CN1827820A - Non-oriented electrical steel sheet excellent in magnetic properties in rolling direction and method of production of same - Google Patents
Non-oriented electrical steel sheet excellent in magnetic properties in rolling direction and method of production of same Download PDFInfo
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Abstract
Non-oriented electrical steel sheet remarkably improved in magnetic properties in the rolling direction by a method superior in cost and productivity, that is, non-oriented electrical steel sheet excellent in magnetic properties in the rolling direction comprising, by wt %, Si in an amount of 2.0% or less, Mn in 3.0% or less, Al in 1.0% to 3.0%, at least one of Sn, Sb, Cu, Ni, Cr, P, REM, Ca, and Mg in a total of 0.002% to 0.5%, and a balance of Fe and unavoidable impurities and having a ratio (B50<SUB>L</SUB>/Bs) of the magnetic flux density B50<SUB>L </SUB>in the rolling direction after stress relief annealing and a saturated magnetic flux density Bs of 0.85 or more and an core loss W15/50<SUB>L </SUB>of 2.0 W/kg or less, produced by the method of annealing the hot band at 800 DEG C. to 1100 DEG C. for 30 seconds or more to achieve a crystal grain size after final annealing of 50 mum or less, skin pass rolling the sheet by a reduction of 3% to 10%, then stress relief annealing it. Further, a cold rolling reduction of 60% to 75% is preferable.
Description
Technical field
The present invention relates to non-oriented magnetic steel sheet and the manufacture method thereof used as the core material of electric installation, particularly after the stress relieving in the non-oriented magnetic steel sheet of the excellent in magnetic characteristics of rolling direction.
Background technology
In recent years, owing to worldwide require electric installation to develop,, also require further to reduce iron loss and improve magneticflux-density for the non-oriented magnetic steel sheet that uses as the electric machine iron core material to more energy-conservation direction.In general, improve resistivity and the particle diameter of product is increased, can reduce iron loss by adding Si; And then, can seek high magnetic flux densityization by optimizing hot-rolled sheet annealing and cold rolling draft.
On the other hand, as the making method of micro-machine, the built-up type motor increases in recent years.It is to carry out stamping-out and stacked with the form of segmentation stator, is bonded together after the coiling and forms the stator core of circular arc, and this method has the advantage that the utilization ratio that can make steel plate and coiling filling ratio are improved.And then may make the specific direction of the good steel plate of magnetic for example consistent with the tooth direction (tooth direction) of flux concentrating, therefore can expect the raising of electrical efficiency.
(sigmented core) uses steel plate as such composite core, can consider to adopt the very good grain-oriented magnetic steel plate of magnetic of rolling direction, but the example that almost not have employing because the bad and cost of stamping-out increases substantially, thereby adopt non-oriented magnetic steel sheet equally with former motor.That is to say that if can significantly improve the magnetic of non-oriented magnetic steel sheet at specific direction, then it ought to become the best materials of combined small motor.
As the composite core non-oriented magnetic steel sheet, for example specially open the 2004-332042 communique and disclose following method: it is by controlling crystal particle diameter and the cold rolling draft after the particularly hot-rolled sheet annealing, make behind the final annealing 100}＜001〉be the texture prosperity, thereby in face in rolling direction and this plate face vertical direction obtain good magnetic properties.
But present practical situation are: non-oriented magnetic steel sheet up to now, even the good rolling direction of magnetic (below be made as the L direction), with respect to other direction of steel plate, the advantage of its magnetic is also little.Moreover, be purpose to reduce high frequency iron loss recently, to the increase in demand of the more advanced material of thin type and Si amount, but the problem that such steel plate exists is: the magnetic advantage of L direction further reduces.
[patent documentation 1] spy opens the 2004-332042 communique
[patent documentation 2] spy opens clear 57-203718 communique
[patent documentation 3] spy opens flat 5-247537 communique
[patent documentation 4] spy opens the 2002-146490 communique
[patent documentation 5] spy opens the 2005-240050 communique
Summary of the invention
The present invention although make thickization of crystal grain and add a large amount of alloys, still wishes to provide with cheap price a kind of extremely good non-oriented magnetic steel sheet of magnetic properties of L direction in view of the above-mentioned problems.
