WO2013146879A1 - 無方向性電磁鋼板およびその製造方法 - Google Patents
無方向性電磁鋼板およびその製造方法 Download PDFInfo
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- WO2013146879A1 WO2013146879A1 PCT/JP2013/058999 JP2013058999W WO2013146879A1 WO 2013146879 A1 WO2013146879 A1 WO 2013146879A1 JP 2013058999 W JP2013058999 W JP 2013058999W WO 2013146879 A1 WO2013146879 A1 WO 2013146879A1
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F3/00—Cores, Yokes, or armatures
- H01F3/02—Cores, Yokes, or armatures made from sheets
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
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- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
- C21D8/1233—Cold rolling
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- C—CHEMISTRY; METALLURGY
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
- C21D8/1261—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest following hot rolling
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- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
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- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- 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
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- 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
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- 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
- H01F1/18—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 with insulating coating
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- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F41/00—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties
- H01F41/02—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets
- H01F41/0206—Manufacturing of magnetic cores by mechanical means
- H01F41/0233—Manufacturing of magnetic circuits made from sheets
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/004—Dispersions; Precipitations
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
- C21D8/1222—Hot rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
- C21D8/1266—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest between cold rolling steps
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
- C21D8/1272—Final recrystallisation annealing
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
- H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
- H01F1/147—Alloys characterised by their composition
- H01F1/14766—Fe-Si based alloys
- H01F1/14775—Fe-Si based alloys in the form of sheets
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- H—ELECTRICITY
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- 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
- H01F1/14791—Fe-Si-Al based alloys, e.g. Sendust
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T29/00—Metal working
- Y10T29/49—Method of mechanical manufacture
- Y10T29/4998—Combined manufacture including applying or shaping of fluent material
- Y10T29/49982—Coating
- Y10T29/49986—Subsequent to metal working
Definitions
- the present invention mainly relates to a non-oriented electrical steel sheet used as an iron core of a motor of an electric device or a hybrid vehicle, and a manufacturing method thereof.
- Patent Document 1 describes this method. Yes.
- high alloying necessary for increasing the specific resistance has a problem of reducing the saturation magnetic flux density Bs.
- the steel sheet is significantly embrittled, which has a great adverse effect on productivity.
- the amount of Si exceeds 3%, the reduction of Bs and the embrittlement of the steel plate become remarkable, and it becomes very difficult to realize all of the required magnetic properties and productivity.
- Patent Document 1 the Si + Al content is limited to 4.5% or less, but it is insufficient to avoid embrittlement of the steel sheet, and the influence of Mn which is the essence of the present invention is considered. It wasn't done. Further, Bs was not evaluated, and good magnetic properties were not always obtained.
- Patent Document 2 describes that the specific resistance and Bs have a certain relationship, but it is not premised on obtaining a high torque, and it cannot avoid embrittlement of the steel sheet. Furthermore, it is not intended to improve iron loss at higher frequencies, and does not take into account improvement of brittleness, Bs, and iron loss in steel sheets with an Si content exceeding 3.0%, and good magnetic properties are not necessarily obtained. It wasn't something that could be done.
- the present invention solves the problems of the prior art as described above, and provides a non-oriented electrical steel sheet having a low iron loss, a high saturation magnetic flux density Bs and excellent productivity, and a method for producing the same. Specifically, it is an object to provide a non-oriented electrical steel sheet having low high-frequency iron loss and high Bs without impairing productivity, and a method for manufacturing the same.
- the gist of the present invention is as follows.
- the first aspect of the present invention is mass%, C: 0.0001% or more and 0.0040% or less, Si: more than 3.0%, 3.7% or less, sol. Al: 0.3% to 1.0%, Mn: 0.5% to 1.5%, Sn: 0.005% to 0.1%, Ti: 0.0001% to 0.0030%
- P: 0.005% to 0.000 It is a non-oriented electrical steel sheet consisting of only 05% or less, the balance being composed only of Fe and impurities, and has a specific resistance ⁇ ⁇ 60 ⁇ cm and a saturation magnetic flux density Bs ⁇ 1.945T at room temperature.
- the second aspect of the present invention is a hot rolling step of hot rolling the slab containing the chemical component described in (1) above, and without any hot-rolled sheet annealing after the hot rolling step. Or, hot-rolled sheet annealing or self-annealing, pickling to perform pickling, cold rolling to perform cold rolling twice or once with intermediate annealing, and finish annealing after the cold rolling step And in the cold rolling step, the steel plate temperature at the start of cold rolling is 50 ° C. or higher and 200 ° C. or lower, and the sheet passing speed in the first pass rolling is 60 m / It is a manufacturing method of the non-oriented electrical steel sheet as described in said (1) made into min-200m / min.
