NON-ORIENTED ELECTRICAL STEEL SHEET AND METHOD FOR PRODUCING THE SAME

Description

TECHNICAL FIELD

This disclosure relates to a non-oriented electrical steel sheet and a method for producing the same.

BACKGROUND

In recent years, there has been a growing worldwide demand for energy conservation in electrical equipment. Thus, more excellent magnetic properties are being demanded of non-oriented electrical steel sheets used in the iron cores of rotating machines. Recently, there has been a strong need for smaller and high-output drive motors for hybrid electric vehicles (HEVs) and electric vehicles (EVs), and in order to achieve these needs, increasing the motor rotational speed is being considered.

The motor core is divided into a stator core and a rotor core. The rotor core of the HEV drive motor is subjected to large centrifugal forces due to its large outer diameter. The rotor core structurally has a very narrow section (width: 1 mm to 2 mm) called the rotor core bridge section, which is under particularly high stress during motor drive. Furthermore, the rotor core is subjected to high repetitive stress due to centrifugal force as the motor repeatedly rotates and stops, so the electrical steel sheet used in the rotor core must have excellent fatigue resistance. In particular, the temperature of the rotor core rises to about 100° C. to 150° C. when the motor is driven, so the electrical steel sheet used in the rotor core must have excellent fatigue resistance nearly at 100° C.

On the other hand, the electrical steel sheet used in the stator core should have high magnetic flux density and low iron loss in order to obtain a smaller and higher-output motor. In detail, for the ideal properties required of the electrical steel sheet used in the motor core, the electrical steel sheet for rotor cores should have excellent fatigue resistance and electrical steel sheet for stator cores should have high magnetic flux density and low iron loss.

Thus, even if the electrical steel sheet is used in the same motor core, the required properties for rotor cores and stator cores are different. In producing motor cores, however, in order to increase material yield and productivity, rotor core materials and stator core materials should be obtained simultaneously from the same blank sheet by blanking, and then the respective core materials should be stacked into a rotor or stator core.

As a technique for producing a non-oriented electrical steel sheet with high-strength and low iron loss for motor cores, for example, PTL 1 (JP2008-050686A) discloses a technique for producing a high-strength rotor core and stator core with low iron loss from the same material in which a high-strength non-oriented electrical steel sheet is produced, rotor and stator core materials are collected from the steel sheet by blanking to be stacked into a rotor and a stator core, and then only the stator core is subjected to stress relief annealing.

CITATION LIST

Patent Literature

• • PTL 1: JP2008-050686A

SUMMARY

Technical Problem

However, according to our study, the technique disclosed in PTL 1 improves the yield stress by using the high-strength non-oriented electrical steel sheet but does not necessarily improve fatigue strength under warm conditions, which is the most important property. Furthermore, the technique disclosed in PTL 1 requires stress relief annealing at high temperatures to promote grain growth, and the cost of installing such equipment makes it difficult to spread the technique from an economic standpoint, except for some manufacturers who already have annealing equipment.

It could thus be helpful to provide a non-oriented electrical steel sheet having good fatigue resistance suitable for rotor cores and excellent magnetic properties suitable for stator cores, and to propose an inexpensive method for producing the non-oriented electrical steel sheet.

Solution to Problem

We have made intensive studies to find that by controlling the crystal grain size distribution, a non-oriented electrical steel sheet with high fatigue strength, especially under warm conditions, and low iron loss can be obtained. We also found that crystal grain size distribution can be controlled by optimizing rolling conditions in the final pass of cold rolling.

This disclosure has been contrived on the basis of the aforementioned findings and is configured as follows.

[1] A non-oriented electrical steel sheet, comprising a chemical composition containing (consisting of), in mass %,

• • C: 0.01% or less,
  • Si: 2.0% or more and less than 4.5%,
  • Mn: 0.05% or more and 5.00% or less,
  • P: 0.1% or less,
  • S: 0.01% or less,
  • Al: 3.0% or less, and
  • N: 0.0050% or less,
    with the balance being Fe and inevitable impurities, where Si+Al is less than 4.5%, wherein
  • crystal grains in the steel sheet have an average grain size X₁ of 60 μm or more and 200 μm or less, a standard deviation S₁ of a grain size distribution satisfies the following formula (1):

S 1 / X 1 < 0 . 7 ⁢ 5 ( 1 )

and a kurtosis K₁ of the crystal grain size distribution is 2.00 or less.

[2] The non-oriented electrical steel sheet according to [1], wherein the chemical composition further contains, in mass %,

• • Co: 0.0005% or more and 0.0050% or less.

[3] The non-oriented electrical steel sheet according to [1] or [2], wherein the chemical composition further contains, in mass %,

• • Cr: 0.05% or more and 5.00% or less.

[4] The non-oriented electrical steel sheet according to any of [1] to [3], wherein the chemical composition further contains, in mass %, at least one selected from the group of

• • Ca: 0.001% or more and 0.100% or less,
  • Mg: 0.001% or more and 0.100% or less, and
  • REM: 0.001% or more and 0.100% or less.

[5] The non-oriented electrical steel sheet according to any of [1] to [4], wherein the chemical composition further contains, in mass %, at least one selected from the group consisting of

• • Sn: 0.001% or more and 0.200% or less and
  • Sb: 0.001% or more and 0.200% or less.

[6] The non-oriented electrical steel sheet according to any of [1] to [5], wherein the chemical composition further contains, in mass %, at least one selected from the group consisting of

• • Cu: 0% or more and 0.5% or less,
  • Ni: 0% or more and 0.5% or less,
  • Ti: 0% or more and 0.005% or less,
  • Nb: 0% or more and 0.005% or less,
  • V: 0% or more and 0.010% or less,
  • Ta: 0% or more and 0.002% or less,
  • B: 0% or more and 0.002% or less,
  • Ga: 0% or more and 0.005% or less,
  • Pb: 0% or more and 0.002% or less,
  • Zn: 0% or more and 0.005% or less,
  • Mo: 0% or more and 0.05% or less,
  • W: 0% or more and 0.05% or less,
  • Ge: 0% or more and 0.05% or less, and
  • As: 0% or more and 0.05% or less.

[7] A method for producing the non-oriented electrical steel sheet according to any of [1] to [6], comprising

• • hot rolling a steel material having the chemical composition according to any of [1] to [6] to obtain a hot-rolled sheet,
  • pickling the hot-rolled sheet to obtain a pickled hot-rolled sheet,
  • cold rolling the pickled hot-rolled sheet under the following conditions: a final pass work roll diameter D of 150 mmφ or more, a final pass rolling reduction r of 15% or more, and a final pass strain rate ε_m of 100 s⁻¹ or more and 1300 s⁻¹ or less to obtain a cold-rolled sheet, and
  • heating the cold-rolled sheet to an annealing temperature T₂ of 875° C. or higher and 1050° C. or lower with an average heating rate V₁ of 10° C./s or more within a temperature range of 500° C. to 700° C. and then performing cooling to obtain a cold-rolled and annealed sheet that is the non-oriented electrical steel sheet.

Advantageous Effect

According to this disclosure, it is possible to provide a non-oriented electrical steel sheet that has both the characteristics suitable for rotor cores, namely high fatigue strength under warm conditions, and characteristics suitable for stator cores, namely excellent magnetic properties. Therefore, the non-oriented electrical steel sheet of this disclosure can be used to provide high-performance motor cores at low cost with good material yield. The above effects are not affected in any way by the application of stress relief annealing to the steel sheet of this disclosure for the purpose of reducing the increase in iron loss due to distortion during blanking.

DETAILED DESCRIPTION

The details of this disclosure are described below, along with the reasons for its limitations.

<Chemical Composition of Non-Oriented Electrical Steel Sheet>

The following describes the preferable chemical composition that the non-oriented electrical steel sheet of this disclosure has. While the unit of the content of each element in the chemical composition is “mass %”, the content is expressed simply in “%” unless otherwise specified.

C: 0.01% or Less

C is a harmful element that forms carbides while the motor is in use, causing magnetic aging and degrading iron loss properties. To avoid magnetic aging, the C content in the steel sheet is set to 0.01% or less. The C content is preferably 0.004% or less. No lower limit is placed on the C content, but since steel sheets with excessively reduced C are very expensive, the C content is preferably 0.0001% or more.

