CN1131532C - Orientationless electric steel plate with fine mangetic performance and manufacturing method thereof - Google Patents

Orientationless electric steel plate with fine mangetic performance and manufacturing method thereof Download PDF

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Publication number
CN1131532C
CN1131532C CN97120376A CN97120376A CN1131532C CN 1131532 C CN1131532 C CN 1131532C CN 97120376 A CN97120376 A CN 97120376A CN 97120376 A CN97120376 A CN 97120376A CN 1131532 C CN1131532 C CN 1131532C
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electromagnetic steel
oriented electromagnetic
manufacture method
carry out
annealing
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CN1190241A (en
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裴秉根
张三奎
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Pohang Comprehensive Iron And Steel Co Ltd
Posco Co Ltd
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Pohang Comprehensive Iron And Steel Co Ltd
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    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/14766—Fe-Si based alloys
    • H01F1/14775—Fe-Si based alloys in the form of sheets
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
    • C21D8/1222—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
    • C21D8/1233—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
    • C21D8/1272—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon

Abstract

The present invention is related to a non-oriented magnetic steel plate and a process for making the same. The objective of the present invention is to provide a non-oriented magnetic steel plate with a high magnetic permeability and a process for making the same. The non-oriented magnetic steel plate according to the present invention comprises: less than 0.02% of C, less than 1.0% of Si, less than 0.5% of Mn, less than 0.15% of P, less than 0.02% of S, less than 0.005% of Sol.Al, less than 0.006% of N, 0.03 to 0.30% of Sn, and 0.0004 to 0.003% of B. Preferably, the B/N ratio is 0.1 to 0.5. Furthermore, the steel plate also comprises Fe and other inevitable impurities.

Description

Non-oriented electromagnetic steel sheet that has excellent magnetic characteristics and manufacture method thereof
Technical field
The present invention relates to non-oriented electromagnetic steel sheet and the manufacture method thereof used in the iron core etc. of the electricapparatus as middle-size and small-size motor and transformer, relate to particularly that iron loss is low, magnetic flux density and high non-oriented electromagnetic steel sheet and the manufacture method thereof of permeability.
Background technology
In general, non-oriented electromagnetic steel sheet is used for electric energy is transformed into the rotation energy, produces the motor of power or with the transformer of input voltage buck or boost etc., and truth is that the major part consumption of energy output is in such use.
Therefore, the magnetic property of non-oriented electromagnetic steel sheet is directly connected to energy loss, sees it is important from the conserve energy aspect, and especially iron loss, magnetic flux density and permeability are important in magnetic property.
Apply certain magnetic flux density, by relatively iron loss and/or permeability, magnetic property that can more above-mentioned steel plate.
On the one hand, non-oriented electromagnetic steel sheet is classified according to Si content, in view of the above, can divide into Si content and be raw material and 1.0% above raw material below 1.0%, if Si content height, then resistance increases, and iron loss also reduces, but magnetic flux density and permeability reduce.
Iron loss means energy loss in magnetic property, can divide into magnetic hysteresis loss and eddy current loss.
Eddy current loss depends on raw-material composition and thickness, and magnetic hysteresis loss depends primarily on impurity element and manufacture method thereof, but the magnetic hysteresis loss proportion is big in iron loss, therefore is necessary to reduce magnetic hysteresis loss by the control manufacture method.
Increase the method for permeability as reducing magnetic hysteresis loss, known have the method that reduces impurity element S, N and oxygen etc., but this method is in order to contain these elements as few as possible, the time of cost length and big manufacturing expense in steelmaking process.
Especially be 1.0% when following at Si content, need to reduce the influence of N, so by make grain growth, make the texture that helps magnetic 200}＜hk1〉and 110}＜wxy〉develop well, improve magnetic property with this.
In Japanese kokai publication sho 63-33518, disclosed and contained 1.0～1.5%Mn, improve the method for magnetic property, still, the rolling property deterioration of this method, and, the problem that increases manufacturing cost is arranged owing to add Al etc.
