Patent Application
20230139246
The present disclosure relates to a non-oriented electrical steel sheet and a method of manufacturing the same.
In recent years, global environmental issues have attracted attention, and demands for energy saving efforts have further increased. Above all, there is a strong demand for higher efficiency of electric equipment. For this reason, there is a further increasing demand for enhancement in magnetic properties in a non-oriented electrical steel sheet widely used as an iron core material for a motor, a generator, or the like. This tendency is remarkable in drive motors for electric vehicles and hybrid vehicles and compressor motors for air conditioners.
A motor core of various motors as described above includes a stator as a stationary part and a rotor as a rotating part. The properties required for the stator and the rotor included in the motor core are different from each other. The stator is required to have excellent magnetic properties (low iron loss and high magnetic flux density), particularly low iron loss, whereas the rotor is required to have excellent mechanical properties (high strength).
Since properties required for the stator and the rotor are different, desired properties can be achieved by producing a non-oriented electrical steel sheet for the stator and another non-oriented electrical steel sheet for the rotor. However, preparing two types of non-oriented electrical steel sheets adversely causes a decrease in yield. Therefore, a non-oriented electrical steel sheet having excellent strength and also having excellent magnetic properties has been conventionally studied in order to achieve low iron loss while achieving high strength required for the rotor.
For example, in Patent Documents 1 to 4, attempts have been made to achieve excellent magnetic properties and high strength.
Patent Document 1: Japanese Patent Application Laid-Open (JP-A) No. 2004-300535
Patent Document 2: JP-ANo. 2007-186791
Patent Document 3: JP-ANo. 2012-140676
Patent Document 4: JP-ANo. 2010-90474
However, reduction in iron loss for a stator material has been insufficient in the techniques disclosed in Patent Documents 1 to 4 for achieving energy saving properties that has been recently required for a motor of an electric vehicle or a hybrid vehicle.
The present disclosure has been made to solve such a problem, and an object of the present disclosure is to stably obtain a non-oriented electrical steel sheet having high strength and excellent magnetic properties at low cost.
The gist of the present disclosure is a non-oriented electrical steel sheet and a method of manufacturing the same described below.
According to the present disclosure, a non-oriented electrical steel sheet having high strength and excellent magnetic properties can be obtained.
Intensive studies have been made by inventors of the present disclosure in order to solve the above problem, whereby the following findings have been obtained.
In a case in which higher strength of a steel is desired to be attained, a method of incorporating a large amount of an alloy element such as Cu, Ni, Ti, or V is often performed. However, in a case in which a large amount of the alloy element such as Cu, Ni, Ti, or V is incorporated, not only the cost is increased but also the magnetic properties are deteriorated.
Utilizing Si is effective in order to attain the higher strength without incorporating the special alloy element such as Cu, Ni, Ti, or V as much as possible. In addition, it is necessary to improve high-frequency iron loss in order to enhance the magnetic properties of a non-oriented electrical steel sheet. The iron loss mainly includes hysteresis loss and eddy current loss. Si also has an effect of increasing the electrical resistance of a steel to reduce the eddy current loss.
However, an increase in the Si content deteriorates the toughness and leads to embrittlement cracking during cold rolling, thereby causing a problem that manufacturing becomes difficult. As a countermeasure for this problem, it is conceivable to strengthen the grain boundary by segregating C at the crystal grain boundary in order to suppress embrittlement cracking during cold rolling. However, C precipitates as a carbide in a usage environment, which hinders domain wall displacement and results in increasing hysteresis loss.
Therefore, although C is incorporated to some extent at the time of cold rolling, it is desired to perform decarburization thereafter to reduce the C content in a final product. This makes it possible to achieve both enhancement in cold workability and reduction in the iron loss.
In addition, the structure of a base metal can be fine-grained by adding a small amount of Al. In general, micronization of the structure leads to an increase in the iron loss and may thereby deteriorate the magnetic properties. However, appropriate amount of Al is incorporated, which thereby makes it possible to adjust the crystal grain size and improve the strength while minimizing increase in the iron loss.
