, the 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%, the sosoloid C in 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.For 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%, the hardness of steel plate increases, and has reduced thus stamping-out.Therefore, the amount of Si is limited to 0.2～1.0%.
Aluminium (Al) can increase resistance with Si is the same, reduces thus eddy losses, thereby reduces iron loss.Compare with the Si of same amount, the degree that Al increases steel plate hardness is less, therefore increases simultaneously workability and magnetic property, so be important element.For increasing simultaneously workability and magnetic property, the consumption of Al is preferably more than 0.9%.But,, if its amount surpasses 2.0%, can make the formability variation, and when preparing 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%, 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 large solid solution hardening effect, and has the intra-face anisotropy of improvement and propose high-intensity effect.The consumption of P can be more than 0.01%, in order to promote the formation of texture.But if the content of P surpasses 0.05%, 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 thus the magnetic property variation, therefore should control its amount the least possible.If use excessive S, 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 Growable 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 thus crystal grain also promotes to be unfavorable for the texture of magnetic property, namely 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 thus iron loss, therefore should make the value of Si+Al more than 1.4.But, if the value of Si+Al surpasses 2.4, the cold rolling difficulty that becomes.
For further improving magnetic property, the value of preferred Al/Si meets 1≤Al/Si≤5.If the value of Al/Si is less than 1, a cubic texture minute rate reduces after SRA.Comparatively speaking, if the value of Al/Si surpasses 5, when preparing steel because 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 consider these two kinds of elements and select suitable content.
In the present invention, comprise a kind of cubic texture at section on whole steel plate plane (cube texture) minute rate increases before than SRA after SRA non-oriented electromagnetic steel sheet, also comprise a kind of after SRA the cubic texture minute 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 SRA, and iron loss (W15/50) is below 2.6w/kg.
The invention provides a kind of method for preparing described steel plate, the 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 inevitable impurity, wherein Si and Al meet 1.4≤Si+Al≤2.4 and 1≤Al/Si≤5, obtain thus hot-rolled steel sheet; Annealing and cold rolling this hot-rolled steel sheet, prepare cold-rolled steel sheet thus; Then with it 770～830 ℃ of annealing.Described inevitable impurity comprises that C:0.003wt% is following, S:0.002wt% following, below N:0.002wt%, and below Ti:0.002wt%.
Described hot-rolled steel sheet can be in smelting furnace keeps 2～4min time inside furnace to anneal at the temperature of 800～1100 ℃.If anneal at the temperature lower than 800 ℃, and time inside furnace is less than 2min, and texture possibly can't be grown or fine growth, and the degree that magneticflux-density is increased diminishes.Comparatively speaking, if anneal at the temperature higher than 1100 ℃, and time inside furnace is greater than 4min, although texture can fully grow, energy waste for the improvement of magneticflux-density too much.
In addition, described cold-rolled steel sheet is annealed in the temperature range of 770～830 ℃.If annealing temperature is lower than 770 ℃, abundant recrystallization, at first produce the texture that is unfavorable for magnetic property thus when SRA.Comparatively speaking, if annealing temperature higher than 830 ℃, crystal grain greatly grew before SRA 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, to be heated to after 850～950 ℃, is carried out all heat treated modes of 30sec～4min and is carried out at 770～830 ℃ of temperature.Fully guarantee cubic texture even be heated to 850～950 ℃, when carrying out equal thermal treatment in the said temperature scope, on cubic texture, divide rate to produce adversely impact.Therefore,, by described cold-rolled steel sheet is heated to the said temperature scope, then reduces temperature and carry out equal thermal annealing, thereby keep higher cubic texture to divide rate.
Therefore in addition,, due to being grown in lower than insufficient at the temperature of 850 ℃ of recrystallization grains, have the orientation that is unfavorable for magnetic property＜111〉the amount of texture increase, cubic texture divides rate to reduce thus.Comparatively speaking, if temperature higher than 950 ℃, 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, the crystal grain of cold-rolled steel sheet can't recrystallize, to cubic texture, divides rate to produce adverse influence.Comparatively speaking, if annealing time greater than 4min, 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 intrinsic resistance (ρ) is represented by following equation.
Show in following table 1, 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 thus hot-rolled steel sheet, and its thickness is 2.0mm.Described hot-rolled steel sheet, at 1000 ℃ of annealing 4min, then is cold-rolled to 0.5mm, thereafter the cold-rolled steel sheet of gained is heated to 900 ℃, 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, with EBSD (Electron Back-Scattered Diffraction (Electron Back Scattered Diffraction)), the section (TD direction) before and after SRA is observed.The orientation distribution function as a result (ODF, Orientation Distribution Function) that obtains is shown in 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 in ODF
2The section of=45 ° carries out graphic extension, 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 Φ 2=45 ° section in ODF.The position of texture shown in Fig. 4 is desirable position, usually uses level line to represent the intensity of texture.
In non-oriented electromagnetic steel sheet, comprise cubic texture ({ 001}＜100 〉) and rotation cubic texture ({ 001}＜110 〉)＜100 //minute rate of ND is more, and is more favourable to magnetic property.Particularly, minute 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 less just more favourable to magnetic property.
As shown in Figure 3, no matter whether implement SRA, the maximum strength (f (g) max) of Fe-Al base F1 texture is all higher than the maximum strength of the basic F12 texture of Fe-Si.Think that this is because formed Fe-Al base F1 texture is more firm.For Fe-Al base F1, before its cubic texture after SRA (F (g) max=6.4) and SRA, the phase specific tenacity of (F (g) max=5.3) is higher.
