CN101346484B - Non-oriented electrical steel sheets with improved magnetic property and method for manufacturing the same - Google Patents
Non-oriented electrical steel sheets with improved magnetic property and method for manufacturing the same Download PDFInfo
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- CN101346484B CN101346484B CN2006800493271A CN200680049327A CN101346484B CN 101346484 B CN101346484 B CN 101346484B CN 2006800493271 A CN2006800493271 A CN 2006800493271A CN 200680049327 A CN200680049327 A CN 200680049327A CN 101346484 B CN101346484 B CN 101346484B
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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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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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
- C21D8/1216—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
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- 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
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
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- 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
- 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
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Abstract
The present invention relates to a non-oriented electrical steel sheet, widely used as an iron core in electric devices, and to a method of manufacturing the same. The non-oriented electrical sheet includes 0.004 wt. % or less C; 1.0-3.5 wt. % Si; 0.02 wt. % or l ess P ; 0.001 wt. % or less S ; 0.2-2.5 wt. % Al; 0.003 wt. % or less N; 0.004 wt. % or less Ti; Mn, in which the amount of thereof is represented by the following formula (1): 0.10+100 X S(wt. %) = Mn(wt. %) = 0.21+200 X S(wt. %) - (1); a balance of iron; and inevitable impurities. According to the present invention, final magnetic properties are greatly improved because fine precipitates are formed by S, the amount of Mn can be suitably determined in order to inhibit the formation of the fine precipitates, the formation of fineprecipitate CuS is inhibited because precipitates CuS, MnS are formed by adding Sn, Ni and Cu, and a texture, which determines a temperature of annealing a hot rolled steel plate and magnetic properties, is controlled, thereby manufacturing an inexpensive and optimum non-oriented electrical steel sheet.
Description
Technical field
The present invention relates to a kind of for example non-oriented electromagnetic steel sheet of the iron core in electric motor, the transformer etc. of power equipment that is widely used as, and relate to its preparation method, and, more specifically, relate to that a kind of wherein iron loss reduces and magneticflux-density improves, have non-oriented electromagnetic steel sheet of fine magnetic property and preparation method thereof.
Background technology
Usually, non-oriented electromagnetic steel sheet is electric energy to be changed into the essential vitals of mechanical energy in power equipment.For reducing energy expenditure, must reduce iron loss and improve magneticflux-density.Particularly, when improving magneticflux-density, can reduce the power loss in the power equipment, thereby make the power equipment can miniaturization.
This non-oriented electromagnetic steel sheet is used as for example electric motor, generator etc. and the fixture core material in the miniature transformer for example of rotating equipment, and is most important parts in these power equipments.When forming magnetic field by the supply electric current, iron core is used to improve magneticstrength.In the case, when the having excellent magnetic characteristics of non-oriented electromagnetic steel sheet, the efficient of electric motor is high and can reduce electrical loss.
Recently, the electrical sheet that is used to drive the electric motor of electromobile has caused extensive concern, is non-oriented electromagnetic steel sheet because be used for the most important material of electric motor.
The magnetic property of non-oriented electromagnetic steel sheet comprises iron loss and magneticflux-density.Iron loss is the loss that takes place when applying magnetic field, and magneticflux-density is producible merit when applying magnetic field, i.e. rotary power in the electric motor.Therefore, preferred iron loss is low, and needs the magneticflux-density height.
In the case, thickness that can be by reducing electrical sheet or roll up alloying element and reduce iron loss.But it is difficult not only having improved iron loss but also improved magneticflux-density.
For preparation has the material of low iron loss and high magnetic flux density, must prepare Clean Steel with small amount of impurities, perhaps must have the steel that improves magnetic property by adding other elements preparations.But wherein the problem of Cun Zaiing is, among the former, preparation cost is owing to the additional process in the preparation Clean Steel process increases, and among the latter, the cost of other elements is owing to the interpolation of other elements increases.
In non-oriented electromagnetic steel sheet, the factor that magnetic property is had influence comprises binder component and impurity composition, and the texturizing properties in grain size and the material (texture in materialproperties).
In the case, along with the raising of grain size, iron loss reduces.But,, therefore infer that texture is more important than grain size because when the magnetized texture of steel plate was not formed, although the steel plate granularity significantly improves, magnetic property is variation still.In texture, preferred (200) plane comprises that steel plate is easily at the magnetized crystalline orientation of the direction that is parallel to the milled sheet surface.In addition, preferably have less (111) plane or (211) plane.
In the routine techniques of non-oriented electromagnetic steel sheet, in the Japanese uncensored patent application of publication number 1996-283803, because the amount of Mn is limited to 0.1% or still less, it is difficult therefore making finer precipitates MnS alligatoring.
In addition, in the Japanese uncensored patent application of publication number 1996-283853, if possible, the amount of restriction impurity.But owing to there is a plurality of impurities, the amount of control impurity is difficult, and impurity it be unclear that with the relation of manufacturing condition.