The content of Mn, which has a relatively low contribution to the higher strength and effect of increasing electric resistance, is reduced.
The present disclosure has been made based on the above findings. Hereinafter, each requirement of the present disclosure will be described in detail.
In the present disclosure, a numerical range represented by “to” means a range including numerical values described before and after “to” as a lower limit value and an upper limit value.
A numerical range in a case in which “greater than” or “less than” is attached to a numerical value described before and after “to” means a range not including these numerical values as a lower limit value or an upper limit value.
The term “step” includes not only an independent step, but also a step as long as the intended purpose of the step is achieved even if the step cannot be clearly distinguished from other steps.
In numerical ranges described in stages in the present disclosure, the upper limit value described in one numerical range may be replaced with the upper limit value of the numerical range described in another stage, or the lower limit value described in one numerical range may be replaced with the lower limit value of the numerical range described in another stage.
In a numerical range described in the present disclosure, the upper limit value or the lower limit value of the numerical range may be replaced with a value shown in Examples.
In the present disclosure, a combination of preferred embodiments is a more preferred embodiment.
A non-oriented electrical steel sheet according to the present disclosure has high strength and excellent magnetic properties and is thereby suitable for both a stator and a rotor. The non-oriented electrical steel sheet according to the present disclosure preferably includes an insulation coating on a surface of a base metal described below.
The reasons for limiting elements are as follows. Note that, in the following description, “%” for a content means “% by mass”.
C (carbon) is an element that causes iron loss deterioration. If the C content exceeds 0.0040%, iron loss deterioration occurs in the non-oriented electrical steel sheet, and favorable magnetic properties cannot be obtained. However, C is an element that is effective for higher strength of the steel sheet. Therefore, the C content is set to 0.0010 to 0.0040%. The C content is preferably 0.0012% or more, and more preferably 0.0015% or more. The C content is preferably 0.0035% or less, and more preferably 0.0030% or less.
Si (silicon) is an element that increases the electrical resistance of a steel to reduce the eddy current loss and improve the high-frequency iron loss. Si is an element that is also effective for higher strength of the steel sheet because Si has a high solid-solution strengthening ability. However, if the Si content is excessive, workability is significantly deteriorated, and cold rolling is hardly carried out. Therefore, the Si content is set to 4.0 to 5.0%. The Si content is preferably 4.1% or more, and more preferably 4.2% or more. The Si content is also preferably 4.9% or less, and more preferably 4.8% or less.
Although Mn (manganese) has an effect of increasing the electrical resistance of a steel to reduce the eddy current loss and improve the high-frequency iron loss, the effect is less than that of Si and Al. On the other hand, the magnetic flux density decreases as the Mn content increases. Therefore, the Mn content is set to 0.20% or less. The Mn content is preferably 0.19% or less, and more preferably 0.18% or less. However, Mn has an effect of suppressing embrittlement during hot rolling due to S that is inevitably contained in a steel. Therefore, the Mn content is preferably 0.05% or more, and more preferably 0.07% or more.
Al (aluminum) is an element that binds to N to form AlN and is effective for stable micronization of crystal grains. The moderate Al content has an effect of fine-graining the structure and thereby increasing the strength of a steel. If the Al content is 0.050% or more, the effect of micronization of crystal grains is decreased. Therefore, the Al content is set to 0.010% or more and less than 0.050%. The Al content is preferably 0.012% or more, and more preferably 0.015% or more. The Al content is also preferably 0.045% or less, more preferably 0.040% or less, and still more preferably 0.035% or less.
P (phosphorus) is contained in a steel as an impurity. If the content of P is excessive, the toughness of the steel sheet is significantly lowered. Therefore, the P content is set to 0.030% or less. The P content is preferably 0.025% or less, and more preferably 0.020% or less. Extreme reduction in the P content may lead to an increase in manufacturing cost, and therefore, the P content may be 0.005% or more, 0.008% or more, or 0.010% or more.