And then, disclose in 0084980 at european patent application, disclosed and added Sn and B, regulate B and N ratio, make B/N than the method that reaches 0.5～1.5.Yet the B/N of this method is than high, and therefore not only the addition of B is many, and must add Al.
On the other hand,, many effort have also been poured in the improvement of manufacturing process,, can enumerate and after hot rolling, carry out hot rolled plate annealing, after cold-reduced sheet annealing, carried out the method for dress rolling (skin-pass) etc. then as its example in order to reduce magnetic hysteresis loss, to increase permeability.
But existing in above-mentioned manufacture method increases operation, must carry out the problem that the problem of stress relief annealing and the plate shape behind the dress rolling worsen when needing.
Summary of the invention
Therefore, the inventor is in order to solve the problem of above-mentioned conventional art, many-side is studied, the result has confirmed from containing N inevitably, the B amount that can adjust arbitrarily of control more energetically by only adding the Al that uses as deoxidation, suppresses the separating out of B precipitate that AlN and other are harmful to magnetic property, improve magnetic property, propose the present invention based on this.
The objective of the invention is to, provide that iron loss is low, magnetic flux density and high non-oriented electromagnetic steel sheet and the manufacture method thereof of permeability.
Another object of the present invention is to,, suppress the precipitate of B and N, good non-oriented electromagnetic steel sheet of permeability and manufacture method thereof are provided by suitably controlling the ratio of B and N.
The non-oriented electromagnetic steel sheet that has excellent magnetic characteristics that non-oriented electromagnetic steel sheet of the present invention is following by C:0.02 weight % (hereinafter to be referred as " % "), Si:1.0%, Mn:0.5% following, P:0.15% following, S:0.02% is following, solid solution Al:0.005% is following, N:0.006% is following, Sn:0.03～0.30%, B:0.0004～0.003% and all the other are formed for Fe and other unavoidable impurities.
And above-mentioned non-oriented electromagnetic steel sheet is that the ratio of B/N satisfies 0.1～0.5 the good non-oriented electromagnetic steel sheet of permeability.
And then, the invention provides the method for making non-oriented electromagnetic steel sheet, to contain below the C:0.02 weight % (hereinafter to be referred as " % "), below the Si:1.0%, below the Mn:0.5%, below the P:0.15%, below the S:0.02%, below the solid solution Al:0.005%, below the N:0.006%, Sn:0.03～0.30%, B:0.0004～0.0030%, the ratio of B/N satisfies 0.1～0.5, all the other plate slabs for Fe and other unavoidable impurities composition heat again, after carrying out hot rolling, batch in the temperature below 750 ℃, carry out hot rolled plate annealing then, perhaps do not carry out hot rolled plate annealing and carry out pickling, then carry out cold rolling after, under 700～1050 ℃ temperature, implement cold-reduced sheet annealing, make the method for the non-oriented electromagnetic steel sheet that has excellent magnetic characteristics with this.
And the manufacture method of above-mentioned non-oriented electromagnetic steel sheet of the present invention is the manufacture method that the ratio of B/N satisfies the good non-oriented electromagnetic steel sheet of 0.1～0.5 permeability.
Below explain the present invention.
The present invention is that the steel of the composition below 1.0% will reduce N content as far as possible for Si content, thereby the method that magnetic property is improved is provided.
N generally separates out with the AlN precipitate of tiny and wire from end article, owing to suppress grain growth, makes the magnetic deterioration.
For the influence that makes N minimizes, by interpolation intercrystalline segregation element S n, so that the big B of the adhesion of interpolation and N, in steel, be suppressed at the N in steel-making stage and the N of rolling and annealing stage effectively, can improve magnetic.
At Si content is in the steel of the composition below 1.0%, and N suppresses grain growth with tiny and mainly be that the AlN of wire separates out.
Therefore, must suppress N and Al as much as possible.
Above-mentioned B combines with N in raw material inside, replaces tiny AlN, forms thick boron precipitate BN, is that grain growth is played the more element of advantageous effect.
But, when too much interpolation B, with B 2O 3Separate out with FeB, therefore the result who brings the impurity in the steel to increase the most important thing is that the addition of B is no more than the required amount of BN that is combined into as far as possible.
