EP1411138A1 - Nicht orientiertes elektromagnetisches stahlblech - Google Patents

Nicht orientiertes elektromagnetisches stahlblech Download PDF

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Publication number
EP1411138A1
EP1411138A1 EP02738812A EP02738812A EP1411138A1 EP 1411138 A1 EP1411138 A1 EP 1411138A1 EP 02738812 A EP02738812 A EP 02738812A EP 02738812 A EP02738812 A EP 02738812A EP 1411138 A1 EP1411138 A1 EP 1411138A1
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content
steel
sheet
oriented electrical
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French (fr)
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EP1411138A4 (de
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Masaaki Intellectual Property Dept. KOHNO
Masaki Intellectual Property Dept. KAWANO
Atsuhito Intellectual Property Dept. HONDA
Akio Intellctual Property Dept. FUJITA
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JFE Steel Corp
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JFE Steel Corp
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • 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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C22C38/004—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
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • H01F1/147—Alloys characterised by their composition
    • 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
    • H01F1/14708—Fe-Ni based alloys
    • H01F1/14716—Fe-Ni based alloys in the form of sheets
    • 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
    • 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

Definitions

  • the present invention relates to non-oriented electrical steel sheets used for iron core materials for electric apparatus.
  • the present invention relates to a non-oriented electrical steel sheet suitable for an iron core material for reluctance motors, IPM-type DC brushless motors, and the like, and relates to a method for manufacturing the non-oriented electrical steel sheet, wherein the reluctance and DC brushless motors need to have high dimensional accuracy in punching together with high magnetic flux density, and the DC brushless motors further need to have high strength.
  • the non-oriented electrical steel sheet is of a soft magnetic material mainly used for iron cores of electric apparatus such as motors and transformers.
  • the non-oriented electrical steel sheet needs to have a small core loss and a high magnetic flux density.
  • magnetic characteristics of the non-oriented electrical steel sheet for iron cores are being improved, that is, the core loss is being lowered and the magnetic flux density is being increased.
  • Conventional AC induction motors which are of an asynchronous type, are being replaced with synchronous motors having high efficiency, and high-performance motors are being increased, rapidly.
  • a synchronous motor is classified into a DC brushless motor type and a reluctance motor type, wherein the DC brushless motor includes a surface permanent magnet (SPM) type and an interior permanent magnet (IPM) type, and the reluctance motor uses reluctance torque generated by the magnetic saliency of the rotor and the stator.
  • SPM surface permanent magnet
  • IPM interior permanent magnet
  • the reluctance motor uses reluctance torque generated by the magnetic saliency of the rotor and the stator.
  • the magnitude of the torque depends on the shapes of the rotor and the stator, the gap between the rotor and the stator, and the magnetic flux density of the materials. Accordingly, it is important for the iron core material for the reluctance motor to have high magnetic flux density and high dimensional accuracy in punching than other motors.
  • the non-oriented electrical steel sheet which is a motor material, needs to be improved in magnetic characteristic not only at a conventional commercial frequency (50-60 Hz) but also at a high frequency of 400 Hz or higher.
  • the Si content is generally increased.
  • top-grade non-oriented electrical steel sheets have an Si content of about 3.5% by mass in some cases.
  • the Si content is increased, the core loss is lowered but the magnetic flux density is caused to decrease simultaneously.
  • the P content is controlled in a range of about 0.08-0.1% by mass.
  • the following technique is disclosed in Japanese Unexamined Patent Application Publication No. 56-130425: the punching properties are improved by adding P in an amount of less than 0.2% by mass.
  • the following technique is disclosed in Japanese Unexamined Patent Application Publication No. 2-66138: P is added to Al-containing steel to improve the magnetic characteristics with the combined effects of Al and P, wherein the Si content in the steel is limited to 0.1% by mass or less and the Al content is in the range of 0.1-1.0% by mass.
  • the technique for improving the punching properties by adding P is focused on reducing the burrs by adjusting the hardness but does not make any consideration for the dimensional accuracy in punching.
  • the interior permanent magnet-type DC brushless motor needs to have high punching accuracy and magnetic flux density in order to increase the torque and in order to downsize the motor constitution.
  • the electrical steel sheet needs to have high strength in order to become possible to rotate in higher speed of the rotor and in order to prevent the interior permanent magnet from being detached.
  • high Si steel is advantageous from the point of view of the strength but low Si content steel is preferred from the point of view of the magnetic flux density. Thus, it is conventionally difficult to obtain high strength together with high magnetic flux density.
  • high magnetic flux density and low core loss are characteristics that are commonly preferred for all the applications of non-oriented electrical steel sheets, such as various motors and transformers.
  • the high magnetic flux density and high dimensional accuracy are particularly important from the point of view of the operating principle.
  • non-oriented electrical steel sheet having the following characteristics has not been found: excellent magnetic characteristics such as high magnetic flux density and low core loss, and superior punching properties that is, particularly high dimensional accuracy.
  • another non-oriented electrical steel sheet further having the following characteristic has also not been found: high strength required for the interior permanent magnet-type DC brushless motor and the like.
  • non-oriented electrical steel sheet further having the following characteristics has also not been found: high-frequency characteristics adapted to the high-speed rotation of recent motors and to multipolar motors.
