WO2018131712A1 - 無方向性電磁鋼板 - Google Patents
無方向性電磁鋼板 Download PDFInfo
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
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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
- 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
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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
- 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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- 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
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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- C22C2202/02—Magnetic
Definitions
- the present invention relates to a non-oriented electrical steel sheet.
- Si When adding alloy elements with the same content (mass%), except for P, which has a large adverse effect on cold rolling properties, Si tends to increase electrical resistance and reduce iron loss. It is an effective element. Therefore, in the said patent document 1, it is disclosed that Si content shall be 6 mass% or less, and in the said patent document 2, it is disclosed that Si content shall be 5.0 mass% or less, Patent Document 3 discloses that the Si content is 8.0% by mass or less. Patent Document 1 and Patent Document 2 also disclose that the Al content is 0.0050% or less and the electrical resistance is increased with Si and Mn to reduce the iron loss.
- Patent Documents 1 to 3 have not been sufficiently reduced in high-frequency iron loss such as W 10/400 .
- the reason for this is that high alloying is indispensable for reducing high-frequency iron loss.
- Patent Documents 1 to 3 do not discuss high-frequency iron loss. Since the lower limit and the distribution of appropriate addition amounts of Si, Al, and Mn are not considered, it is considered that the reduction of high-frequency iron loss as in W 10/400 was not sufficient.
- An object of the present invention is to provide a non-oriented electrical steel sheet having good cold rollability and excellent magnetic properties, particularly high-frequency iron loss.
- the non-oriented electrical steel sheet according to one aspect of the present invention has a chemical composition of mass%, C: more than 0%, 0.0050% or less, Si: 3.0% to 4.0%, Mn : 1.2% to 3.3%, P: more than 0%, less than 0.030%, S: more than 0%, 0.0050% or less, sol.
- Al more than 0%, 0.0040% or less, N: more than 0%, 0.0040% or less, one or more of La, Ce, Pr, Nd: 0.0005% to 0.0200% in total , Ca: 0.0005% to 0.0100%, Ti: 0.0005% to 0.0100%, Sn: 0% to 0.10%, Sb: 0% to 0.10%, Mg: 0% to 0.0100%, and the balance consists of Fe and impurities, Si-0.5 ⁇ Mn: 2.0% or more, and Si + 0.5 ⁇ Mn: 3.8% or more.
- the chemical composition is selected from Sn: 0.005% to 0.10%, Sb: 0.005% to 0.10% 1 You may contain seed or two kinds.
- the chemical composition may contain Mg: 0.0005% to 0.0100%.
- a non-oriented electrical steel sheet having good cold rollability and excellent magnetic properties can be obtained.
- Al is an alloying element that exhibits an effect of increasing electric resistance like Si.
- Al as well as Si, causes a decrease in cold rollability.
- the Al content increases, the hysteresis loss tends to deteriorate and the magnetic properties tend to deteriorate. Therefore, it is difficult to contain a large amount of Al as an alloy element in the non-oriented electrical steel sheet.
- the non-oriented electrical steel sheet it is preferable to reduce the Al content in order to suppress a decrease in magnetic properties due to deterioration of hysteresis loss.
- the steel material with a reduced Al content has a decreased grain growth property and a reduced magnetic property.
- the present inventors diligently studied a method capable of suppressing a decrease in grain growth property and improving both the cold rolling property and the magnetic property even when the Al content is reduced. As a result, it is effective to contain Mn, which has little adverse effect on cold rollability, together with Si, and to further contain one or more of La, Ce, Pr, Nd and Ti in combination. I found out.
- non-oriented electrical steel sheet according to one embodiment of the present invention (the non-oriented electrical steel sheet according to this embodiment) will be described in detail with reference to FIG.
- FIG. 1 is a diagram schematically showing the structure of a non-oriented electrical steel sheet according to this embodiment.
- the non-oriented electrical steel sheet 10 according to the present embodiment includes a ground iron 11 having a predetermined chemical composition, as schematically shown in FIG.
- the non-oriented electrical steel sheet according to the present embodiment may be composed only of the ground iron 11, it is preferable to further have an insulating coating 13 on the surface of the ground iron 11.
- ground iron 11 of the non-oriented electrical steel sheet 10 will be described in detail.
- the base iron 11 of the non-oriented electrical steel sheet 10 according to the present embodiment is in mass%, C: more than 0%, 0.0050% or less, Si: 3.0% to 4.0%, Mn: 1.2 % To 3.3%, P: more than 0%, less than 0.030%, S: more than 0%, 0.0050% or less, sol.
- Al more than 0%, 0.0040% or less, N: more than 0%, 0.0040% or less, one or more of La, Ce, Pr, Nd: 0.0005% to 0.0200% in total , Ca: 0.0005% to 0.0100%, Ti: 0.0005% to 0.0100%, Sn: 0% to 0.10%, Sb: 0% to 0.10%, Mg: 0% to When the value represented by “Si + 0.5 ⁇ Mn” is calculated using the Si content and the Mn content, the balance is 3.8 when 0.0100% is contained and the balance is Fe and impurities. %, And when the value represented by “Si ⁇ 0.5 ⁇ Mn” is calculated using the Si content and the Mn content, it is 2.0% or more.
- the ground iron 11 of the non-oriented electrical steel sheet 10 contains at least one selected from Sn: 0.005% to 0.10%, Sb: 0.005% to 0.10%. It is preferable to do.
- ground iron 11 of the non-oriented electrical steel sheet 10 preferably contains Mg: 0.0005% to 0.0100%.
- C is an element that is inevitably contained, and is an element that causes iron loss deterioration (increase in iron loss).
- the C content exceeds 0.0050%, iron loss deterioration occurs in the non-oriented electrical steel sheet, and good magnetic properties cannot be obtained. Therefore, in the non-oriented electrical steel sheet according to the present embodiment, the C content is set to 0.0050% or less.
- the C content is preferably 0.0040% or less, and more preferably 0.0030% or less. The smaller the C content, the better.
- C is an inevitably contained element, and the lower limit is made to exceed 0%. Further, if the C content is reduced to less than 0.0005%, the cost is significantly increased. Therefore, the C content may be 0.0005% or more.
- Si silicon
- Si is an element that increases the electrical resistance of steel, reduces eddy current loss, and improves high-frequency iron loss.
- Si has a large solid solution strengthening ability, it is an element effective for increasing the strength of non-oriented electrical steel sheets.