Therefore, the inventor has found less to add than the N amount that contains inevitably the method for the B amount that can adjust arbitrarily, finds that the ratio of B/N is being lower than 0.5, is being higher than 0.1 scope, and permeability is the highest.
And then found out, in the steel that contains the Si below 1.0%, do not add the Al element as far as possible, more favourable on the contrary than adding more than 0.005% steel to 0.15%.
Thereby Al as deoxidation usefulness, only adds the amount that will add inevitably in steel-making in the present invention.
That is, will be that the content that can dissolve the solid solution Al (Sol.Al) of Al is limited in below 0.005% in the present invention, wish that the content of Al is limited in below 0.005%.
The composition of steel of the present invention below is described and limits reason.
Above-mentioned C causes magnetic aging, the magnetic property in reduce using, so its content is limited in below 0.02%, wishes to reach in slab below 0.02%, is controlled at below 0.003% in end article.
For above-mentioned C is reduced to below 0.003%, when final annealing, also often carry out decarburization.
Above-mentioned Si is the element that increases non-resistance, reduces iron loss, but considers from improving the permeability aspect, wishes to be controlled at below 1.0%.
Above-mentioned Mn is to improving the iron loss effective elements, but surpasses 0.5%, makes the iron loss deterioration on the contrary, also reduces magnetic flux density, therefore wishes to be limited in below 0.5%.
Above-mentioned P is the element that forms the favourable texture of magnetic, but surpasses 0.15%, worsens cold-rolling property, therefore wishes to be limited in below 0.15%.
Above-mentioned S forms tiny precipitate MnS and the element that suppresses grain growth, and it is favourable therefore controlling it low as much as possible, controls to maximum 0.02% in the present invention.
Above-mentioned Al is the AlN precipitate that forms tiny wire, suppresses the element of grain growth, therefore only is added on the Al that the steel-making stage uses as deoxidation in the present invention, wishes not contain Al as far as possible in steel, and content is up to 0.005% in steel.
And in the present invention, above-mentioned Al content exists and will be limited in below 0.005% with solid solution Al form.
At this, solid solution Al refers in total Al and removes AlN, Al 2O 3Outside the Al compound, the Al of state of atom, soluble Al (solid solution Al).
Above-mentioned N forms elongated AlN precipitate, thereby inhibition is necessary as much as possible, in the present invention its content is limited in below 0.006%.
Above-mentioned Sn suppresses the diffusion of N at cyrystal boundary segregation, play the effect of inhibition to the texture of magnetic disadvantageous (222) face, and it is necessary adding more than 0.03% for this reason, but surpass 0.30%, cold-rolling property is worsened, and therefore the shape defect of hot rolled plate wishes that its content is limited in 0.03～0.30%.
Above-mentioned B is inner and N combination at raw material, replaces tiny AlN, forms thick boron precipitate BN, be that grain growth is played the more element of advantageous effect, it is necessary adding more than 0.0004% for this reason, still, the many permeabilities that can make on the contrary of its amount reduce, and therefore can add maximum 0.003% to.
In the present invention,, thick BN precipitate is more suitably formed, the ratio of B/N must be adjusted to 0.1～0.5 in order to replace AlN.If the ratio of B/N is less than 0.1, the amount of B is just few, and N uprises with the possibility that AlN separates out, thereby suppresses grain growth, and the ratio of B/N surpasses 0.5, and the change that the content of B is relative is many, and B is with B 2O 3Separate out the result who brings the impurity in the steel to increase with FeB.
That is, in the present invention, be adjusted at 0.1～0.5 o'clock in the ratio with B/N, suitably form the BN precipitate, it is thicker that crystal grain becomes, and then prevent to form B 2O 3With precipitates such as FeB, can improve the magnetic property, particularly permeability of steel plate thus significantly.
Manufacturing process of the present invention below is described.
To pack in the heating furnace as the above-mentioned plate slab of making, and after the heating of the temperature below 1250 ℃, adopt usual way to carry out hot rolling.This moment, the impurity element of then separating out in slab can dissolve again, and slightly separates out if heating-up temperature is too high, therefore was preferably in alap temperature and heated.
