WO2009128428A1 - 高強度無方向性電磁鋼板及びその製造方法 - Google Patents
高強度無方向性電磁鋼板及びその製造方法 Download PDFInfo
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- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
- H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
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- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2201/00—Treatment for obtaining particular effects
- C21D2201/05—Grain orientation
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/004—Dispersions; Precipitations
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
- H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
- H01F1/147—Alloys characterised by their composition
Definitions
- the present invention relates to a high-strength non-oriented electrical steel sheet suitable for iron core materials for motors for electric vehicles and motors for electric devices, and a method for manufacturing the same.
- High-speed rotary motors are also used in electrical equipment such as machine tools and vacuum cleaners.
- the outer shape of the high-speed rotation motor for electric vehicles is larger than the outer shape of the high-speed rotation motor for electric devices.
- a DC brushless motor is mainly used as a high-speed rotation motor for an electric vehicle.
- a magnet is embedded in the vicinity of the outer periphery of the rotor.
- the width of the bridge portion on the outer peripheral portion of the rotor (the width from the outermost outer periphery of the rotor to the steel plate between the magnets) is very narrow as 1 to 2 mm depending on the place. For this reason, high-speed rotary motors for electric vehicles are required to have higher strength steel plates than conventional non-oriented electrical steel plates.
- Patent Document 1 describes a non-oriented electrical steel sheet in which Mn and Ni are added to Si to enhance solid solution.
- Mn and Ni are added to Si to enhance solid solution.
- the toughness tends to decrease with the addition of Mn and Ni, and sufficient productivity and yield cannot be obtained.
- the price of the added alloy is high. In particular, in recent years, the price of Ni has risend due to the global demand balance.
- Patent Documents 2 and 3 describe non-oriented electrical steel sheets that are strengthened by dispersing carbonitrides in steel. However, sufficient strength cannot be obtained even with these non-oriented electrical steel sheets.
- Patent Document 4 describes a non-oriented electrical steel sheet reinforced with Cu precipitates.
- the heat treatment conditions are restricted when manufacturing the non-oriented electrical steel sheet. For this reason, the required strength and magnetic properties cannot be obtained.
- An object of the present invention is to provide a high-strength non-oriented electrical steel sheet that can easily obtain high strength and magnetic characteristics and a method for producing the same.
- the present invention is summarized as follows in order to solve the above problems.
- a method for producing a strength non-oriented electrical steel sheet is 50 ° C./sec or more, and a ductile brittle fracture surface transition temperature in the Charpy impact test of the hot-rolled sheet is 70 ° C. or less.
- the present inventors investigated the reason why the strength and magnetic properties of the conventional steel strengthening method utilizing Cu precipitates are greatly influenced by the heat treatment conditions. As a result, it has been found that in order to strengthen the steel sheet by precipitation of Cu, a high annealing temperature at which Cu is once dissolved is required in finish annealing after cold rolling.
- the present inventors have further studied earnestly on a method for solving these problems while enjoying precipitation strengthening of Cu.
- a certain amount of C, N, Nb, Zr, Ti, and V it is possible to achieve both Cu precipitation strengthening and crystal grain refinement, and solve the above-mentioned problems. I found out that I can do it.
- the magnetic property required for the rotor which is the main application of the high-strength electrical steel sheet, is eddy current loss (We) at a high frequency of 400 Hz or higher, and C, N, Nb, Zr, Ti, And it has been found that refinement of crystal grains by containing V and V is effective.
- Example 1 In a laboratory vacuum melting furnace, by mass%, Si: 3.1%, Mn: 0.2%, Al: 0.5%, Cu: 2.0%, C, N, Nb, Steels with Zr, Ti and V mass% in Table 1 were prepared, heated at 1100 ° C. for 60 minutes, and then immediately hot-rolled to obtain hot-rolled sheets having a plate thickness of 2.0 mm. Thereafter, the hot-rolled sheet was pickled and a cold-rolled sheet having a thickness of 0.35 mm was obtained by one cold rolling. The cold-rolled sheet was subjected to a finish annealing at 800 ° C. to 1000 ° C. for 30 seconds. Table 2 shows the measurement results of various properties after finish annealing.
- Nb precipitates are dispersed and deposited moderately
- Ti precipitates are dispersed and deposited moderately, and crystal grain growth at 900 ° C. and 1000 ° C.