- the Si content needs to be 3.0% or more. Si content becomes like this. Preferably it is 3.1% or more, More preferably, it is 3.2% or more.
- the Si content exceeds 4.0%, the workability is remarkably deteriorated and it is difficult to perform cold rolling, or the steel sheet is broken during the cold rolling (that is, , Cold rollability is reduced). Therefore, the Si content is 4.0% or less.
- the Si content is preferably 3.9% or less, more preferably 3.8% or less.
- Mn manganese
- Mn manganese
- Si silicon
- the Mn content is preferably 1.3% or more, more preferably 1.4% or more, and further preferably 1.5% or more.
- the Mn content is 3.3% or less.
- the Mn content is preferably 3.2% or less, more preferably 3.1% or less, and even more preferably 3.0% or less.
- P more than 0%, less than 0.030%
- P phosphorus
- the P content is preferably 0.020% or less, and more preferably 0.010% or less. The smaller the P content, the better.
- P is an element that is inevitably contained, and the lower limit is made to exceed 0%. If the P content is less than 0.001%, a significant cost increase is caused. Therefore, the lower limit is preferably set to 0.001% or more. More preferably, it is 0.002% or more.
- S sulfur
- S is an element inevitably contained.
- S is an element that increases the iron loss by forming fine precipitates of MnS and degrades the magnetic properties of the non-oriented electrical steel sheet. Therefore, the S content needs to be 0.0050% or less.
- the S content is preferably 0.0040% or less, and more preferably 0.0035% or less. The smaller the S content, the better.
- S is an element that is unavoidably contained, and the lower limit is made to exceed 0%. An attempt to reduce the S content below 0.0001% results in a significant cost increase. Therefore, the S content is preferably 0.0001% or more.
- Al is an element that, when dissolved in steel, reduces eddy current loss and improves high-frequency iron loss by increasing the electrical resistance of the non-oriented electrical steel sheet.
- the non-oriented electrical steel sheet according to the present embodiment positively contains Mn, which is an element that increases the electrical resistance without degrading workability as compared with Al. Therefore, it is not necessary to positively contain Al.
- sol. If the Al (acid-soluble Al) content exceeds 0.0040%, fine nitrides precipitate in the steel, hinders crystal grain growth during hot-rolled sheet annealing and finish annealing, and deteriorates magnetic properties. . Therefore, sol.
- the Al content is 0.0040% or less.
- the Al content is preferably 0.0030% or less, more preferably 0.0020% or less.
- Al is an element inevitably contained, and the lower limit is made over 0%. Also, sol. Attempting to reduce the Al content below 0.0001% results in a significant cost increase. Therefore, sol.
- the Al content may be 0.0001% or more.
- N nitrogen
- nitrogen is an element inevitably contained.
- N is an element that forms fine nitrides in the steel to increase iron loss and degrade the magnetic properties of the non-oriented electrical steel sheet. Therefore, the N content needs to be 0.0040% or less.
- the N content is preferably 0.0030% or less, more preferably 0.0020% or less.
- N is an element inevitably contained, and the lower limit is made over 0%. Further, the smaller the N content, the better.
- the N content may be 0.0001% or more. More preferably, it is 0.0003% or more.
- Ti titanium
- Ti titanium
- C, N, O, etc. in the ground iron to form fine precipitates such as TiN, TiC, Ti oxide, etc., and inhibits the growth of crystal grains during annealing, thereby deteriorating magnetic properties. It is. Therefore, conventionally, in order to reduce the Ti content in the ground iron as much as possible, highly purified raw materials of Mn and Si have been used.
- one or more of La, Ce, Pr and Nd described below are compounded together with Ti to grow crystal grains during annealing.
- the Ti content is set to 0.0005% or more.
- the Ti content is set to 0.0005% or more and 0.0100% or less.
- the Ti content is Preferably, they are 0.0015% or more and 0.0080% or less, More preferably, they are 0.0025% or more and 0.0060% or less.
- La, Ce, Pr and Nd are elements that combine with S to form coarse sulfides, sulfates, or both, thereby suppressing the precipitation of fine MnS and promoting crystal grain growth during annealing. is there. Furthermore, La, Ce, Pr, and Nd are fine precipitates such as TiN, TiC, and Ti oxide generated due to Ti, sulfides or sulfides of La, Ce, Pr, and Nd, or both. It is an element which improves the magnetic properties by improving the grain growth property by composite precipitation.
- the content of one or more of La, Ce, Pr and Nd needs to be 0.0005% or more in total.
- the content of one or more of La, Ce, Pr and Nd exceeds 0.0200% in total, the coarsening effect of the fine precipitates is saturated and economical. This is not preferable because it is disadvantageous. Therefore, the content of one or more of La, Ce, Pr and Nd is 0.0200% or less in total.
- the content of one or more of La, Ce, Pr and Nd is preferably 0.0010% or more and 0.0150% or less in total, more preferably 0.0020% or more and 0.005% or less in total. 0100% or less.
- Ca 0.0005% to 0.0100%
- Ca is an element that suppresses the precipitation of fine MnS and promotes the growth of crystal grains during annealing by combining with S to form a coarse compound. Furthermore, it is an element effective in avoiding nozzle clogging caused by oxides during continuous casting by containing one or more of La, Ce, Pr, and Nd in combination.
- the Ca content needs to be 0.0005% or more. Preferably, it is 0.0010% or more.
- the Ca content exceeds 0.0100%, the effect of improving crystal grain growth and the effect of suppressing nozzle clogging are saturated, which is economically disadvantageous. Therefore, the Ca content is set to 0.0100% or less.
- the Ca content is preferably 0.0080% or less, more preferably 0.0060% or less.
- Sn (tin) and Sb (antimony) are elements useful for securing a low iron loss by segregating on the surface and suppressing oxidation and nitridation during annealing. Therefore, in the non-oriented electrical steel sheet according to the present embodiment, at least one of Sn and Sb may be contained in the ground iron in order to obtain the above effect.
- the Sn or Sb content is preferably 0.005% or more. More preferably, it is 0.010% or more.
- the Sn or Sb content is preferably 0.10% or less in each case. More preferably, each is 0.05% or less.
- Sn and Sb are optional elements and do not necessarily need to be contained, so the lower limit is 0%.
- the non-oriented electrical steel sheet according to the present embodiment may contain Mg in order to obtain the above effect.
- the Mg content is preferably 0.0005% or more.
- the Mg content is preferably 0.0100% or less.