- the present invention it is possible to provide a non-oriented electrical steel sheet having a low high-frequency iron loss and a high saturation magnetic flux density Bs while maintaining high productivity, and a method for manufacturing the same.
- a non-oriented electrical steel sheet having a low high-frequency iron loss and a high saturation magnetic flux density Bs while maintaining high productivity, and a method for manufacturing the same.
- it can contribute to higher efficiency and higher performance of motors for air conditioners and refrigerators in the field of hybrid cars and electric cars, and it is excellent in manufacturing cost because it can maintain higher productivity.
- the inventors of the present invention have provided the non-oriented electrical steel sheet in accordance with the current motor trend, that is, when the Si content exceeds 3.0% with respect to the magnetic properties of the non-oriented electrical steel sheet.
- the elements contained in the steel sheet We intensively studied the manufacturing conditions.
- the present inventors have included Si, sol. It has been clarified that by making Al and Mn in an appropriate balance, productivity can be maintained while maintaining low high-frequency iron loss and high Bs.
- the present inventors have clarified that the degree of embrittlement can be evaluated by Al + (1/5) ⁇ Mn, and by setting this value to 4.25 or less, the brittleness is alleviated and the risk of fracture in the middle of threading It was found that can be reduced.
- the present inventors further effectively control the steel plate temperature during cold-rolling plate to further reduce the risk of breakage during the plate-feeding. I found.
- non-oriented electrical steel sheet made based on the above-described knowledge (hereinafter, may be simply referred to as a steel sheet) will be described in detail.
- C (C: 0.0001% or more and 0.0040% or less) C is desirably reduced as much as possible because it causes magnetic aging and deteriorates magnetic properties, and is set to 0.0040% or less.
- the C content is preferably 0.0030% or less, more preferably 0.0025% or less.
- the lower limit of the C content is 0.0001%, preferably 0.0003%, due to manufacturing load.
- Si is an element that increases the specific resistance of the electrical steel sheet and is effective in reducing iron loss.
- Si needs to exceed 3.0% for economical reasons that the specific resistance can be increased at a low cost.
- Si 3.0% or less, it is not desirable because it is necessary to increase the amount of other more expensive elements in order to obtain the specific resistance ⁇ ⁇ 60 ⁇ cm.
- the more Si is added the more effective it is for reducing the iron loss.
- the Si content is too large, the steel sheet becomes brittle and the fracture risk during the production is remarkably increased, so the upper limit of the Si content is 3.7. %, Preferably 3.5%.
- sol.Al 0.3% to 1.0%) sol.
- Al is an element that increases the specific resistance of the electrical steel sheet.
- sol. Al contributes significantly to lowering Bs and has a great influence on embrittlement of the steel sheet.
- the upper limit of the Al content is 1.0%, preferably 0.9%, more preferably 0.8%.
- the lower limit of the Al content is 0.3%, preferably 0.4%, more preferably 0.5%.
- Mn is an element that increases the specific resistance of the electrical steel sheet without significantly worsening the brittleness of the steel sheet, and is effective for reducing iron loss, and is required to be 0.5% or more. The more Mn is added, the more effective it is to reduce iron loss. However, since Mn is an austenite former, if it is too much, it will not be a single phase of ferrite during high-temperature treatment during production, and the magnetic properties will be remarkably reduced in the product plate. There are concerns that make it worse. For this reason, the upper limit of the Mn content is 1.5%, preferably 1.3%.
- the saturation magnetic flux density Bs ⁇ 1.945T at room temperature is required.
- the saturation magnetic flux density Bs at room temperature is an important magnetic characteristic that itself contributes to motor torque and the like.
- it directly affects the magnetization process it also affects the iron loss, and in order to obtain a good iron loss, it is important to design a component in consideration of the saturation magnetic flux density Bs at room temperature.
- sol. It is desirable to reduce the Al content.
- Si + (2/3) ⁇ sol By satisfying Al + (1/5) ⁇ Mn ⁇ 4.25, a non-oriented electrical steel sheet having the above-mentioned good magnetic properties can be manufactured without significantly reducing the risk of breakage during the manufacturing process. It becomes possible.
- Si, sol. Al and Mn mean numbers when the respective contents in the steel sheet are expressed by mass%.
- the upper limit of Al + (1/5) ⁇ Mn is preferably 4.1, more preferably 4.0, from the viewpoint of threading.
- Si since the resistivity at room temperature must be 60 ⁇ cm or more, Si, sol. It is necessary to change the balance of the added amounts of Al and Mn. That is, Si + (2/3) ⁇ sol.
- Si + (2/3) ⁇ sol When the value of Al + (1/5) ⁇ Mn is lower than 3.5, it is difficult to obtain a desired specific resistance. Therefore, Si + (2/3) ⁇ sol.
