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WO2004013365A1 - Tole d'acier magnetique non orientee, element pour machine tournante et machine tournante - Google Patents

Tole d'acier magnetique non orientee, element pour machine tournante et machine tournante Download PDF

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Publication number
WO2004013365A1
WO2004013365A1 PCT/JP2003/009947 JP0309947W WO2004013365A1 WO 2004013365 A1 WO2004013365 A1 WO 2004013365A1 JP 0309947 W JP0309947 W JP 0309947W WO 2004013365 A1 WO2004013365 A1 WO 2004013365A1
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WIPO (PCT)
Prior art keywords
steel sheet
oriented electrical
less
electrical steel
annealing
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Ceased
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PCT/JP2003/009947
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English (en)
Japanese (ja)
Inventor
Tadashi Nakanishi
Tishito Takamiya
Masaki Kawano
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JFE Steel Corp
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JFE Steel Corp
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Application filed by JFE Steel Corp filed Critical JFE Steel Corp
Priority to KR1020047004538A priority Critical patent/KR100567239B1/ko
Publication of WO2004013365A1 publication Critical patent/WO2004013365A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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Classifications

    • 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
    • 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
    • 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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • 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
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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
    • H01F1/16—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 in the form of sheets
    • H—ELECTRICITY
    • H02—GENERATION; CONVERSION OR DISTRIBUTION OF ELECTRIC POWER
    • H02K—DYNAMO-ELECTRIC MACHINES
    • H02K1/00—Details of the magnetic circuit
    • H02K1/02—Details of the magnetic circuit characterised by the magnetic material
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations

Definitions

  • the present invention relates to a non-oriented electrical steel sheet used for assembling a rotary machine.
  • the present invention also relates to a rotating machine member and a rotating machine assembled using the above non-oriented electrical steel sheet.
  • BACKGROUND ART To reduce the energy consumption of a rotating machine, it is necessary to increase the magnetic flux density of the iron core of the rotating machine, that is, a rotor (rotor) and a stator (stator), and to reduce iron loss of these iron cores. Is effective.
  • means for reducing iron loss means for increasing the electric resistance of the iron core material by increasing the content of Si, Al, Mn, etc., has been generally used.
  • the method of adding B disclosed in JP-A-58-151453 and the method of adding Ni disclosed in JP-A-3-281758 are known.
  • non-oriented electrical steel sheets manufactured by these means it is possible to manufacture iron cores with high magnetic flux density and low iron loss.
  • the non-oriented electrical steel sheet used for the core of the rotating machine is subjected to finish annealing (final annealing) by the steel sheet manufacturer and shipped as a product sheet. Assembled into theta. In this assembling process, after a core plate for a rotor or a core plate for a stator is punched from a steel plate, strain relief annealing is performed as necessary.
  • JP-B-58-55210 and JP-A-8-269532 disclose that the amount of Sol.A1 in a steel sheet is reduced to 0.0010% or less and 0.003% or less, respectively, to reduce fine A1N. Suppressing precipitation improves grain growth during strain relief annealing and reduces low iron loss. The techniques obtained are disclosed.
  • Japanese Patent Application Laid-Open No. 3-24229 also discloses that the amount of Sol. A 1 is reduced to 0.001% or less, and the product of the N and V contents is suppressed to a predetermined value or less.
  • a technique for improving grain growth during annealing and obtaining a low iron loss is disclosed.
  • JP-A-63-195217 and JP-A-7-150248 disclose that, in addition to reducing A1, the composition of inclusions composed of a composite oxide of Si, Al, and Mn is controlled. It is disclosed that by preventing ductility, grain growth during strain relief annealing can be improved and low iron loss can be obtained.
  • a steel sheet of about 6 W / kg is strain relief-annealed to 5 W / kg.
  • it is possible to improve to less than about 4.4 W / kg it is possible to improve the steel sheet to about 5 W / kg after finish annealing (at the time of shipment).
  • a rotor core plate and a stator core plate are generally stamped out from the same copper plate by a press in order to maintain a high yield of materials. Then, the rotor core plate and the stator core plate are respectively laminated and assembled into a rotor and a stator.
  • the rotor is a rotating member, and is subjected to high stress due to high-speed rotation, so that it must have high strength.