Yet when heating-up temperature was too low, the temperature distributing disproportionation in the slab was even, thereby the hot rolling difficulty.
Therefore, wish that in the present invention slab heating temperature is selected in 1100～1250 ℃.
As mentioned above, after hot rolling, batch the hot rolled plate after the hot rolling, but consider pickling performance, wish that coiling temperature is selected in below 750 ℃.
As mentioned above, as required, the hot rolled plate that has batched also can be annealed.When carrying out hot rolled plate annealing, wish that annealing temperature is 800～1100 ℃ a temperature range, annealing time was limited in below 5 minutes.
Such hot rolled plate annealing makes the tiny precipitate chap in the hot rolled plate big, makes even tissue, improves raw-material complete characteristic, and then forms the texture favourable to magnetic, plays the effect that makes grain growth.
Above-mentioned hot rolled plate carries out pickling with common pickle, then carry out cold rolling, obtain cold-reduced sheet after, carry out final annealing.
The final annealing of this moment is wished the temperature at 700～1050 ℃, anneals with the continuous processing more than 30 seconds, below 5 minutes.Its reason is, during less than 700 ℃, crystallization is insufficient again, and surpasses 1050 ℃, produces oxide layer on the surface in the final annealing temperature.And during less than 30 seconds, the residual stress of cold-reduced sheet is excessively residual at annealing time, and permeability reduces, and when surpassing 5 minutes, the shape of annealed sheet is bad.
Aforesaid cold-reduced sheet through final annealing behind the coating insulating coating, dispatches from the factory to the needs person, and stamping-out is processed into desirable shape.At this moment, the raw material through stamping-out processing can be carried out stress relief annealing as required.Stress relief annealing is wished in nonoxidizing atmosphere, carries out more than 10 minutes 700～850 ℃ of temperature.
By such stress relief annealing, can remove the residual stress that adds the generation in man-hour at stamping-out, thereby especially improve permeability.If the stress relief annealing temperature is less than 700 ℃, annealing time is just long, and surpasses 850 ℃, the easy damaged dielectric film.
Illustrate in greater detail the present invention below by embodiment.
Embodiment 1
Have the plate slab of the composition of following table 1 with the heating of the temperature conditions of following table 2, be rolled into the thickness of 2.0mm after, in the temperature of following table 2 hot rolled plate is batched, carry out pickling and cold rolling after, with the temperature and time condition of following table 2 cold-reduced sheet is annealed.
At this moment, the thickness of cold-reduced sheet is 0.5mm, and cold-reduced sheet annealing is carried out in the mixed atmosphere of 20% hydrogen and 80% nitrogen.
To measuring iron loss, magnetic flux density and permeability as the above-mentioned non-oriented electromagnetic steel sheet that manufactures, it the results are shown in the table 2.
In following table 2, iron loss is represented the core loss value with 50Hz, generation when 1.5T magnetizes, the magnetic flux density of induction when magnetic flux density is illustrated in the 5000A/m magnetization, permeability (μ 1.5) permeability of expression during with the magnetic flux density induced field of 1.5T.