In addition, in the Japanese uncensored patent application of the flat 11-222653 of publication number, when having described the amount that waits when the sulphur (S) that reduces as impurity, magnetic property improves, but the amount of sulphur (S) and manufacturing condition have nothing to do.
In addition, U.S. Patent No. 6,139,650 disclose a kind of non-oriented magnetic steel sheet and preparation method thereof, and wherein the amount of sulphur (S) reduces to 0.001% or still less, and has added element for example Sn, Sb etc. in addition.In this patent, though reduced the amount of impurity and added other elements, undeclared other components are with the relation between the manufacturing condition.
Summary of the invention
The technical problem to be solved in the present invention
The present invention sincerely remembers the above-mentioned problems in the prior art, therefore a target of the present invention is for providing non-oriented electromagnetic steel sheet that has fine magnetic property and preparation method thereof, wherein, even control impurity, magnetic property is also effectively improved, and remove the impurity that steel plate is had very big influence by the consideration working condition, thereby satisfy the requirement of required foreign matter content and working condition economically.
Technical scheme
For realizing above-mentioned target, the invention provides a kind of non-oriented electromagnetic steel sheet with fine magnetic property, it contains 0.004wt.% or C still less; 1.0 the Si of～3.5wt.%; 0.02wt.% or P still less; 0.001wt.% or S still less; 0.2 the Al of～2.5wt.%; 0.003wt.% or N still less; 0.004wt.% or Ti still less; Mn, wherein the amount of Mn is represented with following formula (1):
0.10+100 * S (wt.%)≤Mn (wt.%)≤0.21+200 * S (wt.%)---(1); Surplus is an iron; And unavoidable impurities.
In addition, non-oriented electromagnetic steel sheet of the present invention also can contain the Ni of Sb, 0.005-0.50wt.% of 0.005-0.07wt.% and the Cu of 0.005-0.20wt.%.
In addition, for realizing above-mentioned target, non-oriented electromagnetic steel sheet of the present invention is characterised in that following formula (2) expression of the texture coefficient (texture coefficient) of the mid-depth of prepared steel plate:
P200＞P211----(2)
In addition, for realizing above-mentioned target, the invention provides the method that a kind of preparation has the non-oriented electromagnetic steel sheet of fine magnetic property, may further comprise the steps: (steel slab) is rolled into steel plate with steel ingot, and described steel ingot has as above-mentioned composition; This hot-rolled steel sheet is carried out continuous annealing in the temperature range of being determined by following formula (3), the hot-rolled steel sheet annealing temperature depend on the amount of S in this continuous annealing stage: 771+165000 * S (wt.%)≤hot-rolled steel sheet annealing temperature (℃)≤851+195000 * S (wt.%)--(3); With annealed cold-rolling of steel plate; And cold-rolled steel sheet annealed, thereby obtain steel plate of the present invention.
In addition, for realizing above-mentioned target, prepare non-oriented electromagnetic steel sheet method of the present invention and be characterised in that, the texture coefficient of the mid-depth of the steel plate that makes is by representing with following formula (2).
In the case, it is characterized in that, in this steel ingot process of hot rolling, steel ingot is reheated to 1200 ℃ or following, and 680 ℃ or following curling, this cold-rolling of steel plate to the compression ratio (reduction ratio) with 70～88%, and is carried out continuous annealing with this steel plate under 800～1070 ℃ temperature.
Beneficial effect
According to the present invention, greatly improved final magnetic property, because tiny throw out is formed by S, the amount of Mn can be determined aptly so that suppress this tiny sedimentary formation, owing to formed throw out CuSMnS by adding Sn, Ni and Cu, therefore suppressed the formation of tiny throw out CuS, and controlled texture---the annealing temperature and the magnetic property of its decision hot-rolled steel sheet, thus make a kind of cheap and good non-oriented electromagnetic steel sheet.
Embodiment
Hereinafter will describe the preferred embodiments of the invention in detail.
In the non-oriented electromagnetic steel sheet that contains Si, Al and Mn, S is considered to form the impurity element of sulfide.In the present invention, thus providing a kind of effectively improves the method for magnetic property by control impurity.
In the present invention, add Mn and form tiny throw out CuS and MnS so that suppress S.
Herein, Mn is for suppressing a kind of element that tiny precipitation MnS and CuS add according to the amount of S.
Seen in (1), the amount of Mn is determined according to the amount of S.The preferred generation that suppresses unnecessary Mn as much as possible.
That is, the amount of Mn is determined according to the amount of S.
According to following formula (1), if the amount of Mn more than predetermined amount, then excessive Mn becomes impurity.