- the Mg content is more preferably 0.0050% or less. Since Mg is an optional element and does not necessarily need to be contained, the lower limit is 0%.
- the non-oriented electrical steel sheet according to the present embodiment basically includes the above elements, with the balance being Fe and impurities.
- the non-oriented electrical steel sheet according to the present embodiment may further contain elements such as Ni (nickel), Cr (chromium), Cu (copper), and Mo (molybdenum) other than the elements described above. . Even if each of these elements is contained in an amount of 0.50% or less, the effect of the non-oriented electrical steel sheet according to the present embodiment is not impaired.
- elements such as Pb (lead), Bi (bismuth), V (vanadium), As (arsenic), and B (boron) may be further contained. Even if 0.0050% or less of each of these elements is contained, the effect of the non-oriented electrical steel sheet according to the present embodiment is not impaired.
- the non-oriented electrical steel sheet according to the present embodiment needs to be controlled so that the Si content and the Mn content satisfy a predetermined relationship after controlling the content of each element as described above. is there.
- Si + 0.5 ⁇ Mn 3.8% or more
- the alloy is increased in alloy to increase the electrical resistance of the steel sheet. It is effective.
- high-frequency iron loss can be further reduced by adding Si and Mn so that Si + 0.5 ⁇ Mn is 3.8% or more. Therefore, Si + 0.5 ⁇ Mn is set to 3.8% or more.
- Si + 0.5 ⁇ Mn is preferably 3.9% or more, more preferably 4.0% or more, and further preferably 4.4% or more.
- the substantial upper limit of Si + 0.5 ⁇ Mn is a value calculated from the upper limits of the contents of Si and Mn.
- Si-0.5 ⁇ Mn 2.0% or more
- Si-0.5 ⁇ Mn ⁇ 2.0 it is possible to suppress a decrease in magnetic characteristics. The reason for this is not clear, but by setting Si-0.5 ⁇ Mn ⁇ 2.0, a thin oxide layer of dense SiO 2 is likely to be formed on the surface of the steel sheet during finish annealing, so that the finish annealing is smooth. This is considered to be because oxidation and nitridation in the thermal process are suppressed.
- Si is a ferrite phase formation promoting element (so-called ferrite former element).
- Mn is an austenite phase formation promoting element (so-called austenite former element). Therefore, depending on the respective contents of Si and Mn, the metal structure of the non-oriented electrical steel sheet changes, and the non-oriented electrical steel sheet becomes a component system having a transformation point or a component system having no transformation point. It becomes.
- the non-oriented electrical steel sheet according to the present embodiment it is required to appropriately increase the average crystal grain size in the base iron, and the component system having no transformation point is to increase the crystal grain size. It becomes an effective means. Therefore, it is preferable that the respective contents of Si and Mn satisfy a predetermined relationship so that the component system does not have a transformation point.
- the ability to promote austenite phase formation by Mn (in other words, the effect of canceling the ability to promote ferrite phase formation) is considered to be about 0.5 times the ability to promote ferrite phase formation by Si. Therefore, the equivalent amount of the ferrite phase formation promoting ability in the present embodiment can be expressed as “Si ⁇ 0.5 ⁇ Mn” based on the Si content.
- the value of Si-0.5 ⁇ Mn is set to 2.0% or more. Preferably it is 2.1% or more.
- the upper limit of Si-0.5 ⁇ Mn is not particularly specified, but from the range of Si content and Mn content of the non-oriented electrical steel sheet according to the present embodiment, Si-0.5 ⁇ Mn. The value of Mn cannot exceed 3.4%. Therefore, the upper limit value of Si-0.5 ⁇ Mn is substantially 3.4%.
- spark discharge emission analysis method ICP emission analysis method
- combustion-infrared absorption method when measuring C and S with high accuracy
- inert gas melting-red when measuring O and N with high accuracy
- An external absorption method / thermal conductivity method or the like may be used as appropriate.
- the thickness (the thickness t in FIG. 1) of the ground iron 11 in the non-oriented electrical steel sheet 10 according to the present embodiment is set to 0.40 mm or less. Is preferred.
- the thickness t of the ground iron 11 in the non-oriented electrical steel sheet 10 is preferably 0.10 mm or more and 0.40 mm or less.
- the plate thickness t of the ground iron 11 in the non-oriented electrical steel sheet 10 is more preferably 0.15 mm or more and 0.35 mm or less.
- ground iron 11 of the non-oriented electrical steel sheet 10 according to the present embodiment has been described in detail.
- the iron loss is composed of eddy current loss and hysteresis loss.
- the insulating coating 13 provided in the non-oriented electrical steel sheet 10 according to the present embodiment is not particularly limited as long as it is used as an insulating film of the non-oriented electrical steel sheet, and a known insulating coating is used. It is possible to use.
- an insulating film for example, a composite insulating film mainly containing an inorganic substance and further containing an organic substance can be exemplified.
- the composite insulating film is mainly composed of at least one of inorganic substances such as metal chromate, metal phosphate or colloidal silica, Zr compound, Ti compound, and fine organic resin particles are dispersed. It is an insulating coating.
- metal phosphates, Zr or Ti coupling agents, or insulating films using these carbonates or ammonium salts as starting materials are available.
- metal phosphates, Zr or Ti coupling agents, or insulating films using these carbonates or ammonium salts as starting materials are available.
- metal phosphates, Zr or Ti coupling agents, or insulating films using these carbonates or ammonium salts as starting materials are available.
- insulating films using these carbonates or ammonium salts as starting materials are available.
- insulating films using these carbonates or ammonium salts as starting materials are available.
- the adhesion amount of the insulating coating 13 as described above is not particularly limited. For example, it is preferably about 0.1 g / m 2 or more and 2.0 g / m 2 or less per side, and 0.3 g per side. / M 2 or more and 1.5 g / m 2 or less is more preferable.
- the insulating coating 13 so as to have the above-described adhesion amount, it is possible to maintain excellent uniformity.
- various known measuring methods can be used.
- the adhesion amount of the insulating coating 13 is calculated from, for example, a mass difference between before and after removing the insulating coating 13 by removing only the insulating coating 13 by immersing the non-oriented electrical steel sheet 10 on which the insulating coating 13 is formed in a hot alkaline solution. Is possible.
- the non-oriented electrical steel sheet 10 according to the present embodiment has excellent magnetic properties by having the above structure.
- various magnetic properties shown by the non-oriented electrical steel sheet 10 according to the present embodiment are the Epstein method defined in JIS C2550 and the single plate magnetic property measurement method (Single Sheet Tester: SST) defined in JIS C2556. ) And can be measured.