Si: 2.0% or More and Less than 4.5%

Si has the effects of increasing the specific resistance of steel to reduce iron loss and increasing the strength of steel through solid solution strengthening. To obtain such an effects, the Si content is set to 2.0% or more. On the other hand, Si content of 4.5% or more results in a decrease in saturation magnetic flux density and an associated significant decrease in magnetic flux density. Thus, the Si content is set to less than 4.5%. Therefore, the Si content is set to 2.0% or more and less than 4.5%. The Si content is preferably 2.5% or more. The Si content is preferably less than 4.5%. The Si content is more preferably 3.0% or more. The Si content is more preferably less than 4.5%.

Mn: 0.05% or More and 5.00% or Less

Mn, like Si, is a useful element in increasing the specific resistance and strength of steel. To obtain such an effect, the Mn content needs to be 0.05% or more. On the other hand, Mn content exceeding 5.00% may promote MnC precipitation to degrade the magnetic properties, so the upper limit of Mn content is 5.00%. Therefore, the Mn content is 0.05% or more and 5.00% or less. The Mn content is preferably 0.10% or more. The Mn content is preferably 3.00% or less.

P: 0.1% or Less

P is a useful element used to adjust the strength (hardness) of steel. However, P content exceeding 0.1% decreases toughness and thus cracking is likely to occur during working, so the P content is set to 0.1% or less. No lower limit is placed on the P content, but since steel sheets with excessively reduced P are very expensive, the P content is preferably 0.001% or more. The P content is preferably 0.003% or more. The P content is preferably 0.08% or less.

S: 0.01% or Less

S is an element that adversely affects iron loss properties by forming fine precipitates. In particular, when the S content exceeds 0.01%, the adverse effect becomes more pronounced, so the S content is set to 0.01% or less. No lower limit is placed on the S content, but since steel sheets with excessively reduced S are very expensive, the S content is preferably 0.0001% or more. The S content is preferably 0.0003% or more. The S content is preferably 0.0080% or less, and more preferably 0.0050% or less.

Al: 3.0% or Less

Al, like Si, is a useful element that increases the specific resistance of steel to reduce iron loss. To obtain such an effect, the Al content is preferably 0.005% or more. The Al content is more preferably 0.010% or more, and further preferably 0.015% or more. On the other hand, Al content exceeding 3.0% may promote nitriding of the steel sheet surface, resulting in degradation of magnetic properties, so the upper limit of Al content is 3.0%. The Al content is preferably 2.0% or less.

N: 0.0050% or Less

N is an element that adversely affects iron loss properties by forming fine precipitates. In particular, when the N content exceeds 0.0050%, the adverse effect becomes more pronounced, so the N content is set to 0.0050% or less. The N content is preferably 0.0030% or less. No lower limit is placed on the N content, but since steel sheets with excessively reduced N are very expensive, the N content is preferably 0.0005% or more. The N content is preferably 0.0008% or more. The N content is preferably 0.0030% or less.

Si+Al: Less than 4.5%

By setting Si+Al (total content of Si and Al) to less than 4.5% and performing cold rolling under appropriate conditions, the kurtosis of the crystal grain size distribution of cold-rolled and annealed sheet can be reduced. This increases fatigue strength. Therefore, the Si+Al value is set to less than 4.5%. The reason why the kurtosis of the crystal grain size distribution is reduced by setting the Si+Al value to less than 4.5% and combining it with appropriate cold rolling is unknown. However, we assume that this effect is caused by a change in the balance of the slip system, which is active during cold rolling, optimizing the shear strain distribution during cold rolling.

The balance other than the aforementioned components in the chemical composition of the electrical steel sheet according to one of the disclosed embodiments is Fe and inevitable impurities. However, the chemical composition of electrical steel sheet according to another embodiment may further contain at least one of the elements described below in predetermined amounts in addition to the above components (elements) depending on the required properties.

Co: 0.0005% or More and 0.0050% or Less

Co has the effect of reinforcing the action of decreasing the kurtosis of the crystal grain size distribution of annealed sheet through appropriate control of Si+Al and cold rolling conditions. In detail, the addition of a small amount of Co can stably decrease the kurtosis of the crystal grain size distribution. To obtain such an effect, the Co content should be set to 0.0005% or more. On the other hand, Co content exceeding 0.0050% saturates the effect and unnecessarily increases the cost. Therefore, when Co is added, the upper limit of Co content is 0.0050%. Therefore, the chemical composition preferably further contains Co of 0.0005% or more. The chemical composition preferably further contains Co of 0.0050% or less.

Cr: 0.05% or More and 5.00% or Less

Cr has the effect of increasing the specific resistance of steel to reduce iron loss. To achieve such an effect, the Cr content should be 0.05% or more. On the other hand, Cr content exceeding 5.00% results in a decrease in saturation magnetic flux density and an associated significant decrease in magnetic flux density. Therefore, when Cr is added, the upper limit of the Cr content is 5.00%. Accordingly, the chemical composition preferably further contains Cr of 0.05% or more. The chemical composition preferably further contains Cr of 5.00% or less.

Ca: 0.001% or More and 0.100% or Less

Ca is an element that fixes S as sulfide to contribute to iron loss reduction. To obtain such an effect, the Ca content should be 0.001% or more. On the other hand, Ca content exceeding 0.100% saturates the effect and unnecessarily increases the cost. Therefore, when Ca is added, the upper limit of Ca content is 0.100%.

Mg: 0.001% or More and 0.100% or Less

Mg is an element that fixes S as sulfide to contribute to iron loss reduction. To obtain such an effect, the Mg content should be 0.001% or more. On the other hand, Mg content exceeding 0.100% saturates the effect and unnecessarily increases the cost. Therefore, when Mg is added, the upper limit of Mg content is 0.100%.

REM: 0.001% or More and 0.100% or Less

REM is a group of elements that fix S as sulfide to contribute to iron loss reduction. To obtain such an effect, the REM content should be 0.001% or more. On the other hand, REM content exceeding 0.100% saturates the effect and unnecessarily increases the cost. Therefore, when REM is added, the upper limit of REM content is 0.100%.

From the same perspective, the chemical composition preferably further contains at least one selected from the group of Ca: 0.001% or more, Mg: 0.001% or more, and REM: 0.001% or more. The chemical composition preferably further contains at least one selected from the group of Ca: 0.100% or less, Mg: 0.100% or less, and REM: 0.100% or less.

Sn: 0.001% or More and 0.200% or Less

Sn is an effective element for improving magnetic flux density and reducing iron loss through texture improvement. To obtain such an effect, the Sn content should be 0.001% or more. On the other hand, Sn content exceeding 0.200% saturates the effect and unnecessarily increases the cost. Therefore, when Sn is added, the upper limit of Sn content is 0.200%.

Sb: 0.001% or More and 0.200% or Less

Sb is an effective element for improving magnetic flux density and reducing iron loss through texture improvement. To obtain such an effect, the Sb content should be 0.001% or more. On the other hand, Sb content exceeding 0.200% saturates the effect and unnecessarily increases the cost. Therefore, when Sb is added, the upper limit of Sb content is 0.200%.

From the same perspective, the chemical composition preferably further contains at least one selected from the group of Sn: 0.001% or more and Sb: 0.001% or more. The chemical composition preferably further contains at least one selected from the group of Sn: 0.200% or less and Sb: 0.200% or less.

Cu: 0% or More and 0.5% or Less

Cu is an element that improves the toughness of steel and can be added as needed. However, Cu content exceeding 0.5% saturates the effect and thus, when Cu is added, the upper limit of Cu content is 0.5%. When Cu is added, the Cu content is more preferably 0.01% or more. The Cu content is more preferably 0.1% or less. The Cu content may be 0%.

Ni: 0% or More and 0.5% or Less

Ni is an element that improves the toughness of steel and can be added as needed. However, Ni content exceeding 0.5% saturates the effect and thus, when Ni is added, the upper limit of Ni content is 0.5%. When Ni is added, the Ni content is more preferably 0.01% or more. The Ni content is more preferably 0.1% or less. The Ni content may be 0%.

Ti: 0% or More and 0.005% or Less

Ti can be added as appropriate to improve fatigue strength under warm conditions by forming fine carbonitrides and increasing steel sheet strength through strengthening by precipitation. On the other hand, Ti content exceeding 0.005% deteriorates grain growth in the annealing process and increases iron loss. Therefore, when Ti is added, the upper limit of Ti content is 0.005%. The Ti content is more preferably 0.002% or less. The Ti content may be 0%.