  • a rotating machine motor
  • a rotor in which a rare-earth magnet is embedded has been developed, and the rotation speed of the rotor has been significantly increased. Therefore, the magnetic steel sheet constituting the rotor is required to have a higher magnetic flux density and strength, for example, a higher yield point (YP) than before.
  • YP yield point
  • the present invention discloses that a rotor material and a stator material are simultaneously sampled from the same steel plate while a rotor material has a high magnetic flux density and a high strength, and a stator material has a high V magnetic flux density and a low strength.
  • An object of the present invention is to propose a high magnetic flux density non-oriented electrical steel sheet capable of achieving iron loss, and to further propose a rotating machine member and a rotating machine using the same.
  • the term “grain growth-inhibiting ductile nonmetallic inclusions” refers to the average recrystallized grain size (average grain size of recrystallized grains) of a steel sheet among the ductile nonmetallic inclusions, where D is 3 XD to 9XD.
  • the steel sheet refers to the state of the finished annealed product sheet, that is, the steel sheet that has not been subjected to strain relief annealing, and the average recrystallized grain size and the length of ductile nonmetallic inclusions are, of course, the product sheet. It is a value in the state of.
  • ductile nonmetallic inclusions refer to relatively coarse nonmetallic inclusions that expand relatively easily by rolling (or expand in product sheets, etc.), but do not expand in steel sheets. Are mostly non-metallic inclusions, henceforth simply referred to as ductile inclusions.
  • composition of the non-oriented electrical steel sheet substantially consists of the above Si, Mn, Sol. Al, N, the balance of Fe and inevitable impurities.
  • T i, N b and V in mass% are Ti: 0.0020% or less (including 0), b: 0.0050% or less (including 0), and V : The high magnetic flux density non-oriented electrical steel sheet for a rotating machine according to any one of the above-mentioned inventions, which is limited to 0.0060% or less (including 0). .
  • S and O are limited by mass% to S: 0.0050% or less (including 0) and O: 0.0100% or less (including 0), respectively.
  • the average grain size D of the recrystallized grains is 6 ⁇ ! Above: which is ⁇ 25 m! A high magnetic flux density non-oriented electrical steel sheet for a rotating machine according to any one of the above-described inventions.
  • non-oriented electrical steel sheet according to any one of the above-mentioned inventions 1 to 8, wherein the average recrystallized grain size grows twice or more by strain relief annealing at 750 ° C for 2 hours (ie, strain relief annealing).
  • a high magnetic flux density non-oriented electrical steel sheet for rotating machines characterized by having a crystal grain growth ratio of 2 or more.
  • High magnetic flux density non-oriented electrical steel sheet for rotating machines obtained by subjecting the high magnetic flux density non-oriented electrical steel sheet for rotating machines (product board) according to any one of the above inventions 1 to 9 to strain relief annealing. (Strain relief annealing plate).
  • the non-oriented electrical steel according to each of the above-mentioned inventions is obtained by processing a slab for a non-oriented electrical steel sheet by a conventional method to obtain a cold-rolled steel sheet having a final thickness of 700 to 800 ° C. Can be subjected to finish annealing, and further subjected to strain relief annealing at 700 to 800, so that the average recrystallized grain size preferably grows to be at least twice the grain size after finish annealing. .
  • a high-flux-density non-oriented electrical steel sheet for a rotating machine according to any one of the above-mentioned inventions, preferably punched and punched out, and then laminated.
  • a high-flux-density non-oriented electrical steel sheet for a rotating machine according to any one of the above-described inventions 1 to 9, preferably a punched and laminated stator member for a rotating machine subjected to strain relief annealing.
  • a rotating machine comprising the same high magnetic flux density non-oriented electrical steel sheet for a rotating machine as the material and having the rotor member according to the above-described invention 12 and the stator member according to the above-described invention 13.
  • the non-oriented electrical steel sheets according to the inventions of the above:! To 9 can be punched and laminated to form a high-strength rotating machine rotor member. Moreover, after punching and laminating, it can be further subjected to strain relief annealing to obtain a low iron loss rotating machine stator member. Furthermore, a high-performance rotating machine can be obtained using a rotor member and a stator member obtained from the same non-oriented electrical steel sheet. BRIEF DESCRIPTION OF THE DRAWINGSFIG.
  • 1 shows the grain growth ratio of the non-oriented electrical steel sheet, that is, the ratio of the average grain size of the steel sheet after strain relief annealing to the average grain size of the steel sheet after finish annealing, and the N of the steel sheet.