  • the present invention has been developed in view of the above situation, and it is an object of the present invention to provide non-oriented electrical steel sheets suitable for iron cores of motors and transformers and the like, and particularly to provide the following non-oriented electrical steel sheets:
  • low-Si steel steel having a total Si and Al content of 0.03 to 0.5% by mass
  • medium-to-high Si steel steel having a total Si and Al content of more than 0.5% by mass
  • the inventors have found that not only excellent magnetic characteristics such as high magnetic flux density and low core loss can be obtained but also dimensional accuracy in punching is significantly improved when steel having a small Si and Al content the same as that of low-Si steel and thus essentially having high magnetic flux density is manufactured to adjust the average crystal grain diameter within a predetermined range and to add P to the resulting steel in an appropriate amount.
  • the inventors have also found that the addition of P in an appropriate amount in addition to the adjustment of the total Si and Al content within a range of more than 0.05% by mass to about 2.5% by mass provides a greatly increased strength without reducing the magnetic flux density, that is, unprecedented well-balanced magnetic and strength characteristics can be obtained, in addition to high dimensional accuracy in punching.
  • the present invention is based on the above findings.
  • the outline of the present invention is as follows.
  • hot rolled steel sheets may be annealed after hot rolling.
  • treatment for providing an insulating coating may be performed after finish-annealing.
  • steel ingots having basic composition including a C content of 0.0016-0.0028%, an Mn content of 0.20-0.22%, an Al content of 0.0007-0.0014%, an N content of 0.0012-0.0022%, and an Sb content of 0.03%, which are approximately constant, and containing 0.02% of P and 0.03-1.49% of Si, wherein the P content is constant and the Si content is varied; and steel products having the above basic composition and containing 0.10-0.11% of Si and 0.02-0.29% of P, wherein the Si content is approximately constant and the P content is varied.
  • These steel products were heated to 1100°C for 60 minutes and then hot-rolled so as to have a thickness of 2 mm.
  • the hot-rolled sheets were treated in a soaking process under the conditions of a temperature of 600°C and a time of two hours, which correspond to the coiling conditions, and then air cooled.
  • the resulting hot-rolled sheets were annealed at 900°C for 60 seconds, pickled, and cold-rolled so as to have a thickness of 0.5 mm.
  • the cold-rolled sheets were finish-annealed at different temperatures of 700-900°C to form recrystallized crystal grains having different diameters.
  • a semi-organic insulating coating having an average thickness of 0.6 ⁇ m was provided onto each finish-annealed sheet and then baked, and the baked sheets were used as samples for a punching test.
  • a circular die having a diameter of 21 mm was used and the clearance was set to 8% of the thickness.
  • the diameter (inner diameter) of a punched hole was measured in four directions that make angles of 0°, 45°, 90°, and 135° with respect to the rolling direction to determine the average of the four obtained diameters.
  • the difference between the maximum and the minimum of the four diameters was determined to be used as the index of punching anisotropy.
  • FIGS. 1 and 2 show the relationship between the result of the above test and the yield strength (YP) obtained using tensile specimens (JIS No. 5) obtained by cutting the above steel sheets in the rolling direction.
  • the soft samples having low YP each have a large difference between the die diameter and the punched hole diameter, and as YP increases, the punched hole diameter becomes closer to the die diameter, that is, the dimensional accuracy tends to improved. This tendency is considered to be due to the effect that shear drop deformation arising during the punching process is suppressed when the strength is large, as conventionally known.
  • the samples of which the strength is adjusted by changing the P content have superior dimensional accuracy as compared with the conventional electrical steel sheets of which the strength is adjusted by changing the Si content, when both have substantially the same strength. Furthermore, the above samples have a small difference between the die diameter and the punched hole diameter, even in the relatively low YP range (FIG. 1).
  • FIG. 3 shows the relationship between the punched hole diameter and the average crystal grain diameter of the finish-annealed steel sheets
  • FIG. 4 shows the relationship between the anisotropy and the average crystal grain diameter (average grain size).
  • the inventors have studied the relationship between the manufacturing conditions and the magnetic characteristics using the steel sheets essentially having high magnetic flux density by minimizing the content of Si and Al, as much as possible, improving the core loss but lowering the saturation magnetic flux density.
  • FIG. 5 shows the relationship between the crystal grain diameter and the core loss (W 15/50 : a value at a frequency of 50 Hz and a maximum magnetic flux density of 1.5 T) of the finish-annealed sheets for the samples having a thickness of 0.5 mm, wherein the core loss is measured at a commercial frequency band.
  • the core loss is large because the electrical resistance is decreased.
  • the core loss greatly changes depending on the crystal grain diameter, the core loss is stable and small when the crystal grain diameter is about 30 ⁇ m or more. It is also confirmed that the core loss is small when the grain diameter is about 30 ⁇ m or more in the case that the electrical resistance is lowered by reducing the Al content.
  • the steel sheets having a high P content have superior dimensional accuracy in punching even when the grain size is about 30 ⁇ m or more.
  • FIG. 6 shows the relationship between the average crystal grain diameter and the magnetic flux density of the steel sheets
  • FIG. 7 shows the relationship between the core loss and the magnetic flux density.