- Cu was once dissolved at the final annealing temperatures of 900 ° C. and 1000 ° C., and further precipitated finely during the cooling of the final annealing, so that the precipitation strengthening of Cu could be utilized to the maximum. As a result, it is presumed that high yield strength and elongation at break and low eddy current loss were obtained.
- Material E had high yield strength but low elongation at break. This is thought to be due to the adverse effect of excess C. In any of the conditions, recrystallization was not performed by finish annealing at 800 ° C. This is presumably because Cu that had been dissolved before annealing precipitated during annealing and delayed recrystallization.
- Example 2 In a laboratory vacuum melting furnace, by mass%, Si: 2.8%, Mn: 0.1%, Al: 1.0%, Cu: 1.8%, C, N, Nb, Steels with Zr, Ti, and V mass% in Table 3 were prepared, heated at 1150 ° C. for 60 minutes, and then immediately hot-rolled to obtain a hot-rolled sheet having a thickness of 2.2 mm. Thereafter, the hot-rolled sheet was pickled and a cold-rolled sheet having a thickness of 0.35 mm was obtained by one cold rolling. The cold-rolled sheet was subjected to a finish annealing at 800 ° C. to 1000 ° C. for 30 seconds. Table 4 shows the measurement results of various characteristics after finish annealing.
- Nb precipitates are moderately dispersed and precipitated.
- Ti precipitates are moderately dispersed and precipitated, and crystal grain growth at 900 ° C. and 1000 ° C. It is inferred that On the other hand, Cu was once dissolved at the final annealing temperatures of 900 ° C. and 1000 ° C., and further precipitated finely during the cooling of the final annealing, so that the precipitation strengthening of Cu could be utilized to the maximum. As a result, it is presumed that high yield strength and elongation at break and low eddy current loss were obtained.
- Material J had high yield strength but low elongation at break. This is thought to be due to the adverse effect of excess N. In any of the conditions, recrystallization was not performed by finish annealing at 800 ° C. This is thought to be because Cu, which had been dissolved before annealing, precipitated during annealing and delayed recrystallization.
- Finish annealing at 800 ° C. has so far been performed as a process for refining crystal grains. That is, this finish annealing has been carried out for the purpose of once dissolving Cu to increase the strength, recrystallizing the steel sheet, and preventing coarsening of the crystal grains.
- this finish annealing temperature was adjusted while adding Cu, it was difficult to obtain sufficient strength by itself. In other words, it is difficult to achieve both mechanical characteristics and magnetic characteristics with the conventional technology.
- both mechanical characteristics and magnetic characteristics can be achieved.
- C is an element necessary for crystal grain refinement. Fine carbides have the effect of increasing nucleation sites during recrystallization and further suppressing crystal grain growth. In order to enjoy the effect, the C content is 0.002% or more. In particular, when N is less than 0.005%, the preferable C content is 0.01% or more, more preferably 0.02% or more. On the other hand, if added over 0.05%, the elongation at break is significantly reduced. Therefore, the upper limit of the C content is 0.05%.
- Si is an element effective for reducing eddy current loss and also effective for solid solution strengthening.
- the upper limit of the Si content is 4.0%.
- the lower limit is made 2.0%.
- Mn is an element effective for lowering eddy current loss and increasing strength in the same manner as Si. However, even if the Mn content exceeds 1.0%, the effect is not improved and saturation occurs. Therefore, the upper limit of the Mn content is 1.0%. On the other hand, the lower limit is made 0.05% from the viewpoint of sulfide formation.
- Al is an element effective for increasing the specific resistance like Si.
- the upper limit of the Al content is set to 3.0%.
- the Al content in the case of Al deoxidation is 0.02% or more, and the Al content in the case of Si deoxidation is 0.01%. % Or more is preferable.
- N is an element necessary for crystal grain refinement. Fine nitride has the effect of increasing the number of nucleation sites during recrystallization and further suppressing crystal grain growth. In order to enjoy the effect, the N content is set to 0.002% or more. When N is contained more than the normal level by 0.005 or more, the effect of suppressing crystal grain growth becomes more remarkable. Since this effect is greater as the N content is higher, the N content is preferably further increased to 0.01% or more, and more preferably 0.02 or more. In particular, when the C content is less than 0.005%, the effect obtained by the addition of N is more pronounced. On the other hand, if added over 0.05%, the elongation at break is significantly reduced. Therefore, the upper limit of the N content is 0.05%.