The present invention finishes in order to solve above-mentioned problem, and its main idea is described below:
(1) a kind of non-oriented magnetic steel sheet of excellent in magnetic characteristics of rolling direction, it is characterized in that: described non-oriented magnetic steel sheet is in quality %, comprise that Si:2.0% or following, Mn:3.0% or following, Al:1.0%～3.0%, surplus are Fe and unavoidable impurities, after the stress relieving in the magneticflux-density B50 of rolling direction
LRatio (B50 with saturation magnetic flux density Bs
L/ Bs) be 0.85 or more than.
(2) non-oriented magnetic steel sheet of the excellent in magnetic characteristics of basis (1) described rolling direction is characterized in that: the iron loss W15/50 of the rolling direction of described steel plate after stress relieving
LBe 2.0W/kg or following.
(3) non-oriented magnetic steel sheet of the excellent in magnetic characteristics of basis (1) or (2) described rolling direction, it is characterized in that: described steel plate further contains Sn or Sb:0.002%～0.5% in quality %.
(4) non-oriented magnetic steel sheet of the excellent in magnetic characteristics of basis (1) or (2) described rolling direction, it is characterized in that: described steel plate is in quality %, further contains at least a kind that adds up among 0.002%～0.5% Cu, Ni, Cr, P, REM, Ca, the Mg.
(5) a kind of manufacture method of non-oriented magnetic steel sheet of excellent in magnetic characteristics of rolling direction, it is characterized in that: described steel plate is in quality %, comprises that Si:2.0% or following, Mn:3.0% or following, Al:1.0%～3.0%, surplus are Fe and unavoidable impurities; In the manufacturing process that implements hot rolling, hot-rolled sheet annealing, pickling, cold rolling, final annealing and skin-pass rolling, to having the steel plate of 50 μ m or following crystal particle diameter behind the final annealing, the draft with 3%～10% carries out skin-pass rolling.
(6) a kind of manufacture method of non-oriented magnetic steel sheet of excellent in magnetic characteristics of rolling direction, it is characterized in that: described steel plate is in quality %, comprises that Si:2.0% or following, Mn:3.0% or following, Al:1.0%～3.0%, surplus are Fe and unavoidable impurities; Implement hot rolling, hot-rolled sheet annealing (perhaps being omitted), pickling, be inserted with for 2 times of process annealing or the manufacturing process of repeatedly cold rolling, final annealing and skin-pass rolling in, to having the steel plate of 50 μ m or following crystal particle diameter behind the final annealing, the draft with 3%～10% carries out skin-pass rolling.
(7) according to the manufacture method of the non-oriented magnetic steel sheet of the excellent in magnetic characteristics of (5) or (6) described rolling direction, it is characterized in that: described steel plate further contains among 0.002%～0.5% Sn, Sb, Cu, Ni, Cr, P, REM, Ca, the Mg a kind or multiple.
(8) manufacture method of the non-oriented magnetic steel sheet of the excellent in magnetic characteristics of basis (5) or (6) described rolling direction is characterized in that: described cold rolling final cold rolling draft is set at 60%～75%.
(9) manufacture method of the non-oriented magnetic steel sheet of the excellent in magnetic characteristics of basis (5) or (6) described rolling direction, it is characterized in that: in annealing of described hot-rolled sheet and process annealing, the annealing of carrying out at last to the major general 800 ℃～1100 ℃ carry out 30 seconds or more than.
According to the present invention, can provide a kind of extremely good non-oriented magnetic steel sheet of magnetic properties of L direction with cheap price.
Embodiment
Below just the present invention be described in detail.The present inventor is for non-oriented magnetic steel sheet, is devoted to further to improve the magnetic of the L direction of magnetic properties optimum.Its result, obtained following opinion: Si be set at 2.0% or following steel in, add 1.0% or above Al, and behind final annealing, implement 3～10% skin-pass rolling and stress relieving, make the characteristic of L direction be able to raising by leaps and bounds by this, thereby the present invention is accomplished.Narrate with regard to experimental result of the present invention below.