S (sulfur) is an element that forms fine precipitates of MnS, thereby increasing the iron loss and deteriorating the magnetic properties of the steel sheet. Therefore, the S content is set to 0.0030% or less. The S content is preferably 0.0025% or less, and more preferably 0.0020% or less. Extreme reduction in the S content may lead to an increase in manufacturing cost, and therefore, the S content may be 0.0001% or more, 0.0003% or more, or 0.0005% or more.
N (nitrogen) is an element that binds to Al to form AlN and is effective for stable micronization of crystal grains. However, if a large amount of AlN is contained, excessive AlN is formed, which leads to deterioration of the iron loss. Therefore, the N content is set to 0.0005 to 0.0030%. The N content is preferably 0.007% or more, and more preferably 0.0010% or more. The N content is also preferably 0.0027% or less, and more preferably 0.0025% or less.
O (oxygen) is an element that inevitably mixed and is an element that forms an oxide, thereby increasing the iron loss and deteriorating the magnetic properties of the steel sheet. Therefore, it is preferable that the O content is low. However, it is difficult to reduce the content of O because O forms an oxide layer on a surface layer during decarburization. In this regard, excessive oxidation of a surface layer of the base metal also causes deterioration of the magnetic flux density. Therefore, the average content of O in the total thickness of the base metal is set to 0.0100 to 0.0400%. The O content is preferably 0.0350% or less, and more preferably 0.0300% or less.
Although formation of an oxide layer on a surface layer of the base metal is inevitable as mentioned above, it is desirable to reduce the O content in a region excluding the surface layer as much as possible. Specifically, it is necessary to set the O content to less than 0.0050% in a region excluding a portion from the surface of the base metal to a position of 10 µm in a depth direction of the base metal. Oxygen in the central portion of the base metal at a depth of 10 µm or more from the surface of the base metal is considered to be oxygen contained in an oxide formed during solidification in a steelmaking process. That is, in a case in which the surface layer portion is oxidized by controlling the dew point in a finish-annealing step, the internal oxidation occurs within about several µm depth from the surface of the base metal, and the O content at a depth of 10 µm or more from the surface of the base metal corresponds to that during steelmaking. If this amount of oxygen is 0.0050% or more, a large amount of an oxide of the base metal is formed, and the hysteresis loss increases. Therefore, the O content in a region excluding a portion from the surface of the base metal to a position of 10 µm in the depth direction of the base metal is less than 0.0050%. The O content in a region excluding a portion from the surface of the base metal to a position of 10 µm in the depth direction of the base metal is preferably 0.0045% or less, and more preferably 0.0040% or less.
The O content in a region excluding a portion from the surface of the base metal to a position of 10 µm in the depth direction of the base metal can be measured by an inert gas fusion-non-dispersive infrared absorption method after removing regions that are from the front surface of the base metal to a position of 10 µm depth and from the back surface of the base metal to a position of 10 µm depth of the base metal by chemical polishing using a mixed aqueous solution of hydrofluoric acid and hydrogen peroxide water.
Ca (calcium) is added as a desulfurization agent at a steelmaking stage. Ca remaining in the base metal binds to S to form a Ca-based sulfide. This sulfide is precipitated coarsely, thereby having little adverse effect on crystal grain growth and having an effect of coarsening the crystal grains. However, it is necessary to appropriately micronize the crystal grain size for the higher strength in the present disclosure, and adding a large amount of Ca is therefore unnecessary and also increases the cost. Therefore, the Ca content is less than 0.0010%. The Ca content is preferably 0.0008% or less, and more preferably 0.0005% or less. Extreme reduction in the Ca content may lead to an increase in manufacturing cost, and therefore, the Ca content may be 0.0001% or more.