- the lower limit value of Al + (1/5) ⁇ Mn is 3.5, preferably 3.6, and more preferably 3.7.
- Sn has the effect of improving the B50 (magnetic flux density when excited at 5000 A / m) by improving the texture after finish annealing, so the Sn content is 0.005% or more, preferably 0.01 %. This effect is more effective as the amount added is increased. However, when the Sn content is 0.1% or more, the effect is saturated, and further, the steel sheet becomes brittle to increase the risk of breakage during sheet passing. %, Preferably 0.9%, more preferably 0.8%.
- Ti degrades magnetic properties and grain growth during finish annealing due to precipitation of TiN, TiC, etc., so it is desirable to reduce it as much as possible, and its content is 0.0030% or less, preferably 0.0025. % Or less. However, due to manufacturing load, the lower limit of the Ti content is set to 0.0001%, preferably 0.0003%.
- S (S: 0.0001% or more and 0.0020% or less) S is desirably reduced as much as possible because the magnetic properties and grain growth during finish annealing are deteriorated by precipitation of MnS, MgS, TiS, CuS, and the like. These sulfides are likely to precipitate finely and have a great influence on the deterioration of hysteresis loss in iron loss. Therefore, the S content is 0.0020% or less, preferably 0.0015% or less. However, due to manufacturing load, the lower limit of the S content is set to 0.0001%, preferably 0.0003%.
- N degrades the magnetic properties and grain growth during finish annealing due to the precipitation of TiN, AlN, etc., so it is desirable to reduce N as much as possible. Therefore, the N content is 0.0030% or less, preferably 0.0025%. However, due to manufacturing load, the lower limit of the N content is set to 0.0001%, preferably 0.0003%.
- C, Ti, S, and N increase the hysteresis loss by forming precipitates.
- an increase in the specific resistance that reduces the eddy current loss is effective.
- Bs which is another important magnetic property.
- Ni 0.001% to 0.2%)
- Ni has the effect of improving the toughness of the steel sheet and lowering the risk of fracture during production, so it is made 0.001% or more.
- the effect of Ni is higher as the amount added is higher, but the upper limit is set to 0.2% for economic reasons.
- P has an effect of improving B50 by improving the texture after finish annealing, so is 0.005% or more. This effect is more effective as the amount added is increased. However, if the P content exceeds 0.05%, the steel sheet becomes brittle and the risk of fracture at the time of sheet passing increases, so the upper limit is 0.05%, preferably 0.8. 03%.
- the chemical composition of the steel sheet contains Fe and impurities as the balance other than the above elements.
- the balance may consist only of Fe and impurities.
- the impurities include O and B which are unavoidable impurities that are inevitably mixed in the manufacturing process and the like, and Cu, Cr, Ca, REM, Sb, and the like, which are trace elements added to improve the magnetic characteristics. You may contain these impurities in the range which does not impair the mechanical characteristic and magnetic characteristic of this invention.
- FIG. An example of the component range in the present invention is shown in FIG.
- the Si addition amount was changed to 3.2%, 3.5%, and 3.7%, respectively, sol.
- Appropriate ranges of Al and Mn are shown as a portion surrounded by a frame. Note that the portions where the lines overlap are appropriately shifted. In the case of 3.2% Si indicated by a solid line, 0.3% ⁇ sol.
- sol. There is a limit of ⁇ ⁇ 60 ⁇ cm in a portion where Al and Mn are small, and sol.
- a steel slab that is melted in a converter and manufactured by continuous casting or ingot-bundling rolling can be used as the steel material composed of the above-mentioned components.
- the steel slab is heated by a known method and subsequently hot-rolled to obtain a hot-rolled sheet having a required thickness. Thereafter, hot-rolled sheet annealing or self-annealing is performed as necessary.
- the hot-rolled sheet is pickled, cold-rolled, or subjected to cold-rolling twice including intermediate annealing to a predetermined thickness, finish-annealed, and coated with an insulating coating.
- the risk of rupture in cold rolling and subsequent finish annealing can be further reduced by increasing the steel plate temperature at the start of cold rolling and lowering the sheeting speed in the first pass cold rolling. .
- This temperature needs to be 50 ° C. or higher. The higher the temperature, the higher the effect.
- the load on the equipment increases, so the upper limit is set to 200 ° C.
- the effect of reducing the risk of rupture appears when the plate passing speed is 200 m / min or less.
- the plate passing speed is too slow, the effect of increasing the temperature of the steel sheet due to processing heat generation is significantly reduced, and the plate temperature after the second pass.
- the effect of reducing the risk of breakage due to high temperatures is reduced.
- the rolling cost significantly increases, so the lower limit is set to 60 m / min.
- the production is carried out with a plate thickness of 0.50 mm or less, but it is desirable to make it 0.30 mm or less for reducing the iron loss, and when it is made 0.25 mm or less, a better iron loss can be obtained.