(experiment 1)
In quality %, the steel of melting Si:1.0%, Mn:0.2%, Al:0.001～2.5%.These steel ingots are rolled into the steel plate that thickness is 2.7mm, and in 1000 ℃ of hot-rolled sheet annealing of implementing 60 seconds, making its thickness of slab by once cold rolling then is 0.37mm.Cold-reduced sheet carries out the final annealing in 30 seconds under 800 ℃, be 5% skin-pass rolling through draft after, 780 ℃ of stress relievings of implementing 1 hour, measured the magnetic properties of L direction thereafter.Its result is as shown in table 1, find the Al amount be 1.0% or above test portion 4 and 5 can obtain lower iron loss and higher magneticflux-density.In the lump the calculated value of saturation magnetic flux density (Bs) is charged in the table 1, as shown in Table 1,, but still obtained higher magneticflux-density although test portion 4 and 5 its saturation magnetic flux densities are lower.Can think that its reason is that the crystal orientation of easy magnetization is collected at the L direction.B50/Bs as the expression its aggregation extent parameter, if estimate with this parameter, then find test portion 4 and 5 B50/Bs in the L direction reach 0.85 or more than.
Table 1
| Test portion | Si(％) | Al(％) | W15/50 L (W/kg) | B50 L (T) | Bs (T) | B50 L/Bs | Remarks |
| 1 | 1.1 | 0.001 | 2.6 | 1.71 | 2.11 | 0.81 | Comparative example |
| 2 | 0.2 | 2.5 | 1.70 | 2.10 | 0.81 | Comparative example | |
| 3 | 0.4 | 2.2 | 1.69 | 2.09 | 0.81 | Comparative example | |
| 4 | 1.0 | 1.9 | 1.74 | 2.05 | 0.85 | Example | |
| 5 | 2.5 | 1.8 | 1.73 | 1.96 | 0.88 | Example |
(experiment 2)
Then verify Si amount to testing the influence of 1 effect that obtains, for this reason, a plurality of steel that melting changes Si amount and Al amount, with test 1 same test conditions and estimate.Its result is as shown in table 2, and is when Si surpasses 2.0%, irrelevant with the Al amount as can be known, do not obtain the iron loss of L direction and the effect that magneticflux-density is improved.On the other hand, when Si is 2.0% or when following, be added with 1.0% or the test portion 3,4,7,8,11,12 of above Al, find that iron loss and magneticflux-density rapidly improve, B50/Bs has also obtained up to 0.85 or above value.
Table 2
| Test portion | Si(％) | Al(％) | W15/50 L (W/kg) | B50 L (T) | B50 L/Bs | Remarks |
| 1 | 0.8 | 0.2 | 2.7 | 1.69 | 0.81 | Comparative example |
| 2 | 0.5 | 2.3 | 1.70 | 0.83 | Comparative example | |
| 3 | 1.2 | 2.1 | 1.74 | 0.86 | Example | |
| 4 | 2.5 | 2.0 | 1.74 | 0.90 | Example | |
| 5 | 1.5 | 0.2 | 2.4 | 1.67 | 0.80 | Comparative example |
| 6 | 0.5 | 2.0 | 1.68 | 0.82 | Comparative example | |
| 7 | 1.2 | 1.8 | 1.72 | 0.85 | Example | |
| 8 | 2.5 | 1.7 | 1.72 | 0.89 | Example | |
| 9 | 2.0 | 0.2 | 2.3 | 1.65 | 0.80 | Comparative example |
| 10 | 0.5 | 2.1 | 1.65 | 0.81 | Comparative example | |
| 11 | 1.2 | 1.7 | 1.69 | 0.85 | Example | |
| 12 | 2.5 | 1.6 | 1.70 | 0.89 | Example | |
| 13 | 2.5 | 0.2 | 2.3 | 1.67 | 0.82 | Comparative example |
| 14 | 0.5 | 2.2 | 1.66 | 0.82 | Comparative example | |
| 15 | 1.2 | 2.2 | 1.63 | 0.82 | Comparative example | |
| 16 | 2.5 | 2.2 | 1.58 | 0.83 | Comparative example |
So, the present invention has obtained following opinion first: with Si be limited in 2.0% or below, contain up to 1.0% or above Al in addition, such steel plate is carried out skin-pass rolling behind final annealing, then implement stress relieving, the magnetic properties of L direction is significantly improved.It is generally acknowledged that the major cause that shows this effect is: owing to added 1.0% or above Al, so Goss orientation when final annealing ({ 110}＜001 〉) and near the orientation increase is arranged slightly, preferential growth in the stress relieving of this orientation after skin-pass rolling.In addition, surpass at 2.0% o'clock at Si, the reason that does not show effect does not still have final conclusion, but can think that Si has bigger influence than Al to the sclerization of material.