Ti (titanium) is an element that is inevitably mixed, and may bind to carbon or nitrogen to form precipitates (carbides or nitrides). The precipitates themselves deteriorate the magnetic properties in a case in which the carbides or nitrides are formed. Therefore, the Ti content is set to less than 0.0050%. The Ti content is preferably 0.0040% or less, more preferably 0.0030% or less, and still more preferably 0.0020% or less. Extreme reduction in the Ti content may lead to an increase in manufacturing cost, and therefore, the Ti content may be 0.0005% or more.
Nb (niobium) is an element that contributes to the higher strength by binding to carbon or nitrogen to form precipitates (carbides), but these precipitates themselves deteriorate the magnetic properties. Therefore, the Nb content is set to less than 0.0050%. The Nb content is preferably 0.0040% or less, more preferably 0.0030% or less, and still more preferably 0.0020% or less. The Nb content is preferably as low as possible, and is preferably equal to or less than the measurement limit.
Zr (zirconium) is an element that contributes to the higher strength by binding to carbon or nitrogen to form precipitates (carbides, nitrides), but these precipitates themselves deteriorate the magnetic properties. Therefore, the Zr content is set to less than 0.0050%. The Zr content is preferably 0.0040% or less, more preferably 0.0030% or less, and still more preferably 0.0020% or less. The Zr content is preferably as low as possible, and is preferably equal to or less than the measurement limit.
V (vanadium) is an element that contributes to the higher strength by binding to carbon or nitrogen to form precipitates (carbides, nitrides), but these precipitates themselves deteriorate the magnetic properties. Therefore, the V content is set to less than 0.0050%. The V content is preferably 0.0040% or less, more preferably 0.0030% or less, and still more preferably 0.0020% or less. The V content is preferably as low as possible, and is preferably equal to or less than the measurement limit.
Cu (copper) is an element that is inevitably mixed. The intentional addition of Cu increases manufacturing cost of the steel sheet. Therefore, Cu is not required to be voluntarily added and may be an impurity level in the present disclosure. The Cu content is set to less than 0.20%, which is the maximum value that can be inevitably mixed in a manufacturing process. The Cu content is preferably 0.15% or less, and more preferably 0.10% or less. The lower limit value of the Cu content is not particularly limited, but extreme reduction in the Cu content may lead to an increase in manufacturing cost. Therefore, the Cu content may be 0.001% or more, 0.003% or more, or 0.005% or more.
Ni (nickel) is an element that is inevitably mixed. However, Ni is also an element that enhances the strength of the steel sheet, and therefore, Ni may be intentionally added. In this regard, since Ni is expensive, the content of Ni is set to less than 0.50% in a case in which Ni is intentionally added. The Ni content is preferably 0.40% or less, and more preferably 0.30% or less. The lower limit value of the Ni content is not particularly limited, but extreme reduction in the Ni content may lead to an increase in manufacturing cost. Therefore, the Ni content may be 0.001% or more, 0.003% or more, or 0.005% or more.
Sn (tin) and Sb (antimony) are elements that are useful for securing low iron loss by segregating on the surface and suppressing oxidation and nitriding during annealing. Sn and Sb also have an effect of segregating at the crystal grain boundary to improve the texture and to increase the magnetic flux density. Therefore, at least one of Sn or Sb may be incorporated, if necessary. However, if the content of Sn or Sb element is excessive, the toughness of a steel may be reduced, whereby cold rolling may be difficult. Therefore, the contents of Sn and Sb are each 0.05% or less. The contents of Sn and Sb are each preferably 0.03% or less. The content of at least one of Sn or Sb is preferably 0.005% or more, and more preferably 0.01% or more, in a case in which the above effect is desired to be obtained.
In a chemical composition of the base metal of the non-oriented electrical steel sheet of the present disclosure, a balance is Fe and impurities. In this regard, the term “impurities” means components that are mixed due to raw materials such as ore and scrap, and various factors of a manufacturing process when a steel is industrially manufactured, and that are acceptable within a range not adversely affecting the effect of the present disclosure.