  • 4 is a graph showing the relationship with the content using the number of existing non-metallic inclusions inhibiting grain growth as a parameter.
  • the saturation magnetic flux density of non-oriented electrical steel sheets is determined by the iron content (% by mass) of the material.
  • the saturation magnetic flux density decreases when the content of elements other than iron, such as Si and Mn, is high. Inevitable.
  • the magnetic flux density and strength are governed by the crystal grain size of the steel sheet.
  • strain relief annealing is performed by the customer, and the annealing may increase the crystal grain size and reduce iron loss.
  • the product sheet after finish annealing should have relatively fine grains and high strength, and ensure high crystal grain growth during strain relief annealing.
  • the crystal grain size can be appropriately adjusted in the manufacturing process of the rotor and the stator, so that the rotor and the stator can each have required characteristics.
  • the present inventors have further searched for factors governing the growth of the crystal grain size in the strain relief annealing process performed in the process of assembling the stator, and have found that the following methods are combined.
  • the Si content is in the range of 0.1 to 1.2%. Mn: 0.005 to 0.30%
  • Mn is a component necessary for obtaining good workability in hot rolling, and therefore, it is necessary to contain 0.005% or more. However, when it exceeds 0.30%, the magnetic flux density decreases. Therefore, the content of Mn should be 0.005-0.30%.
  • the content must be as low as possible to suppress magnetic aging degradation. Further, in order to sufficiently exhibit the effect of improving the texture under the ultralow A1 conditions employed in the present invention, the content must be reduced to 0.0050% or less. However, this reduction of C does not necessarily have to be achieved at the stage of molten steel or slurp, which is the starting material. That is, it may be achieved by the end of finish annealing in the steel sheet manufacturing process.
  • a typical decarburization method is decarburization annealing. When decarburization is performed during the production process, the C content in the starting material is preferably in the range of 0.0050% to 0.1%.
  • the A1 content of the steel sheet In order to obtain excellent grain growth and magnetic properties, it is necessary to reduce the A1 content of the steel sheet to 0.0004% or less. If the A1 content exceeds 0.0004%, A1N precipitates in the steel sheet, and the magnetic flux density in the finish-annealed product sheet decreases. Further, the recrystallized grain growth during strain relief annealing is also reduced, and the excellent effect of the present invention of remarkably reducing the iron loss value cannot be obtained.
  • N 0.0030% or less (including 0)
  • N combines with A1 to cause the precipitation of nitrides (A1N), and combines with Ti and the like to form various nitrides, thereby reducing the magnetic flux density of finish-annealed products.
  • A1N nitrides
  • Ti and the like nitrides
  • it hinders the growth of recrystallized grains during strain relief annealing, which hinders a sufficient decrease in iron loss value. Therefore, it is necessary to reduce the N content to 0.0030% or less. Preferably it is 0.0025% or less.
  • the non-oriented electrical steel sheet of the present invention can be added in addition to the basic composition described above, in addition to Sb, Sn, P, Ni, REM, and Ca according to the properties of the steel sheet. These preferred The high content will be described later.
  • containing at least one of Cr: 5% or less and Cu: 5% or less does not hinder the effects of the present invention.
  • Non-oriented electrical steel sheet of the present invention cannot achieve the object of the present invention only by controlling the force composition having the above basic composition.
  • the nonmetallic inclusions dispersed in the finish-annealed steel sheet when the average recrystallized grain size of the steel sheet (finish-annealed product sheet) is D, the ductile inclusion has a length of 3 XD to 9 XD.
  • This ductile non-metallic inclusion having a length of 3 XD to 9 XD is hereinafter defined as a grain growth-inhibiting ductile non-metallic inclusion.
  • average recrystallization grain size and measure the number of crystal grains present in the area of 0.5 s Awakening 2 of the steel sheet to calculate the average area of crystal grains per unit based on it, the average The diameter used when calculating the diameter of a circle equal to the area was adopted.
  • This average crystal grain size is measured by observing a cross section (so-called L cross section) cut perpendicularly to the width direction of the steel sheet with an optical microscope.
  • the ductile inclusions are rod-shaped inclusions elongated in the rolling direction and inclusions continuously arranged in the rolling direction. When two or more inclusions within a distance of ⁇ 5 ° are aligned in a direction of ⁇ 5 ° with respect to the rolling direction, these inclusions are considered to be connected and regarded as one ductile inclusion. .