- Cu is an important element that brings about precipitation strengthening. If it is less than 0.5%, it will dissolve completely in the steel and the effect of precipitation strengthening will not be obtained, so the lower limit of the Cu content is 0.5%. The upper limit is set to 3.0% considering that the strength is saturated.
- Ni is an effective element that can increase the strength of a steel sheet without making it too brittle. However, since it is expensive, it may be added according to the required strength. When adding, in order to fully obtain the effect, it is preferable to contain 0.5% or more. The upper limit is set to 3.0% in consideration of cost. Moreover, it is preferable to add 1/2 or more of Cu addition amount from a viewpoint of suppressing the beard wrinkle which generate
- Sn has the effect of improving the texture and suppressing nitriding and oxidation during annealing.
- the effect of improving the magnetic flux density that is lowered by the addition of Cu is great.
- the addition amount of Sn is preferably 0.01% or more and 0.10% or less.
- B segregates at the grain boundaries and has the effect of increasing the toughness of the hot-rolled sheet and hot-rolled annealed sheet.
- the addition amount of B is preferably 0.0010% or more and 0.0050% or less.
- Nb, Zr, Ti, and V have the effect of generating carbides or nitrides and suppressing the coarsening of the crystal grain size.
- [Nb] indicates the Nb content (% by mass)
- [Zr] indicates the Zr content (% by mass)
- [Ti] indicates the Ti content (% by mass)
- [V] indicates V Content (mass%). 2.0 ⁇ 10 ⁇ 4 ⁇ [Nb] / 93 + [Zr] / 91 + [Ti] / 48 + [V] / 51 (1)
- the value on the right side when the value on the right side is less than 2.0 ⁇ 10 ⁇ 4 , the precipitation amount is insufficient, and a sufficient crystal grain suppression effect cannot be obtained. Therefore, the lower limit of the value on the right side is 2.0 ⁇ 10 ⁇ 4 . On the other hand, since the excessive content of these elements is dissolved in steel and does not affect the properties of the steel, the upper limit is not particularly specified. However, considering the characteristics and cost, the value on the right side is preferably 1.0 ⁇ 10 ⁇ 2 or less.
- Formula (2) that defines the relationship among the six elements C, N, Nb, Zr, Ti, and V is an important parameter for miniaturizing crystal grains in combination with Formula (1).
- [C] indicates the C content (% by mass)
- [N] indicates the N content (% by mass).
- Formula (1) merely defines the maximum amount of carbide or nitride that can be generated, and the crystal growth of the final annealing cannot be sufficiently suppressed only by this condition.
- the second term of the formula (2) is obtained by subtracting the right side of the formula (1) from the sum of values obtained by dividing the mass% of C and N by the atomic weight, and an excessive amount of C that does not form carbonitrides. This is a parameter indicating the amount of N.
- This excess C and / or N is extremely important in making crystal grains fine. This is because when C and / or N is excessively contained, the carbonitride precipitates with an appropriate dispersion before the finish annealing, and the crystal grain growth during the annealing can be reliably suppressed.
- carbides, nitrides, and carbonitrides have a very important role.
- nitrides and carbonitrides are useful, and nitrides have a remarkable effect. That is, when carbide and nitride are compared, nitride is more effective for the effect of the present invention, and nitride contributes to the effect of the present invention in a smaller amount.
- nitride can provide a more favorable effect, and undesirable side effects can be suppressed.
- “preferable effect” means crystal grain refinement, increased strength, and stability at high temperatures, and “unfavorable side effects” include increased iron loss, cracks originating from precipitates ( In particular embrittlement).
- the present invention since the N content is appropriate in consideration of not only the contents of Nb, Zr, Ti, and V but also the balance with the content of C and the thermal history in the manufacturing process, the present invention Then, nitride is formed preferentially as compared with the conventional electromagnetic steel sheet. As a result, crystal grain growth at a high temperature is suppressed, and an increase in iron loss and embrittlement can be suppressed.
- the ratio of the N content to the C content is preferably high, and [N] / [C] is preferably 3 or more, and more preferably 5 or more.
- the composition of nitride is, for example, whether carbide is an initial formation, nitride is an initial formation, has a structure similar to carbide in the growth process, or is similar to nitride in the growth process. It is considered to change due to the effect of having a structure.