0.10+100×S(wt.％)≤Mn(wt.％)≤0.21+200×S(wt.％)---(1)
In addition, among the present invention, provide a kind of non-oriented electromagnetic steel sheet with fine magnetic property, wherein the amount of Mn depends on the amount of S, and the texture of the steel plate of preparation is represented with following formula (2).
In the case,---only supplying a spot of electric current to it also easily is magnetized---is (200) plane, comprises many＜100 even described texture〉direction, and according to the Horta formula, the texture coefficient that obtains in (200) plane is P200.
In addition, the plane that comprises in a large number in the crystalline structure and be difficult for being magnetized is (211) plane, and according to the Horta formula, the texture coefficient that obtains in (211) plane is P211.
Among the present invention, the texture coefficient in the steel plate that makes according to component of the present invention and preparation condition is with following formula (2) expression:
P200＞P211---(2)
In addition, for realizing target, the invention provides a kind of non-oriented electromagnetic steel sheet with fine magnetic property that obtains by the preparation method who may further comprise the steps, described step is: steel ingot is rolled into steel plate, and described steel ingot contains 0.004wt.% or C still less; 1.0 the Si of～3.5wt.%; 0.02wt.% or P still less; 0.001wt.% or S still less; 0.2 the Al of～2.5wt.%; 0.003wt.% or N still less; 0.004wt.% or Ti still less; Mn, wherein the amount of Mn is represented in order to following formula (1); Surplus is an iron; And unavoidable impurities; Hot-rolled steel sheet is carried out continuous annealing in the temperature range of being determined by following formula (3), the hot-rolled steel sheet annealing temperature depends on the amount of S in this continuous annealing stage; The cold-rolling of steel plate that this is annealed; And cold-rolled steel sheet annealed, thereby make steel plate of the present invention.
In the case, S precipitates into MnS, thereby and causes crystal grain tiny.This texture---it has the plane that can reduce in the throw out ambient magnetic owing to being easy to form, and therefore, if possible, the amount of S must be lacked.But the annealing temperature of hot-rolled steel sheet must change according to the amount of S in aftertreatment.
The hot-rolled steel sheet annealing temperature that depends on the amount of S is represented with following formula (3):
The annealing temperature of 771+165000 * S (wt.%)≤hot-rolled steel sheet (℃)≤851+195000 * S (wt.%)---(3)
In addition, for realizing target, the invention provides the method that a kind of preparation has the non-oriented electromagnetic steel sheet of fine magnetic property, wherein, with steel ingot---it contains Al, the 0.003wt.% of 0.004wt.% or C still less, 1.0～3.5wt.%Si, 0.02wt.% or P still less, 0.001wt.% or S still less, 0.2～2.5wt.% or N still less, 0.004wt.% or Ti still less, its amount Mn with following formula (1) expression; The iron of surplus; And unavoidable impurities---be rolled into steel plate, wherein said steel ingot is reheated to 1200 ℃ or following and 680 ℃ or following curling; With the annealing in of this hot-rolled steel sheet by the temperature range of following formula (3) expression; Annealed sheet steel is cold-rolled to has 70～85% compression ratio; And, obtain steel plate of the present invention with the temperature continuous annealing of cold-rolled steel sheet at 800～1070 ℃, wherein texture is represented with following formula (3).
The numerical limits condition of component ratio of the present invention hereinafter will be described.
[C:0.004wt.% or still less]
Thereby the magnetic property when causing the magneticaging phenomenon in the finished product and being reduced in these the finished product of use owing to C, so the amount of C is in 0.004wt.% or scope still less.And, because when the amount of C reduced, magnetic property was better, therefore preferably in the finished product amount of C be limited to 0.003wt.% or still less.
[Si：1.0～3.5wt.％]
Thereby Si is a kind of component that increases resistivity and reduce eddy losses in the iron loss.When the amount of Si is 1.0wt.% or still less the time, the texture that realization can strengthen magnetic property is difficult.On the contrary, when the amount of Si is 3.5wt.% when above, cold rolling performance reduces, thereby and the band phenomenon of rupture takes place.The amount of therefore preferred Si is limited in the scope of 1.0～3.5wt.%.
[P:0.02wt.% or still less]
Can add P, because it increases resistivity, and thereby improvement magnetic property.But in the present invention, P is isolated in the grain boundary and thereby suppresses the impurity of grain growing.
When adding excessive P, damage cold rolling performance.Therefore, the amount of preferred P is limited in 0.02wt.% or the scope still less.
[S:0.001wt.% or still less]
Because S forms MnS, it is a kind of tiny throw out, and thereby damage magnetic property, it is favourable therefore keeping low S amount.When the amount of S when 0.001wt.% is above, the amount of the Mn of interpolation must increase so that suppress tiny CuS throw out.In addition, when the amount of S excessively increases, the magnetic property variation.Therefore, the amount of preferred S is limited to 0.001wt.% or still less.