  • the inclusions include isolated circular inclusions in addition to the ductile inclusions. This is a non-ductile inclusion and is not counted as a ductile inclusion. Inclusions were classified as circular if the major axis was less than twice the minor axis, and ductile if greater than twice the minor axis.
  • Exemplary ductile inclusions Si0 2, A1 2 0 3 , Mn0, CaO or a number thereof; is ⁇ or Ranaru composite oxide (some, however if the non-ductile depending on the composition).
  • the length of a ductile inclusion refers to the maximum value of the length of a line segment drawn between any two points at the interface between the base metal (matrix structure) and the inclusion, that is, the distance between both ends of the ductile inclusion. (This is the major axis Do).
  • the number of ductile inclusions having a predetermined length was measured by the following procedure.
  • a cross section perpendicular to the width direction of the steel sheet was polished, and the as-polished surface (without performing any corrosion treatment, etc.) was observed with an optical microscope, and a small area different in color from the ground iron part was identified as an inclusion.
  • the observation field against one sample as 5 Yuzuru 2, the number of the form deemed extended inclusions having a predetermined length of the inclusions was approved by the measuring, the number per 1 cm 2 The number density was converted to the number.
  • the resulting slab is 1100. Heated to C, hot rolled to a thickness of 2.3 mm, pickled, cold rolled and finished to a final thickness of 0.35 ram. C, Finished annealing (recrystallization annealing) for 15 seconds to obtain a finished annealed plate (product plate). Adjustment of the amount of ductile inclusions (number density) and the form (length)
  • the average grain size of the obtained product was measured and the inclusions were observed to measure the length and the number density of the ductile inclusions. Then, 750 for the above products in an argon (Ar) atmosphere. C, annealing for 2 hours (hereinafter simply referred to as “strain relief annealing”) was performed, and the average crystal grain size was measured as in the case of the finish-annealed sheet.
  • the above annealing condition is a condition corresponding to the strain relief annealing at the customer.
  • Figure 1 shows the ratio of the average grain size of the steel sheet after strain relief annealing to the average grain size of the steel sheet after finish annealing obtained in this way (hereinafter referred to as the “strain relief annealing grain growth ratio” or simply “grain rate”). It is a graph showing the relationship between the growth ratio) and the N content.
  • the average recrystallized grain size after finish annealing is D
  • inclusions with a length of 3XD to 9XD grain growth inhibiting ductile nonmetallic inclusions
  • the grain growth inhibition ductility If the number density of nonmetallic inclusions is 1000 or less Zcm 2 , the strain growth annealing grain growth ratio Becomes 2 or more. However, the number density of grain growth inhibition ductile nonmetallic inclusions, the number of 1000 / cm 2 even less, when N content exceeds 0030% 0., or grain growth inhibiting ductile nonmetallic inclusions When the density exceeds 1000 / cm 2 , the strain relief annealing crystal grain growth ratio is less than 2.
  • the obtained product sheet was subjected to strain relief annealing at 750 ° C for 2 hours in an Ar atmosphere.
  • the cross sections perpendicular to the sheet width direction of these product plates (finished annealing plates) and strain relief annealing plates were observed with an optical microscope, and the average crystal grain size was measured.
  • the number density of the grain growth-inhibiting ductile nonmetallic inclusions was measured. The results are shown in Table 2. As shown in the table, in the sample in which the number density of the grain growth-inhibiting ductile non-metallic inclusions on the product sheet is 1000 ra2 or less, the strain relief annealing crystal grain growth ratio is large.
  • the average crystal grain size of the steel sheet (iron core material assembled into the stator) after strain relief annealing is determined by the finish annealing. It can be twice or more the size of the subsequent particles. This greatly reduces iron loss in the stator.
  • the crystal grains are relatively small. State, and the strength, especially the upper yield point (hereinafter abbreviated as YP), can be kept high. Further, by using the rotor and the stator, a high-performance rotating machine for high-speed rotation can be efficiently assembled. Since the strength level required for the rotor varies depending on the characteristics of the rotating machine, the size of the average crystal grain size, which is a factor controlling the steel sheet strength, is designed according to the required strength level of the rotor. Just fine. However, for a general rotating machine, the average crystal grain size after finish annealing of the steel sheet is preferably 6 to 25 ⁇ ra.