- the non-oriented electrical steel sheet 10 according to this embodiment has been described in detail above with reference to FIG.
- FIG. 2 is a diagram illustrating an example of a flow of a method for manufacturing a non-oriented electrical steel sheet according to the present embodiment.
- a steel ingot (slab) having the above-described chemical composition is heated, and hot rolling is performed on the heated steel ingot to obtain a hot-rolled steel sheet. Is obtained (step S101).
- the heating temperature of the steel ingot at the time of hot rolling is not particularly specified, but it is preferably, for example, 1050 ° C. to 1300 ° C.
- the heating temperature of the steel ingot is more preferably 1050 ° C. to 1250 ° C.
- the thickness of the hot-rolled steel sheet after hot rolling is not particularly specified, but is preferably about 1.6 mm to 3.5 mm in consideration of the final sheet thickness of the base iron.
- the hot rolling step is preferably completed while the temperature of the steel sheet is in the range of 700 ° C to 1000 ° C.
- the end temperature of hot rolling is more preferably 750 ° C. to 950 ° C.
- hot-rolled sheet annealing (annealing for hot-rolled steel sheet) is performed (step S103).
- continuous annealing it is preferable to perform annealing on a hot-rolled steel sheet, for example, at 750 ° C. to 1200 ° C. and including soaking for 10 seconds to 10 minutes.
- box annealing it is preferable to perform annealing on a hot-rolled steel sheet, for example, at 650 ° C. to 950 ° C. and including soaking for 30 minutes to 24 hours.
- the hot-rolled plate annealing step may be omitted for cost reduction.
- step S105 pickling is performed (step S105). Thereby, the scale layer mainly composed of oxides formed on the surface of the steel sheet during the hot-rolled sheet annealing is removed.
- hot-rolled sheet annealing is box annealing, it is preferable to implement a pickling process before hot-rolled sheet annealing from a viewpoint of descaling property.
- Step S107 After the pickling step (when hot-rolled plate annealing is performed by box annealing, it may be after the hot-rolled plate annealing step), cold rolling is performed on the hot-rolled steel plate. (Step S107). In the cold rolling, it is preferable to roll the pickled plate from which the scale has been removed at a rolling reduction such that the final thickness of the base iron is 0.10 mm or more and 0.40 mm or less.
- finish annealing is performed on the cold-rolled steel sheet obtained by the cold rolling step (step S109).
- the temperature raising process of finish annealing is rapid heating. By rapidly performing the heating in the temperature raising process, a recrystallized texture that is advantageous in magnetic properties is formed in the iron core 11.
- the finish annealing is preferably performed by continuous annealing.
- the average temperature raising rate is preferably 1 ° C./second to 2000 ° C./second.
- the dew point is preferably 30 ° C. or lower.
- the average heating rate is more preferably 5 ° C./second to 1500 ° C./second, the ratio of H 2 in the atmosphere is more preferably 15% to 90% by volume, and the dew point of the atmosphere is More preferably, it is 20 degrees C or less, More preferably, it is 10 degrees C or less.
- the above average heating rate is obtained by using direct heating or indirect heating using a radiant tube, or using a known heating method such as energization heating or induction heating. It is possible to realize.
- the soaking temperature is set to 700 ° C. to 1100 ° C.
- the soaking time is set to 1 second to 300 seconds
- the atmosphere has an H 2 ratio of 10% to 100% by volume.
- the dew point of the atmosphere is preferably 20 ° C. or lower.
- the soaking temperature is more preferably 750 ° C. to 1050 ° C.
- the proportion of H 2 in the atmosphere is more preferably 15% by volume to 90% by volume
- the dew point of the atmosphere is more preferably 10%. It is 0 degreeC or less, More preferably, it is 0 degreeC or less.
- the average cooling rate is preferably 1 ° C./second to 50 ° C./second to 200 ° C. or lower.
- the average cooling rate is more preferably 5 ° C./second to 30 ° C./second.
- the non-oriented electrical steel sheet 10 according to this embodiment can be manufactured.
- step S111 After the finish annealing, an insulating coating forming process is performed as necessary (step S111).
- the step of forming the insulating film is not particularly limited, and the treatment liquid may be applied and dried by a known method using the above-described known insulating film treatment liquid.
- the surface of the base iron on which the insulating film is formed may be subjected to any pretreatment such as degreasing with alkali or pickling with hydrochloric acid, sulfuric acid or phosphoric acid before applying the treatment liquid. Moreover, the surface as it is after finish annealing without performing these pretreatments may be used.
- non-oriented electrical steel sheet according to the present invention will be specifically described with reference to examples.
- the examples shown below are merely examples of the non-oriented electrical steel sheets according to the present invention, and the non-oriented electrical steel sheets according to the present invention are not limited to the following examples.
- Example 1 A steel slab containing the composition shown in Table 1 below, the balance being Fe and impurities, was heated to 1150 ° C. and then rolled to 2.0 mm thickness by hot rolling. Subsequently, the hot-rolled steel sheet was subjected to hot-rolled sheet annealing in a continuous annealing type annealing furnace with a soaking temperature of 1000 ° C. and a soaking time of 40 seconds, followed by cold rolling to obtain a 0.25 mm thick cold steel sheet. A rolled steel sheet was used. This cold-rolled steel sheet was subjected to finish annealing with a soaking temperature of 1000 ° C. and a soaking time of 15 seconds. Thereafter, a non-oriented electrical steel sheet was manufactured by further applying and baking a solution containing an acrylic resin emulsion mainly composed of a metal phosphate to both surfaces of the steel sheet to form a composite insulating film.
- the finish annealing was performed in a mixed atmosphere of H 2 and N 2 with a dew point of ⁇ 30 ° C. and a H 2 ratio of 30% by volume in the temperature raising process and the soaking process. Moreover, the average temperature increase rate in the temperature rising process during the finish annealing was 20 ° C./second, and the average cooling rate in the cooling process was 20 ° C./second. After finish annealing, it was cooled to 200 ° C. or lower.
- test number 1 the Ti content deviated higher than the present range.
- Test No. 8 in which the total content of La, Ce, Pr and Nd deviated lower than the range of the present invention, was inferior in iron loss and magnetic flux density.
- test number 9 in which the Ca content deviated lower than the range of the present invention was abandoned because of nozzle clogging during continuous casting.