The contents of Cr and Mo as impurity elements are not particularly limited. Even if these elements are contained at 0.5% or less, the effect of the present disclosure is not particularly affected in the non-oriented electrical steel sheet according to the present disclosure. Even if Mg is contained in a range of 0.002% or less, the effect of the present disclosure is not particularly affected. Even if a rare earth element (REM) is contained in a range of 0.004% or less, the effect of the present disclosure is not particularly affected. REM is a generic term for 17 elements in total, which are Sc, Y, and lanthanoids. The content of REM refers to the total content of one or more elements of REM.
In addition to the above elements, elements such as Pb, Bi, As, B, and Se may be contained, and the effect of the present disclosure is not impaired as long as the content of each element is in a range of 0.0050% or less.
In the present disclosure, the average crystal grain size of the base metal is not particularly limited. However, crystals in a steel are desirably fine grains from the viewpoint of the higher strength. Crystal grains are preferably coarsened in order to reduce the hysteresis loss, and the crystal grains are preferably micronized in order to reduce the eddy current loss.
Deterioration of the hysteresis loss can be minimized, and the magnetic characteristics can be improved, by setting the average crystal grain size of the base metal to 10 µm or more. The effect of improving the strength of a steel can be obtained by setting the average crystal grain size to 80 µm or less. Therefore, the average crystal grain size of the base metal is preferably set to 10 to 80 µm. The average crystal grain size is preferably 12 µm or more, and more preferably 14 µm or more. The average crystal grain size is also preferably 70 µm or less, and more preferably 60 µm or less.
In the present disclosure, an average crystal grain size of the base metal is determined according to JIS G 0551 (2013) “Steels-Micrographic determination of the apparent grain size”. A crystal grain size in an entire sheet thickness of a base metal is measured at arbitrary three points in a rolling direction by a cutting method, and an average value is taken as the average crystal grain size of the base metal.
In the non-oriented electrical steel sheet according to the present disclosure, excellent magnetic properties mean that the iron loss W10/400 is low and the magnetic flux density B50 is high. In this regard, the magnetic properties are measured by an Epstein method defined in JIS C 2550-1 (2011). In a case in which measurement by an Epstein method is difficult, for example, a test piece is too small, measurement may be performed by correcting a measurement value to be equivalent to a measurement value of an Epstein method according to a single sheet magnetic property measurement method (Single Sheet Tester: SST) defined in JIS C 2556 (2015). In the present disclosure, a low iron loss W10/400 means that the iron loss is 35.0 W/kg or less for a sheet thickness of 0.26 mm or more, 25.0 W/kg or less for a sheet thickness of 0.21 to 0.25 mm, and 20.0 W/kg or less for a sheet thickness of 0.20 mm or less. A high magnetic flux density B50 means that the magnetic flux is 1.60 T or more regardless of the sheet thickness.
In the non-oriented electrical steel sheet according to the present disclosure, having high strength means that the tensile strength is preferably 650 MPa or more. The tensile strength is more preferably 660 MPa or more, and still more preferably 700 MPa or more. In this regard, the tensile strength is measured by performing a tensile test in accordance with JIS Z 2241 (2011).
In the non-oriented electrical steel sheet according to the present disclosure, it is preferable that an insulation coating is formed on the surface of the base metal as mentioned above. The non-oriented electrical steel sheets are layered and used after a core blank is punched out, and therefore, providing an insulation coating on the surface of the base metal can reduce the eddy current between the sheets and makes it possible to reduce the eddy current loss as a core.
The type of the insulation coating is not particularly limited, and a known insulation coating used as an insulation coating for a non-oriented electrical steel sheet can be used. Examples of such an insulation coating include a composite insulation coating mainly containing an inorganic substance and further containing an organic substance. In this regard, the composite insulation coating is an insulation coating that has fine organic resin particles dispersed therein and that mainly contains at least any one of inorganic substances, for example, a chromate metal salt, a phosphate metal salt, and colloidal silica, a Zr compound, and a Ti compound. In particular, an insulation coating employing a metal phosphate salt, a coupling agent with Zr or Ti, or a carbonate or ammonium salt thereof as a starting material is preferably used from the viewpoint of reducing the environmental load during manufacturing, which has been increasingly required in recent years.