[Mn: the amount according to S represents that with formula (1) promptly numerical value is between 0.10+100 * S (wt.%) and 0.21+200 * S (wt.%)]
Thereby form MnS because Mn combines with S, MnS is a kind of tiny throw out that suppresses grain growing, therefore adds Mn so that MnS forms than first lees, and can prevent S in conjunction with forming CuS, and CuS is a kind of more tiny throw out.In addition, in the present invention, even because the amount of Mn can not be improved magnetic property more greatly, the therefore preferred Mn that adds 0.4wt.% or less amount.
Also preferably add Mn according to the amount of S by formula (1).
[Al：0.2～2.5wt.％]
Thereby add Al is because it is a kind of component that can effectively increase resistivity and reduce eddy losses.When adding the Al of 0.2wt.% or less amount, form a kind of throw out AlN that suppresses grain growing.On the contrary, when the amount of the Al that adds when 2.5wt.% is above because the improved degree of magnetic property is compared reduction with the amount of the Al that adds, the amount of therefore preferred Al is limited to 2.5wt.%.Therefore, add the interior Al of 0.2-2.5wt.% scope.
[N:0.003wt.% or still less]
Add minor N, thereby because it forms the growth that a kind of tiny and long AlN throw out suppresses crystal grain.In the present invention, the amount of preferred N is limited to 0.003wt.% or still less.
[Ti:0.005wt.% or still less]
Thereby Ti forms tiny TiN and TiC throw out and suppresses the growth of crystal grain.In the present invention, the amount of preferred T i is 0.005wt.% or still less.
When the amount of Ti when 0.005wt.% is above, form many tiny throw outs, so that texture is damaged, thereby reduces magnetic property.
[Sb：0.005-0.07wt.％]
Sb causes the grain boundary segregation phenomena, it is characterized by Sb and is embedded in the grain boundary and hot-rolled steel sheet annealing process surface of steel plate afterwards.In the present invention, adding Sb is to infiltrate the grain boundary because it suppresses S, prevents excessive grain growth, and (200) plane of growing in texture.When adding the Sb of 0.005wt.% or less amount, its additive effect is little.On the contrary, when adding 0.07wt.% or more Sb, additive effect reduces equally.Therefore, in the present invention, add the Sb in 0.005～0.07wt.% scope.
[Ni：0.005-0.50wt.％]
Adding Ni is because its improves texture, suppresses S and is precipitated as tiny CuS by adding with Sb and Cu, and have oxidation-resistance and erosion resistance.When adding the Ni of 0.005wt.% or less amount, the effect of interpolation is little.On the contrary, when adding 0.50wt.% or more Ni, additive effect reduces equally.Therefore, in the present invention, add the Ni in 0.005～0.50wt.% scope.
[Cu：0.005-0.20wt.％]
Adding Cu is because it improves texture, suppresses S and precipitates into tiny CuS, helps S to be precipitated as thicker CuS and MnS, and has anti-oxidant and erosion resistance.When adding the Cu of 0.005wt.% or less amount, additive effect is little.On the contrary, when adding 0.20wt.% or more during the Cu of volume, additive effect reduces equally.Therefore, in the present invention, add the Cu in 0.005～0.20Wt.% scope.
Composition of the present invention also comprises Fe and unavoidable impurities except that said components.
To reheat to 1200 ℃ or following by the steel ingot that said components is formed, hot rolling then.
In the method for hot-rolled steel ingot, steel ingot carries out roughing earlier and carries out finish rolling then.Herein, the steel that contains a small amount of Si and Al is earlier rolling, rolling in ferritic phase at last in mutually at austenite.Final rolling in the finish rolling process carries out in ferritic phase.In this hot-rolled step, rolling proceeding to has 40% final compression ratio to allow rectification plate shape.
To under envrionment conditions, cool off then by the hot-rolled steel sheet of above-mentioned preparation 680 ℃ or following curling.
When hot-rolled steel sheet is unannealed, can be with hot-rolled steel sheet 800 ℃ or following curling to substitute the annealing of hot-rolled steel sheet.
Reason is, when hot-rolled steel sheet during 800 ℃ or above curling, hot-rolled steel sheet may thereby be damaged the acid pickling performance by severe oxidation.
With the hot-rolled steel sheet that curls anneal, acid pickling, carry out cold rolling then.Hot-rolled steel sheet is annealed in the hot-rolled steel sheet annealing temperature of being determined by the amount according to S of formula (3) expression.
That is, the temperature of this hot-rolled steel sheet between 771+165000 * S (wt.%) and 851+195000 * S (wt.%) annealed.
Because the size of crystal grain depends on the influence of impurity, therefore the amount of the AlN that generates is controlled by the amount of the Al of interpolation.Especially, in the present invention, because the annealing temperature of hot-rolled steel sheet is by the amount restriction of S, therefore when hot-rolled steel sheet when being lower than the annealing temperature of 771+165000 * S (wt.%), the growth of crystal grain is insufficient, when hot-rolled steel sheet when being higher than the annealing temperature of 851+195000 * S (wt.%), texture is damaged.