- test numbers 2, 3, 4, 5, 6, 7, and 10 in which the chemical composition of the steel sheet is within the scope of the present invention were excellent in both iron loss and magnetic flux density.
- Example 2 A steel slab containing the composition shown in Table 2 and the balance being Fe and impurities was heated to 1150 ° C. and then rolled to 2.0 mm thickness by hot rolling. Subsequently, the hot-rolled steel sheet was subjected to hot-rolled sheet annealing in a continuous annealing-type annealing furnace under a condition that the soaking temperature was 1000 ° C. and the soaking time was 40 seconds, and then cold-rolled to perform 0.25 mm thick A rolled steel sheet was obtained. Thereafter, the cold-rolled steel sheet was subjected to finish annealing under conditions where the soaking temperature was 1000 ° C. and the soaking time was 15 seconds. Thereafter, a non-oriented electrical steel sheet was manufactured by further applying and baking a solution containing an acrylic resin emulsion mainly composed of a metal phosphate to both surfaces of the steel sheet to form a composite insulating film.
- the above-described finish annealing was performed in a mixed atmosphere of H 2 and N 2 with an atmospheric dew point of ⁇ 30 ° C. and a H 2 ratio of 20% by volume in the temperature raising process and the soaking process. Moreover, the average temperature increase rate in the temperature rising process during the finish annealing was 20 ° C./second, and the average cooling rate in the cooling process was 20 ° C./second. After finish annealing, it was cooled to 200 ° C. or lower.
- Test No. 14 in which the P content deviated higher than the range of the present invention and Test No. 23 in which the Si content deviated higher than the range of the present invention were broken during cold rolling, so magnetic measurement could not be performed.
- test number 22 in which the Mn content deviated higher than the range of the present invention was inferior in iron loss and magnetic flux density. Further, in test No. 21 in which Si-0.5 ⁇ Mn was out of the range of the present invention, the iron loss and the magnetic flux density were inferior.
- Example 3 A steel slab containing the composition shown in Table 3 below, the balance being Fe and impurities, was heated to 1150 ° C. and then rolled to a thickness of 2.0 mm by hot rolling. Subsequently, the hot-rolled steel sheet was subjected to hot-rolled sheet annealing in a continuous annealing-type annealing furnace under the conditions that the soaking temperature was 1000 ° C. and the soaking time was 40 seconds, and then cold-rolled to perform 0.25 mm thick A rolled steel sheet was obtained. Thereafter, the cold-rolled steel sheet was subjected to finish annealing under conditions where the soaking temperature was 800 ° C. and the soaking time was 15 seconds.
- the non-oriented electrical steel sheet was manufactured by apply
- the above-described finish annealing was performed in a mixed atmosphere of H 2 and N 2 with an atmospheric dew point of ⁇ 30 ° C. and a H 2 ratio of 20% by volume in the temperature raising process and the soaking process. Moreover, the average temperature increase rate in the temperature rising process during finish annealing was 15 ° C./second, and the average cooling rate in the cooling process was 15 ° C./second. After finish annealing, it was cooled to 200 ° C. or lower.