- the thickness is preferably 0.10 mm or more, and more preferably 0.20 mm or more. Examples of the present invention are shown below.
- Table 1 The various components shown in Table 1 were appropriately adjusted so that the specific resistance ⁇ was approximately 60 ⁇ cm, and the remainder was hot-rolled to a plate thickness of 2.0 mm with a steel slab composed of Fe and inevitable impurities.
- Hot-rolled sheet annealing was performed at 1000 ° C. for 1 minute, pickled, and cold-rolled to a sheet thickness of 0.30 mm.
- the plate temperature in the first pass of cold rolling was 70 ° C., and the plate passing speed was 100 m / min. This cold-rolled sheet was subjected to finish annealing at 1000 ° C. for 15 seconds, and an insulating coating was applied.
- Magnetic measurement was evaluated based on iron loss (W10 / 800) when sinusoidal excitation was performed at a maximum magnetic flux density of 1.0 T and a period of 800 Hz. The presence or absence of breakage was evaluated by whether or not breakage occurred during cold rolling and finish annealing when three coils were passed.
- Magnetic measurement was evaluated based on iron loss when sinusoidal excitation was performed at a maximum magnetic flux density of 1.0 T and a period of 800 Hz. The presence or absence of breakage was evaluated by whether or not breakage occurred during cold rolling and finish annealing when three coils were passed.
- Magnetic measurement was evaluated based on iron loss when sinusoidal excitation was performed at a maximum magnetic flux density of 1.0 T and a period of 800 Hz. The presence or absence of breakage was evaluated by whether or not breakage occurred during cold rolling and finish annealing when three coils were passed.
- This cold-rolled sheet was subjected to finish annealing at 1000 ° C. for 15 seconds, and an insulating coating was applied. The presence or absence of breakage was evaluated by whether or not breakage occurred during cold rolling and finish annealing when three coils were passed.
- the various components shown in Table 5 were appropriately adjusted so that the specific resistance ⁇ was about 69 ⁇ cm, and the remainder was hot-rolled to a sheet thickness of 2.0 mm with a steel slab composed of Fe and unavoidable impurities. Without hot-rolled sheet annealing, it was pickled as it was and cold-rolled to a thickness of 0.30 mm.
- the plate temperature in the first pass of cold rolling was 70 ° C., and the plate passing speed was 100 m / min. This cold-rolled sheet was subjected to finish annealing at 1050 ° C. for 15 seconds, and an insulating coating was applied. Magnetic measurement was evaluated based on iron loss when sinusoidal excitation was performed at a maximum magnetic flux density of 1.0 T and a period of 800 Hz.
- the iron loss W10 / 800 in the case of no hot-rolled sheet annealing increased the finish annealing temperature to 1050 ° C., but no. Compared to 23-35.
- no. In No. 49 the iron loss W10 / 800 was higher than 37.0 W / kg, and Bs was lower than 1.945T which is the standard of the present invention.
- sol. Al was outside the scope of the present invention.
- No. 47 and 48 are examples of the present invention. Good iron loss with W10 / 800 lower than 37.0 W / kg was obtained, and Bs was 1.945 T or more.
- the present invention it is possible to provide a non-oriented electrical steel sheet having a low iron loss, a high saturation magnetic flux density Bs, and excellent productivity, and a method for manufacturing the same.