Nb: 0% or More and 0.005% or Less

Nb can be added as appropriate to improve fatigue strength under warm conditions by forming fine carbonitrides and increasing steel sheet strength through strengthening by precipitation. On the other hand, Nb content exceeding 0.005% deteriorates grain growth in the annealing process and increases iron loss. Therefore, when Nb is added, the upper limit of Nb content is 0.005%. The Nb content is more preferably 0.002% or less. The Nb content may be 0%.

V: 0% or More and 0.010% or Less

V can be added as appropriate to improve fatigue strength under warm conditions by forming fine carbonitrides and increasing steel sheet strength through strengthening by precipitation. On the other hand, V content exceeding 0.010% deteriorates grain growth in the annealing process and increases iron loss. Therefore, when V is added, the upper limit of V content is 0.010%. The V content is more preferably 0.005% or less. The V content may be 0%.

Ta: 0% or More and 0.002% or Less

Ta can be added as appropriate to improve fatigue strength under warm conditions by forming fine carbonitrides and increasing steel sheet strength through strengthening by precipitation. On the other hand, Ta content exceeding 0.002% deteriorates grain growth in the annealing process and increases iron loss. Therefore, when Ta is added, the upper limit of Ta content is 0.002%. The Ta content is more preferably 0.001% or less. The Ta content may be 0%.

B: 0% or More and 0.002% or Less

B can be added as appropriate to improve fatigue strength under warm conditions by forming fine nitrides and increasing steel sheet strength through strengthening by precipitation. On the other hand, B content exceeding 0.002% deteriorates grain growth in the annealing process and increases iron loss. Therefore, when B is added, the upper limit of B content is 0.002% or less. The B content is more preferably 0.001% or less. The B content may be 0%.

Ga: 0% or More and 0.005% or Less

Ga can be added as appropriate to improve fatigue strength under warm conditions by forming fine nitrides and increasing steel sheet strength through strengthening by precipitation. On the other hand, Ga content exceeding 0.005% deteriorates grain growth in the annealing process and increases iron loss. Therefore, when Ga is added, the upper limit of Ga content is 0.005%. The Ga content is more preferably 0.002% or less. The Ga content may be 0%.

Pb: 0% or More and 0.002% or Less

Pb can be added as appropriate to improve fatigue strength under warm conditions by forming fine Pb particles and increasing steel sheet strength through strengthening by precipitation. On the other hand, Pb content exceeding 0.002% deteriorates grain growth in the annealing process and increases iron loss. Therefore, when Pb is added, the upper limit of Pb content is 0.002%. The Pb content is more preferably 0.001% or less. The Pb content may be 0%.

Zn: 0% or More and 0.005% or Less

Zn is an element that increases iron loss by increasing fine inclusions, and especially when its content exceeds 0.005%, the adverse effect becomes more pronounced. Therefore, when Zn is added, the upper limit of Zn content is 0.005%. The Zn content is more preferably 0.003% or less. The Zn content may be 0%.

Mo: 0% or More and 0.05% or Less

Mo can be added as appropriate to improve fatigue strength under warm conditions by forming fine carbides and increasing steel sheet strength through strengthening by precipitation. On the other hand, Mo content exceeding 0.05% deteriorates grain growth in the annealing process and increases iron loss. Therefore, when Mo is added, the upper limit of Mo content is 0.05%. The Mo content is more preferably 0.02% or less. The Mo content may be 0%.

W: 0% or More and 0.05% or Less

W can be added as appropriate to improve fatigue strength under warm conditions by forming fine carbides and increasing steel sheet strength through strengthening by precipitation. On the other hand, W content exceeding 0.05% deteriorates grain growth in the annealing process and increases iron loss. Therefore, when W is added, the upper limit of W content is 0.05%. The W content is more preferably 0.02% or less. The W content may be 0%.

Ge: 0% or More and 0.05% or Less

Ge can be added as appropriate because it is an effective element in improving magnetic flux density and reducing iron loss by improving the texture. On the other hand, Ge content exceeding 0.05% saturates the effect and thus, when Ge is added, the upper limit of Ge content is 0.05%. The Ge content is more preferably 0.002% or more. The Ge content is more preferably 0.01% or less. The Ge content may be 0%.

As: 0% or More and 0.05% or Less

As can be added as appropriate because it is an effective element in improving magnetic flux density and reducing iron loss by improving the texture. On the other hand, As content exceeding 0.05% saturates the effect and thus, when As is added, the upper limit of As content is 0.05%. The As content is more preferably 0.002% or more. The As content is more preferably 0.01% or less. The As content may be 0%.

The balance other than the aforementioned components in the chemical composition is Fe and inevitable impurities.

<Microstructure of Non-Oriented Electrical Steel Sheet>

Next, the microstructure (crystal grain state) of the non-oriented electrical steel sheet will be explained.

(Average Grain Size X₁: 60 μm or More and 200 μm or Less)

Our study revealed that fine crystal grains in the steel sheet improve the fatigue strength. In detail, when the average grain size X₁ is 200 μm or less, the fatigue strength under warm conditions can satisfy the value required in rotor materials of motors applied to HEVs or EVs (hereinafter referred to as HEV/EV motors). Thus, in the non-oriented electrical steel sheet of this disclosure, the average grain size X₁ is set to 200 μm or less. The required value for fatigue strength under warm conditions for rotor materials is 300 MPa or more.

On the other hand, if the average grain size X₁ is excessively fine, iron loss increases. Therefore, the average grain size X₁ is set to 60 μm or more in the non-oriented electrical steel sheet of this disclosure. This allows the target iron loss properties (W_10/400≤15.0 (W/kg)) to be achieved.

(Standard Deviation S₁ of Crystal Grain Size Distribution: Satisfying Formula (1))

When the value of the standard deviation of the crystal grain size distribution is large relative to the average grain size, iron loss will increase because there will be many excessively fine crystal grains or excessively coarse crystal grains, which are unfavorable for reducing iron loss. Therefore, in the non-oriented electrical steel sheet of this disclosure, the standard deviation S₁ of the crystal grain size distribution should satisfy the formula (1) below in order for the iron loss to exhibit the above target value required for the stator materials of HEV/EV motors:

S 1 / X 1 < 0.75 ( 1 )

In the non-oriented electrical steel sheet of this disclosure, it is preferable that the standard deviation S₁ of the crystal grain size distribution satisfies the following formula (1′):

S 1 / X 1 < 0.7 ( 1 ’ )

(Kurtosis K₁ of Crystal Grain Size Distribution: 2.00 or Less)

We have found that by controlling the kurtosis of the crystal grain size distribution, it is possible to achieve a non-oriented electrical steel sheet with high fatigue strength under warm conditions and low iron loss. This is achieved by controlling the kurtosis of the crystal grain size distribution simultaneously with the standard deviation S₁ of the crystal grain size distribution described above.

Here, kurtosis corresponds to sample coefficient of kurtosis in JISZ8101-1:2015 and is related to the tail weight of a distribution. JISZ8101-1:2015 corresponds to ISO3534-1:2006. When the kurtosis is high, it means that the distribution has a high probability of having values that are extremely out of the mean, compared to a distribution with the same standard deviation but a normal distribution in terms of distribution shape. In other words, in this disclosure, kurtosis is a measure of the presence frequency of extremely coarse crystal grains and/or extremely fine crystal grains relative to the variation in crystal grain size distribution. When the kurtosis is high, the presence frequency of extremely coarse crystal grains and/or extremely fine crystal grains is high. The mixture of extremely coarse crystal grains and extremely fine crystal grains easily causes excessive stress concentration and results in localized cyclic strain during cyclic stress loading. Under warm conditions of about 100° C., strain aging hardens the strain concentrated areas and enhances hardness non-uniformity in the microstructure, which deteriorates fatigue resistance, especially under warm conditions of about 100° C. Further, the extremely coarse crystal grains induce an increase in eddy current losses and extremely fine crystal grains induce an increase in hysteresis loss, thus degrading the iron loss properties of the steel sheet as a whole. Specifically, when the kurtosis K₁ of the crystal grain size distribution is 2.00 or less, the presence frequency of extremely coarse crystal grains and/or extremely fine crystal grains is sufficiently small, and the fatigue limit will satisfy the above value required for the rotor materials of HEV/EV motors and the iron loss will exhibit the above value required for the stator materials of HEV/EV motors. Therefore, in the non-oriented electrical steel sheet of this disclosure, the kurtosis K₁ of the crystal grain size distribution is set to 2.00 or less. The kurtosis K₁ of the crystal grain size distribution is preferably 1.50 or less and more preferably 1.00 or less. No lower limit is placed on the kurtosis K₁, but K₁ is usually 0 or more when the steel sheet is produced using the method of this disclosure.