Table 1
Steel grade Chemical composition (weight %)
C Si Mn P Al S N Sn B B/N
The invention steel a 0.005 0.55 0.34 0.04 0.002 0.005 0.0035 0.09 0.0009 0.25
b 0.006 0.57 0.27 0.07 0.001 0.005 0.0037 0.10 0.0010 0.27
Comparative steel a 0.004 0.55 1.15 0.04 0.005 0.004 0.0030 0.11 0.0010 0.33
b 0.006 0.56 0.35 0.07 0.027 0.005 0.0020 0.10 0.0020 0.74
Table 2
The examination item number Steel grade Slab heating temperature (℃) Hot rolled plate batch temperature (℃) Cold-reduced sheet annealing Iron loss (W 15/50) W/kg Magnetic flux density (B 50) Permeability (μ 1.5)
Temperature (℃) Time (s)
Invention material 1 Invention steel a 1200 700 950 90 3.62 1.79 4200
Invention material 2 Invention steel a 1150 600 1000 30 3.50 1.79 4500
Compare material 1 Invention steel a 1280 800 950 90 3.90 1.76 3500
Compare material 2 Invention steel a 1200 700 850 10 4.12 1.75 3200
Invention material 3 Invention steel b 1200 600 1000 60 3.52 1.80 4700
Compare material 3 Comparative steel a 1200 700 950 60 3.74 1.75 2800
Compare material 4 Comparative steel b 1200 700 950 60 3.98 1.76 3100
Compare material 5 Comparative steel b 1200 800 950 60 4.08 1.75 2900
Shown in above-mentioned table 2, the invention material 1～3 of forming and creating conditions and make with steel according to the invention and is formed with the steel that breaks away from the scope of the invention and/or the comparison material of making 1～5 of creating conditions is compared, and iron loss, magnetic flux density and permeability are good.
Embodiment 2
C:0.03%, Si:0.95%, Mn:0.25%, P:0.025%, S:0.003%, Al:0.0005%, N:0.003%, Sn:0.08%, B:0.0009%, plate slab that all the other are Fe and other unavoidable impurities are formed are heated with the temperature conditions shown in the following table 3, after hot rolling, temperature conditions with following table 3 batches hot rolled plate, carries out pickling then.
Behind the thickness as the cold rolling one-tenth of the above-mentioned plate through pickling 0.50mm, in order to make grain growth, cold-reduced sheet is in the dry atmosphere that contains 20% hydrogen and 80% nitrogen, carry out annealing in 1 minute at 1000 ℃.
The steel plate of making is as mentioned above measured iron loss, magnetic flux density, permeability and grain size, and it the results are shown in the table 3.
Table 3
The examination item number Slab heating temperature (℃) Hot rolled plate batch temperature (℃) Cold-reduced sheet annealing Iron loss (W 15/50) W/kg Magnetic flux density (B 50) Permeability (μ 1.5) Grain size (μ m)
Temperature (℃) Time (s)
Invention material 4 1200 700 1000 60 3.21 1.77 4100 75
Compare material 6 1280 800 1000 60 3.71 1.74 3200 45
Invention material 4 as shown in table 3, as to form and create conditions and make with steel according to the invention and is formed with the steel that breaks away from the scope of the invention and/or the comparison material of making 6 of creating conditions is compared, and iron loss, magnetic flux density and permeability are good.And invention material 4 compares with material 6 relatively, and crystal grain is thick.
Embodiment 3
The plate slab of composition that will have following table 4 is 1200 ℃ of heating, be rolled into thick 2.1mm after, batch and cool off at 730 ℃.Cooled hot rolled plate does not perhaps carry out hot rolled plate annealing after carrying out hot rolled plate annealing with the condition of following table 5, carries out pickling, and cold rolling then one-tenth final thickness is 0.50mm, carries out final annealing in the mixed atmosphere of hydrogen and nitrogen.After 90 minutes, carry out the stress relief annealing of the cold mode of stove at 800 ℃, heating then, measure permeability and texture intensity, it the results are shown in the table 5.
In following table 5, permeability (μ 1.5) permeability of expression during with 1.5T magnetic flux density induced field, texture intensity is { 200} face and the { texture intensity of 110} face of measuring the texture that helps magnetic.