Improvement about the former magnetic properties that causes by skin-pass rolling, for example erect image is opened seen in the clear 57-203718 communique such the spy, its purpose is to promote the grain growth after the stress relieving and obtains lower iron loss, is specially adapted for the few rudimentary steel grade of Si amount.Its reason is: do not undergo phase transition in adding the advanced material of 2～3% left and right sides Si, therefore, do not rely on skin-pass rolling and adopt these the simple means of final annealing high temperatureization that make, also can seek thickization of crystal grain and obtain lower iron loss.
Skin-pass rolling among the present invention is not only the means that make thickization of crystal particle diameter, but in order to control crystalline orientation, thereby the magnetic properties that makes the L direction obtains improvement at full speed, and what have great importance especially is: this effect by add 1.0% or above Al just show.Its reason is: the effect that resistivity is increased almost improves with Si of equal valuely, and that resistivity is the reduction institute of iron loss, particularly high frequency iron loss is indispensable.That is to say, part or all that comprises about 2～3%Si that advanced material is added is replaced as the method for Al, by being suitable for method of the present invention, can make the L direction have tangible magnetic advantages, this is very difficult realization of advanced material, particularly thin type advanced material up to now.
As the magnetic properties that the makes the L direction in this wise former opinion that improves at full speed, Te Kaiping 5-247537 communique discloses following method, promptly the edge becomes less than the direction of 45 to carry out skin-pass rolling with the length direction of steel plate, but can infer: carry out skin-pass rolling along tilted direction and realize in industrial being difficult to.
In addition, open the 2002-146490 communique and the spy opens in the 2005-240050 communique, disclose the high Al non-oriented magnetic steel sheet that carries out skin-pass rolling with the present invention equally, but the method for this communique can not obtain B50 as the present invention the spy
LThe non-oriented magnetic steel sheet of/Bs 〉=0.85.Its reason is: these examples are not implemented hot-rolled sheet annealing and can not fully add is to show Goss orientation before the necessary skin-pass rolling of characteristic ({ 110}＜001 〉) and near orientation thereof.
Narrate the reason that logarithmic value limits in the product of the present invention below.
Si is the effective element that is used to increase resistance, but addition surpasses at 2.0% o'clock, and the magnetic that can not fully obtain the L direction is improved effect, therefore its upper limit is set at 2.0%.As for lower limit, in order to increase resistance, be preferably 0.4% or more than, more preferably 0.5% or more than, more preferably 0.7% or more than.Be the situation of high Al as in the present invention particularly, too reduce the Al after Si will cause pickling
2O
3Oxide skin increases, so Si is particularly preferred above 1.0%.
Mn has the effect that generates sulfide and improve resistance, therefore preferred add 0.1% or more than.But consider cost, the upper limit is defined as 3.0%.
Al is a necessary element of the present invention, when carrying out final annealing in less than 1.0%, Goss orientation ({ 110}＜001 〉) and near orientation thereof are very inflourishing, can not obtain the magnetic properties of good L direction after stress relieving, thus be set at 1.0% or more than.From B50
LThe angle of/Bs considers, be preferably 1.5% or more than, more preferably 2.0% or more than.In addition, add Al and can obtain almost equal high resistivity, therefore can adjust addition according to the difference of target iron loss with interpolation Si.In order to reduce high frequency iron loss, preferably carry out positive interpolation especially.But consider the production efficiency of casting etc., its upper limit is set at 3.0%.Consider the easy degree of operation, be preferably 2.7% or below, more preferably 2.5% or below.
Sn and Sb have the effect that increases the Goss orientation when final annealing, and have the nitrogenize when suppressing annealing and the effect of oxidation, thereby preferably add.As the addition that obtains effect, be set at 0.002% or more than.In addition, surpass at 0.5% o'clock at addition, its effect reaches capacity, therefore be defined as 0.5% or below.
About Cu and Ni, the nitrogenize when having inhibition annealing and the effect of oxidation, thereby also can add, preferred especially and Sn carries out compound interpolation.As the addition that obtains effect, be set at 0.002% or more than.Surpass at 0.5% o'clock at addition, its effect reaches capacity, thus be defined as 0.5% or below.