The hot-rolled steel sheet annealing time is in 10 seconds to 10 hours scope.
Reason is that when annealing time was too short, crystal grain was not grown, and on the contrary, when annealing time was long, texture was damaged.
With hot-rolled steel sheet anneal, acid pickling, carry out cold rolling then.
In cold annealing process, hot-rolled steel sheet finally is rolled into the steel plate with 0.15mm to 0.70mm thickness.
In the case, preferred compression forms large-sized crystal grain in 70～88% scope so that in the finished product.
Cold-rolled steel sheet is at 800～1070 ℃ annealing temperature.In the case, when annealing temperature below 800 ℃ the time, grain growing is insufficient.On the contrary, when annealing temperature more than 1070 ℃ the time, the surface temperature of steel plate excessively increases, thereby forms surface imperfection on the surface of steel plate, and the over-dimension of crystal grain increases, thereby damages magnetic property.Therefore, the annealing temperature of preferred cold-rolled steel sheet is limited to 800～1070 ℃ temperature.
The annealed steel plate is transported to the human consumer after insulation film is handled.
The annealed steel plate can use organic film, inorganic thin film or organic, inorganic composite film to cover.In addition, the annealed steel plate can cover with other insulation films.
After this, the human consumer can directly use this steel plate after further handling.
Hereinafter, present invention is described with reference to embodiment.
Embodiment
[embodiment 1]
To reheat to 1100 ℃ temperature by the steel ingot that the component in the table 1 is formed, and carry out finally rolling in the course of hot rolling 860 ℃ temperature.
In the case, the final compression ratio in the finish rolling process is 18%.Rolling from Ingot is made the thickness of 1.8mm, curl 650 ℃ temperature then.
Hot-rolled steel sheet curled and under envrionment conditions, cool off, as shown in table 2, with this hot-rolled steel sheet anneal, acid pickling, the thickness that is cold-rolled to 0.35mm then forms cold-rolled steel sheet.Then this cold-rolled steel sheet was being annealed 1 minute in the atmosphere of 35% hydrogen and 65% nitrogen under 1050 ℃ the annealing temperature.
After the annealed sheet steel cutting, the texture coefficient that compares magnetic property and obtain according to the Horta formula.The result provides in table 2.
[table 1]
[table 2]
1) iron loss (W
15/50) be the loss (W/Kg) that when answering the magnetic field of 1.5 tesla's magneticflux-densities with the sensation of frequency of 50Hz, takes place.
2) magneticflux-density (B
50) be the intensity (tesla) of induced magnetic flux when using the magnetic field of 5000 A/m.
3) P200 and P211 are the texture coefficients with the metering of Horta formula, are 3 at steel plate mid-depth place or multiple-point mean value more.P200 is the crystallographic plane that helps magnetic property, and P211 is the crystallographic plane that is unfavorable for magnetic property.
As shown in table 2, can see, when working condition not simultaneously, even compositing range is identical, (A～D) the same reference product of product of the present invention (1～7) (1～2) of preparation is compared and is also had low iron loss and high magneticflux-density to use the steel of the present invention that satisfies compositing range of the present invention under working condition of the present invention.
In addition, what determine is, has the different contrast steel of forming (even A～E) prepare under identical working condition still has poor magnetic property.
And in contrast steel A, B and D, the amount of Mn surpasses higher limit of the present invention, and in contrast steel C and E, the amount of Mn does not surpass higher limit of the present invention.
[embodiment 2]
A kind of steel ingot contains 0.0021wt.%C; 2.52wt.%Si; 0.011wt.%P; 0.0005wt.%S; 0.55wt.%Al; 0.0012wt.%N; 0.0011wt.%Ti; 0.21wt.%Mn, wherein the preferred amounts of Mn is 0.15～0.31%; The iron of surplus; And unavoidable impurities.This steel ingot is reheated to 1150 ℃ temperature, carry out hot rolling then.In the hot rolling stage, the final rolling temperature at 880 ℃ in the finish rolling process proceeds to has 17% compression ratio, thereby obtains a kind of hot-rolled steel sheet of the 2.2mm of having thickness.
This hot-rolled steel sheet is curled 600 ℃ temperature, carry out air cooling then.Then, this hot-rolled steel sheet 920 ℃ temperature continuous annealing 5 minutes, is carried out acid pickling, be cold-rolled to the thickness of 0.5mm then.
In the case, the optimal temperature scope in the hot-rolled steel sheet annealing process is in 854～979 ℃ scope, and the cold-rolled steel sheet annealing process was carried out 1 minute 1000 ℃ temperature in the atmosphere of 70% nitrogen and 30% hydrogen.