The kurtosis K₁ can be determined according to the procedure described in the EXAMPLES section below, and is calculated using the formula in which the value of the normal distribution is adjusted to 0.

<Motor Core>

The motor core can be formed of a rotor core, which is a lamination of the above non-oriented electrical steel sheets, and a stator core, which is a lamination of the above non-oriented electrical steel sheets. The motor core can be easily downsized and achieve higher output because the rotor core has high fatigue strength under warm conditions and the stator core has excellent magnetic properties.

<Method for Producing Non-Oriented Electrical Steel Sheet>

The following describes a method for producing a non-oriented electrical steel sheet according to this disclosure.

Generally stated, in the method, a steel material having the above chemical composition is used as a starting material, and hot rolling, optional hot-rolled sheet annealing, pickling, cold rolling, and annealing are performed in sequence. This method can produce the non-oriented electrical steel sheet of this disclosure. In this disclosure, as long as the conditions of the chemical composition of the steel material, cold rolling process, and annealing process are within predetermined ranges, other conditions are not limited. The method for producing a motor core is not particularly limited and can be based on commonly-known methods.

(Steel Material)

The steel material is not limited as long as it has the chemical composition previously described for the non-oriented electrical steel sheet.

The method for smelting the steel material is not particularly limited, and any publicly known smelting method using a converter or electric furnace, etc., can be employed. For productivity and other reasons, it is preferable to make a slab (steel material) by continuous casting after smelting, but the slab may also be made by publicly known casting methods such as the ingot casting and blooming or the thin slab continuous casting.

(Hot Rolling Process)

The hot rolling process is the process of applying hot rolling to the steel material having the above chemical composition to obtain a hot-rolled sheet. The hot rolling process is not particularly limited, and any commonly used hot rolling process in which the steel material having the above chemical composition is heated and subjected to hot rolling to obtain a hot-rolled sheet of a predetermined size can be applied.

Examples of the commonly used hot rolling process include a process in which a steel material is heated to a temperature of 1000° C. or higher and 1200° C. or lower, the heated steel material is subjected to hot rolling at a finisher delivery temperature of 800° C. or higher and 950° C. or lower, and after the hot rolling is completed, appropriate post-rolling cooling (for example, cooling at an average cooling rate of 20° C./s or more and 100° C./s or less within a temperature range of 450° C. to 950° C.) is applied, and coiling is performed at a coiling temperature of 400° C. or higher and 700° C. or lower to make a hot-rolled sheet of a predetermined size and shape.

(Hot-Rolled Sheet Annealing Process)

The hot-rolled sheet annealing process is the process of heating the hot-rolled sheet and holding it at a high temperature to thereby anneal the hot-rolled sheet. The hot-rolled sheet annealing process is not particularly limited, and the commonly used hot-rolled sheet annealing process can be applied. This hot-rolled sheet annealing process is not essential and may be omitted.

(Pickling Process)

The pickling process is the process of applying pickling to the hot-rolled sheet after the above hot rolling process or optional hot-rolled sheet annealing process. The pickling process is not particularly limited and any pickling process in which the steel sheet is pickled to the extent that cold rolling can be performed after pickling, for example, a commonly used pickling process using hydrochloric acid or sulfuric acid, can be applied. When the hot-rolled sheet annealing process is performed, the pickling process may be carried out continuously in the same line as the hot-rolled sheet annealing process or in a separate line.

(Cold Rolling Process)

The cold rolling process is the process of applying cold rolling to the hot-rolled sheet that has undergone the above pickling (pickled sheet). In more detail, in the cold rolling process, the hot-rolled sheet that has been pickled as described above is cold rolled under the following conditions: the final pass work roll diameter D of 150 mmφ or more, final pass rolling reduction r of 15% or more, and final pass strain rate ε_m of 100 s⁻¹ or more and 1300 s⁻¹ or less to obtain a cold-rolled sheet. In the cold rolling process, as long as the above cold rolling conditions are met, cold rolling may be performed twice or more with intermediate annealing performed therebetween as necessary to produce a cold-rolled sheet of a predetermined size. In this case, the conditions for intermediate annealing are not particularly limited, and normal intermediate annealing process can be applied.

[Final Pass Work Roll Diameter D: 150 Mmoφ or More]

In the cold rolling process, the final pass work roll diameter D is set to 150 mmφ or more. The reason for setting the final pass work roll diameter D to 150 mmφ or more is to make the kurtosis K₁ of the crystal grain size distribution in the resulting non-oriented electrical steel sheet 2.00 or less to form the desired steel sheet microstructure.

If the final pass work roll diameter D is smaller than 150 mmφ, it will be far away from the plane compression state, which will enhance the non-uniformity of shear strain in crystal grain units compared to when the work roll diameter is larger. This non-uniformity of shear strain results in the generation of a certain amount of regions with very high and very low nucleation frequency of recrystallized nuclei in the subsequent annealing process, which increases the kurtosis of the crystal grain size distribution in the annealed sheet.

On the other hand, when the final pass work roll diameter D is 150 mmφ or more, after the annealing process described below, the kurtosis K₁ of the crystal grain size distribution is 2.00 or less. As a result, the desired steel sheet microstructure is obtained.

The final pass work roll diameter D is preferably 170 mmφ or more, more preferably 200 mmφ or more. No upper limit is placed on the final pass work roll diameter D, but the final pass work roll diameter D is preferably 700 mmφ or less because an excessively large roll diameter increases the rolling load.

[Final Pass Rolling Reduction r: 15% or More]

In the cold rolling, the final pass rolling reduction r is set to 15% or more. The reason for setting the final pass rolling reduction r to 15% or more is to obtain the effect of a series of cold rolling control to form the desired steel sheet microstructure.

If the final pass rolling reduction r is less than 15%, the rolling reduction is too low, making it difficult to control the microstructure after annealing. On the other hand, when the final pass rolling reduction r is 15% or more, the series of cold rolling control is effective. As a result, the desired steel sheet microstructure is obtained.

The final pass rolling reduction r is preferably 20% or more. No upper limit is placed on the final pass rolling reduction r, but because an excessively high rolling reduction requires a large amount of equipment capacity and makes it difficult to control the shape of the cold-rolled sheet, the final pass rolling reduction r is usually 50% or less.

[Final Pass Strain Rate ε_m: 100 s⁻¹ or More and 1300 s⁻¹ or Less]

In the cold rolling process, the final pass strain rate ε_m is set to 100 s⁻¹ or more and 1300 s⁻¹ or less. The reason for setting the final pass strain rate ε_m to 100 s⁻¹ or more and 1300 s⁻¹ or less is to suppress fracture during rolling while keeping the kurtosis K₁ of the crystal grain size distribution in the resulting non-oriented electrical steel sheet 2.00 or less to form the desired steel sheet microstructure.

When the final pass strain rate ε_m is less than 100 s⁻¹, because the non-uniformity of shear strain in the crystal grain units of the cold-rolled sheet is enhanced and the location dependence of nucleation and grain growth in the subsequent annealing process is accentuated, the kurtosis K₁ of the crystal grain size distribution of the annealed sheet is larger. The reason for this is not necessarily clear, but we speculate that it is because the low strain rate ε_m lowers the flow stress, making it easier for strain to concentrate in crystal grains with a crystal orientation in which the crystal grains are easily deformed, resulting in non-uniform strain distribution. On the other hand, when the final pass strain rate ε_m exceeds 1300 s⁻¹, the flow stress increases excessively and brittle fracture is likely to occur during rolling.

When the final pass strain rate ε_m is 100 s⁻¹ or more and 1300 s⁻¹ or less, the kurtosis K₁ of the crystal grain size distribution is 2.00 or less after the annealing process described below, while suppressing fracture during rolling. As a result, the desired steel sheet microstructure is obtained.