Cr has the effect that obtains high resistivity and improve rust resistance, P has the effect of improving crystalline orientation and stamping-out, REM, Ca and Mg have the effect of improving grain growing when hot-rolled sheet annealing, final annealing and stress relieving, they all improve the characteristic of non-oriented magnetic steel sheet.As the addition that obtains effect, be set at 0.002% or more than.Surpass 0.5% when adding at addition, its effect reaches capacity, thus be defined as 0.5% or below.
About the magnetic properties of L direction, stipulate: the ratio (B50 of magneticflux-density and saturation magnetic flux density according to experimental result
L/ Bs) be 0.85 or more than, the iron loss W15/50 of commercial frequency
LBe 2.0W/kg or following.At this, saturation magnetic flux density Bs is calculated by the formula of 2.1561-0.0413 * Si-0.0198 * Mn-0.0604 * Al, and wherein the concentration of composition is represented with quality %.
Describe with regard to qualification reason of creating conditions of the present invention below.
About hot-rolled sheet annealing and process annealing, consider the necessity that crystal grain is fully grown up, with its temperature be set at 800 ℃ or more than.But, when crystal grain is too thick, then damage surface texture, therefore be defined as 1100 ℃ or following.
About cold rolling draft, increase the purpose in Goss orientation during based on final annealing, be preferably 60%～75%.Under the situation that hot-rolled sheet is annealed and once cold rolling can not meet the demands, cold rolling and process annealing in the middle of also can implementing after hot-rolled sheet is annealed is 60%～75% thereby make finally cold rolling preceding draft.But, consider that from the angle of taking into account manufacturing cost the cold rolling draft of this scope is not necessary.
About the crystal particle diameter before the skin-pass rolling, if too thick, then stress relieving almost can not make grain growing, therefore its upper limit is defined as 50 μ m.The not special regulation of lower limit is as long as recrystallize finishes just to be out of question.
The skin-pass rolling draft makes the important factor of particular orientation preferential growth when being stress relieving.When less than 3%, strained applies and is insufficient, so lower limit set is 3%.In addition, when surpassing 10%, apply strain equally and preferential growth can not take place, so the upper limit is set at 10%.
In addition,, also can in the manufacturing processed of steel plate, be implemented,, also can become back unshakable in one's determination to implement, even and in the manufacturing processed of steel plate, becomes back unshakable in one's determination enforcement 2 times also it doesn't matter with stamping-out at stamping-out by the user perhaps as unshakable in one's determination about stress relieving.The not special regulation of annealing conditions is as long as the condition for crystal grain is fully grown up is that all it doesn't matter for box annealing or continuous annealing.At this, the state that so-called crystal grain is fully grown up, the average crystalline particle diameter that is meant section of steel plate be 60 μ m or more than.In addition, about annealing temperature, generally annealing time reached 10 minutes or above box annealed situation under, be preferably 700～850 ℃ and be, and be as short as at annealing time under the situation of the continuous annealing about 10～60 seconds, be preferably 850～1000 ℃.
Embodiment 1
In quality %, the steel of melting Si:1.0～3.0%, Mn:0.5%, Al:0.3～2.4%.These steel ingots are rolled into the steel plate that thickness is 1.8mm, and in 1050 ℃ of hot-rolled sheet annealing of implementing 60 seconds, making its thickness of slab by once cold rolling then is 0.37mm.Cold-reduced sheet under 850 ℃, carry out the final annealing in 15 seconds and make its particle diameter be about 40 μ m after, be 5% skin-pass rolling through draft after, 800 ℃ of stress relievings of implementing 1 hour.The test portion that like this obtains has carried out the magnetic measurement of L direction.Its result is as shown in table 3, Si:2.0% or following and Al:1.0% or above test portion 3,4,7,8, and its iron loss and magneticflux-density are all good, W15/50
LBe 2.0W/kg or following, B50
L/ Bs be 0.85 or more than.