  • the strength of the steel sheet is about 200 to 400 MPa in YP and about 100 to 170 in Vickers hardness Hv.
  • the reason why the strain relief annealing crystal grain growth ratio is controlled by the number density of the grain growth inhibiting ductile non-metallic inclusions is as follows. Conceivable.
  • the volume fraction of the steel is considered to be almost constant, so that the crystal grain can be calculated from the Zener equation as shown below. Inclusions that are extremely long compared to the diameter are less likely to inhibit grain growth. In other words, the degree to which the ductile inclusions inhibit the grain growth depends on the length of the inclusions. According to the knowledge of the present inventors, the length of the ductile inclusions is 3 to 9 times the average crystal grain of the finish-annealed sheet. When it is twice, that is, when it is a grain growth-inhibiting ductile nonmetallic inclusion, it becomes the maximum. Therefore, the “strain relief annealing crystal grain growth ratio” is affected by the number density of the ductile inclusions having a length in this range, that is, “grain growth inhibiting ductile nonmetallic inclusions”.
  • the Zener's equation is the following equation that indicates the inhibitory force I on the growth of the inhibitor.
  • V is the molar volume of the matrix
  • ⁇ is the grain boundary energy
  • ⁇ is the volume fraction of the precipitate
  • r 0 is the average grain radius of the precipitate.
  • the content of Si, Mn, C, Sol is controlled to 1,000 or less per cm 2 .
  • the effect can be further improved. This was confirmed by the following experiment.
  • annealing recrystallization annealing
  • the average crystal grain size in each product plate was 10 to 20 tubes. Further, the number density of the grain growth inhibiting ductile nonmetallic inclusions in each product plate was 1,000 / cm 2 or less.
  • the magnetic properties after strain relief annealing are further improved by limiting Ti to 0.0020% or less, Nb to 0.0050% or less, and the V content to 0.0060% or less. be able to.
  • the iron loss after strain relief annealing can be greatly improved.
  • Ti, Nb, and V are both nitride and carbide forming elements, and when these nitrides precipitate finely, it is thought that, similarly to finely precipitated A1N, they have an adverse effect on texture formation and grain growth. Can be Therefore, it is considered that the above harm is prevented by reducing these elements, and as a result, good magnetic properties can be obtained.
  • Ti 0.0020% or less (including 0)
  • b 0.0050% or less (including 0)
  • V 0.0060% or less (including 0)
  • Ti, Nb, and V form fine nitrides or carbides and inhibit the growth of texture forming crystal grains.
  • the tendency is remarkable in non-oriented electrical steel sheets in which the contents of Sol.
  • These elements are respectively Ti: 0.0020% or less, Nb: 0.0050% or less, V: 0.0060 »/. If it is reduced below, the tendency to form nitrides or carbides is suppressed, which contributes to the improvement of iron loss especially after strain relief annealing. Suitable amounts of Sb and Sn are as shown below.
  • Sb 0.005-0.10% and Sn: 1 or 2 types selected from 0.005 to 0.2%
  • Sb and Sn suppress the fine precipitation of nitride and reduce the grain growth inhibiting effect of the nitride, thereby effectively promoting the formation of a texture advantageous in magnetic properties.
  • the effect appears at Sb: 0.005% or more and Sn: 0.005% or more, but exceeds 0.10% and 0.2 ° /, respectively. Above this, the grain growth is rather hindered.
  • the characteristics of the steel of the present invention can be more effectively exhibited by limiting or adding the following elements.
  • REM and Ca have the effect of increasing (ie reducing) iron loss by coarsening sulfides. Therefore, these elements are expressed in the range of expression of the effect, that is, REM: 0.0001 to 0.10%,
  • Ca 0.0001-0. 01 Ca can be added as appropriate.
  • a value of 6 to 25 / zm is advantageous in that the above-mentioned strain relief annealing grain growth ratio is relatively large, for example, 3 or more.
  • the method for producing the non-oriented electrical steel sheet according to the present invention is not particularly limited. Typically, it can be manufactured by the following process.
  • molten steel adjusted to a suitable component composition is formed into a slab by, for example, a continuous mirror manufacturing method. Then, this is hot-rolled into a hot-rolled sheet. After subjecting this to hot-rolled sheet annealing as needed, it is subjected to one or more cold rolling steps with intermediate annealing as necessary to finish to the final sheet thickness. The obtained cold rolled sheet is subjected to continuous annealing (finish annealing), and then an insulating coating is applied as necessary.