The final pass strain rate ε_m is preferably 150 s⁻¹ or more. The final pass strain rate ε_m is preferably 1000 s⁻¹ or less.

The strain rate ε_m in each pass during cold rolling was derived using the following Ekelund's approximation formula:

ε m ≈ v R R ′ ⁢ h 1 ⁢ 2 2 - r · r [ Math . 1 ]

where, v_R is a roll peripheral speed (mm/s), R′ is a roll radius (mm), h₁ is a roll entry side sheet thickness (mm), and r is a rolling reduction (%).

(Annealing Process)

The annealing process is the process of applying annealing to the cold-rolled sheet that has undergone the cold rolling process. In more detail, in the annealing process, the cold-rolled sheet that has undergone the cold rolling process is heated to an annealing temperature T₂ of 875° C. or higher and 1050° C. or lower with an average heating rate V₁ of 10° C./s or more within a temperature range of 500° C. to 700° C., and then cooled to obtain a cold-rolled and annealed sheet (non-oriented electrical steel sheet). After the annealing process, an insulation coating can be applied to the surface. The coating method and type of coating are not particularly limited, and the commonly used insulation coating process can be applied.

[Average Heating Rate V₁ within a Range of 500° C. To 700° C.: 10° C./s or More]

In the annealing process, the average heating rate V₁ within a range of 500° C. to 700° C. is set to 10° C./s or more. The reason for setting the average heating rate V₁ to 10° C./s or more is to ensure that the standard deviation S₁ of the crystal grain size distribution in the resulting non-oriented electrical steel sheet satisfies the above formula (1) to form the desired steel sheet microstructure.

If the average heating rate V₁ is less than 10° C./s, the nucleation frequency of recrystallized nuclei decreases due to excessive recovery, and the location dependence of the number of recrystallized nuclei increases. As a result, fine crystal grains and coarse crystal grains are mixed, and the standard deviation S₁ of the grain size distribution becomes large and the above formula (1) is not satisfied.

On the other hand, when the average heating rate V₁ is 10° C./s or more, the nucleation frequency of recrystallized nuclei increases and the location dependence of the number of recrystallized nuclei decreases. As a result, the standard deviation S₁ of the grain size distribution becomes smaller and the above formula (1) is satisfied.

The average heating rate V₁ within a range of 500° C. to 700° C. is preferably 20° C./s or more, and more preferably 50° C./s or more. No upper limit is placed on the average heating rate V₁, but the average heating rate V₁ is preferably 500° C./s or less because an excessively high heating rate tends to cause temperature irregularities.

[Annealing Temperature T₂: 875° C. Or Higher and 1050° C. Or Lower]

In the annealing process, the annealing temperature T₂ is set to 875° C. or higher and 1050° C. or lower. The reason for setting the annealing temperature T₂ to 875° C. or higher and 1050° C. or lower is as follows.

When the annealing temperature T₂ is lower than 875° C., the recrystallized grains do not grow sufficiently and the average grain size X₁ in the resulting non-oriented electrical steel sheet cannot be 60 μm or more. On the other hand, when the annealing temperature T₂ is 875° C. or higher, sufficient grain growth occurs and the average grain size can be 60 μm or more, and thus the desired steel sheet microstructure can be obtained. The annealing temperature T₂ is preferably 900° C. or higher.

On the other hand, if the annealing temperature T₂ is above 1050° C., recrystallized grains grow excessively and the average grain size X₁ cannot be 200 μm or less. Therefore, the annealing temperature T₂ is set to 1050° C. or lower. The annealing temperature T₂ is preferably 1025° C. or lower.

In the annealing process, the cold-rolled sheet is heated to the above annealing temperature T₂ and then cooled. This cooling is preferably performed at a cooling rate of 50° C./s or less to prevent uneven cooling.

Examples

This disclosure will be described in detail below by way of examples However, this disclosure is not limited to them.

<Production of Cold-Rolled and Annealed Sheet (Non-Oriented Electrical Steel Sheet>

Molten steels having the chemical compositions listed in Table 1 were obtained by steelmaking using a commonly known method and continuously cast into slabs (steel materials) having a thickness of 230 mm.

The resulting slabs were hot rolled to obtain hot-rolled sheets with a thickness of 2.0 mm. The obtained hot-rolled steel sheets were subjected to hot-rolled sheet annealing and pickled by a publicly known technique, and then cold rolled to the sheet thickness listed in Table 2 to obtain cold-rolled steel sheets.

The resulting cold-rolled sheets were annealed under the conditions listed in Table 2 and then coated by a publicly known method to obtain cold-rolled and annealed sheets (non-oriented electrical steel sheets).

<Evaluation>

(Observation of Microstructure)

A test piece for microstructural observation was collected from each of the obtained cold-rolled and annealed sheets. The collected test piece was then thinned and mirrored by chemical polishing on its rolled surface (ND surface) so that the observation plane was at the position corresponding to ¼ of the sheet thickness. Electron backscatter diffraction (EBSD) measurements were performed on the mirrored observation plane to obtain local orientation data. The step size was 10 μm and the measurement area was 100 mm² or more. The size of the measurement area was adjusted appropriately so that the number of crystal grains was 5000 or more in the subsequent analysis. The entire area may be measured in a single scan, or the results of multiple scans may be combined using the Combo Scan function. The obtained local orientation data was analyzed using analytical software, OIM Analysis 8.

Prior to data analysis, grain-averaged data points were sorted using the analysis software, Partition Properties under the condition of Formula: GCI[&;5.000,2,0.000,0,0,0,8.0,1,1,1.0,0;]>0.1 to exclude unsuitable data points for the analysis. At this time, the valid data points were 98% or more.

For the above adjusted data, the crystal grain boundary was defined as follows: Grain Tolerance Angle: 5°, Minimum Grain Size: 2, Minimum Anti-Grain Size: 2, Multiple Rows Requirement and Anti-Grain Multiple Rows Requirement: both OFF, and the analysis was performed as described below.

Crystal grain information was output for preprocessed data using the Export Grain File function. Grain Size (Diameter in microns) of Grain File Type 2 was used as crystal grain size (X_i). The average grain size, standard deviation, and kurtosis were calculated for all obtained crystal grain information. The obtained average grain size, standard deviation and kurtosis are X₁, S₁, and K₁, respectively.

Average · grain · size ⁢ ⁢ X _ = 1 n ⁢ ∑ i = 1 n x i [ Math . 2 ] Standard · deviation ⁢ S = 1 n - 1 ⁢ ∑ i = 1 n ( x i - X _ ) 2 Kurtosis ⁢ K = n ⁡ ( n + 1 ) ( n - 1 ) ⁢ ( n - 2 ) ⁢ ( n - 3 ) ⁢ ∑ i = 1 n ( x i - X _ ) 4 S 4 - 3 ⁢ ( n - 1 ) 2 ( n - 2 ) ⁢ ( n - 3 )

where, n is the number of crystal grains and X_i is each crystal grain size data (i: 1, 2, . . . , n).

(Evaluation of Fatigue Strength Under Warm Conditions)

From each of the obtained cold-rolled and annealed sheets, a tensile fatigue test piece (having the same shape as No. 1 test piece in accordance with JIS Z2275:1978, b: 15 mm, R: 100 mm) was collected so that the rolling direction was the longitudinal direction and subjected to the fatigue test. Here, the end faces of the test piece were smoothed by machining. The fatigue test was conducted under the following conditions: test temperature: 100° C., pulsating tension loading, stress ratio (=minimum stress/maximum stress): 0.1, and frequency: 20 Hz. The maximum stress that did not cause fatigue fracture at 10⁷ repetitions was measured as fatigue limit under warm conditions. When the fatigue limit under warm conditions was 300 MPa or more, it was evaluated as having excellent fatigue strength under warm conditions.

(Evaluation of Magnetic Properties)

From each of the resulting annealed sheets, test pieces of 30 mm wide and 280 mm long were collected for magnetic property measurement so that the rolling direction and direction orthogonal to the rolling direction were the longitudinal direction, and the iron loss W_10/400 of the heat-treated sheet was measured by Epstein's method in accordance with JIS C2550-1:2011. The iron loss properties were evaluated as good when W_10/400≤15.0 (W/kg).

The results are listed in Table 3.