Here, the amount of adhesion of the insulation coating is not particularly limited, but is, for example, preferably about 200 to 1500 mg/m2 per one surface, and more preferably 300 to 1200 mg/m2 per one surface. Excellent uniformity can be maintained by forming the insulation coating so as to have the amount of adhesion in the above range. For the case of measuring the amount of adhesion of the insulation coating afterwards, various known measurement methods can be used, and for example, a method of measuring a mass difference before and after immersion in an aqueous sodium hydroxide solution, a fluorescent X-ray method using a calibration curve method, or the like may be appropriately used.
A method of manufacturing the non-oriented electrical steel sheet according to the present disclosure will be described. The non-oriented electrical steel sheet according to the present disclosure can be manufactured by sequentially performing a hot rolling step, a cold rolling step, and a finish-annealing step on a steel ingot that has a chemical composition including, in mass%, C: 0.0020 to 0.0060%, Si: 4.0 to 5.0%, Mn: 0.20% or less, Al: 0.010% or more and less than 0.050%, P: 0.030% or less, S: 0.0030% or less, N: 0.0005 to 0.0030%, O: less than 0.0050%, Ca: less than 0.0010%, Ti: less than 0.0050%, Nb: less than 0.0050%, Zr: less than 0.0050%, V: less than 0.0050%, Cu: less than 0.20%, Ni: less than 0.50%, Sn: 0 to 0.05%, Sb: 0 to 0.05%, and a balance: Fe and impurities. A hot-rolled sheet annealing step may be further provided between the hot rolling step and the cold rolling step. In a case in which the insulation coating is formed on the surface of the base metal, the insulation coating is formed after the finish annealing. Hereinafter, each step will be described in detail.
Because the chemical composition of the steel ingot is the same as the chemical composition of the steel sheet except for C and O, the description thereof is omitted. The reasons for limitation of C and O will be described below.
C has an effect of suppressing embrittlement cracking during cold rolling by segregating at grain boundaries. The C content in the steel ingot is preferably 0.0020% or more in order to obtain this effect. However, if excessive C is contained in a final product, favorable magnetic properties cannot be obtained as mentioned above. In the present disclosure, decarburization is performed in the finish-annealing step to reduce the C content in the final product. However, if the C content in the steel ingot exceeds 0.0060%, it is difficult to control the C content in the final product to 0.0040% or less. Therefore, the C content in the steel ingot is preferably 0.0020 to 0.0060%, more preferably 0.0025 to 0.0050%, and still more preferably 0.0030 to 0.0045%.
O is an element that inevitably mixed and forms an oxide, thereby increasing the iron loss and deteriorating the magnetic properties of the steel sheet. The O content in the steel ingot is preferably less than 0.0050% in order to make the O content in a region excluding a portion from the surface of the base metal to a position of 10 µm in the depth direction of the base metal less than 0.0050% in the final product as mentioned above.
The steel ingot (slab) having the above-described chemical composition is heated, and the heated steel ingot is hot-rolled to obtain a hot-rolled sheet. Here, the heating temperature for the steel ingot at the time of subjecting the steel ingot to the hot rolling is not particularly limited, but is preferably, for example, 1050 to 1250° C. The thickness of the hot-rolled sheet after the hot rolling is not particularly limited, but is preferably, for example, about 1.5 to 3.0 mm in consideration of the final thickness of the base metal.
Thereafter, hot-rolled sheet annealing is carried out, if necessary, for the purpose of increasing the magnetic flux density of the steel sheet. Heat treatment conditions in the hot-rolled sheet annealing are not particularly specified, but for example, heating at a temperature of 950° C. or lower is preferable. Heating time is preferably 1 to 300 s. The hot-rolled sheet annealing step may be omitted for cost reduction although the magnetic properties are inferior to those in the case of carrying out the hot-rolled sheet annealing step.