  • B 50 represents the magnetic flux density at a magnetizing force of 5000 A/m.
  • the core loss is improved but the magnetic flux density is significantly decreased.
  • the magnetic flux density remains large when the core loss is improved due to the growth of the crystal grains.
  • P is an embrittling element
  • defects such as edge cracks and delamination cracks mainly arise during a cold-rolling process in some cases when the P content is large in the same manner as for the present invention.
  • the inventors have intensively studied this phenomenon to obtain the following findings: when a slab is heated to a temperature in the ferrite-austenite coexisting region during a hot-rolling process, redistribution of P between austenite grains and ferrite grains to cause the significant segregation of P in the ferrite grains, thereby promoting the embrittlement of the slab.
  • the heating temperature of slabs during a hot-rolling step must be in the single-phase austenite region (or the single-phase ferrite region, if possible).
  • P is a ferrite-forming element
  • P has a function of reducing the single-phase austenite area at around the heating temperature of slabs.
  • single-phase austenite can be obtained when the Si content is small and the heating temperature of slabs is 1000-1200°C.
  • the steel sheets containing more than 0.26% of P had delamination cracks even if the steel sheets had any composition.
  • Steel products having a various Si, Mn, Al, P content were prepared in a laboratory to investigate the conditions of suppressing the segregation of P at a temperature range of about 1000-1200°C to the extent not to cause the rolling defect.
  • the above slab-reheating temperature is preferable in view of the stable precipitation of carbides, nitrides, and sulfides contained in the steel products.
  • the P content needs to be 0.26% or less.
  • the conditions for avoiding the embrittlement in the double phase coexistent region and the conditions for avoiding the embrittlement in the single-phase ferrite region can be combined into the condition P ⁇ about 0.26% and the condition P F ' ⁇ about 0.26.
  • the conditions for avoiding the embrittlement due to P are as follows: P ⁇ about 0.26%, and P ⁇ P A ' or P F ' ⁇ about 0.26.
  • steel sheets can be manufactured without causing defects such as delamination cracks after a cold rolling step when the steel sheets are heated at a temperature in the single-phase austenite region or in the single-phase ferrite region during a hot rolling step, and steel sheets can be manufactured when the Si content and the Al content are relatively large, that is, the quantity of P distributed to the ferrite phase is small, even if the steel sheets are heated at a temperature in the ferrite-austenite double phase region.
  • the inventors investigated such steel composition that the single-phase austenite or single-phase ferrite structure is formed in a slab-reheating temperature range (about 1000-1200°C) during a hot rolling step even if the P content is about 0.1% or more.
  • Ni is effective in enhancing the austenite area at the hot-rolling temperature of P-containing steel, wherein Ni is an element suitable for improving the magnetic characteristics and suitable for maintaining the strength.
  • the following steel samples were prepared: steel products having the basic composition including a C content of 0.0013-0.0026%, an Mn content of 0.18-0.23%, an Al content of 0.0007-0.0013%, an N content of 0.0014-0.0025%, and an P content of 0.16-0.18%, which are approximately constant, and containing 0.95-2.44% of Si and 0-2.20% of Ni, wherein the Si content and the Ni content are varied.
  • the steel samples were rolled so as to have a thickness of 0.50 mm in the similar prosess as EXPERIMENT 2, and the delamination cracks in the obtained cold-rolled sheets were investigated. The results are shown in FIG. 9.
  • the steel sheets containing 1.1-1.5% of Si and no Ni have cracks, but the steel sheets containing 1.1-1.5% of Si and Ni have no cracks and thus the hot rolling is possible.
  • the steel sheets containing 1.95% of Si and no Ni and the steel sheets containing 2.4% of Si and no Ni can be hot-rolled without cracks.
  • the steel sheets when such steel sheets contains Ni in a large amount, the steel sheets have cracks in some cases.
  • the slab-reheating temperature which is 1000-1200°C, is in the single-phase austenite region, and in the latter case, the degree of the concentration of P is small when the slab-reheating temperature is in the double phase region or in the single-phase ferrite region.
  • the cold-rolled steel sheets, having a thickness of 0.50 mm, prepared in Experiments 2 and 3 were finish-annealed, and a semi-organic insulating coating having an average thickness of 0.6 ⁇ m was provided onto each resulting steel sheet and then baked. These samples were provided to the punching test according to the procedure described in Experiment 1 to investigate the punched hole diameters and the anisotropy thereof. The results are shown in FIGS. 10 and 11. As shown in the figures, among the steel sheets having an Si and Al total content of more than 0.5%, the steel sheets satisfying the condition P ⁇ 0.10% have superior dimensional accuracy in punching. In the Ni-containing steel sheets, the Ni content varies for 0.38% to 2.20%.
  • FIG. 12 shows the relationship between the magnetic flux density B 50 and the tensile strength TS of these samples.
  • the tensile strength was obtained from the same tensile test as in the Experiment 1, and the magnetic flux density was also obtained according to the procedure in the Experiment 1.