  • decarburizing annealing is appropriately performed after hot rolling.
  • the amount of ductile inclusions among the inclusions is controlled to be 1000 / cm 2 or less.
  • Such a con Trolling can be accomplished by any one or combination of the following means.
  • the length of nonmetallic inclusions is adjusted by controlling the manufacturing conditions, especially rolling conditions, to reduce the length of non-metallic inclusions to less than 3 times or more than 9 times the average recrystallized grain size of the finish-annealed steel sheet.
  • the length of the ductile inclusion in the hot-rolled sheet can be adjusted by increasing or decreasing the rolling reduction in hot rolling by increasing or decreasing the slab thickness or the hot-rolled sheet thickness.
  • the length of the ductile inclusion can be changed by increasing or decreasing the rolling reduction in a high-temperature region where the inclusions are stretched.
  • the cumulative rolling reduction after hot rolling increases, the ductile inclusions become longer, and if the cumulative rolling reduction decreases, the ductile inclusions tend to become shorter.
  • the length of the nonmetallic inclusion can also be adjusted by increasing or decreasing the thickness.
  • the conditions of the finish annealing temperature and soaking time are changed to increase or decrease the average grain size, and as a result, the length of the non-metallic inclusions is reduced to less than three times or more than nine times the average grain size. It can also be the main.
  • the annealing temperature of the continuous annealing (finish annealing) applied to the cold-rolled sheet cold-rolled to the final sheet thickness was 700 to 800.
  • C is preferable for adjusting the average crystal grain size to 6 to 25 / xm or adjusting the hardness of the steel sheet to an appropriate level, for example, the Vickers hardness (Hv) to 100 to 170.
  • the Vickers hardness be in the above range in order to secure the strength and punching property of the steel sheet.
  • the non-oriented electrical steel sheet thus manufactured can be punched into an iron core for a rotating machine and assembled into a rotor and a stator.
  • the core material for the rotor and the stator are simultaneously punched from the same steel plate, laminated and assembled into a rotor and a stator member, and then only the stator member is subjected to strain relief annealing to promote grain growth, The iron loss can be reduced.
  • the core material for the rotor is not subjected to strain relief annealing accompanied by grain growth, and maintains high strength. It is better to leave.
  • the strain relief annealing temperature is preferably in the range of 700 ° C to 800 ° C.
  • the annealing time is preferably about 10 minutes to 3 hours.
  • the conditions of the strain relief annealing are more preferably those in which the strain relief annealing grain growth ratio is 2 or more within the above range, but, for example, the temperature is preferably 750 ° C for about 2 hours in an inert gas atmosphere. desirable. Further, it is preferable to perform the strain relief annealing at a temperature equal to or higher than the finish annealing from the viewpoint of ensuring grain growth.
  • the non-oriented electrical steel sheet subjected to finish annealing is further subjected to a slight strain, for example, a rolling strain of about 0.5 to 5%, punched out, subjected to a strain relief annealing of 700 to 800, and recrystallized.
  • the crystal grain size can be increased to 30 ⁇ : LOO / zm.
  • the steel sheet treated in this way can be used particularly for assembling a stator requiring low iron loss. Suitable strain relief annealing conditions in this case are also as described in the previous paragraph.
  • a slab having the component composition shown in Table 4 and comprising the balance of iron and inevitable impurities was produced by a continuous production method. Note that the amounts of Ti, Nb, V, S, and 0 were reduced to the above preferable ranges. After heating these slabs at 1110 ° C for 40 minutes, they were hot rolled into hot rolled sheets with a thickness of 2.5 m. The obtained hot-rolled sheet was pickled, the scale was removed, and then cold-rolled to obtain a cold-rolled sheet having a thickness of 0.50. Then, by volume ratio, hydrogen: 50% _nitrogen: 50 ° /. In the atmosphere of 780 ° C for 10 seconds. A semi-organic coating solution consisting of dichromate and resin was applied to the resulting annealed plate, and baked at 300 ° C to obtain a product plate.
  • the amount of grain growth-inhibiting ductile nonmetallic inclusions was varied by changing the slab thickness and changing the rolling schedule in hot rolling.