Minute 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, in Fe-Al, cubic texture minute rate increases to 6% after SRA by 5% before SRA, and in Fe-Si, cubic texture minute rate is decreased to 2% after SRA by 3% before SRA.
Therefore, when grain growing, with Fe-Si, compare, Fe-Al has the texture that more is conducive to magnetic property, particularly cubic texture.To the observed result of this texture as can be known, in the situation that sample of the present invention, in whole steel plate plane, all increases SRA after of the intensity of cubic texture and minute rate, obtain good magnetic property thus.
[embodiment 2]
Table 2
Composition shown in table 2 is carried out vacuum melting, prepare thus steel ingot, then with Heating Steel Ingots to 1150 ℃, and 870 ℃ of hot rollings, make thus the hot-rolled steel sheet of the thickness with 2.0mm, thereafter with hot-rolled steel sheet 1000 ℃ annealing 4min, pickling, then being cold-rolled to thickness is 0.5mm, under condition, cold-rolled steel sheet is being annealed separately afterwards.Then, implemented SRA 2 hours in 750 ℃ in nitrogen atmosphere.Use the sample that obtains thus, by EBSD, evaluate the annealing temperature of cold-rolled steel sheet and the relation between cubic texture minute rate.
As can be seen from Table 2, when annealing for 770～830 ℃, minute rate that is conducive to the cubic texture of magnetic property after SRA increases when Fe-Al base cold-rolled steel sheet.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 minute rate in Fe-Si.And as can be known in the present composition Al/Si greater than 1 and in the situation that in each processing conditions the annealing temperature of cold-rolled steel sheet be 770～830 ℃, can mainly be formed with the texture that is beneficial to magnetic property after SRA.
[embodiment 3]
Table 3
Shown in his-and-hers watches 3, composition carries out vacuum melting, make thus steel ingot, then, with this Heating Steel Ingots to 1150 ℃, and 870 ℃ of hot rollings, make thus the hot-rolled steel sheet of the thickness with 2.0mm, afterwards, with hot-rolled steel sheet 1000 ℃ annealing 4min, pickling, being cold-rolled to steel plate thickness is 0.5mm, then by being heated to 900 ℃, and 800 ℃ of equal thermal treatments of carrying out 30sec, implement annealing.Acquired results is shown in Table 3 under the title of " before SRA " thus, and will 750 ℃ in nitrogen atmosphere after SRA 2 hours the results are shown in table 3 under the title of " after SRA ".Composition therefor in the present embodiment is plotted in Fig. 1 as the function of Al and Si.
The amount of Vickers' hardness and Al is closely related., greater than 1 sample of the present invention, before SRA, record Vickers' hardness extremely low for Al/Si, below 130Hv, and further reduce after SRA.In the present invention, compare before with SRA, magneticflux-density increases to 1.74T after SRA more than.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 2.6w/kg, and for duplicate, iron loss is more much bigger than 2.6w/kg.Compare before with SRA, in sample of the present invention, a cubic texture minute rate increases to more than 6% after SRA, but cubic texture divides rate to reduce in duplicate.
Therefore, can confirm after SRA, owing to hanging down iron loss and high magnetic flux density, make the best composition ratio of magnetic property increase can be 1.4≤Si+Al≤2.4 and 1≤Al/Si≤5.Described optimum range is corresponding to the scope in thick line in Fig. 1.
Claims (5)
1. non-oriented electromagnetic steel sheet that has fine magnetic property after stress relief annealing SRA, 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 inevitable impurity, wherein Si and Al meet 1.4≤Si+Al≤2.4 and 1≤Al/Si≤5, wherein said inevitable impurity comprises below C:0.003wt%, below S:0.002wt%, and
Wherein after SRA, compared increase before the cubic texture minute rate of section on the whole plane of described non-oriented electromagnetic steel sheet and SRA, and after SRA, the cubic texture of section divides rate more than 5%, described non-oriented electromagnetic steel sheet have 30～42 μ Ω ㎝ resistivity, have the above magneticflux-density (B50) of 1.74T and the iron loss (W15/50) below 2.6w/kg and in the Vickers' hardness that has before SRA below 130Hv.
2. the non-oriented electromagnetic steel sheet of claim 1, wherein said inevitable impurity also comprises below N:0.002wt%, and below Ti:0.002wt%.
3. method for preparing the non-oriented electromagnetic steel sheet that has fine magnetic property after SRA, the 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 inevitable impurity, wherein Si and Al meet 1.4≤Si+Al≤2.4 and 1≤Al/Si≤5, obtain thus hot-rolled steel sheet; 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 ℃, equal thermal treatment 30sec～4min at 770～830 ℃ of temperature then,
Wherein said inevitable impurity comprises below C:0.003wt%, below S:0.002wt%.
4. the method for claim 3, the annealing of wherein said hot-rolled steel sheet is to keep the mode of 2～4min to anneal at the temperature of 800～1100 ℃ in smelting furnace.
5. the method for claim 3, wherein said inevitable impurity also comprise below N:0.002wt%, and below Ti:0.002wt%.
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| 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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| JP5782527B2 (en) * | 2011-12-19 | 2015-09-24 | ポスコ | Low iron loss high magnetic flux density grained electrical steel sheet and manufacturing method thereof |
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| 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 |
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| 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 |
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| JP4828095B2 (en) * | 2003-09-10 | 2011-11-30 | 新日本製鐵株式会社 | Non-oriented electrical steel sheet |
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| WO2010074447A2 (en) | 2010-07-01 |
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| JP5707333B2 (en) | 2015-04-30 |
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| JP2012512961A (en) | 2012-06-07 |
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