  • the steel sheets containing about 0.1% or more of P have good balance between the magnetic flux density B 50 and the tensile strength TS, as compared with conventional electrical steel sheets having a medium-to-high Si content (that is, Si + Al > 0.5%). Particularly, as the P content is increased, the tensile strength is increased and the magnetic flux density is not decreased but tended to increase. This is characteristic of the steel sheets as compared with conventional electrical steel sheets to which alloy elements such as Si and Al, which are not of a ferromagnetic material, are added to increase the strength thereof, wherein such a method causes a decrease in magnetic flux density.
  • the Si, Al, P, and Ni content of steel are limited to the following range.
  • the average grain size of finish-annealed sheets are limited to the following range.
  • Total content of one or two of Si and Al in low-Si steel about 0.03-0.5%
  • Si and Al in steel have a deoxidizing function
  • Si and Al are used as deoxidizing agents alone or in combination.
  • the alone Si or Al content or the Si and Al total content must be about 0.03% or more.
  • Si and Al have a function of increasing the resistivity and a function of improving the core loss.
  • Si and Al decrease the saturation magnetic flux density.
  • the upper limit of the content thereof is limited to 0.5%.
  • Total content of one or two of Si and Al in medium-to-high Si steel more than 0.5% to about 2.5%
  • the Si and Al total content may exceed 0.5%.
  • the medium-to-high Si steel having a large P content has high dimensional accuracy in punching and good balance between the strength and the magnetic flux density, as compared with conventional medium-to-high Si steel having a small P content.
  • the Si and Al total content exceeds 2.5%, it is difficult to cold-roll such steel by a method of the present invention.
  • the content is limited to the range from more than 0.5% to about 2.5%.
  • P is an especially important element in the present invention.
  • P has high ability to promote the formation of a solid solution and therefore has a function of adjusting the steel strength, as previously known.
  • the average crystal grain diameter must be about 30 ⁇ m or more in order to obtain low core loss in the present invention, there is a problem in that the hardness is further decreased.
  • P is essential to improve the punching accuracy, that is, to suppress the increase of shear drops and burrs caused by the insufficient strength of the steel sheets.
  • P has ability to decrease the rupture limit during a punching process to reduce the total quantity of the punching deformation and ability to increase the ⁇ 100 ⁇ ⁇ uvw> orientation in the texture of finish-annealed sheets. Therefore, P can improve the dimensional accuracy in punching with these effects.
  • P has the property of being able to increase the strength of steel sheets and not to decrease the magnetic flux density. In the medium-to-high Si steel, such effects can also be obtained.
  • the P content must be about 0.10% or more.
  • P is originally an element that makes steel brittle. Therefore, when the P content is excessively high, edge cracks and delamination cracks are readily formed, thereby lowering the productivity.
  • high-P steel can be manufactured by improving a manufacturing method thereof and by adding Ni, wherein the production of such steel is conventionally thought to be difficult.
  • the P content exceeds 0.26%, the production of the high-P steel is difficult even if a manufacturing method according to the present invention is used.
  • the P content is limited to the range from about 0.10% to about 0.26%.
  • Ni content about 2.3% or less (Ni can be optionally contained)
  • Ni has not only a function of improving the texture of steel to increase the magnetic flux density but also functions such as a function of increasing the electrical resistance to decrease the core loss and a function of increasing the strength of steel by solid solution strengthening to reduce shear drops during a punching process or so. Therefore, Ni can be positively added to steel.
  • Ni is an element that contributes to form an austenite phase
  • Ni has a function of extending the austenite region (the ⁇ -loop in the phase diagram) at about 1000-1200°C, wherein such a temperature range is suitable for heating a slab.
  • Ni is effective in increasing the manufactural stability. When this effect is used, low manufactural stability during a hot-rolling step can be greatly improved, wherein such low manufactural stability arises when the P content is high.
  • the slab-reheating temperature must avoid the ferrite-austenite. double phase region, which is a key point.
  • the Si and Al total content exceeds 0.5%, the ferrite-austenite double phase is readily formed at the slab-reheating temperature.
  • Ni has an effect of extending the ⁇ region, the single austenite phase can be obtained during a slab-reheating step even if the Si and Al total content is in the above range.
  • the Ni content exceeds about 2.3%, there is a risk that the magnetic flux density is lowered because the temperature at which transformation from the ferrite ( ⁇ ) phase to the austenite ( ⁇ ) phase starts is decreased to cause the austenite transformation to arise. Furthermore, in case of low-Si steel sheet, it is difficult to obtain an average crystal grain diameter of about 30 ⁇ m or more at a finish-annealing temperature lower than the transformation temperature, and thus, the core loss is decreased. Thus, the Ni content should be about 2.3% or less. When Ni is added to steel, the Ni content is preferably about 0.50% or more.
  • Average crystal grain diameter of finish-annealed sheet made of low-Si steel from about 30 ⁇ m to about 80 ⁇ m
  • a finish-annealed sheet needs to have an average crystal grain diameter of 30 ⁇ m or more, as shown in FIG. 5.
  • the crystal grain diameter exceeds about 80 ⁇ m, further improved core loss cannot be obtained.
  • steel products according to the present invention are of transformable steel, and the single-phase ferrite region suitable for recrystallization-annealing is in a range of 700-900°C.
  • Such a temperature range is relatively low as compared with that of ferrite steel having a high Si content, and therefore the excessive growth of crystal grains is disadvantageous to the productivity of a continuous short-time annealing facility.