TABLE 1
Steel	Chemical Composition [mass %]

sample ID	C	Si	Mn	P	S	Al	N	Si + Al	Co	Cr	Ca	Mg	REM	Sn	Sb	Cu
A	0.0011	2.9	1.35	0.015	0.0017	1.0	0.0018	3.9	—	—	—	—	—	—	—	—
B	0.0016	3.3	0.31	0.007	0.0007	0.4	0.0020	3.7	—	—	—	—	—	—	—	—
C	0.0027	2.5	0.92	0.020	0.0039	1.4	0.0028	3.9	—	—	—	—	—	—	—	—
D	0.0011	3.3	0.24	0.005	0.0027	0.5	0.0016	3.8	—	—	—	—	—	—	—	—
E	0.0028	3.1	1.08	0.016	0.0005	0.4	0.0022	3.5	—	—	—	—	—	—	—	—
F	0.0015	3.2	2.78	0.017	0.0016	0.7	0.0027	3.9	—	—	—	—	—	—	—	—
G	0.0034	3.7	0.88	0.013	0.0027	0.5	0.0029	4.2	—	—	—	—	—	—	—	—
H	0.0029	2.1	0.33	0.017	0.0021	2.3	0.0025	4.4	—	—	—	—	—	—	—	—
I	0.0012	3.9	0.59	0.007	0.0005	0.5	0.0019	4.4	—	—	—	—	—	—	—	—
J	0.0008	2.6	0.38	0.006	0.0024	1.3	0.0018	3.9	—	—	—	—	—	—	—	—
K	0.0061	2.1	0.31	0.006	0.0006	0.4	0.0014	2.5	—	—	—	—	—	—	—	—
L	0.0008	1.3	0.39	0.007	0.0023	1.3	0.0017	2.6	—	—	—	—	—	—	—	—
M	0.0008	1.9	0.38	0.006	0.0022	1.3	0.0020	3.2	—	—	—	—	—	—	—	—
N	0.0008	4.3	0.37	0.006	0.0025	0.1	0.0022	4.4	—	—	—	—	—	—	—	—
O	0.0012	3.9	0.02	0.008	0.0005	0.5	0.0017	4.4	—	—	—	—	—	—	—	—
P	0.0013	3.9	0.09	0.008	0.0005	0.5	0.0016	4.4	—	—	—	—	—	—	—	—
Q	0.0010	3.9	3.60	0.007	0.0005	0.5	0.0015	4.4	—	—	—	—	—	—	—	—
R	0.0014	3.9	5.30	0.006	0.0004	0.5	0.0016	4.4	—	—	—	—	—	—	—	—
T	0.0024	2.1	0.34	0.014	0.0024	0.003	0.0020	2.1	—	—	—	—	—	—	—	—
U	0.0022	2.1	0.33	0.018	0.0019	0.014	0.0026	2.1	—	—	—	—	—	—	—	—
V	0.0024	2.1	0.33	0.019	0.0025	2.3	0.0024	4.4	—	—	—	—	—	—	—	—
W	0.0029	2.1	0.34	0.013	0.0022	3.1	0.0028	5.2	—	—	—	—	—	—	—	—
X	0.0012	3.3	0.25	0.005	0.0029	1.3	0.0018	4.6	—	—	—	—	—	—	—	—
Y	0.0026	3.1	1.13	0.020	0.0006	0.4	0.0023	3.5	0.0009	—	—	—	—	—	—	—
Z	0.0033	3.1	1.12	0.018	0.0006	0.4	0.0021	3.5	0.0046	—	—	—	—	—	—	—
AA	0.0033	3.2	1.13	0.013	0.0004	0.4	0.0022	3.6	—	0.3	—	—	—	—	—	—
AB	0.0021	3.1	1.11	0.019	0.0005	0.4	0.0019	3.5	—	—	0.004	—	—	—	—	—
AC	0.0029	3.1	1.10	0.014	0.0006	0.4	0.0021	3.5	—	—	—	0.003	—	—	—	—
AD	0.0030	3.0	1.04	0.019	0.0006	0.4	0.0025	3.4	—	—	—	—	0.012	—	—	—
AE	0.0033	3.1	1.06	0.013	0.0006	0.4	0.0019	3.5	—	—	—	—	—	0.05	—	—
AF	0.0026	3.2	1.09	0.019	0.0005	0.4	0.0023	3.6	—	—	—	—	—	—	0.03	—
AG	0.0021	3.1	1.13	0.014	0.0005	0.4	0.0023	3.5	0.0007	—	—	—	—	—	—	—
AH	0.0027	3.1	1.07	0.018	0.0004	0.4	0.0023	3.5	—	4.7	—	—	—	—	—	—
AI	0.0031	3.1	1.13	0.018	0.0005	0.4	0.0025	3.5	—	—	0.002	—	—	—	—	—
AJ	0.0024	3.1	1.06	0.017	0.0006	0.4	0.0017	3.5	—	—	—	0.089	—	—	—	—
AK	0.0034	3.2	1.06	0.013	0.0005	0.4	0.0018	3.6	—	—	—	—	0.080	—	—	—
AL	0.0030	3.2	1.05	0.014	0.0005	0.4	0.0018	3.6	—	—	—	—	—	0.19	—	—
AM	0.0022	3.2	1.04	0.012	0.0004	0.4	0.0018	3.6	—	—	—	—	—	—	0.16	—
AN	0.0011	3.3	0.23	0.006	0.0026	0.5	0.0015	3.8	—	—	—	—	—	—	—	0.04
AO	0.0012	3.4	0.24	0.004	0.0031	0.5	0.0014	3.9	—	—	—	—	—	—	—	0.46
AP	0.0010	3.3	0.25	0.005	0.0026	0.5	0.0015	3.8	—	—	—	—	—	—	—	—
AQ	0.0010	3.3	0.24	0.005	0.0021	0.5	0.0016	3.8	—	—	—	—	—	—	—	—
AR	0.0011	3.3	0.23	0.006	0.0024	0.5	0.0016	3.8	—	—	—	—	—	—	—	—
AS	0.0008	3.3	0.23	0.006	0.0033	0.5	0.0019	3.8	—	—	—	—	—	—	—	—
AT	0.0012	3.2	0.24	0.005	0.0023	0.5	0.0012	3.7	—	—	—	—	—	—	—	—
AU	0.0013	3.4	0.23	0.004	0.0031	0.5	0.0013	3.9	—	—	—	—	—	—	—	—
AV	0.0011	3.4	0.24	0.005	0.0032	0.5	0.0019	3.9	—	—	—	—	—	—	—	—
AW	0.0008	3.3	0.24	0.006	0.0020	0.5	0.0020	3.8	—	—	—	—	—	—	—	—
AX	0.0009	3.3	0.24	0.006	0.0021	0.5	0.0014	3.8	—	—	—	—	—	—	—	—
AY	0.0011	3.3	0.24	0.006	0.0021	0.5	0.0019	3.8	—	—	—	—	—	—	—	—
AZ	0.0012	3.2	0.23	0.005	0.0026	0.5	0.0014	3.7	—	—	—	—	—	—	—	—
BA	0.0011	3.3	0.23	0.004	0.0024	0.5	0.0016	3.8	—	—	—	—	—	—	—	—
BB	0.0009	3.3	0.25	0.004	0.0029	0.5	0.0019	3.8	—	—	—	—	—	—	—	—
BC	0.0011	3.2	0.25	0.005	0.0029	0.5	0.0018	3.7	—	—	—	—	—	—	—	—
BD	0.0009	3.4	0.25	0.005	0.0028	0.5	0.0014	3.9	—	—	—	—	—	—	—	—
BE	0.0010	3.4	0.25	0.004	0.0024	0.5	0.0013	3.9	—	—	—	—	—	—	—	—
BF	0.0011	3.3	0.23	0.006	0.0024	0.5	0.0017	3.8	—	—	—	—	—	—	—	—
BG	0.0009	3.2	0.25	0.005	0.0028	0.5	0.0016	3.7	—	—	—	—	—	—	—	—
BH	0.0013	3.2	0.25	0.006	0.0023	0.5	0.0016	3.7	—	—	—	—	—	—	—	—
BI	0.0013	3.4	0.24	0.005	0.0033	0.5	0.0016	3.9	—	—	—	—	—	—	—	—
BJ	0.0010	3.3	0.25	0.005	0.0030	0.5	0.0012	3.8	—	—	—	—	—	—	—	—
BK	0.0009	3.3	0.25	0.005	0.0025	0.5	0.0018	3.8	—	—	—	—	—	—	—	—
BL	0.0010	3.4	0.23	0.004	0.0027	0.5	0.0014	3.9	—	—	—	—	—	—	—	—
BM	0.0012	3.3	0.23	0.005	0.0025	0.5	0.0014	3.8	—	—	—	—	—	—	—	—
BN	0.0013	3.3	0.25	0.006	0.0026	0.5	0.0019	3.8	—	—	—	—	—	—	—	—
BO	0.0011	3.4	0.25	0.004	0.0026	0.5	0.0018	3.9	—	—	—	—	—	—	—	—