- the iron loss and the magnetic flux density were inferior.
- the iron loss was inferior in the test number 30 in which Si + 0.5 ⁇ Mn was slightly lowered.
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Abstract
Description
本願は、2017年01月16日に、日本に出願された特願2017-005212号に基づき優先権を主張し、その内容をここに援用する。
また、特許文献1及び特許文献2では、Al含有量を0.0050%以下とし、SiとMnで電気抵抗を上昇させて、鉄損を低減することも開示されている。
上記知見に基づき完成された本発明の要旨は、以下の通りである。
無方向性電磁鋼板においては、先だって説明したように、高周波鉄損を低減するために、一般的には、鋼中に合金元素を含有させて鋼板の電気抵抗を上げて、渦電流損を低減させる。ここで、同一の含有量(質量%)の合金元素を含有させることを考えた場合に、Siが、電気抵抗を上昇させやすいので、鉄損の低減に有効な元素である。しかしながら、本発明者らによる検討の結果、Si含有量が4.0質量%を超える場合には、無方向性電磁鋼板の冷間圧延性が著しく低下することが明らかとなった。
本実施形態に係る無方向性電磁鋼板10の地鉄11は、質量%で、C:0%超、0.0050%以下、Si:3.0%~4.0%、Mn:1.2%~3.3%、P:0%超、0.030%未満、S:0%超、0.0050%以下、sol.Al:0%超、0.0040%以下、N:0%超、0.0040%以下、La、Ce、Pr、Ndの1種又は2種以上:合計で0.0005%~0.0200%、Ca:0.0005%~0.0100%、Ti:0.0005%~0.0100%、 Sn:0%~0.10%、Sb:0%~0.10%、Mg:0%~0.0100%を含有し、残部がFe及び不純物からなり、Si含有量、及び、Mn含有量を用いて、「Si+0.5×Mn」で表される値を計算した場合に、3.8%以上であり、Si含有量、及び、Mn含有量を用いて、「Si-0.5×Mn」で表される値を計算した場合に、2.0%以上である。
C(炭素)は、不可避的に含有される元素であるとともに、鉄損劣化(鉄損の増加)を引き起こす元素である。C含有量が0.0050%を超える場合には、無方向性電磁鋼板において鉄損劣化が生じ、良好な磁気特性を得ることができない。従って、本実施形態に係る無方向性電磁鋼板では、C含有量を、0.0050%以下とする。C含有量は、好ましくは0.0040%以下であり、より好ましくは0.0030%以下である。
C含有量は、少なければ少ないほど好ましいが、Cは不可避的に含有される元素であり、下限を0%超とする。また、C含有量を0.0005%よりも低減させようとすると、大幅なコストアップとなる。従って、C含有量は、0.0005%以上としてもよい。
Si(ケイ素)は、鋼の電気抵抗を上昇させて渦電流損を低減させ、高周波鉄損を改善する元素である。また、Siは、固溶強化能が大きいため、無方向性電磁鋼板の高強度化にも有効な元素である。無方向性電磁鋼板において、高強度化は、モータの高速回転時の変形抑制や疲労破壊抑制といった観点から必要である。このような効果を十分に発揮させるためには、Si含有量を3.0%以上とすることが必要である。Si含有量は、好ましくは3.1%以上、より好ましくは3.2%以上である。
一方、Si含有量が4.0%を超える場合には、加工性が著しく劣化し、冷間圧延を実施することが困難となったり、冷間圧延の途中で鋼板が破断したりする(すなわち、冷間圧延性が低下する)。従って、Si含有量は、4.0%以下とする。Si含有量は、好ましくは3.9%以下であり、より好ましくは3.8%以下である。
Mn(マンガン)は、電気抵抗を上昇させることで渦電流損を低減し、高周波鉄損を改善するために有効な元素である。また、Mnは、Siより固溶強化能は小さいものの、加工性を劣化させることなく、高強度化に寄与できる元素である。このような効果を十分に発揮させるために、Mn含有量を1.2%以上とすることが必要である。Mn含有量は、好ましくは1.3%以上、より好ましくは1.4%以上、更に好ましくは1.5%以上である。
一方、Mn含有量が3.3%を超える場合には、磁束密度の低下が顕著となる。従って、Mn含有量は、3.3%以下とする。Mn含有量は、好ましくは3.2%以下であり、より好ましくは3.1%以下であり、更に好ましくは3.0%以下である。
P(リン)は、Si及びMn含有量が多い高合金鋼において、著しく加工性を劣化させて冷間圧延を困難にする元素である。従って、P含有量は、0.030%未満とする。P含有量は、好ましくは0.020%以下であり、より好ましくは、0.010%以下である。
P含有量は、少なければ少ないほど良いが、Pは不可避的に含有される元素であり、下限を0%超とする。P含有量を0.001%未満にしようとすると、大幅なコストアップを招く。従って、下限を0.001%以上とすることが好ましい。より好ましくは0.002%以上である。
S(硫黄)は、不可避的に含有される元素である。また、Sは、MnSの微細析出物を形成することで鉄損を増加させ、無方向性電磁鋼板の磁気特性を劣化させる元素である。そのため、S含有量は、0.0050%以下とする必要がある。S含有量は、好ましくは0.0040%以下であり、より好ましくは、0.0035%以下である。
S含有量は、少なければ少ないほど好ましいが、Sは不可避的に含有される元素であり、下限を0%超とする。S含有量を0.0001%よりも低減させようとすると、大幅なコストアップを招く。従って、S含有量は、0.0001%以上とすることが好ましい。
Al(アルミニウム)は、鋼中に固溶されると、無方向性電磁鋼板の電気抵抗を上昇させることで渦電流損を低減し、高周波鉄損を改善する元素である。しかしながら、本実施形態に係る無方向性電磁鋼板では、Alよりも加工性を劣化させずに電気抵抗を上昇させる元素であるMnを積極的に含有させる。そのため、Alを積極的に含有させる必要はない。また、sol.Al(酸可溶Al)含有量が0.0040%を超えると、鋼中に微細な窒化物が析出して熱延板焼鈍や仕上焼鈍での結晶粒成長を阻害し、磁気特性が劣化する。従って、sol.Al含有量は、0.0040%以下とする。sol.Al含有量は、好ましくは0.0030%以下、より好ましくは0.0020%以下である。
一方、Alは不可避的に含有される元素であり、下限を0%超とする。また、sol.Al含有量を0.0001%よりも低減させようとすると、大幅なコストアップを招く。従って、sol.Al含有量は、0.0001%以上としてもよい。
N(窒素)は、不可避的に含有される元素である。また、Nは、鋼中で微細な窒化物を形成して鉄損を増加させ、無方向性電磁鋼板の磁気特性を劣化させる元素である。そのため、N含有量は、0.0040%以下とする必要がある。N含有量は、好ましくは0.0030%以下であり、より好ましくは0.0020%以下である。
一方、Nは不可避的に含有される元素であり、下限を0%超とする。また、N含有量は、少なければ少ないほど良いが、N含有量を0.0001%よりも低減させようとすると、大幅なコストアップを招く。従って、N含有量は、0.0001%以上としてもよい。より好ましくは、0.0003%以上である。