Table 4
Steel grade Chemical composition (weight %)
C Si Mn Al Sol.Al P S N Sn B B/N
The invention steel c 0.003 0.25 0.21 0.0012 0.0007 0.081 0.003 0.0026 0.10 0.0008 0.30
d 0.002 0.23 0.23 0.0016 0.0010 0.080 0.004 0.0035 0.15 0.0012 0.34
Comparative steel c 0.003 0.24 0.22 0.0027 0.0023 0.082 0.003 0.0026 0.12 0.0028 1.07
d 0.004 0.21 0.24 0.0061 0.0055 0.079 0.004 0.0026 0.12 0.0032 1.23
Table 5
The examination item number Steel grade Hot rolled plate annealing (℃) Final annealing Whether carry out stress relief annealing Permeability (μ 1.5) Texture intensity (P110+P200)
Temperature (℃) Time (s)
Invention material 5 Invention steel c Do not carry out 850 60 Carry out 5860 3.2
Invention material 6 Do not carry out 800 90 Carry out 4850 2.9
Compare material 7 Do not carry out 600 60 Do not carry out 3610 2.1
Invention material 7 Invention steel d 950 900 90 Carry out 6200 3.4
Invention material 8 850 950 90 Carry out 5620 3.0
Compare material 8 Comparative steel c 850 950 90 Carry out 3840 2.3
Compare material 9 Comparative steel d 850 950 90 Carry out 3250 1.9
As shown in table 5, surpass the comparison material 8-9 that 0.5 comparative steel c-d makes with the ratio of B/N, permeability and texture intensity are all low.
In contrast, satisfy the invention material 5-8 that the invention steel c-d of condition of the present invention makes with the ratio of composition of steel and B/N, permeability height, texture intensity are also good.And then as can be known, the magnetic property that carries out hot rolled plate annealing (invention material 7-8) in the present invention is better than not carrying out hot rolled plate annealing (invention material 5-6).
And then the effect of stress relief annealing also is identical.But at 600 ℃ of comparison materials 7 that carry out final annealing, permeability and texture intensity are all low with steel c of the present invention.
Embodiment 4
With the ratio of C:0.003%, Si:0.62%, Mn:0.32%, P:0.069%, S:0.003%, Al:0.0006% (solid solution Al:0.0003%), N:0.0028%, Sn:0.07%, B:0.0011% and B/N is 0.39, all the other are formed for Fe and other unavoidable impurities plate slab after 1150 ℃ of heating, carry out hot rolling with 900 ℃ of finishing temperature conditions, then 650 ℃ batch and cool off after, carry out pickling, cold rolling one-tenth final thickness is 0.50mm.Above-mentioned cold-reduced sheet is in the atmosphere of 20% hydrogen and 80% nitrogen, carry out final annealing 1000 ℃ temperature.After cutting off processing then, carry out stress relief annealing in 90 minutes at 790 ℃, and stove is cold.
Raw-material iron loss (the W that makes like this 15/50) be 3.31W/kg, permeability (μ 1.5) be 5670.And then the performance of test material, the result is, grain size is 70 μ m, according to { the 200} face and { the texture intensity sum of 110} face is 3.9 of Horta.
The effect of the non-oriented electromagnetic steel sheet that as mentioned above, the present invention has can provide that iron loss is low, magnetic flux density and permeability are good.
And then, the present invention is because permeability is high, so easily magnetization, can reduce thus the copper cash amount for iron core, thereby can reduce the ratio of copper loss, and in order to ensure magnetic property, though behind final annealing without dress rolling, also can guarantee good magnetic property, therefore the effect that shortens manufacture process is arranged.

Claims (9)

1. the non-oriented electromagnetic steel sheet that has excellent magnetic characteristics, it is characterized in that, this non-oriented electromagnetic steel sheet by percentage by weight be below the C:0.02%, below the Si:1.0%, below the Mn:0.5%, below the P:0.15%, below the S:0.02%, below the solid solution Al:0.005%, below the N:0.006%, Sn:0.03～0.30%, B:0.0004～0.0030%, all the other form for Fe and other impurity that contains inevitably.
2. non-oriented electromagnetic steel sheet as claimed in claim 1 is characterized in that the ratio of B/N is 0.1～0.5.
3. the manufacture method of the non-oriented electromagnetic steel sheet that has excellent magnetic characteristics, it is characterized in that, in this manufacture method, to be below the C:0.02% by percentage by weight, below the Si:1.0%, below the Mn:0.5%, below the P:0.15%, below the S:0.02%, below the solid solution Al:0.005%, below the N:0.006%, Sn:0.03～0.30%, B:0.0004～0.0030%, all the other plate slabs for Fe and other impurity that contains inevitably composition heat again, after carrying out hot rolling, batch in the temperature below 750 ℃, the pickling hot rolled plate, then carry out cold rolling after, anneal 700～1050 ℃ temperature.