  • the upper limit of the crystal grain diameter is limited to about 80 ⁇ m.
  • the crystal grain diameter is not particularly limited and may be in an ordinary range. Generally, the crystal grain diameter is about 20-200 ⁇ m.
  • the inventors have studied a method for improving the magnetic characteristics at a high frequency. Such characteristics have recently become important because the high-speed rotation and the increase of poles of motors have been advancing. As a result, it became clear that reducing the thickness is effective and the effect is particularly significant for low-Si steel. The experiment that provides the above result will now be described.
  • FIG. 13 shows the dependency of the coreless with the sheet thickness, at 400 Hz, of the steel sheet containing 0.11% of Si and 0.18% of P, the steel sheet containing 0.95% of Si and 0.02% of P and the steel sheet containing 2.0% of Si and 0.5% of Al.
  • FIG. 14 shows the dependency of the magnetic flux density with the thickness of these steel sheets.
  • the magnetic flux density is slightly decreased, wherein the degree of the decrease is very small.
  • the steel sheet having a smaller Si content has a significantly larger magnetic flux density than that of the other steel sheets all over the thickness range.
  • EV electric vehicles
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  • high magnetic flux density and low core loss at high frequency are important.
  • Such characteristics can be obtained by reducing the thickness of a low-Si and low-Al steel sheet, essentially having high magnetic flux density, according to the present invention.
  • the lower limit of the thickness is not particularly limited. However, when the thickness is excessively lowered, the number of man-hours needed to stack the cores is increased to raise the manufacturing cost and there is a problem in that it is difficult to interlock the stacked cores. Thus, the lower limit of the thickness is preferably about 0.10 mm for general applications.
  • C content 0 to about 0.010%
  • Element C having an age-hardening function deteriorates the magnetic characteristic (core loss) with the passage of time after the production of the steel sheet. Since the degree of the deterioration becomes significant when the C content exceeds about 0.010%, the C content is limited to 0.010% or less. In consideration of the deterioration due to the age-hardening function, smaller C content is more preferable. Thus, in the present invention, the C content may include substantially zero (below the lower limit of analysis).
  • Mn content about 0.5% or less
  • Mn has a function of fixing S by reacting with S to form MnS, thereby preventing the embrittlement caused by FeS during a hot-rolling step.
  • the resistivity is increased to improve the core loss.
  • the increase of the Mn content causes the decrease of the magnetic flux density.
  • the upper limit of the Mn content is limited to about 0.5%.
  • S is an unavoidable impurity.
  • S causes the embrittlement during a hot-rolling step, as described above and fine particles made of precipitated FeS prevent grain growth.
  • it is advantageous to minimize the S content as much as possible. Since the deterioration of the core loss becomes significant when the S content exceeds 0.015%, the upper limit thereof is limited to 0.015%.
  • S has a function of improving the shape of a sheared surface during a punching step. Therefore, the extent of traversing S is determined depending on the applications.
  • N content about 0.010% or less
  • N is also an unavoidable impurity. Fine particles made of precipitated AlN prevent crystal grain growth to increase the core loss. Thus, the N content is limited to 0.010% or less.
  • Sb and/or Sn content in a total amount of about 0.40% or less
  • the total content is preferably 0.01% or more when these elements are contained alone or in combination. However, if the content is excessively increased, the effect is not greatly increased. When the content exceeds 0.40%, the embrittlement arises to cause cracks during a cold-rolling step.
  • the total content is preferably 0.40% or less when the elements are contained alone or in combination.
  • Ca can be contained in an amount of about 0.01% or less, wherein Ca functions as a deoxidizing agent and effectively captures S, which is an impurity, together with Mn.
  • B can be contained in an amount of about 0.005% or less and Cr can be contained in an amount of about 0.1% or less in order to suppress the oxidation and nitridation during stress relief annealing.
  • the content of each element is preferably about 0.1% or less.
  • the excessive local segregation of P is suppressed to produce steel having high P content in a reproducible manner by performing the design for obtaining the following composition: the composition in which either one of the single ferrite or austenite phase can be obtained at a slab-reheating temperature; or the composition in which the concentration of P distributed into the ferrite phase, in which P is more readily concentrated, is suppressed when there is the austenite-ferrite duplex phase.
  • Molten steel having the above preferable composition is prepared by a converter-refining method, an electric furnace-melting method or the like to manufacture a slab by a continuous casting method or an ingot-blooming method.
  • the slab is then heated and then hot-rolled.
  • the preferable temperature is about 1000-1200°C.
  • the state of the phase is important in order to suppress the excessive local segregation of P.
  • P is an element that contributes to form the ferrite phase
  • P has a function of reducing the single-phase austenite region close to the slab-reheating temperature.
  • the single austenite phase can be obtained at a slab-reheating temperature of about 1000-1200°C.
  • the single austenite phase can be obtained at a slab-reheating temperature of about 1000-1200°C.
  • the degree of the segregation of P in the ferrite phase is in such a range that the embrittlement can be avoided, even if the ferrite-austenite coexisting phase is formed.
  • the slab is heated at a temperature in the single-phase ferrite region, a steel sheet can be made without forming delamination cracks if the P content is about 0.26% or less.