  • a sample was cut out from the obtained product plate, and the magnetic flux density, iron loss, upper yield point (YP), and Vickers hardness (Hv) were measured in accordance with JIS C2550.
  • the upper yield point ( ⁇ ) is the average value of the rolling direction and the direction perpendicular to the rolling direction.
  • the average crystal grain size and the number density of the grain growth inhibiting ductile nonmetallic inclusions were measured. What The measurement was performed on a plane perpendicular to the width direction. Next, the above product plate was subjected to a strain relief annealing at 50 ° C for 2 hours in an argon atmosphere, and then the iron loss and average crystal grain size were measured in the same manner as performed for the product. Furthermore, the strain relief annealing crystal grain growth ratio was calculated. Table 4
  • Table 5 shows the obtained results.
  • those having the component composition and the grain growth-inhibiting ductile nonmetallic inclusion number density according to the present invention have a large strain relief annealing crystal grain growth ratio, and particularly iron loss after strain relief annealing. Value is low.
  • the rotor and stator of the rotating machine can be stamped out and manufactured at the same time. It is suitable.
  • the magnetic flux density is also high enough.
  • examples (27, 29) to which Sb and Sn are added the magnetic properties are significantly improved by the strain relief annealing. Table 5
  • a continuous steel slab having the composition shown in Table 6 and having a thickness of 210 and consisting of iron and inevitable impurities was manufactured.
  • the grain growth inhibition ductile nonmetallic inclusions amount is to fit a range of N 1000 m 2 or less by optimizing optimizing the hot rolling condition of slag composition in steelmaking process.
  • Example 2 The obtained slap was treated in the same manner as in Example 1 to obtain a product, and tested in the same manner as in Example 1. However, the finish annealing of steel symbol 58 was performed at 680 ° C, and the finish annealing of steel symbol 59 was performed at 850.
  • Table 7 shows the obtained results. As shown in Table 7, those having the component composition and the average crystal grain size according to the present invention have excellent strain relief annealing crystal grain growth ratio and strength and magnetic properties with excellent deviation, and It is suitable for simultaneous stamping production of rotor and stator.
  • controlling the finish annealing temperature to 700 to 800 ° C or controlling the average recrystallized grain size of the product sheet to 6 to 25 m increases the strength before strain relief annealing and the strength after strain relief annealing. It can be seen that it is advantageous for achieving both low iron loss values.
  • the non-oriented electrical steel sheet according to the present invention has a feature that it is excellent in so-called recyclability as well as the non-oriented electrical steel sheet. That is, when a conventional iron core material having a high A1 content is recycled to form a motor shaft or the like, the surface oxidation of molten steel proceeds and the viscosity increases. For this reason, the fillability of molten steel in the mold is reduced, and a sound solid may not be obtained. Therefore, although scrap containing A1 is generally considered to have poor recyclability, the non-oriented electrical steel sheet according to the present invention is a low-A1 material, and recyclability for manufacturing is extremely high.
  • the high magnetic flux density non-oriented electrical steel sheet according to the present invention allows the rotor material and the stator material to be simultaneously sampled from the same steel sheet while providing the rotor material with high magnetic flux density and high strength.
  • a high magnetic flux density and low iron loss can be imparted to the stator material.
  • the production efficiency and output characteristics of the rotating machine member and, consequently, the rotating machine can be greatly improved.
  • the non-oriented electrical steel sheet according to the present invention is excellent in recyclability at the time of forging, and has improved resilience at the time of recycling punched material scrap.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Power Engineering (AREA)
  • Dispersion Chemistry (AREA)
  • Soft Magnetic Materials (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)
  • Physics & Mathematics (AREA)
  • Manufacturing & Machinery (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Electromagnetism (AREA)
  • Iron Core Of Rotating Electric Machines (AREA)

Abstract

L'invention concerne une tôle d'acier magnétique non orientée possédant une composition chimique en % en masse dans laquelle la teneur en Si et Mn est respectivement de 0,1 à 1,2 % et de 0,005 à 0,30 %, et la teneur en C, Sol. Al et N est limitée respectivement à 0,0050 ou moins, à 0,0004 % ou moins et à 0,0030 % ou moins, 0 % étant inclus, et possède un nombre volumique de molécules d'inclusions non métalliques ductiles inhibant la croissance de grain, dispersées dans la tôle d'acier, de 1 000 parties/cm2 ou moins dont 0. Une inclusion non métallique ductile inhibant la croissance de grain correspond à une inclusion contenue dans une tôle d'acier ayant subi un recuit de finition d'une longueur de 3 x D à 9 x D, D représentant un diamètre de particule moyen de grains recristallisés dans la tôle d'acier. La tôle d'acier magnétique non orientée permet la production, à partir d'une tôle d'acier, d'un matériau pour rotor possédant une densité de flux magnétique élevée ainsi qu'une grande résistance, et d'un matériau pour stator présentant une densité de flux magnétique élevée et des faibles pertes dans le fer après recuit de suppression des contraintes.