Table 3
| Test portion | Si(％) | Al(％) | W15/50 L (W/kg) | B50 L (T) | B50 L/Bs | Remarks |
| 1 | 1.2 | 0.3 | 3.42 | 1.72 | 0.83 | Comparative example |
| 2 | 0.6 | 3.05 | 1.71 | 0.83 | Comparative example | |
| 3 | 1.2 | 1.95 | 1.76 | 0.87 | Example | |
| 4 | 2.4 | 1.77 | 1.74 | 0.89 | Example | |
| 5 | 1.8 | 0.3 | 3.11 | 1.68 | 0.82 | Comparative example |
| 6 | 0.6 | 2.86 | 1.67 | 0.82 | Comparative example | |
| 7 | 1.2 | 1.88 | 1.73 | 0.87 | Example | |
| 8 | 2.4 | 1.74 | 1.72 | 0.89 | Example | |
| 9 | 2.4 | 0.3 | 3.03 | 1.67 | 0.82 | Comparative example |
| 10 | 0.6 | 2.33 | 1.65 | 0.82 | Comparative example | |
| 11 | 1.2 | 2.21 | 1.63 | 0.83 | Comparative example | |
| 12 | 2.4 | 2.16 | 1.58 | 0.83 | Comparative example |
Embodiment 2
In quality %, the steel of melting Si:1.3%, Mn:1.0%, Al:1.8%, Sn:0.003～0.2%.These steel ingots are rolled into the steel plate that thickness is 2.0mm, in 950 ℃ of hot-rolled sheet annealing of implementing 60 seconds, become 0.65～2.0mm (it is cold rolling that 2.0mm does not carry out the centre) by cold rolling its thickness that makes in centre again, and, be 0.26mm by final cold rolling its thickness of slab that makes then in 900 ℃ of process annealings (2.0mm does not carry out process annealing) of implementing for 60 seconds.It is about 30 μ m that cold-reduced sheet makes its particle diameter by final annealing, then stands draft and be 5% skin-pass rolling, then 750 ℃ of stress relievings of implementing 2 hours.The test portion that like this obtains has carried out the magnetic measurement of L direction.Its result is as shown in table 4 like that, and any test portion has all obtained W15/50
LBe 2.0W/kg or following, B50
L/ Bs is 0.85 or above good magnetic characteristics.Especially for add 0.01% or above Sn and final cold rolling draft be set at 60～75% test portion 5,6,9,10, obtain extremely good iron loss and magneticflux-density.
Table 4
| Test portion | Si(％) | Middle cold rolling thickness (mm) | Final cold rolling draft (%) | W15/50 L (W/kg) | B50 L (T) | B50 L/Bs | Remarks |
| 1 | 0.003 | 0.7 | 62.9 | 1.79 | 1.73 | 0.88 | ○ |
| 2 | 1.0 | 74.0 | 1.88 | 1.72 | 0.87 | ○ | |
| 3 | 1.5 | 82.7 | 1.91 | 1.70 | 0.86 | ○ | |
| 4 | 2.0 | 87.0 | 1.96 | 1.68 | 0.85 | ○ | |
| 5 | 0.02 | 0.7 | 62.9 | 1.72 | 1.77 | 0.90 | ◎ |
| 6 | 1.0 | 74.0 | 1.83 | 1.76 | 0.89 | ◎ | |
| 7 | 1.5 | 82.7 | 1.86 | 1.73 | 0.88 | ○ | |
| 8 | 2.0 | 87.0 | 1.91 | 1.71 | 0.87 | ○ | |
| 9 | 0.12 | 0.7 | 62.9 | 1.68 | 1.78 | 0.90 | ◎ |
| 10 | 1.0 | 74.0 | 1.71 | 1.77 | 0.90 | ◎ | |
| 11 | 1.5 | 82.7 | 1.76 | 1.74 | 0.88 | ○ | |
| 12 | 2.0 | 87.0 | 1.81 | 1.72 | 0.87 | ○ |
Zero is good
◎ is good especially
Embodiment 3
In quality %, the steel of melting Si:1.5%, Mn:1.5%, Al:2.3%, Sn:0.05%, Cu:0.2%, Ni:0.3%.These steel ingots are rolled into the steel plate that thickness is 2.5mm, after 1000 ℃ of hot-rolled sheets of implementing 60 seconds are annealed, make the range of cold rolling thickness of slab at 0.30～0.35mm.After cold-reduced sheet obtains the particle diameter of about 30 μ m by final annealing, carry out skin-pass rolling and reach 0.30mm when thickness 0.30mm (cold rolling do not carry out skin-pass rolling), then 750 ℃ of stress relievings of implementing 2 hours until thickness of slab.The test portion that obtains has like this been carried out the magnetic measurement of L direction.Its result is as shown in table 5, is that 50 μ m or following and skin-pass rolling draft are 3～10% test portion 4,5,7,8,10,11 for the particle diameter of final annealing, obtains extremely good iron loss and magneticflux-density.