  • the coiling temperature is also an important factor in order to manufacture a high-P steel sheet. That is, when the coiling temperature is high, iron phosphide (Fe 3 P) is formed to deteriorate the bending properties and the rolling properties of the hot-rolled sheet. Therefore, the coiling temperature is about 650°C or less, preferably about 600°C or less, and more preferably about 550°C or less. That is, the winding is preferably performed at a temperature as low as possible. It is effective that the coil is acceleratingly cooled by such a method that the coil is soaked in a water bath or water is sprayed on the coil.
  • the hot-rolled coil is descaled by a pickling method or the like and then subjected to a cold-rolling step. In order to further increase the magnetic characteristics, the resulting hot-rolled coil may be annealed.
  • the hot-rolled sheet is preferably annealed at a temperature outside the ferrite-austenite coexisting region (two-phase coexisting region).
  • the reason is that the magnetic characteristics such as the magnetic flux density are not improved because the crystal grains cannot sufficiently grow at an annealing temperature in the two-phase coexisting region.
  • the suitable annealing temperature of the hot-rolled sheets made of the low-Si steel will now be described on an Ni content basis.
  • a steel sheet containing no Ni or a steel sheet having a relatively small Ni content of 1.0% or less can be annealed at such a temperature that is about 900°C and is within the single-phase ferrite region in the same manner as that a hot-rolled non-oriented electrical steel sheet is usually annealed.
  • the annealing temperature can be increased to such a temperature that is higher than the Ac3 transformation point and in the single-phase austenite region (preferably about 1050-1100°C): It is important to avoid an annealing temperature (particularly about 950°C) in the duplex region, which is the intermediate region between the two regions.
  • an annealing temperature of about 900°C corresponds to the duplex region since the austenite-forming temperature is lowered, thereby decreasing the magnetic flux density.
  • the crystal grains cannot sufficiently grow at an annealing temperature is 900°C or less, single-phase ferrite region, high magnetic flux density cannot be achieved.
  • the annealing temperature of the hot-rolled sheet having this content is limited to such a temperature that is in the single-phase austenite region (preferably about 1050-1100°C) which is the Ac3 transformation point or more.
  • the grain growth during an annealing step is not an important factor as compared with the low-Si steel sheet because low core loss can be achieved if the grain diameter is small.
  • the annealing temperature of the hot-rolled sheet is not particularly limited and is preferably 700-1100°C usually.
  • the obtained coil is descaled and then cold or warm-rolled once, or cold-rolled (or warm-rolled) twice or more with an intermediate annealing step therebetween so as to have a predetermined thickness.
  • the finish-annealing is then performed.
  • the finish-annealing is preferably performed at such a temperature that is 700°C or more and is in the single-phase ferrite region.
  • the reason is as follows: it is difficult to make the crystal grains to uniformly grow so as to have an average diameter of about 30 ⁇ m or more when the annealing temperature is less than 700°C, and the texture is deteriorated to decrease the magnetic flux density and to increase the core loss when the annealing temperature exceeds the single-phase ferrite region to form austenite grains.
  • the finish-annealing temperature is not particularly limited and is preferably 700-1100°C usually.
  • the temperature region in which single-phase ferrite or single-phase austenite is formed can be obtained by observing samples with an optical microscope, wherein the samples are prepared by heating and then water-cooling the pieces of each steel sheet having certain composition.
  • the temperature region can be estimated using a computational phase diagram obtained with a softwear for thermodynamic calculation, for example, Thermo-CalcTM.
  • an insulating coating may be provided onto the steel sheet in the same manner as for ordinary non-oriented electrical steel sheets.
  • the providing method is not particularly limited. The following procedure is preferable: the application of a coating solution and the baking treatment are performed in that order.
  • the obtained coil is slit into strips having a desired width and length.
  • the strips are punched into pieces having shapes of motor stators and rotors, and the resulting pieces are then stacked to form products, by users.
  • stress relief annealing will be carried out to these stacked cores (usually at 750°C for 1-2 hours), and then used for manufacturing products.
  • Each molten steels having the composition shown in Table 1 were experimentally casted.
  • the obtained ingots were hot-rolled into a sheet bar having a thickness of 30 mm.
  • the sheet bar was heated at 1100°C for 60 minutes and then hot-rolled so as to have a thickness of 2 mm.
  • the hot-rolled sheet was maintained at 600°C for two hours in a soaking step and was then air cooled, wherein such conditions correspond to coiling conditions.
  • the hot-rolled sheet was annealed at 950°C for 60 second, pickled, and then cold-rolled (once) so as to have a thickness of 0.50 mm.
  • the cold-rolled sheet was finish-annealed at various temperatures of 700-900°C to obtain different recrystallized grain diameters.
  • subsequent treatment and the evaluation were not performed.
  • the samples No. 56-59 were each prepared by the following procedure: a sheet bar was hot-rolled and then cold-rolled twice with an intermediate annealing step therebetween at 800°C, without annealing the hot-rolled sheet.
  • a semi-organic insulating coating was provided onto the finish-annealed sheet so as to have an average thickness of 0.6 ⁇ m to form samples, which were used in various tests.
  • a circular die having a diameter of 21 mm was used and the clearance was set to 8% of the thickness.