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Abstract
Description
このような背景から、例えば自動車分野に於いては省エネルギーに寄与するハイブリッド自動車や電気自動車の躍進が目覚ましい。
また家電製品分野に於いても、消費電力の低い高効率エアコンや冷蔵庫の需要が高まっている。
これらの製品では共通してモータが使用されており、その高効率化が重要性を増している。
これらの機器では省スペース化、小重量化へのニーズからモータの小型化が図られており、出力を確保する必要から高速回転化が進んでいる。
高速回転に伴う損失の増大とそれに伴う機器の発熱を抑えるために、モータのコアとして用いられている無方向性電磁鋼板には高周波鉄損の低減が求められている。
一方でモータの性能としては高トルクを得ることも重要であり、特にモータの加速時などでは飽和磁束密度:Bsが高いことが無方向性電磁鋼板に求められる。
しかし固有抵抗を高めるために必要な高合金化は、飽和磁束密度Bsを低減するという問題がある。
これに加えて鋼板を著しく脆化させることから生産性に多大な悪影響を持つ。
特にSi量が3%を超えるとBsの低下と鋼板の脆化が著しくなり、求められる磁気特性と生産性の全てを実現することが非常に困難となる。
特許文献1ではSi+Al量が4.5%以下となるように制限しているが鋼板の脆化を回避するには不十分なものであり、更に本発明の骨子であるMnの影響について考慮がなされていなかった。
またBsについても評価されておらず、必ずしも良好な磁気特性が得られるものではなかった。
更に、より高周波での鉄損改善を目指したものではなく、Si量が3.0%を超えた鋼板での脆性やBs、鉄損の改善について考慮されておらず必ずしも良好な磁気特性が得られるものではなかった。
(2)本発明の第二の態様は、上記(1)に記載された化学成分を含むスラブを熱間圧延する熱間圧延工程と、前記熱間圧延工程後に、そのまま熱延板焼鈍無しで、あるいは熱延板焼鈍又は自己焼鈍を施し、酸洗を行う酸洗工程と、一回または中間焼鈍を挟む二回の冷間圧延を行う冷間圧延工程と、前記冷間圧延工程後に仕上げ焼鈍を行い、コーティングを施す工程と、を備え、前記冷間圧延工程では、冷間圧延の圧延開始時の鋼板温度を50℃以上200℃以下とし、1パス目の圧延における通板速度を60m/min以上200m/min以下とする上記(1)に記載の無方向性電磁鋼板の製造方法である。
自動車分野ではハイブリッド自動車や電気自動車、家電分野ではエアコンや冷蔵庫向けのモータの高効率化、高性能化に寄与することができ、更に高い生産性を維持できることから製造コストの面でも優れている。
その結果、本発明者らは、含有させるSi、sol.Al、Mnを適切なバランスとすることにより、低い高周波鉄損と高いBsを維持しながら生産性を損なわないことが可能であることを明らかにした。
特にSi、sol.Al、MnについてはSi+(2/3)×sol.Al+(1/5)×Mnにより脆化の程度を評価することができることを本発明者らは明らかにし、この値を4.25以下とすることで脆性を緩和し通板途中での破断リスクを低減できることが分かった。
また、本発明者らは、化学成分を上記の範囲とすることに加えて冷延通板時の鋼板温度を適正に制御することが更に通板途中での破断リスクの低減に有効であることを見出した。
なお、含有割合を示す「%」及び「ppm」は特に断りの無い限り「質量%」及び「質量ppm」を意味する。
Cは、磁気時効を起こし磁気特性が劣化してしまうことから極力低減することが望ましく、0.0040%以下とする。
C含有量は、好ましくは0.0030%以下、より好ましくは0.0025%以下である。
一方、製造上の負荷から、C含有量の下限を0.0001%、好ましくは0.0003%とする。
Siは、電磁鋼板の固有抵抗を高める元素で鉄損の低減に有効であることに加えて、安価に固有抵抗を高めることができるとの経済的な理由から3.0%を超える必要がある。
Siが3.0%以下である場合には固有抵抗ρ≧60μΩcmを得るためにその他のより高価な元素を増量する必要があることから望ましくない。
一方で、Siは添加量が多いほど鉄損の低減には有効であるが、多すぎると鋼板が脆化して製造途中での破断リスクを著しく増大することからSi含有量の上限を3.7%、好ましくは3.5%とする。
sol.Alは、電磁鋼板の固有抵抗を高める元素である。
しかしながら、sol.AlはBs低下への寄与が高く、鋼板の脆化にも影響が大きいのでsol.Al含有量の上限を1.0%、好ましくは0.9%、更に好ましくは0.8%とする。
また、sol.Al含有量が低すぎると固有抵抗が低くなってしまう他、AlN等の窒化物が微細に析出して粒成長を悪化し鉄損を悪化する懸念があることからsol.Al含有量の下限を0.3%、好ましくは0.4%、更に好ましくは0.5%とする。