After the hot-rolled sheet annealing, pickling is carried out to remove a scale layer generated on the surface of the base metal. Here, pickling conditions such as the concentration of an acid used for the pickling, the concentration of a promotor used for the pickling, and the temperature of a pickling liquid are not particularly limited, and known pickling conditions can be used.
After the pickling, cold rolling is carried out. In the cold rolling, the pickled sheet from which the scale layer has been removed is rolled at a rolling reduction ratio such that the final sheet thickness of the base metal becomes 0.10 to 0.35 mm.
After the cold rolling, finish annealing is carried out. In the method of manufacturing the non-oriented electrical steel sheet according to the present disclosure, a continuous annealing furnace is used for the finish annealing. The finish-annealing step is an important step for performing decarburization and controlling the C content and the crystal grain size in the base metal.
Here, finish-annealing conditions are not particularly limited, but for example, it is preferable that the soaking temperature is 750 to 1050° C., the soaking time is 1 to 300 s, the atmosphere is a mixed atmosphere of H2 and N2 in which the proportion of H2 is 10 to 100 vol% (i.e., H2 + N2 = 100 vol%), and the dew point of the atmosphere is 0 to 50° C.
In a case in which the soaking temperature is lower than 750° C., the crystal grain size becomes small, and the iron loss is deteriorated, which is not preferable. In a case in which the soaking temperature exceeds 1050° C., the strength becomes insufficient, and the iron loss is also deteriorated, which is not preferable. The soaking temperature is more preferably 770 to 1000° C., and still more preferably 780 to 980° C. The proportion of H2 in the atmosphere is more preferably 15 to 90 vol%. The decarburization can be sufficiently performed by setting the dew point of the atmosphere to 0° C. or higher, whereby the C content in the base metal can be reduced. Excessive oxidation of the surface of the base metal can be suppressed by setting the dew point of the atmosphere to 50° C. or lower. The dew point of the atmosphere is more preferably 10 to 40° C., and still more preferably 15 to 35° C.
After the finish annealing, a step of forming an insulation coating is carried out, if necessary. In this regard, the step of forming an insulation coating is not particularly limited, and using the known insulation film treatment liquid as described above, application of the treatment liquid and drying may be performed by a known method.
The surface of the base metal on which an insulation coating will be formed may be subjected to an arbitrary pretreatment such as a degreasing treatment with alkali or the like or a pickling treatment with hydrochloric acid, sulfuric acid, phosphoric acid, or the like before applying the treatment liquid, or may be a surface as it is after the finish annealing without being subjected to these pretreatments.
Hereinafter, the present disclosure will be described more specifically with reference to examples, but the present disclosure is not limited to these examples.
A slab having a chemical composition shown in Table 1 was heated to 1150° C., then hot-rolled at a finishing temperature of 850° C. and a finishing sheet thickness of 2.0 mm, and wound up at 650° C. to obtain a hot-rolled steel sheet. The hot-rolled steel sheet obtained was subjected to hot-rolled sheet annealing at 900° C. × 50 s with a continuous annealing furnace, and scale on the surface was removed by pickling. The steel sheet thus obtained was cold-rolled into a cold-rolled sheet having a sheet thickness of 0.25 mm.
Annealing was further performed in a mixed atmosphere of H2: 20% and N2: 80% with various finish-annealing conditions (dew point, soaking temperature, and soaking time) so as to obtain chemical compositions as shown in Table 2 below. Specifically, the dew point was raised for a case in which the C content was controlled to be low. The dew point was lowered for a case in which the C content was controlled so as not to be changed. The finish-annealing temperature was made higher and/or the soaking time was made longer for a case in which the average crystal grain size was controlled to be large. The finish-annealing temperature and/or the soaking time was made reversed to the above for a case in which the average crystal grain size was controlled to be small. Thereafter, an insulation coating was applied to manufacture a non-oriented electrical steel sheet, and the sheet was used as a test specimen.