- the thermal stability of the carbonitride is weakened. For example, if the recrystallization is delayed immediately after the recrystallization of the finish annealing and the annealing temperature is further increased, the precipitates are re-dissolved, the crystal grains become coarse, and the formation of stable fine grains is difficult. Become. On the other hand, if C and / or N is excessive to a level where the parameter value exceeds 3.0 ⁇ 10 ⁇ 3 , quenching occurs during cooling, and the elongation and toughness of the steel sheet deteriorate.
- the lower limit of the parameter value in the equation (2) is 1.0 ⁇ 10 ⁇ 3 and the upper limit is 3.0 ⁇ 10 ⁇ 3 .
- the recrystallization area ratio of the high-strength non-oriented electrical steel sheet itself is less than 50%, the product characteristics, particularly the elongation at break, are significantly reduced. Therefore, the recrystallization area ratio is set to 50% or more.
- the yield stress in the tensile test is set to 700 MPa or more in consideration of the strength required for a rotor that rotates at high speed.
- the yield stress specified here is the lower yield point.
- the elongation at break is 10% or more from the viewpoint of suppressing cracks in the punched end face of the motor core.
- Eddy current loss is loss caused by current flowing through a steel plate during excitation. When this loss is large, the motor core easily generates heat and causes demagnetization of the magnet. Since the eddy current loss We 10/400 is highly dependent on the plate thickness of the steel plate, the plate thickness t (mm) is used as a parameter, and the allowable range of heat generation by the rotor is expressed as 70 ⁇ t as shown in Equation (3). 2 or less. We 10/400 ⁇ 70 ⁇ t 2 (3)
- the eddy current loss We 10/400 of W 10/400 is “(W 2 / f 2 ⁇ W 1 / f 1 ) / (f 2 ⁇ f 1 ) ⁇ 400 ⁇ 400 ”.
- the measurement frequency is not particularly specified. However, if possible, it is preferable to calculate at a frequency close to 400 Hz, for example, a frequency range of about 100 to 800 Hz.
- the maximum magnetic flux density Bmax is the maximum magnetic flux density that is excited when the iron loss is measured.
- the soaking temperature T (° C.) of finish annealing must be equal to or higher than the solid solution temperature of Cu. This solid solution temperature depends on the Cu content. Assuming that the Cu content is a (mass%), if the temperature is 200 ⁇ a + 500 or higher (° C.), Cu completely dissolves, so as shown in the equation (4), the soaking temperature of finish annealing T (° C.) is 200 ⁇ a + 500 or more. T ⁇ 200 ⁇ a + 500 (4)
- the coiling temperature during hot rolling exceeds 550 ° C., carbonitride and Cu precipitates remarkably reduce the toughness of some hot rolled sheets. Therefore, the coiling temperature during hot rolling is set to 550 ° C. or lower.
- the toughness of the hot-rolled sheet the ductile brittle fracture surface transition temperature in the Charpy impact test is set to 70 ° C. or less from the viewpoint of suppressing fracture during cold rolling.
- the cooling rate in this temperature range is set to 50 ° C./sec or more.
- the toughness of the steel sheet after annealing is set to 70 ° C. or less from the viewpoint of suppressing fracture during cold rolling.
- the annealing temperature of the hot-rolled sheet is not particularly specified, but 900 ° C. or higher is preferable because the purpose of annealing the hot-rolled sheet is to recrystallize the hot-rolled sheet and promote grain growth. On the other hand, from a brittle viewpoint, 1100 degrees C or less is preferable.
- the transition temperature defined here is a temperature at which the ductile fracture surface ratio is 50% in the transition curve showing the relationship between the test temperature and the ductile fracture surface ratio, as defined in Japanese Industrial Standards (JIS). You may employ
- the length and height of the specimen used for the Charpy impact test shall be the size specified in JIS.
- the width of the test piece is the thickness of the hot rolled plate. Accordingly, the size is 55 mm in length in the rolling direction, the height is 10 mm, and the width is about 1.5 mm to 3.0 mm depending on the thickness of the hot rolled sheet. Further, in the test, it is preferable to stack a plurality of test pieces and bring them closer to a thickness of 10 mm which is a normal test condition.