Table 5
| Test portion | Cold rolling thickness (mm) | Particle diameter behind the final annealing (μ m) | Skin-pass rolling draft (%) | W15/50 L (W/kg) | B50 L (T) | B50 L/Bs | Remarks |
| 1 | 0.30 | 25 | 0 | 2.87 | 1.61 | 0.84 | Comparative example |
| 2 | 41 | 0 | 2.55 | 1.60 | 0.83 | Comparative example | |
| 3 | 65 | 0 | 2.34 | 1.60 | 0.83 | Comparative example | |
| 4 | 0.31 | 26 | 3.2 | 1.81 | 1.72 | 0.89 | Example |
| 5 | 42 | 3.2 | 1.94 | 1.70 | 0.88 | Example | |
| 6 | 66 | 3.2 | 2.31 | 1.60 | 0.83 | Comparative example | |
| 7 | 0.32 | 22 | 6.3 | 1.82 | 1.71 | 0.89 | Example |
| 8 | 43 | 6.3 | 1.73 | 1.73 | 0.90 | Example | |
| 9 | 68 | 6.3 | 2.23 | 1.60 | 0.83 | Comparative example | |
| 10 | 0.33 | 23 | 9.1 | 1.82 | 1.68 | 0.87 | Example |
| 11 | 44 | 9.1 | 1.79 | 1.70 | 0.88 | Example | |
| 12 | 64 | 9.1 | 2.16 | 1.61 | 0.84 | Comparative example | |
| 13 | 0.35 | 24 | 14.3 | 2.58 | 1.58 | 0.82 | Comparative example |
| 14 | 45 | 14.3 | 2.51 | 1.59 | 0.83 | Comparative example | |
| 15 | 63 | 14.3 | 2.44 | 1.58 | 0.82 | Comparative example |
Claims (9)
1. the non-oriented magnetic steel sheet of the excellent in magnetic characteristics of a rolling direction, it is characterized in that: described non-oriented magnetic steel sheet is in quality %, comprises that Si:2.0% or following, Mn:3.0% or following, Al:1.0%～3.0%, surplus are Fe and unavoidable impurities; After the stress relieving in the magneticflux-density B50 of rolling direction
LWith the ratio of saturation magnetic flux density Bs be 0.85 or more than.
2. the non-oriented magnetic steel sheet of the excellent in magnetic characteristics of rolling direction according to claim 1 is characterized in that: the iron loss W15/50 of the rolling direction of described steel plate after stress relieving
LBe 2.0W/kg or following.
3. the non-oriented magnetic steel sheet of the excellent in magnetic characteristics of rolling direction according to claim 1 and 2, it is characterized in that: described steel plate further contains Sn or Sb:0.002%～0.5% in quality %.
4. the non-oriented magnetic steel sheet of the excellent in magnetic characteristics of rolling direction according to claim 1 and 2, it is characterized in that: described steel plate is in quality %, further contains at least a kind that adds up among 0.002%～0.5% Cu, Ni, Cr, P, REM, Ca, the Mg.
5. the manufacture method of the non-oriented magnetic steel sheet of the excellent in magnetic characteristics of a rolling direction, it is characterized in that: described steel plate is in quality %, comprises that Si:2.0% or following, Mn:3.0% or following, Al:1.0%～3.0%, surplus are Fe and unavoidable impurities; In the manufacturing process that implements hot rolling, hot-rolled sheet annealing, pickling, cold rolling, final annealing and skin-pass rolling, to having the steel plate of 50 μ m or following crystal particle diameter behind the final annealing, the draft with 3%～10% carries out skin-pass rolling.