The annealed steel plate with after covering of organic and inorganic compound inslation film and the cutting, is assessed the magnetic property and the grain-size of the steel plate that obtains.
In the magnetic property of steel plate, iron loss (W
15/50) be 2.52W/kg, and magneticflux-density (B
50) be 1.71 teslas.In addition, the texture coefficient at steel sheet product mid-depth place is 1.98 in P200, is 1.03 in P211, be 0.95 in (P200-P211), so P200 is greater than P211.
[embodiment 3]
A kind of steel ingot contains 0.0023wt.%C; 3.12wt.%Si; 0.004wt.%P; 0.0003wt.%S; 1.47wt.%Al; 0.0011wt.%N; 0.23wt.%Mn, wherein the preferred amounts of Mn is 0.13～0.27%; The iron of surplus; And unavoidable impurities.This steel ingot is reheated to 1220 ℃ temperature, carry out hot rolling then.
In the hot rolling stage, the outlet temperature in the finish rolling is 880 ℃, and the hot-rolled steel sheet of preparation has the thickness of 1.8mm.
This hot-rolled steel sheet is curled 620 ℃ temperature, carry out air cooling then.Then, with this hot-rolled steel sheet 890 ℃ annealing temperature 5 minutes.
In the case, the optimal temperature scope in the hot-rolled steel sheet annealing process is in 821 ℃～940 ℃ scope.The annealed hot-rolled steel sheet is carried out acid pickling, and the thickness that is cold-rolled to 0.35mm forms cold-rolled steel sheet, then with this cold-rolled steel sheet 850 ℃ annealing temperature 90 seconds.
With after the covering of organic and inorganic compound inslation film, drying is cut then, the magnetic property and the texture coefficient of the steel plate that assessment obtains with the annealed steel plate.
In the magnetic property of this steel plate, iron loss (W
15/50) be 1.95W/kg, and magneticflux-density (B
50) be 1.66 teslas.In addition, the texture coefficient at this steel sheet product mid-depth place is 2.02 in P200, and is 1.45 in P211.
[embodiment 4]
Will by in the table 3 the steel ingot formed to component---wherein add Mn---and reheat to 1130 ℃ temperature, and the temperature at 900 ℃ carried out finish rolling in the hot rolling stage with the amount of the Mn that provides in the table 4.In the hot rolling stage, steel plate has the thickness of 2.1mm, and curls 600 ℃ temperature.Will through curling and under envrionment conditions the hot-rolled steel sheet in the refrigerative table 3 by the temperature range that provides in the table 4 anneal, acid pickling, be cold-rolled to the thickness of 0.35mm then so that its compression ratio is 83%.Then, cold-rolled steel sheet was annealed 1 minute in the atmosphere of 40% hydrogen and 70% nitrogen 1040 ℃ annealing temperature.After the cutting of this annealed steel plate, the magnetic property of assessment and the steel plate that relatively obtains and the texture coefficient that obtains according to the Horta formula.The result provides in table 4.
[table 3]
[table 4]
[table 5]
1) iron loss (W
15/50) be the loss (W/Kg) that when answering the magneticflux-density of 1.5 teslas with the sensation of frequency of 50Hz, takes place.
2) magneticflux-density (B
50) be the intensity (tesla) of induced magnetic flux when applying the magnetic field of 5000 A/m.
3) P200 and P211 are the texture coefficients with the metering of Horta formula, and are 3 at steel plate mid-depth place or multiple-point mean value more.P200 is the crystallographic plane that helps magnetic property, and P211 is the crystallographic plane that is unfavorable for magnetic property.
As shown in table 5, can see, when working condition not simultaneously, even compositing range is identical, (A～C) product of the present invention (1～5,6) the same reference product (1～2) of preparation are compared and are also had low iron loss and high magneticflux-density to use the steel of the present invention that satisfies compositing range of the present invention under working condition of the present invention.In addition, according to assessment, has the contrast steel that is different from the present invention and forms under identical working condition (even A～C) prepare still has poor magnetic property.And in contrast steel A and C, the amount of Mn surpasses scope of the present invention, and in contrast steel B, the amount of Sb surpasses scope of the present invention.