  • the diameter (inner diameter) of a punched hole was measured in four directions that make angles of 0°, 45°, 90°, and 135° with respect to the rolling direction to determine the average of the four obtained diameters.
  • the difference between the maximum and the minimum of the four diameters was measured to use as the index of punching anisotropy.
  • the magnetic properties were measured by the Epstein method, using rectangular specimens having a length of 180 mm and a width of 30 mm, wherein the rolling direction makes an angle of 0° with respect to the longitudinal direction of one of the specimens and makes an angle of 90° with respect to the longitudinal direction of another.
  • the yield point (YP) was measured by a tensile test method at a crosshead speed of 10 mm/min. using a JIS No. 5 specimen of which the longitudinal direction is parallel to the rolling direction, and the upper yield stress was employed.
  • the P content does not satisfies the condition of the present invention, and the strength varies depending on the Si content and the crystal grain diameter.
  • the punching anisotropy remains relatively large, that is, the anisotropy is about 10-20 ⁇ m, wherein the anisotropy corresponds to the difference between the maximum and the minimum of the punched hole diameter.
  • the magnetic flux density decreases as the Si content increases.
  • the steel products G-H according to the present invention have low Si and Al content and contain a 0.10% of P or more.
  • Such steel products have a good punched hole shape and a small punching anisotropy even if yield point YP is 350 MPa or less, that is, the yield point YP is relatively small.
  • the steel products having an average crystal grain diameter of 30 ⁇ m or more are excellent in magnetic characteristic, that is, such steel products stably have low core loss and high magnetic flux density.
  • the hot-rolled sheet was annealed at 1100°C for 30 seconds, pickled, and then cold-rolled so as to have a thickness of 0.5 mm.
  • the cold-rolled sheet was finish-annealed at various temperatures to obtain different recrystallized grain diameters, wherein the various temperatures are 700°C or more and are in the single-phase ferrite region.
  • samples having a semi-organic insulating coating were prepared in the same manner as that of Example 1. The samples were used in various tests.
  • the steel IDs K-M are such samples that the deoxidization was performed by the Al content and decreasing the Si content.
  • the pair of the steel IDs N and O and the pair of the steel IDs Q and R are samples prepared in order to evaluate the effect of Ni.
  • Steel ID Composition (mass%) C Si Al Mn S Ni P N Sb Sn K 0.0011 0.01 0.32 0.25 0.0032 - 0.05 0.0020 ⁇ 0.001 0.044 L 0.0009 0.01 0.33 0.24 0.0039 - 0.16 0.0021 ⁇ 0.001 0.046 M 0.0019 0.02 0.31 0.22 0.0018 - 0.24 0.0024 ⁇ 0.001 ⁇ 0.001 N 0.0033 0.21 0.23 0.15 0.0028 - 0.16 0.0012 0.060 ⁇ 0.001 O 0.0024 0.21 0.24 0.18 0.0016 1.23 0.16 0.0018 0.055 ⁇ 0.001 P 0.0088 0.35 0.0011 0.35 0.0046 - 0.05 0.0031 ⁇ 0.001 ⁇ 0.001 Q 0.0082
  • Such samples that have composition within the scope of the present invention and have an average crystal grain diameter of 30 ⁇ m or more, which is a proper value, have superior dimensional accuracy in punching, low punching anisotropy, and further excellent magnetic characteristics. From the comparison of the steel products N and O and the comparison of the steel products Q and R respectively, it is clear that the steel products O and R containing Ni have a greatly increased magnetic flux density.
  • the steel ID F having the composition shown in Table 1 and the steel ID N and O having the composition shown in Table 4 were experimentally hot-rolled to have a thickness of 2 mm in the same manner as that of Example 1.
  • Each obtained hot-rolled sheet was annealed at 1100°C for 30 seconds; pickled, and then cold-rolled so as to have a thickness of 0.50-0.2 mm.
  • the obtained cold-rolled sheet was finish-annealed at various temperatures that is 700°C or more and is in the single-phase ferrite region to control the recrystallized grain diameter in a range of 35-45 ⁇ m.
  • Samples having a semi-organic insulating coating were prepared in the same manner as that of Example 1. The samples were used in various tests. For these samples, the core loss at high frequency, that is, at 400 Hz, was measured.
  • the steel products N and O are superior to the steel product F, which is a comparative example, in such a tendency. Furthermore, the examples of the present invention are superior in punching anisotropy at any thickness.
  • Each steel having the composition shown in Table 7 was experimentally casted to form an ingot.
  • the obtained ingots were treated at 1150 °C for one hour in a soaking step and then hot-rolled to form a sheet bar having a thickness of 30 mm.
  • the obtained sheet bar was heated at a temperature (SRT) shown in Table 8 and held for one hour and then hot-rolled so as to have a thickness of 2.0 mm.
  • the hot-rolled sheet was treated under the condition of a temperature of 580°C and a time of one hour, which corresponds to the coiling condition, and then air cooled. With some exception, the resulting hot-rolled sheets were annealed under the conditions shown in Table 8. The annealed sheets were pickled and then cold-rolled so as to have a thickness of 0.50 mm.