Mnは、鋼板の脆性をあまり悪化させずに電磁鋼板の固有抵抗を高める元素で鉄損の低減に有効であることから0.5%以上必要である。
Mnは添加量が多いほど鉄損の低減には有効であるが、Mnはオーステナイトフォーマーであることから多すぎると製造途中の高温処理時にフェライト単相で無くなり製品板に於いて著しく磁気特性を悪化させる懸念がある。
このため、Mn含有量の上限を1.5%、好ましくは1.3%とする。
検討の結果、良好な高周波鉄損を得るには室温における固有抵抗として60μΩcm以上とすることが必要と分かった。
なお、室温における固有抵抗は一般に知られる四端子法により調べた。
室温における飽和磁束密度Bsはそれ自体がモータトルク等に寄与する重要な磁気特性である。
一方で磁化過程に直接影響することから鉄損に対しても影響があり、良好な鉄損を得るためにも室温における飽和磁束密度Bsを考慮した成分設計が重要となる。
このためにはBs低下量の大きいsol.Al含有量を減らすことが望ましく、一方で上述の高固有抵抗化の必要性と後述の脆性への影響からMn添加量を増やすことが望ましい。
Bsは振動試料型磁力計(Vibrating Sample Magnetometer : VSM)等により測定した。
ここでSi、sol.Al、Mnは鋼板に於けるそれぞれの含有量を質量%で表した時の数字を意味するものとする。
Si+(2/3)×sol.Al+(1/5)×Mnの値が小さいほど鋼板の靭性が改善し通板時の破断リスクが更に低減する。
このためSi+(2/3)×sol.Al+(1/5)×Mnの上限値は、通板の観点からは、4.1であることが好ましく、4.0とすることがより好ましい。ただし、室温における固有抵抗を60μΩcm以上とする必要から適宜Si、sol.Al、Mnの添加量のバランスを変更することが必要となる。すなわち、Si+(2/3)×sol.Al+(1/5)×Mnの値が3.5より低い場合、所望の固有抵抗が得ることが難しくなるため、Si+(2/3)×sol.Al+(1/5)×Mnの下限値は、3.5、好ましくは3.6、より好ましくは3.7とする。
更に固有抵抗を十分高める為にはMn≧0.7%とすることが更に好ましい。
Snは、仕上げ焼鈍後の集合組織を改善することでB50(5000A/mで励磁した時の磁束密度)を向上する効果があるので、Sn含有量を0.005%以上、好ましくは0.01%とする。
この効果は添加量が多いほど有効であるが、Sn含有量が0.1%以上では効果が飽和し、更に鋼板を脆化させて通板時の破断リスクを増すことから上限を0.1%、好ましくは0.9%、より好ましくは0.8%とする。
Tiは、TiN、TiC等の析出により磁気特性と、仕上焼鈍時の粒成長性を劣化してしまうので、極力低減することが望ましく、その含有量を0.0030%以下、好ましくは0.0025%以下とする。
しかし製造上の負荷から、Ti含有量の下限を0.0001%、好ましくは0.0003%とする。
Sは、MnS、MgS、TiS、CuS等の析出により磁気特性と、仕上げ焼鈍時の粒成長性を劣化してしまうので、極力低減することが望ましい。
これらの硫化物は微細に析出し易く鉄損の内ヒステリシス損失を悪化してしまう影響が大きい。
そこで、S含有量を0.0020%以下、好ましくは0.0015%以下とする。
しかし製造上の負荷から、S含有量の下限を0.0001%、好ましくは0.0003%とする。
Nは、TiN、AlN等の析出により磁気特性と、仕上焼鈍時の粒成長性を劣化させてしまうので、極力低減することが望ましい。
このため、N含有量は0.0030%以下、好ましくは0.0025%とする。
しかし製造上の負荷から、N含有量の下限を0.0001%、好ましくは0.0003%とする。
高周波鉄損の低減のためには渦電流損失を下げる固有抵抗増加が有効となるが、脆化による生産性阻害に加えてもう一つの重要な磁気特性であるBsの低下を招いてしまう課題がある。
なるべく合金成分を軽減しながら目標となる十分低い高周波鉄損を得ることが望ましく、よってこれらC、Ti、S、Nを出来るだけ低減することが好ましい。
Niは、鋼板の靭性を改善し製造途中での破断リスクを下げる効果があるので0.001%以上とする。
Niは、添加量が多いほどその効果は高いが、経済上の理由から上限を0.2%とする。
Pは、仕上げ焼鈍後の集合組織を改善することでB50を向上する効果があるので0.005%以上とする。
この効果は添加量が多いほど有効であるが、P含有量が0.05%超では鋼板を脆化させて通板時の破断リスクを増すことから上限を0.05%、好ましくは0.03%とする。
Si添加量をそれぞれ3.2%、3.5%、3.7%と変えた時のsol.Al、Mnの適正範囲を枠線で囲まれた部分として示している。
なお、線が重なっている部分については適宜ずらして図示した。