Ti(チタン)は、上記MnやSiの原材料中に不可避的に含有される。Tiは、地鉄中のC、N、Oなどと結合してTiN、TiC、Ti酸化物などの微小析出物を形成し、焼鈍中の結晶粒の成長を阻害して磁気特性を劣化させる元素である。そのため、従来、地鉄中のTi含有量を極力少なくするために、高純度化されたMnやSiの原材料を利用することが行われてきた。
しかしながら、本発明者らが検討を行った結果、以下で説明するLa、Ce、Pr及びNdの1種又は2種以上を、Tiとともに複合的に含有させることで、焼鈍中の結晶粒の成長を阻害せずに、粒成長性を保持可能であることが明らかとなった。その原因はまだ明確ではないが、生成したTiN、TiC、Ti酸化物等の微小析出物がLa、Ce、Pr及びNdの1種又は2種以上の化合物と合体することで粗大化されて、結晶粒の成長を阻害しない、より大きな析出物になったためと考えられる。すなわち、粗大な析出物が生成されることによって粒成長を阻害する微小な析出物が減少し、粒成長性の低下が抑制されると考えられる。
更に、従来、地鉄中におけるTi含有量を極力少なくするために、原材料の高純度化が図られてきたが、La、Ce、Pr及びNdの1種又は2種以上を含有させることでTiの悪影響を回避可能であるので、原材料の過度の高純度化を図らなくともよくなる。その結果、より高性能な無方向性電磁鋼板をより低コストで製造することが可能となる。
La、Ce、Pr、Ndは、Sと結合して粗大な硫化物、硫酸化物又はこれらの両方を形成することで微細なMnSの析出を抑制し、焼鈍時の結晶粒成長を促進する元素である。更に、La、Ce、Pr、Ndは、Tiに起因して生成されるTiN、TiC、Ti酸化物等の微小析出物を、La、Ce、Pr、Ndの硫化物もしくは硫酸化物又はこれらの両方に複合析出させて結晶粒成長性を改善し、磁気特性を向上させる元素である。このような効果を得るために、La、Ce、Pr及びNdの1種又は2種以上の含有量は、合計で0.0005%以上であることが必要である。一方、La、Ce、Pr及びNdの1種又は2種以上の含有量が合計で0.0200%を超える場合には、上記のような微小析出物の粗大化効果が飽和する上、経済的に不利となるので好ましくない。従って、La、Ce、Pr及びNdの1種又は2種以上の含有量は、合計で0.0200%以下とする。La、Ce、Pr及びNdの1種又は2種以上の含有量は、好ましくは合計で0.0010%以上、0.0150%以下であり、より好ましくは合計で0.0020%以上、0.0100%以下である。
Ca(カルシウム)は、Sと結合して粗大な化合物を形成することで微細なMnSの析出を抑制し、焼鈍時の結晶粒成長を促進する元素である。更に、La、Ce、Pr、Ndの1種又は2種以上との複合含有により、連続鋳造時の酸化物起因のノズル閉塞を回避するのに有効な元素である。このような効果を得るために、Ca含有量は、0.0005%以上であることが必要である。好ましくは、0.0010%以上である。
一方、Ca含有量が0.0100%を超える場合には、上記のような結晶粒成長性の改善効果やノズル閉塞の抑制効果が飽和し、経済的に不利となる。従って、Ca含有量は、0.0100%以下とする。Ca含有量は、好ましくは0.0080%以下であり、より好ましくは0.0060%以下である。
[Sb:0%~0.10%]
Sn(スズ)及びSb(アンチモン)は、表面に偏析し焼鈍中の酸化や窒化を抑制することで、低い鉄損を確保するのに有用な元素である。従って、本実施形態に係る無方向性電磁鋼板では、上記効果を得るために、Sn又はSbの少なくとも何れか一方を、地鉄中に含有させてもよい。上記効果を十分に発揮させるためには、Sn又はSbの含有量を、それぞれ0.005%以上とすることが好ましい。より好ましくは、0.010%以上である。
一方、Sn又はSbの含有量がそれぞれ0.10%を超える場合には、地鉄の延性が低下して冷間圧延が困難となる可能性がある。従って、Sn又はSbの含有量は、含有させる場合でも、それぞれ0.10%以下とすることが好ましい。より好ましくは、それぞれ0.05%以下である。
Sn、Sbは任意元素であり、必ずしも含有させる必要がないので、下限は0%である。
Mg(マクネシウム)は、Sと結合して粗大な化合物を形成する。MgとSとの粗大な化合物が形成されると、微細なMnSの析出が抑制され、焼鈍時の結晶粒成長が促進されるので、低い鉄損を確保するのに有利である。従って、本実施形態に係る無方向性電磁鋼板では、上記効果を得るために、Mgを含有させてもよい。効果を十分に発揮させるためには、Mg含有量を、0.0005%以上とすることが好ましい。一方、Mg含有量が0.0100%を超える場合には、結晶粒成長性の改善効果が飽和し、経済的に不利となるので好ましくない。従って、Mg含有量は、0.0100%以下とすることが好ましい。Mgを地鉄中に含有させる場合に、Mg含有量は、より好ましくは、0.0050%以下である。
Mgは任意元素であり、必ずしも含有させる必要がないので、下限は0%である。
鉄損、特に本実施形態に係る無方向性電磁鋼板が目的とするW10/400のような高周波鉄損を低減する(改善する)場合には、高合金化して鋼板の電気抵抗を増加させることが有効である。具体的には、Si+0.5×Mnが3.8%以上となるようにSi、Mnを含有させることで、高周波鉄損をさらに低減することができる。そのため、Si+0.5×Mnを3.8%以上とする。Si+0.5×Mnは、好ましくは3.9%以上、より好ましくは4.0%以上、更に好ましくは4.4%以上である。
Si+0.5×Mnの実質的な上限は、Si及びMnの含有量の上限から計算される値である。
本実施形態に係る無方向性電磁鋼板では、含有されたLa、Ce、Pr、Nd、Caが、Sを硫化物や酸硫化物として固定する。この場合、鋼板の表面の酸化や窒化が促進され、磁気特性が低下するおそれがある。
しかしながら、Si-0.5×Mn≧2.0とすることにより、磁気特性の低下を抑制することができる。その理由は明確ではないが、Si-0.5×Mn≧2.0とすることにより、仕上げ焼鈍の加熱時に、緻密なSiO2の薄い酸化層が鋼板表面に生じやすくなり、仕上げ焼鈍の均熱過程での酸化や窒化が抑制されるためであると考えられる。
一方、Si-0.5×Mnの上限値は、特に規定するものではないが、本実施形態に係る無方向性電磁鋼板のSi含有量及びMn含有量の範囲から、Si-0.5×Mnの値は、3.4%を超えることはあり得ない。従って、Si-0.5×Mnの上限値は、実質的には、3.4%となる。
本実施形態に係る無方向性電磁鋼板10における地鉄11の板厚(図1における厚みt)は、渦電流損を低減させて高周波鉄損を低減するために、0.40mm以下とすることが好ましい。一方、地鉄11の板厚tが0.10mm未満である場合には、板厚が薄いために焼鈍ラインの通板が困難となる可能性がある。従って、無方向性電磁鋼板10における地鉄11の板厚tは、0.10mm以上、0.40mm以下とすることが好ましい。無方向性電磁鋼板10における地鉄11の板厚tは、より好ましくは、0.15mm以上、0.35mm以下である。
続いて、本実施形態に係る無方向性電磁鋼板10が有していることが好ましい絶縁被膜13について、簡単に説明する。
本実施形態に係る無方向性電磁鋼板10は、上記のような構造を有することで、優れた磁気特性を示す。ここで、本実施形態に係る無方向性電磁鋼板10の示す各種の磁気特性は、JIS C2550に規定されたエプスタイン法や、JIS C2556に規定された単板磁気特性測定法(Single Sheet Tester:SST)に則して、測定することが可能である。