  • the machinability during a cold-rolling step was evaluated by observing the state of each sheet that is being cold-rolled and the texture in the cross section of the cold-rolled sheet during the cold-rolling step. Many delamination cracks parallel to a sheet surface were observed in the following steel products and samples: the steel products (W, Z, a, c, d, k, and 1) that have a high P content (0.10% or more) and composition which is outside the scope of the present invention, and the samples (No. 25 and 26) having composition within the scope of the invention but having slab-reheating temperature (SRT) or hot rolled sheet-coiling temperature (CT) that are outside the scope of the present invention. In some samples (No.
  • the cold-rolled sheets were finish-rolled at various temperatures which are 700°C or more.
  • a semi-organic insulating coating was provided onto each cold-rolled sheet, and the resulting cold-rolled sheets were provided to various tests.
  • JIS No. 5 specimens prepared by slitting the cold-rolled sheets in parallel to the rolling direction were used for measuring the strength.
  • the specimens were tested at a crosshead speed of 10 mm/s to obtain tensile strength (TS), which was evaluated. The result is shown also in Table 8.
  • the samples (No. 2-4, 7, 13, 14, 16-18, and 21-24) having composition that is within the scope of the present invention and containing 0.1% or more of P have excellent dimensional accuracy in punching in particular. That is, in the samples (No. 1, 6, 10, and 15) containing less than 0.1% of P, as the Si and Al total content increases, the dimensional accuracy in punching tends to increase but the punching anisotropy remains high. In contrast, it is clear that the examples of the present invention are excellent in both dimensional accuracy and punching anisotropy. Furthermore, the examples of the present invention have magnetic flux density that is the same as that or more than that of the comparative examples having a P content of less than 0.1%. Even more, the examples have high strength. That is, the examples have the excellent balance of the strength and the magnetic flux density.
  • the steel IDs M, N, and O having the composition shown in Table 4 were experimentally prepared.
  • sheet bars having a thickness of 30 mm were obtained by hot rolling.
  • the sheet bars were heated at each temperature (SRT) shown in Table 9 for 60 minutes and hot-rolled so as to have a thickness of 2 mm.
  • the hot-rolled sheets were treated in a soaking process under the conditions of each temperature (CT) and a time of one hour, which correspond to the coiling conditions, and then air cooled. With some exception, the hot-rolled sheets were then annealed at each temperature shown in Table 9 for 60 seconds.
  • the bending test was conducted at room temperature (23°C).
  • a specimen prepared from hot-rolled sheet having a length of 100 mm and a width of 30 mm was used in the bending test, wherein the longitudinal direction of the specimen is parallel to the rolling direction.
  • the repetitive bending test was conducted according to the method defined in JIS-C 2550. In the bending test, the bending radius was 15 mm. Table 9 shows the number of times each specimen was bent until cracks are formed on a surface.
  • Microstructures (phase) of each slab during the heating step and each hot-rolled sheet during the annealing step were investigated by the following procedure: each sheet bar and each hot-rolled sheet are separately maintained at a predetermined temperature (shown in Table 9) for a predetermined time (for one hour when the slab is heated or for 60 seconds when the hot-rolled sheet is annealed) and then quenched with water to fix the microstructure during the heating step. The obtained microstructure was observed with an optical microscope to determine the phase. The result is also shown in Table 9.
  • the above hot-rolled sheets were pickled and then cold-rolled (once) so as to have a thickness of 0.50 mm.
  • the cold-rolled sheets were checked if there are defects (delamination cracks) due to the embrittlement arising during the cold-rolling step.
  • the cold-rolled sheets having no delamination cracks were finish-annealed at various temperatures shown in Table 9.
  • a semi-organic insulating coating was then provided onto each finish-annealed sheet in the same manner as that of Example 1 to form samples, which were used in various tests. The obtained result is shown in Table 9.
  • the hot-rolled sheet has inferior cold-rolling workability and the electrical steel sheet has also inferior core loss.
  • the samples (No. 7 and 12) in which the hot-rolled sheet-annealing temperature is in the two-phase coexisting region and the sample (No. 13) in which the hot-rolled sheet containing more than 1.0% by mass of Ni annealed at a temperature in the single-phase alpha region the obtained electrical steel sheet have low magnetic flux density.
  • the finish-annealing temperature is outside the scope of the present invention and is not sufficient to form recrystallized crystal grains having a diameter of 30 ⁇ m or more, the magnetic characteristics are inferior.
  • the present invention provides a non-oriented electrical steel sheet having excellent magnetic characteristics such as high magnetic flux density and low core loss and further having high dimensional accuracy during a punching step and further provides a non-oriented electrical steel sheet having high strength, with manufactural stablity.
  • a non-oriented electrical steel sheet of the present invention is suitable for an iron core material for reluctance motors and DC brushless motors that are of an interior permanent magnet type, among iron core materials for various motors, wherein the reluctance motors need to have high dimensional accuracy and high magnetic flux density in combination, and the DC brushless motors need to have high strength.

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CN1318627C (zh) 2007-05-30
TW555863B (en) 2003-10-01
JP4329538B2 (ja) 2009-09-09
KR100956530B1 (ko) 2010-05-07
EP1411138A4 (de) 2005-01-12
KR20040014960A (ko) 2004-02-18
JPWO2003002777A1 (ja) 2004-10-21

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