実線で示された3.2%Siの場合では0.3%≦sol.Al≦1.0%及び0.5%≦Mn≦1.5%の制限に加えて、sol.Al、Mnの少ない部分ではρ≧60μΩcmによる制限があり、sol.Al、Mnの多い部分ではBs≧1.945Tによる制限があり、これらの線分で囲まれた六角形の内側が本発明の成分範囲となる。
脆性影響を評価したSi+(2/3)×sol.Al+(1/5)×Mn≦4.25による成分の制限はSi量が高い時に有効となり、3.7%Siでは0.3%≦sol.Al及び0.5%≦Mn≦1.5%の制限とSi+(2/3)×sol.Al+(1/5)×Mn≦4.25の制限で囲まれた一点鎖線でできた台形の内側が望ましい成分範囲となる。
Bs≧1.945Tによる制限とSi+(2/3)×sol.Al+(1/5)×Mn≦4.25による制限はsol.AlとMnの関係でみると若干の係数差があるため、3.5%Siの場合にはMn≒1.0%で交点を持ち、点線で示す様な六角形の内側が3.5%Siにおける本発明の成分範囲となる。
次に本実施形態に係る鋼板の製造条件について説明する。
鋼スラブは公知の方法にて加熱され、引続き熱間圧延されて所要板厚の熱延板とされる。
この後、必要に応じて熱延板焼鈍、または自己焼鈍を行う。
この熱延板を酸洗し、冷間圧延、または中間焼鈍を含む2回の冷間圧延により所定の板厚とし、仕上げ焼鈍を行い、絶縁コーティングを施す。
この温度は50℃以上必要であり、高いほどその効果が高まるが、設備への負荷が高まることから上限を200℃とする。
また通板速度は200m/min以下とすることで破断リスクの低減に効果が現れるが、通板速度が遅すぎると加工発熱による鋼板の高温化効果が著しく低下し2パス目以降での板温度高温化による破断リスク低減効果が減少する。
また、これに加えて圧延コストが著しく増大するため、下限を60m/minとする。
通常は0.50mm以下の板厚で製造が行われるが、鉄損の低減には0.30mm以下とすることが望ましく、更に0.25mm以下とするとより良好な鉄損が得られる。
一方で過度に薄くすると鋼板の生産性やモータの加工コストの増大へ悪影響があるので、板厚を0.10mm以上とすることが好ましく、更に0.20mm以上とするとより好ましい。
以下に本発明の実施例を示す。
なお、冷間圧延の1パス目での板温を70℃、通板速度を100m/minにて行った。
この冷延板を1000℃×15秒の仕上げ焼鈍を行い、絶縁コーティングを施した。
磁気測定は最大磁束密度1.0Tで800Hzの周期にて正弦励磁した時の鉄損(W10/800)にて評価した。
破断有無は3本のコイルを通板した際に冷間圧延及び、仕上げ焼鈍にて破断が起きたかどうかで評価した。
しかしNo.1~4は固有抵抗が60μΩcm以下と低く、その結果として鉄損W10/800が38W/kgを上回っていた。
No.5~12は固有抵抗が60μΩcm以上であるが、No.6~8は鉄損W10/800が38W/kgを上回り、Bsも1.970Tを下回っており磁気特性が劣位であった。
固有抵抗に対して鉄損が劣位であった一因には、もう一つの重要な磁気特性であるBsが低いことも影響していたと考えられる。
これらの鋼板ではsol.Al、Mnのいずれか一方、又は両方が本発明の範囲外であった。
一方でNo.5、9~12は鉄損W10/800が38W/kg以下であり、さらにBsも1.970T以上と高く、鉄損とBsのバランスのとれた優れた磁気特性が得られた。
更にこの内、sol.Al<MnかつMn≧0.7%であるNo.9、12は37.7W/kg以下であり、Bsは1.980Tと特に良好な鉄損が得られている。
この冷延板を1000℃×15秒の仕上げ焼鈍を行い、絶縁コーティングを施した。
磁気測定は最大磁束密度1.0Tで800Hzの周期にて正弦励磁した時の鉄損にて評価した。
破断有無は3本のコイルを通板した際に冷間圧延及び、仕上げ焼鈍にて破断が起きたかどうかで評価した。
その他については破断無く通板できた。No.14、18、22では鉄損W10/800が37.0W/kgを上回っていることに加えてBsが本発明の基準である1.945Tを下回っていた。
これらの鋼板ではsol.Al、Mnの一方あるいは両方が本発明の範囲外であった。
No.13、16、17、20、21は本発明例であり、37.0W/kgを下回る良好な鉄損が得られ、Bsも1.945Tを超えており、鉄損とBsが共に優れた結果が得られた。
特にNo.13、16、20はsol.Al<MnかつMn≧0.7%であり、36.6W/kgを下回り更にBsが1.960T以上であり良好な鉄損が得られた。
なお、冷間圧延の1パス目での板温を70℃、通板速度を100m/minにて行った。
この冷延板を1000℃×15秒の仕上げ焼鈍を行い、絶縁コーティングを施した。
磁気測定は最大磁束密度1.0Tで800Hzの周期にて正弦励磁した時の鉄損にて評価した。
破断有無は3本のコイルを通板した際に冷間圧延及び、仕上げ焼鈍にて破断が起きたかどうかで評価した。
全て冷間圧延の1パス目で破断があった他、冷延コイルの幅方向端面に微小な亀裂が多数発生したことに加えて冷延形状も悪く、続く仕上げ焼鈍でも破断したコイルがあった。