[embodiment 5]
A kind of steel ingot contains 0.0023wt.%C; 3.2wt.%Si; 0.0051wt.%P; 0.0003wt.%S; 0.65wt.%Al; 0.0013wt.%N; 0.0015wt.%Ti; 0.02wt.%Sb; 0.04wt.%Ni; 0.05wt.%Cu; 0.23wt.%Mn, wherein the preferred amounts of Mn is 0.13-0.27wt.%; The iron of surplus; And unavoidable impurities.This steel ingot is reheated to 1100 ℃ temperature, carry out hot rolling then.In the hot rolling stage, the final rolling temperature at 860 ℃ in the finish rolling process is carried out, thereby makes a kind of hot-rolled steel sheet of the 2.1mm of having thickness.This hot-rolled steel sheet is curled 680 ℃ temperature,, carry out acid pickling, be cold-rolled to the thickness of 0.5mm then 890 ℃ temperature continuous annealings 5 minutes.In the case, the optimal temperature scope in the hot-rolled steel sheet annealing process is in 821～910 ℃ scope, and the cold-rolled steel sheet annealing process was carried out 1.5 minutes 1000 ℃ temperature under the environment of 60% nitrogen and 40% hydrogen.After the annealed steel plate covers and cuts with organic and inorganic compound inslation film, the magnetic property and the grain-size of the steel plate that assessment obtains.In the magnetic property of steel plate, iron loss (W
15/50) be 2.19W/kg, and magneticflux-density (B
50) be 1.69 teslas.In addition, the texture coefficient at steel sheet product mid-depth place is 2.70 in P200, is 1.21 in P211, be 1.49 in (P200-P211), so P200 is greater than P211.
[embodiment 6]
A kind of steel ingot contains 0.0021wt.%C; 3.5wt.%Si; 0.025wt.%P; 0.0004wt.%S; 1.35wt.%Al; 0.0012wt.%N; 0.0019wt.%Ti; 0.03wt.%Sb; 0.07wt.%Ni; 0.05wt.%Cu; 0.24wt.%Mn, wherein the preferred amounts of Mn is 0.14-0.29wt.%; The iron of surplus; And unavoidable impurities.This steel ingot is reheated to 1150 ℃ temperature, carry out hot rolling then.In the hot rolling stage, the outlet temperature in the finish rolling process is 880 ℃, and the hot-rolled steel sheet of preparation has 1.6mm thickness.This hot-rolled steel sheet is curled 600 ℃ temperature, then 910 ℃ annealing temperature 5 minutes.Optimal temperature scope in the hot-rolled steel sheet annealing process is in 837～929 ℃ scope.With the annealed hot-rolled steel sheet carry out acid pickling, the thickness that is cold-rolled to 0.35mm to be to form cold-rolled steel sheet, then will this cold rolling steel plate 850 ℃ annealing temperature 90 seconds.After the cutting of annealed steel plate, the magnetic property and the texture coefficient of the steel plate that assessment obtains.In the magnetic property of steel plate, iron loss (W
15/50) be 1.85W/kg, and magneticflux-density (B
50) be 1.65 teslas.In addition, the texture coefficient at this steel sheet product mid-depth place is 2.35 in P200 and is 1.12 in P211, so P200 is greater than P211.
Industrial applicibility
As mentioned above, according to the present invention, greatly improved final magnetic property, because S forms tiny precipitation, the amount of Mn can be determined aptly in order to suppress this tiny sedimentary formation, owing to formed sediment CuS, MnS by adding Sn, Ni and Cu, has therefore suppressed the formation of tiny sediment CuS, and controlled texture---annealing temperature and the magnetic property of its decision hot rolled steel plate, thereby make a kind of cheap and good non-oriented electromagnetic steel sheet.
Claims (5)
1. non-oriented electromagnetic steel sheet with fine magnetic property, contain:
0.004wt.% or C still less;
1.0 the S i of～3.5wt.%;
0.02wt.% or P still less;
0.001wt.% or S still less;
0.2 the Al of～2.5wt.%;
0.003wt.% or N still less;
0.004wt.% or Ti still less;
Mn, wherein the amount of Mn is represented with following formula (1):
0.10+100×S(wt.％)≤Mn(wt.％)≤0.21+200×S(wt.％)---(1)；
The iron of surplus; And
Unavoidable impurities;
The texture coefficient at the mid-depth place of the steel plate that wherein, makes is represented by following formula (2):
P200＞P211----(2)，
Wherein P200 is the texture coefficient that obtains in (200) plane, the texture coefficient of P211 for obtaining in (211) plane.
2. according to the non-oriented electromagnetic steel sheet with fine magnetic property of claim 1, wherein said electrical sheet also contains the Ni of Sb, 0.005-0.50wt.% of 0.005～0.07wt.% and the Cu of 0.005～0.20wt.%.
3. method for preparing the non-oriented electromagnetic steel sheet with fine magnetic property comprises following steps:
A kind of steel ingot with composition described in the claim 1 is rolled into steel plate;
This hot-rolled steel sheet is annealed in the temperature range by following formula (3) expression of the amount that depends on S:
The annealing temperature of 771+165000 * S (wt.%)≤rolled sheet material (℃)≤851+195000 * S (wt.%)---(3);
With this annealed cold-rolling of steel plate; And
This cold-rolled steel sheet is annealed, thereby obtain described steel plate;
Wherein the texture coefficient at the mid-depth place of the steel plate that makes through described method is by following formula (2) expression:
P200＞P211----(2)，
Wherein P200 is the texture coefficient that obtains in (200) plane, the texture coefficient of P211 for obtaining in (211) plane.