The insulation coating was formed by applying an insulation coating including aluminum phosphate and an acryl-styrene copolymer resin emulsion having a particle size of 0.2 µm so as to obtain a predetermined amount of adhesion, and baking the insulation coating at 350° C. in the air.
For each test specimen obtained, the average crystal grain size of the base metal was measured by the above-mentioned cutting method according to JIS G 0551 (2013) “Steels-Micrographic determination of the apparent grain size”.
The O content in a region excluding a portion from the surface of the base metal to a position of 10 µm in the depth direction of the base metal was measured by the method mentioned above.
Epstein test pieces were taken from the rolling direction and the widthwise direction in each test specimen, and the magnetic properties (iron loss W10/400 and magnetic flux density B50) were evaluated by an Epstein test in accordance with JIS C 2550-1 (2011). A JIS No. 5 tensile test piece was taken from each test specimen according to JIS Z 2241 (2011) so that the longitudinal direction coincided with the rolling direction of the steel sheet. A tensile test was then performed according to JIS Z 2241 (2011) using the test piece, and the tensile strength was measured. The results are shown in Table 2.
In Tables 1 and 2, underlines for chemical components mean being outside the ranges of the present disclosure, and underlines for other than the chemical components mean being outside the preferred ranges.
In Test Nos. 2 to 7, 13, 14, 16, and 19 to 22, which satisfy the requirements of the present disclosure, the iron loss was 25.0 W/kg or less, the magnetic flux density was 1.60 T or more, and the tensile strength was 650 MPa or more. Among them, particularly in Test Nos. 2, 4, 5, 7, 13, 14, 16, 19, and 20, which have an average crystal grain size of 10 to 80 µm, the results showed excellent balance between the strength and the magnetic properties.
On the other hand, in Test Nos. 1, 8 to 12, 15, 17, 18, 23, and 24, which are Comparative Examples, at least any one of the magnetic properties or the strength was poor, or the toughness was significantly deteriorated, whereby manufacturing was difficult.
Specifically, in Test No. 1, the Si content was lower than the specified range, which resulted in poor tensile strength. Since the Si content exceeded the specified range in Test No. 8, and the C content was lower than the specified range in Test No. 9, the toughness was deteriorated, whereby fracture during cold rolling occurred, and thereby, measurement of the average crystal grain size, tensile strength, and magnetic properties could not be carried out. In Test No. 10, the C content of the steel ingot was higher than the specified range, and the C content of the base metal of the steel sheet was higher than the specified range, which therefore resulted in poor iron loss.
In Test No. 11, the Mn content exceeded the specified range, which therefore resulted in poor magnetic flux density. Since the Al content was lower than the specified range in Test No. 12, and the Al content was higher than the specified range in Test No. 15, the average crystal grain size could not be stably controlled, and the average crystal grain sizes were larger than the specified range, which therefore resulted in poor tensile strength. In Test No. 17 in which the chemical composition satisfied the specification, since the dew point was higher than the specified range, the O content of the base metal of the steel sheet was higher than the specified range, which therefore resulted in poor magnetic flux density. In Test No. 18, since the dew point was lower than the specified range, the C content of the base metal of the steel sheet was higher than the specified range, which therefore resulted in poor iron loss.
In Test No. 23, the N content exceeded the specified range, which therefore resulted in poor iron loss. In Test No. 24, the O content in a region excluding a 10 µm surface layer of the steel sheet (base metal) exceeded the specified range, which therefore resulted in poor iron loss.
As described above, a non-oriented electrical steel sheet having high strength and excellent magnetic properties can be obtained at low cost according to the present disclosure.
The disclosure of Japanese Patent Application No. 2020-073210 filed on Apr. 16, 2020 is incorporated herein by reference in its entirety. All documents, patent applications, and technical standards described in this specification are incorporated herein by reference to the same extent as if individual document, patent application, and technical standard were specifically and individually described.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2020-073210 | Apr 2020 | JP | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/JP2021/015699 | 4/16/2021 | WO |