特にNo.30、31では脆性が厳しい為に破断後に復旧することができず通板を断念した。
またNo.30は実施例2で示したNo.21と比べてSi、sol.Alは同程度ながら破断しており、破断回避には、Mnも加えたSi+(2/3)sol.Al+(1/5)Mnで評価することが重要であることがわかった。
その他については破断無く通板することができた。
No.25、26、28、29、32、33では鉄損W10/800が36.0W/kgを上回っており、Bsが本発明の基準である1.945Tを下回っていた。
No.25、28、31、32はsol.Alが本発明の範囲外であった。
一方でNo.26、29、33はSi、sol.Al、Mnの成分値だけを見ると本発明の範囲内であるが、鉄損が劣位となっていた。
Bsは単独でも重要な磁気特性であるが、鉄損にも影響しているものと考えられる。
よって本発明に規定するように良好な鉄損を得るためにも成分範囲だけでなくBsを考慮しながらの成分設計が重要であると言える。
No.23、24、27、34は本発明例であり、W10/800が36.0W/kgを下回る良好な鉄損が得られており、Bsも1.945Tを上回っていた。
なお、冷間圧延の1パス目での板温と通板速度を表4に示す通りに変更して冷間圧延を行った。
この冷延板を1000℃×15秒の仕上げ焼鈍を行い、絶縁コーティングを施した。
破断有無は3本のコイルを通板した際に冷間圧延及び、仕上げ焼鈍にて破断が起きたかどうかで評価した。
No.41は通板速度が本発明の範囲よりも速く、冷延途中に破断があった他、冷延板の形状が悪く、続く仕上げ焼鈍に於いて破断が起こった。
No.42、43は本発明の範囲よりも1パス目の通板温度が低く、圧延1パス目での破断があった他、コイルの幅方向端部に微小な亀裂が多数発生し、続く仕上げ焼鈍時に破断に至った。
No.37~40とNo.44~46については本発明の範囲内であり、破断が起こらずに通板することができた。
なお、冷間圧延の1パス目での板温を70℃、通板速度を100m/minにて行った。
この冷延板を1050℃×15秒の仕上げ焼鈍を行い、絶縁コーティングを施した。
磁気測定は最大磁束密度1.0Tで800Hzの周期にて正弦励磁した時の鉄損にて評価した。
破断有無は3本のコイルを通板した際に冷間圧延及び、仕上げ焼鈍にて破断が起きたかどうかで評価した。
Si+(2/3)sol.Al+(1/5)Mnの値が4.25を上回ったNo.50では破断回数が著しく増加した。
冷間圧延の1パス目で破断があった他、冷延コイルの幅方向端面に微小な亀裂が多数発生した事に加えて冷延形状も悪かった。
熱延板焼鈍無しの場合でもSi+(2/3)sol.Al+(1/5)Mnの値を4.25以下とすることにより破断リスクの評価が可能と言える。
熱延板焼鈍無しの場合の鉄損W10/800は、仕上げ焼鈍温度を1050℃に増加させたが、熱延板焼鈍を施したNo.23~35に比べて増加していた。
しかしこの中でもNo.49では鉄損W10/800が37.0W/kgを上回っており、Bsが本発明の基準である1.945Tを下回っていた。
このコイルではsol.Alが本発明の範囲外であった。
No.47、48は本発明例であり、W10/800が37.0W/kgを下回る良好な鉄損が得られており、Bsも1.945T以上であった。
Claims (2)
- 質量%で、
C:0.0001%以上0.0040%以下、
Si:3.0%超3.7%以下、
sol.Al:0.3%以上1.0%以下、
Mn:0.5%以上1.5%以下、
Sn:0.005%以上0.1%以下、
Ti:0.0001%以上0.0030%以下、
S:0.0001%以上0.0020%以下、
N:0.0001%以上0.003%以下、
Ni:0.001%以上0.2%以下、
P:0.005%以上0.05%以下
のみからなり、残部がFe及び不純物のみからなる無方向性電磁鋼板であって、
室温において、固有抵抗ρ≧60μΩcm、飽和磁束密度Bs≧1.945Tであり、
前記含有成分について、3.5≦Si+(2/3)×sol.Al+(1/5)×Mn≦4.25を満たす
ことを特徴とする、無方向性電磁鋼板。 - 請求項1に記載された化学成分を含むスラブを熱間圧延する熱間圧延工程と、
前記熱間圧延工程後に、そのまま熱延板焼鈍無しで、あるいは熱延板焼鈍又は自己焼鈍を施し、酸洗を行う酸洗工程と、
一回または中間焼鈍を挟む二回の冷間圧延を行う冷間圧延工程と、
前記冷間圧延工程後に仕上げ焼鈍を行い、コーティングを施す工程と、
を備え、
前記冷間圧延工程では、冷間圧延の圧延開始時の鋼板温度を50℃以上200℃以下とし、1パス目の圧延における通板速度を60m/min以上200m/min以下とする
ことを特徴とする、請求項1に記載の無方向性電磁鋼板の製造方法。
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