4. the manufacture method of non-oriented electromagnetic steel sheet as claimed in claim 3 is characterized in that, the ratio of B/N is 0.1～0.5.
5. as the manufacture method of claim 3 or 4 described non-oriented electromagnetic steel sheets, it is characterized in that the heating-up temperature again of slab is 1100～1250 ℃.
6. as the manufacture method of claim 3 or 4 described non-oriented electromagnetic steel sheets, it is characterized in that, after cold-reduced sheet annealing, process, carry out stress relief annealing again.
7. the manufacture method of the non-oriented electromagnetic steel sheet that has excellent magnetic characteristics, it is characterized in that, in this manufacture method, to be below the C:0.02% by percentage by weight, below the Si:1.0%, below the Mn:0.5%, below the P:0.15%, below the S:0.02%, below the solid solution Al:0.005%, below the N:0.006%, Sn:0.03～0.30%, B:0.0004～0.0030%, all the other plate slabs for Fe and other impurity that contains inevitably composition heat again, after carrying out hot rolling, batch in the temperature below 750 ℃, after hot rolled plate annealing, carry out pickling, then carry out cold rolling after, anneal 700～1050 ℃ temperature.
8. the manufacture method of non-oriented electromagnetic steel sheet as claimed in claim 7 is characterized in that, the ratio of B/N is 0.1～0.5.
9. as the manufacture method of claim 7 or 8 described non-oriented electromagnetic steel sheets, it is characterized in that, after cold-reduced sheet annealing, process, carry out stress relief annealing again.
CN97120376A 1996-12-09 1997-12-09 Orientationless electric steel plate with fine mangetic performance and manufacturing method thereof Expired - Fee Related CN1131532C (en)

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KR100398389B1 (en) * 1998-12-22 2003-12-18 주식회사 포스코 A method of manufacturing non-oriented electrical steel sheet having superior magnetic properties
KR100368722B1 (en) * 1998-12-29 2003-03-31 주식회사 포스코 Non-oriented electrical steel sheet with excellent magnetic properties and its manufacturing method
KR100479996B1 (en) * 1999-12-09 2005-03-30 주식회사 포스코 The high permeability grain-oriented electrical steel sheet with low core loss and method for manufacturing the same
KR100530069B1 (en) * 2001-12-20 2005-11-22 주식회사 포스코 Manufacturing method for non-oriented electrical steel sheet having low core loss and high magnetic induction after stress relief annealing
KR100544738B1 (en) * 2001-12-20 2006-01-24 주식회사 포스코 Manufacturing Method for Non-Oriented Electrical Steel Sheet having Superior Punchability and Low Core Loss after Stress Relief Annealing
KR20030053769A (en) * 2001-12-24 2003-07-02 주식회사 포스코 A method for manufacturing non-oriented electrical steel sheet with excellent magnetic property
KR100957939B1 (en) * 2002-12-24 2010-05-13 주식회사 포스코 Non-oriented electrical sheets with excellent magnetism and method for manufacturing the same
CN101358318B (en) * 2008-09-05 2011-03-09 首钢总公司 Ingredient design of non-oriented electrical steel with good combination property and preparation method therefor
CN103361544B (en) * 2012-03-26 2015-09-23 宝山钢铁股份有限公司 Non orientating silicon steel and manufacture method thereof
CN103882293B (en) * 2014-04-04 2016-06-29 首钢总公司 Non-oriented electrical steel and production method thereof
CN110640104B (en) * 2018-06-26 2021-11-16 宝山钢铁股份有限公司 Non-oriented electrical steel plate with excellent magnetic property and manufacturing method thereof
CN112143974B (en) * 2020-09-27 2021-10-22 江苏省沙钢钢铁研究院有限公司 Production method of non-oriented silicon steel and non-oriented silicon steel
CN112680656B (en) * 2020-11-27 2023-04-14 中天钢铁集团有限公司 Boron-containing steel for motor claw pole and low-cost smelting process thereof
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