4. the method that has the non-oriented electromagnetic steel sheet of fine magnetic property according to the preparation of claim 3, wherein:
In this steel ingot process of hot rolling, described steel ingot is reheated to 1200 ℃ or following and curl 680 ℃ or following temperature,
Described steel plate is cold-rolled to has 70～88% compression ratio, and
This cold-rolled steel sheet is carried out continuous annealing 800～1070 ℃ temperature.
5. have the method for the non-oriented electromagnetic steel sheet of fine magnetic property according to the preparation of claim 3 or 4, wherein said steel ingot also contains the Sb of 0.005～0.07wt.%, the Ni of 0.005～0.50wt.% and the Cu of 0.005～0.20%wt.%.
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| KR1020050130388A KR100733345B1 (en) | 2005-12-27 | 2005-12-27 | Non-oriented electrical steel sheets with improved magnetic property and method for manufacturing the same |
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| KR1020050130388 | 2005-12-27 | ||
| KR1020060127865 | 2006-12-14 | ||
| KR10-2006-0127865 | 2006-12-14 | ||
| KR1020060127865A KR100832342B1 (en) | 2006-12-14 | 2006-12-14 | Non-oriented electrical steel sheets with improved magnetic property and method for manufacturing the same |
| PCT/KR2006/005521 WO2007074987A1 (en) | 2005-12-27 | 2006-12-18 | Non-oriented electrical steel sheets with improved magnetic property and method for manufacturing the same |
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| TWI531663B (en) * | 2013-04-09 | 2016-05-01 | 新日鐵住金股份有限公司 | Non-oriented electrical steel sheet and manufacturing method thereof |
| CN103388106A (en) * | 2013-06-27 | 2013-11-13 | 宝山钢铁股份有限公司 | Non-oriented electrical steel plate with high magnetic induction and low iron loss, and manufacturing method thereof |
| CN103667900B (en) * | 2013-11-28 | 2016-01-06 | 安徽银力铸造有限公司 | A kind of preparation method of high-magnetic-strengelectrical electrical steel for automobile motor |
| KR101701194B1 (en) * | 2015-12-23 | 2017-02-01 | 주식회사 포스코 | Non-oriented electrical steel sheet and method for manufacturing the same |
| KR101901313B1 (en) | 2016-12-19 | 2018-09-21 | 주식회사 포스코 | Non-oriented electrical steel sheet and method for manufacturing the same |
| KR101902438B1 (en) | 2016-12-19 | 2018-09-28 | 주식회사 포스코 | Non-oriented electrical steel sheet and method for manufacturing the same |
| CN107587039B (en) * | 2017-08-30 | 2019-05-24 | 武汉钢铁有限公司 | The driving motor for electric automobile non-orientation silicon steel and production method of excellent magnetic |
| CN107974620B (en) * | 2017-12-01 | 2019-10-25 | 武汉钢铁有限公司 | A kind of yield strength >=600Mpa high speed rotor of motor non-orientation silicon steel and production method |
| 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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| US5074930A (en) * | 1988-03-11 | 1991-12-24 | Nkk Corporation | Method of making non-oriented electrical steel sheets |
| CN1039352C (en) * | 1991-10-22 | 1998-07-29 | 浦项综合制铁株式会社 | Unoriented electrical engineering steel plate with good magnetism and manufacture of same |
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| KR920005619B1 (en) * | 1989-12-29 | 1992-07-10 | 포항종합제철 주식회사 | Making process for electrical steel sheet |
| JP3307872B2 (en) | 1998-02-06 | 2002-07-24 | 新日本製鐵株式会社 | Motor for electric vehicle using non-oriented electrical steel sheet and method of manufacturing the electrical steel sheet |
| KR20020052863A (en) * | 2000-12-26 | 2002-07-04 | 이구택 | Method for manufacturing non-oriented silicon steel |
| KR100940719B1 (en) * | 2002-12-23 | 2010-02-08 | 주식회사 포스코 | Method for manufacturing non-oriented electrical steel sheet having higher magnetic induction after stress relief annealing |
| JP3931842B2 (en) | 2003-06-11 | 2007-06-20 | 住友金属工業株式会社 | Method for producing non-oriented electrical steel sheet |
| JP4329550B2 (en) | 2004-01-23 | 2009-09-09 | 住友金属工業株式会社 | Method for producing non-oriented electrical steel sheet |
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| US5074930A (en) * | 1988-03-11 | 1991-12-24 | Nkk Corporation | Method of making non-oriented electrical steel sheets |
| CN1039352C (en) * | 1991-10-22 | 1998-07-29 | 浦项综合制铁株式会社 | Unoriented electrical engineering steel plate with good magnetism and manufacture of same |
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