PCT/JP2003/009947 2002-08-06 2003-08-05 Tole d'acier magnetique non orientee, element pour machine tournante et machine tournante Ceased WO2004013365A1 (fr)

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EP1662010A1 (fr) 2004-11-24 2006-05-31 ARVEDI, Giovanni Tole laminée à chaud pour la production de paquets de tole électromagnétiques
US7470333B2 (en) * 2003-05-06 2008-12-30 Nippon Steel Corp. Non-oriented electrical steel sheet excellent in core loss and manufacturing method thereof
EP2762591A4 (fr) * 2011-09-27 2015-07-15 Jfe Steel Corp Feuille d'acier magnétique non à grains orientés
EP2975152A4 (fr) * 2013-03-13 2016-04-06 Jfe Steel Corp Plaque en acier électromagnétique non directionnel dotée d'excellentes caractéristiques magnétiques
EP3358027A4 (fr) * 2015-10-02 2018-08-08 JFE Steel Corporation Tôle d'acier électromagnétique à grains non orientés et procédé de fabrication de cette dernière
EP3404124A4 (fr) * 2016-01-15 2018-12-26 JFE Steel Corporation Tôle d'acier électromagnétique à grains non orientés et procédé de production de celle-ci
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US10526673B2 (en) 2014-07-31 2020-01-07 Jfe Steel Corporation Non-oriented electrical steel sheet and method for producing the same, and motor core and method of producing the same
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US7470333B2 (en) * 2003-05-06 2008-12-30 Nippon Steel Corp. Non-oriented electrical steel sheet excellent in core loss and manufacturing method thereof
EP1662010A1 (fr) 2004-11-24 2006-05-31 ARVEDI, Giovanni Tole laminée à chaud pour la production de paquets de tole électromagnétiques
US9466411B2 (en) 2011-09-27 2016-10-11 Jfe Steel Corporation Non-oriented electrical steel sheet
EP2762591A4 (fr) * 2011-09-27 2015-07-15 Jfe Steel Corp Feuille d'acier magnétique non à grains orientés
US10102951B2 (en) 2013-03-13 2018-10-16 Jfe Steel Corporation Non-oriented electrical steel sheet having excellent magnetic properties
EP2975152A4 (fr) * 2013-03-13 2016-04-06 Jfe Steel Corp Plaque en acier électromagnétique non directionnel dotée d'excellentes caractéristiques magnétiques
US10526673B2 (en) 2014-07-31 2020-01-07 Jfe Steel Corporation Non-oriented electrical steel sheet and method for producing the same, and motor core and method of producing the same
EP3358027A4 (fr) * 2015-10-02 2018-08-08 JFE Steel Corporation Tôle d'acier électromagnétique à grains non orientés et procédé de fabrication de cette dernière
EP3404124A4 (fr) * 2016-01-15 2018-12-26 JFE Steel Corporation Tôle d'acier électromagnétique à grains non orientés et procédé de production de celle-ci
US20190017138A1 (en) * 2016-01-15 2019-01-17 Jfe Steel Corporation Non-oriented electrical steel sheet and production method thereof
US11008633B2 (en) * 2016-01-15 2021-05-18 Jfe Steel Corporation Non-oriented electrical steel sheet and production method thereof
CN110205462A (zh) * 2019-06-28 2019-09-06 武汉钢铁有限公司 高速电机用无取向硅钢生产方法
EP4296392A4 (fr) * 2021-02-19 2024-06-05 Nippon Steel Corporation Tôle d'acier laminé à chaud pour tôle d'acier électromagnétique non orientée ainsi que procédé de fabrication de celle-ci, et procédé de fabrication de tôle d'acier électromagnétique non orientée

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JP2004068084A (ja) 2004-03-04
TW200403346A (en) 2004-03-01

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