続いて、図2を参照しながら、以上説明したような本実施形態に係る無方向性電磁鋼板10の好ましい製造方法について、簡単に説明する。
図2は、本実施形態に係る無方向性電磁鋼板の製造方法の流れの一例を示した図である。
本実施形態に係る無方向性電磁鋼板の製造方法では、まず、上記の化学組成を有する鋼塊(スラブ)を加熱し、加熱された鋼塊に対して熱間圧延を行って、熱延鋼板を得る(ステップS101)。熱間圧延に供する際の鋼塊の加熱温度については、特に規定するものではないが、例えば、1050℃~1300℃とすることが好ましい。鋼塊の加熱温度は、より好ましくは、1050℃~1250℃である。
また、熱間圧延後の熱延鋼板の板厚についても、特に規定するものではないが、地鉄の最終板厚を考慮して、例えば、1.6mm~3.5mm程度とすることが好ましい。熱間圧延工程は、鋼板の温度が700℃~1000℃の範囲にあるうちに終了することが好ましい。熱間圧延の終了温度は、より好ましくは、750℃~950℃である。
上記熱間圧延の後には、熱延板焼鈍(熱延鋼板に対する焼鈍)が実施される(ステップS103)。連続焼鈍の場合には、熱延鋼板に対して、例えば、750℃~1200℃で、10秒~10分の均熱を含む焼鈍を実施することが好ましい。また、箱焼鈍の場合、熱延鋼板に対して、例えば、650℃~950℃で、30分~24時間の均熱を含む焼鈍を実施することが好ましい。
熱延板焼鈍工程を実施した場合と比較して磁気特性はやや劣ることになるが、コスト削減のために、熱延板焼鈍工程を省略してもよい。
上記熱延板焼鈍工程の後には、酸洗が実施される(ステップS105)。これにより、熱延板焼鈍の際に鋼板の表面に形成された、酸化物を主体とするスケール層が除去される。熱延板焼鈍が箱焼鈍である場合、脱スケール性の観点から、酸洗工程は、熱延板焼鈍前に実施することが好ましい。
上記酸洗工程の後(熱延板焼鈍が箱焼鈍で実施される場合は、熱延板焼鈍工程の後となる場合もある。)には、熱延鋼板に対し、冷間圧延が実施される(ステップS107)。冷間圧延では、地鉄の最終板厚が0.10mm以上0.40mm以下となるような圧下率で、スケールの除去された酸洗板を圧延することが好ましい。
上記冷間圧延工程の後には、冷間圧延工程によって得られた冷延鋼板に対し、仕上焼鈍が実施される(ステップS109)。本実施形態に係る無方向性電磁鋼板の製造方法では、仕上焼鈍の昇温過程を、急速加熱とすることが好ましい。昇温過程の加熱を急速に行うことにより、地鉄11において、磁気特性に有利な再結晶集合組織が形成される。仕上焼鈍の昇温過程を急速加熱とする場合、仕上焼鈍は、連続焼鈍で実施することが好ましい。
上記仕上焼鈍の後には、必要に応じて、絶縁被膜の形成工程が実施される(ステップS111)。絶縁被膜の形成工程については、特に限定されるものではなく、上記のような公知の絶縁被膜処理液を用いて、公知の方法により処理液の塗布及び乾燥を行えばよい。
以下の表1に示す組成を含有し、残部がFe及び不純物からなる鋼スラブを、1150℃に加熱した後、熱間圧延にて2.0mm厚に圧延した。続いて、熱延鋼板を連続焼鈍式の焼鈍炉で、均熱温度が1000℃で均熱時間が40秒の熱延板焼鈍を行った後、冷間圧延を行って0.25mm厚の冷延鋼板とした。この冷延鋼板に対し、均熱温度が1000℃で均熱時間が15秒の仕上焼鈍を行った。その後、更にリン酸金属塩を主体とし、アクリル樹脂のエマルジョンを含む溶液を鋼板の両面に塗布及び焼き付けし、複合絶縁被膜を形成することで無方向性電磁鋼板を製造した。
表2に示す組成を含有し、残部がFe及び不純物からなる鋼スラブを、1150℃に加熱した後、熱間圧延にて2.0mm厚に圧延した。続いて、熱延鋼板を均熱温度が1000℃で均熱時間が40秒となる条件で連続焼鈍式の焼鈍炉で熱延板焼鈍した後、冷間圧延を行って0.25mm厚の冷延鋼板を得た。その後、この冷延鋼板に対し、均熱温度が1000℃で均熱時間が15秒となる条件で仕上焼鈍を行った。その後、更にリン酸金属塩を主体とし、アクリル樹脂のエマルジョンを含む溶液を鋼板の両面に塗布及び焼き付けし、複合絶縁被膜を形成することで無方向性電磁鋼板を製造した。
以下の表3に示す組成を含有し、残部がFe及び不純物からなる鋼スラブを、1150℃に加熱した後、熱間圧延にて2.0mm厚に圧延した。続いて、熱延鋼板を均熱温度が1000℃、均熱時間が40秒となる条件で連続焼鈍式の焼鈍炉で熱延板焼鈍した後、冷間圧延を行って0.25mm厚の冷延鋼板を得た。その後、この冷延鋼板に、均熱温度が800℃、均熱時間が15秒となる条件で仕上焼鈍を行った。その後、リン酸金属塩を主体とし、アクリル樹脂のエマルジョンを含む溶液を鋼板の両面に塗布及び焼き付けし、複合絶縁被膜を形成することで無方向性電磁鋼板を製造した。続いて、上記鋼板に対し、750℃×2hrの歪取焼鈍を施した。
11 地鉄
13 絶縁被膜
Claims (3)
- 化学組成が、質量%で、
C:0%超、0.0050%以下、
Si:3.0%~4.0%、
Mn:1.2%~3.3%、
P:0%超、0.030%未満、
S:0%超、0.0050%以下、
sol.Al:0%超、0.0040%以下、
N:0%超、0.0040%以下、
La、Ce、Pr、Ndの1種又は2種以上:合計で0.0005%~0.0200%、
Ca:0.0005%~0.0100%、
Ti:0.0005%~0.0100%、
Sn:0%~0.10%、
Sb:0%~0.10%、
Mg:0%~0.0100%、
を含有し、残部がFe及び不純物からなり、
Si-0.5×Mn:2.0%以上であり、
Si+0.5×Mn:3.8%以上である
ことを特徴とする無方向性電磁鋼板。 - 前記化学組成が、
Sn:0.005%~0.10%、
Sb:0.005%~0.10%、
から選ばれる1種または2種を含有する
ことを特徴とする請求項1に記載の無方向性電磁鋼板。 - 前記化学組成が、
Mg:0.0005%~0.0100%
を含有する
ことを特徴とする請求項1または2に記載の無方向性電磁鋼板。
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EP3569728A4 (en) | 2020-06-03 |
BR112019009604B1 (pt) | 2022-08-02 |
KR102286319B1 (ko) | 2021-08-06 |
JPWO2018131712A1 (ja) | 2019-11-07 |
EP3569728B1 (en) | 2021-09-29 |
PL3569728T3 (pl) | 2022-02-07 |
JP6870687B2 (ja) | 2021-05-12 |
EP3569728A1 (en) | 2019-11-20 |
TWI654317B (zh) | 2019-03-21 |
US11053574B2 (en) | 2021-07-06 |
BR112019009604A2 (pt) | 2019-08-13 |
US20190316239A1 (en) | 2019-10-17 |
TW201829803A (zh) | 2018-08-16 |
CN110023525B (zh) | 2021-04-30 |
KR20190093619A (ko) | 2019-08-09 |
CN110023525A (zh) | 2019-07-16 |
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