Steel

Chemical Composition [mass %]

sample ID	Ni	Ti	Nb	V	Ta	B	Ga	Pb	Zn	Mo	W	Ge	As	Remarks
A	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
B	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
C	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
D	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
E	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
F	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
G	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
H	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
I	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
J	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
K	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
L	—	—	—	—	—	—	—	—	—	—	—	—	—	Comp. Ex.
M	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
N	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
O	—	—	—	—	—	—	—	—	—	—	—	—	—	Comp. Ex.
P	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
Q	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
R	—	—	—	—	—	—	—	—	—	—	—	—	—	Comp. Ex.
T	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
U	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
V	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
W	—	—	—	—	—	—	—	—	—	—	—	—	—	Comp. Ex.
X	—	—	—	—	—	—	—	—	—	—	—	—	—	Comp. Ex.
Y	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
Z	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
AA	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
AB	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
AC	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
AD	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
AE	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
AF	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
AG	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
AH	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
AI	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
AJ	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
AK	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
AL	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
AM	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
AN	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
AO	—	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
AP	0.03	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
AQ	0.44	—	—	—	—	—	—	—	—	—	—	—	—	Ex.
AR	—	0.0011	—	—	—	—	—	—	—	—	—	—	—	Ex.
AS	—	0.0047	—	—	—	—	—	—	—	—	—	—	—	Ex.
AT	—	—	0.0010	—	—	—	—	—	—	—	—	—	—	Ex.
AU	—	—	0.0038	—	—	—	—	—	—	—	—	—	—	Ex.
AV	—	—	—	0.0013	—	—	—	—	—	—	—	—	—	Ex.
AW	—	—	—	0.0092	—	—	—	—	—	—	—	—	—	Ex.
AX	—	—	—	—	0.0004	—	—	—	—	—	—	—	—	Ex.
AY	—	—	—	—	0.0016	—	—	—	—	—	—	—	—	Ex.
AZ	—	—	—	—	—	0.0003	—	—	—	—	—	—	—	Ex.
BA	—	—	—	—	—	0.0022	—	—	—	—	—	—	—	Ex.
BB	—	—	—	—	—	—	0.0001	—	—	—	—	—	—	Ex
BC	—	—	—	—	—	—	0.0047	—	—	—	—	—	—	Ex.
BD	—	—	—	—	—	—	—	0.0001	—	—	—	—	—	Ex.
BE	—	—	—	—	—	—	—	0.0015	—	—	—	—	—	Ex.
BF	—	—	—	—	—	—	—	—	0.0006	—	—	—	—	Ex.
BG	—	—	—	—	—	—	—	—	0.0044	—	—	—	—	Ex
BH	—	—	—	—	—	—	—	—	—	0.010	—	—	—	Ex.
BI	—	—	—	—	—	—	—	—	—	0.048	—	—	—	Ex.
BJ	—	—	—	—	—	—	—	—	—	—	0.005	—	—	Ex.
BK	—	—	—	—	—	—	—	—	—	—	0.048	—	—	Ex.
BL	—	—	—	—	—	—	—	—	—	—	—	0.003	—	Ex.
BM	—	—	—	—	—	—	—	—	—	—	—	0.045	—	Ex.
BN	—	—	—	—	—	—	—	—	—	—	—	—	0.006	Ex.
BO	—	—	—	—	—	—	—	—	—	—	—	—	0.041	Ex.
Note:
Underlined if outside the scope of the disclosure.

	TABLE 2
	Cold rolling process

Final pass

Final pass

Final

Annealing process

			work roll	rolling	pass		Heating	Annealing
	Steel	Sheet	diameter	reduction	strain		rate	temperature
	sample	thickness	D	r	rate	Fracture during	V1	T2
No.	ID	[mm]	[mmφ]	[%]	[s−1]	rolling	[° C./s]	[° C.]	Remarks

1	A	0.25	230	31	460	—	68	920	Ex.
2	B	0.25	202	26	740	—	76	990	Ex.
3	C	0.25	237	31	500	—	95	930	Ex.
4	D	0.25	232	23	340	—	88	960	Ex.
5	E	0.25	223	27	730	—	88	990	Ex.
6	F	0.25	285	23	770	—	75	910	Ex.
7	G	0.25	206	25	810	—	71	950	Ex.
8	H	0.25	211	30	450	—	56	980	Ex.
9	I	0.25	258	24	680	—	104	1020	Ex.
10	J	0.25	220	29	1000	—	108	950	Ex.
11	K	0.25	201	26	740	—	76	990	Ex
12	L	0.25	221	29	1000	—	104	950	Comp. Ex.
13	M	0.25	221	29	1000	—	113	950	Ex.
14	N	0.25	220	29	1000	—	110	950	Ex.
15	O	0.25	254	24	680	—	107	1020	Comp. Ex.
16	P	0.25	253	24	680	—	102	1020	Ex.
17	Q	0.25	260	24	680	—	101	1020	Ex.
18	R	0.25	254	24	680	—	104	1020	Comp. Ex.
19	T	0.25	208	30	450	—	54	980	Ex.
20	U	0.25	210	30	450	—	57	980	Ex.
21	V	0.25	213	30	450	—	56	980	Ex.
22	W	0.25	210	30	450	—	57	980	Comp. Ex.
23	X	0.25	238	23	340	—	104	960	Comp. Ex.
24	Y	0.25	218	27	730	—	86	990	Ex.
25	Z	0.25	224	27	730	—	92	990	Ex.
26	AA	0.25	219	27	730	—	92	990	Ex.
27	AB	0.25	219	27	730	—	92	990	Ex.
28	AC	0.25	223	27	730	—	92	990	Ex.
29	AD	0.25	218	27	730	—	86	990	Ex.
30	AE	0.25	227	27	730	—	89	990	Ex.
31	AF	0.25	227	27	730	—	84	990	Ex.
32	A	0.25	135	31	460	—	67	920	Comp. Ex.
33	A	0.25	158	31	460	—	68	920	Ex.
34	A	0.25	169	31	460	—	70	920	Ex.
35	A	0.25	235	12	460	—	71	920	Comp. Ex.
36	A	0.25	234	17	460	—	70	920	Ex.
37	C	0.25	236	31	90	—	95	930	Comp. Ex.
38	C	0.25	235	31	120	—	96	930	Ex.
39	C	0.25	237	31	1090	partially fractured	97	930	Ex.
40	C	0.25	237	31	1360	wholly fractured	—	—	Comp. Ex.
41	C	0.25	234	31	500	—	9	930	Comp. Ex.
42	C	0.25	243	31	500	—	16	930	Ex.
43	C	0.25	242	31	500	—	39	930	Ex.
44	F	0.25	291	23	770	—	72	870	Comp. Ex.
45	F	0.25	283	23	770	—	77	890	Ex.
46	F	0.25	292	23	770	—	78	1030	Ex.
47	F	0.25	278	23	770	—	73	1060	Comp. Ex.
48	AG	0.25	221	27	730	—	84	990	Ex.
49	AH	0.25	221	27	730	—	92	990	Ex.
50	AI	0.25	227	27	730	—	85	990	Ex.
51	AJ	0.25	221	27	730	—	88	990	Ex.
52	AK	0.25	218	27	730	—	90	990	Ex.
53	AL	0.25	225	27	730	—	86	990	Ex.
54	AM	0.25	223	27	730	—	86	990	Ex.
55	AN	0.25	227	23	340	—	88	960	Ex.
56	AO	0.25	228	23	340	—	88	960	Ex.
57	AP	0.25	229	23	340	—	92	960	Ex.
58	AQ	0.25	238	23	340	—	85	960	Ex.
59	AR	0.25	232	23	340	—	85	960	Ex.
60	AS	0.25	233	23	340	—	85	960	Ex.
61	AT	0.25	227	23	340	—	87	960	Ex.
62	AU	0.25	228	23	340	—	88	960	Ex.
63	AV	0.25	238	23	340	—	87	960	Ex.
64	AW	0.25	237	23	340	—	84	960	Ex.
65	AX	0.25	232	23	340	—	88	960	Ex.
66	AY	0.25	235	23	340	—	92	960	Ex.
67	AZ	0.25	230	23	340	—	90	960	Ex.
68	BA	0.25	232	23	340	—	89	960	Ex.
69	BB	0.25	236	23	340	—	90	960	Ex.
70	BC	0.25	237	23	340	—	84	960	Ex.
71	BD	0.25	231	23	340	—	89	960	Ex.
72	BE	0.25	227	23	340	—	89	960	Ex.
73	BF	0.25	227	23	340	—	89	960	Ex.
74	BG	0.25	235	23	340	—	88	960	Ex.
75	BH	0.25	235	23	340	—	91	960	Ex.
76	BI	0.25	238	23	340	—	85	960	Ex.
77	BJ	0.25	227	23	340	—	90	960	Ex.
78	BK	0.25	232	23	340	—	87	960	Ex.
79	BL	0.25	233	23	340	—	88	960	Ex.
80	BM	0.25	227	23	340	—	91	960	Ex.
81	BN	0.25	235	23	340	—	85	960	Ex.
82	BO	0.25	226	23	340	—	89	960	Ex.
Note:
Underlined if outside the scope of the disclosure.