6. the manufacture method of the non-oriented magnetic steel sheet of the excellent in magnetic characteristics of a rolling direction, it is characterized in that: described steel plate is in quality %, comprises that Si:2.0% or following, Mn:3.0% or following, Al:1.0%～3.0%, surplus are Fe and unavoidable impurities; Implement hot rolling, hot-rolled sheet annealing, pickling, be inserted with for 2 times of process annealing or the manufacturing process of repeatedly cold rolling, final annealing and skin-pass rolling in, perhaps give under the situation of elliptical in hot-rolled sheet annealing, implement hot rolling, pickling, be inserted with for 2 times of process annealing or the manufacturing process of repeatedly cold rolling, final annealing and skin-pass rolling in, to having the steel plate of 50 μ m or following crystal particle diameter behind the final annealing, the draft with 3%～10% carries out skin-pass rolling.
7. according to the manufacture method of the non-oriented magnetic steel sheet of the excellent in magnetic characteristics of claim 5 or 6 described rolling directions, it is characterized in that: described steel plate further contains among 0.002%～0.5% Sn, Sb, Cu, Ni, Cr, P, REM, Ca, the Mg a kind or multiple.
8. according to the manufacture method of the non-oriented magnetic steel sheet of the excellent in magnetic characteristics of claim 5 or 6 described rolling directions, it is characterized in that: described cold rolling final cold rolling draft is set at 60%～75%.
9. according to the manufacture method of the non-oriented magnetic steel sheet of the excellent in magnetic characteristics of claim 5 or 6 described rolling directions, it is characterized in that: in annealing of described hot-rolled sheet and process annealing, the annealing of carrying out at last to the major general 800 ℃～1100 ℃ carry out 30 seconds or more than.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP047289/2005 | 2005-02-23 | ||
| JP2005047289 | 2005-02-23 | ||
| JP372978/2005 | 2005-12-26 |
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| CN1827820A true CN1827820A (en) | 2006-09-06 |
| CN100549206C CN100549206C (en) | 2009-10-14 |
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| CN101713047B (en) * | 2009-12-22 | 2011-05-11 | 武汉钢铁(集团)公司 | Cr-contained non-oriented electrical steel and production method thereof |
| CN101876028B (en) * | 2009-12-22 | 2012-06-27 | 武汉钢铁(集团)公司 | Non-oriented electrical steel for variable frequency motor and production method thereof |
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- 2006-02-23 CN CNB2006100088732A patent/CN100549206C/en active Active
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN101713047B (en) * | 2009-12-22 | 2011-05-11 | 武汉钢铁(集团)公司 | Cr-contained non-oriented electrical steel and production method thereof |
| CN101876028B (en) * | 2009-12-22 | 2012-06-27 | 武汉钢铁(集团)公司 | Non-oriented electrical steel for variable frequency motor and production method thereof |
| CN103582716A (en) * | 2012-02-14 | 2014-02-12 | 新日铁住金株式会社 | Non-oriented electromagnetic steel sheet |
| CN104726794A (en) * | 2013-12-23 | 2015-06-24 | Posco公司 | Non-oriented electrical steel sheets and method for manufacturing the same |
| CN104726794B (en) * | 2013-12-23 | 2017-09-05 | Posco公司 | Non-oriented electromagnetic steel sheet and its manufacture method |
| CN105779877A (en) * | 2014-12-23 | 2016-07-20 | 鞍钢股份有限公司 | Efficient production method for semi-process non-oriented electrical steel |
| CN105779877B (en) * | 2014-12-23 | 2017-10-27 | 鞍钢股份有限公司 | A kind of high-efficiency method for producing of half-technique non oriented electrical steel |
| CN105986176A (en) * | 2015-03-03 | 2016-10-05 | 鞍钢股份有限公司 | Production method of half-process cold-rolled non-oriented electrical steel |
| CN114008224A (en) * | 2019-06-28 | 2022-02-01 | 杰富意钢铁株式会社 | Method for manufacturing non-oriented electromagnetic steel sheet, method for manufacturing motor core, and motor core |
| US11962184B2 (en) | 2019-06-28 | 2024-04-16 | Jfe Steel Corporation | Method for producing non-oriented electrical steel sheet, method for producing motor core, and motor core |
| CN114729415A (en) * | 2019-11-12 | 2022-07-08 | Lg电子株式会社 | Non-oriented electric steel sheet and method for manufacturing same |
| CN114729415B (en) * | 2019-11-12 | 2024-02-13 | Lg电子株式会社 | Non-oriented electrical steel sheet and method for producing same |
Also Published As
| Publication number | Publication date |
|---|---|
| CN100549206C (en) | 2009-10-14 |
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