	TABLE 3
	Cold-rolled and annealed sheet
	(non-oriented electrical steel sheet)

				Kurtosis	Fatigue limit
				of crystal	under warm
	Average	Standard		grain size	conditions	Iron loss
	grain size	deviation		distribution	σmax	W10/400
No.	X1	S1	S1/X1	K1	(MPa)	(W/kg)	Remarks

1	75	41.3	0.55	0.16	440	12.7	Ex.
2	93	61.4	0.66	0.24	410	12.2	Ex.
3	94	63.0	0.67	0.36	400	11.1	Ex.
4	116	75.4	0.65	0.35	380	12.8	Ex.
5	92	48.8	0.53	0.55	410	13.1	Ex.
6	74	42.2	0.57	0.10	460	9.7	Ex.
7	109	73.0	0.67	0.05	400	10.9	Ex.
8	106	57.2	0.54	0.28	360	12.3	Ex.
9	148	79.9	0.54	0.29	360	10.5	Ex.
10	86	52.5	0.61	0.52	410	11.5	Ex.
11	113	78.0	0.69	0.24	340	14.6	Ex.
12	92	58.0	0.63	0.41	350	15.3	Comp. Ex.
13	103	62.8	0.61	0.46	360	14.3	Ex.
14	104	68.6	0.66	0.41	430	11.9	Ex.
15	121	65.3	0.54	0.26	390	15.9	Comp. Ex.
16	99	54.5	0.55	0.33	420	14.2	Ex.
17	97	53.4	0.55	0.26	430	13.5	Ex.
18	128	73.0	0.57	0.25	390	16.0	Comp. Ex.
19	89	50.7	0.57	0.34	370	14.9	Ex.
20	93	49.3	0.53	0.25	360	14.9	Ex.
21	100	57.0	0.57	0.31	380	14.2	Ex.
22	118	61.4	0.52	0.26	350	15.5	Comp. Ex.
23	97	63.1	0.65	2.16	270	15.9	Comp. Ex.
24	136	74.8	0.55	0.65	450	10.5	Ex.
25	87	42.6	0.49	0.54	460	11.7	Ex.
26	114	61.6	0.54	0.45	380	9.7	Ex.
27	90	45.0	0.50	0.50	410	10.9	Ex.
28	92	50.6	0.55	0.64	410	10.0	Ex.
29	109	57.8	0.53	0.49	380	10.1	Ex.
30	87	49.6	0.57	0.44	420	11.4	Ex.
31	131	69.4	0.53	0.45	360	11.2	Ex.
32	105	57.8	0.55	2.21	290	15.6	Comp. Ex.
33	68	37.4	0.55	1.67	300	14.1	Ex.
34	91	50.1	0.55	1.14	320	14.0	Ex.
35	83	65.6	0.79	2.08	280	15.6	Comp. Ex.
36	107	78.1	0.73	1.23	330	14.1	Ex.
37	105	67.2	0.64	2.15	280	15.6	Comp. Ex.
38	87	53.9	0.62	1.18	310	13.5	Ex.
39	85	53.6	0.63	0.34	460	12.0	Ex.
40	—	—	—	—	—	—	Comp. Ex.
41	90	72.9	0.81	0.28	290	16.0	Comp. Ex.
42	79	57.7	0.73	0.43	320	13.9	Ex.
43	114	80.9	0.71	0.40	340	13.4	Ex.
44	56	28.6	0.51	0.11	270	16.0	Comp. Ex.
45	72	38.2	0.53	0.09	320	13.8	Ex.
46	179	97.3	0.54	0.11	310	10.6	Ex.
47	207	114.5	0.55	0.08	280	12.4	Comp. Ex.
48	87	47.9	0.55	0.51	450	9.8	Ex.
49	90	45.0	0.50	0.53	410	9.8	Ex.
50	92	49.7	0.54	0.56	410	9.9	Ex.
51	97	52.4	0.54	0.58	420	9.9	Ex.
52	96	48.0	0.50	0.56	410	9.9	Ex.
53	85	47.6	0.56	0.50	400	9.9	Ex.
54	93	58.6	0.63	0.57	410	9.9	Ex.
55	118	79.1	0.67	0.34	380	13.0	Ex.
56	115	78.2	0.68	0.37	390	13.0	Ex.
57	120	78.0	0.65	0.33	370	13.0	Ex.
58	112	73.9	0.66	0.38	390	13.0	Ex.
59	97	64.0	0.66	0.34	430	12.5	Ex.
60	111	76.6	0.69	0.36	430	12.5	Ex.
61	104	69.7	0.67	0.38	440	12.5	Ex.
62	106	71.0	0.67	0.32	420	12.5	Ex.
63	97	66.0	0.68	0.39	440	12.5	Ex.
64	101	69.7	0.69	0.36	430	12.5	Ex.
65	104	70.7	0.68	0.35	430	12.5	Ex.
66	105	72.5	0.69	0.36	430	12.5	Ex.
67	105	63.0	0.60	0.39	440	12.5	Ex.
68	106	73.1	0.69	0.37	440	12.5	Ex.
69	99	67.3	0.68	0.38	440	12.5	Ex.
70	97	67.9	0.70	0.38	440	12.5	Ex.
71	101	64.6	0.64	0.33	420	12.5	Ex.
72	106	70.0	0.66	0.31	420	12.5	Ex.
73	115	69.0	0.60	0.33	380	12.5	Ex.
74	116	73.1	0.63	0.40	390	12.5	Ex.
75	110	69.3	0.63	0.36	430	12.5	Ex.
76	106	66.8	0.63	0.33	420	12.5	Ex.
77	105	69.3	0.66	0.32	420	12.5	Ex.
78	105	67.2	0.64	0.34	430	12.5	Ex.
79	117	76.1	0.65	0.31	370	10.2	Ex.
80	115	75.9	0.66	0.38	390	10.2	Ex.
81	121	82.3	0.68	0.39	390	10.2	Ex.
82	112	76.2	0.68	0.38	390	10.2	Ex
Note:
Underlined if outside the scope of the disclosure.

The results of 3 indicate that all of the non-oriented electrical steel sheets according to this disclosure have both excellent fatigue strength and excellent iron loss properties. The motor core obtained by combining a rotor core formed by stacking the cold-rolled and annealed sheets according to this disclosure and a stator core formed by stacking the heat-treated sheets according to this disclosure had excellent fatigue resistance.

Furthermore, when stress relief annealing was applied to the steel sheet for the purpose of restoring iron loss reduction due to strain during blanking, the effect of this disclosure was not affected in any way, and both excellent fatigue strength and excellent iron loss properties were achieved.