- Example 1 In a vacuum melting furnace, by mass%, Si: 2.9%, Mn: 0.2%, Al: 0.7%, and Cu: 1.5%, C, N, Nb, Zr, Steels having different mass percentages of Ti and V were prepared, heated at 1150 ° C. for 60 minutes, and then immediately hot-rolled to obtain a hot-rolled plate having a plate thickness of 2.3 mm. Thereafter, the hot-rolled sheet was pickled and a cold-rolled sheet having a thickness of 0.5 mm was obtained by one cold rolling. This cold-rolled sheet was subjected to finish annealing at 900 ° C. for 60 seconds. Table 5 shows the measurement results of the components and various characteristics.
- Example 2 In a vacuum melting furnace, by mass%, Si: 3.7%, Mn: 0.1%, Al: 0.2%, and Cu: 1.4%, C, N, Nb, Zr, Steels having different mass percentages of Ti and V were prepared, heated at 1150 ° C. for 60 minutes, and then immediately hot-rolled to obtain a hot-rolled plate having a plate thickness of 2.3 mm. Thereafter, the hot-rolled sheet was pickled and a cold-rolled sheet having a thickness of 0.5 mm was obtained by one cold rolling. This cold-rolled sheet was subjected to finish annealing at 900 ° C. for 60 seconds. Table 6 shows the measurement results of the components and various characteristics.
- Example 3 In a vacuum melting furnace, in mass%, C: 0.022%, Mn: 0.5%, Al: 2.0%, N: 0.003%, Ni: 1.0%, Nb: 0.031 %, Zr: 0.004%, Ti: 0.003%, and V: 0.004%, a steel with varying amounts of Si and Cu was prepared and heated at 1120 ° C for 120 minutes, Immediately hot-rolled, a hot-rolled sheet having a thickness of 2.0 mm was obtained. Thereafter, the hot-rolled sheet was pickled and a cold-rolled sheet having a thickness of 0.25 mm was obtained by one cold rolling. The cold-rolled sheet was subjected to a finish annealing at 1000 ° C. for 45 seconds. Table 7 shows the measurement results of the Si amount, the Cu amount, and various characteristics.
- the samples with Cu less than 0.5% have low yield stress, and are defined by the present invention. It was out of range. Further, the samples with Ni / Cu of 0.5 or more (reference numerals c1 to c4, c6 to c9, c11 to c14, c16 to c19, and c21 to c24) did not show baldness.
- Example 4 In a vacuum melting furnace, in mass%, C: 0.003%, Si: 3.3%, Mn: 0.2%, Al: 0.7%, N: 0.022%, Ni: 1.5 %, Nb: 0.032%, Zr: 0.004%, Ti: 0.003%, and V: 0.003%, and a steel in which the B content and the Sn content were changed was produced at 1110 ° C. Was heated for 80 minutes and then immediately hot rolled to obtain a hot rolled plate having a thickness of 2.7 mm. The coiling temperature in this hot rolling was 530 ° C. Thereafter, this hot rolled sheet is subjected to annealing (intermediate annealing) at 1050 ° C.
- annealing intermediate annealing
- the transition temperature of the hot-rolled annealed sheet was low when the amount of B was 0.0010% or more and d6 to d25.
- a high magnetic flux density was obtained with the codes d2 to d5, d7 to d10, d12 to d15, d17 to d20, and d22 to d25 having an Sn content of 0.010% or more. It should be noted that slab cracking occurred in the signs d21 to d25 where the B amount exceeded 0.0050%, and baldness occurred in d5, d10, d15, d20, and d25 where the Sn amount exceeded 0.010%. .
- Example 5 In a vacuum melting furnace, in mass%, C: 0.028%, Si: 2.9%, Mn: 0.8%, Al: 1.4%, N: 0.012%, Ni: 1.4 %, Nb: 0.003%, Zr: 0.04%, Ti: 0.003%, and V: 0.003%, and steel with varying amounts of Cu was prepared, and 90 minutes at 1120 ° C. After heating, it was immediately hot rolled to obtain a hot hot rolled sheet having a thickness of 2.0 mm. Thereafter, this hot-rolled sheet is subjected to hot-rolled sheet annealing at 950 ° C. for 60 seconds, further pickled, and a cold-rolled sheet having a thickness of 0.35 mm is obtained by one cold rolling. It was. This cold-rolled sheet was subjected to finish annealing while changing the soaking temperature. Table 9 shows the results of the amount of Cu, the temperature of finish annealing, and various characteristics.
- the recrystallization area ratio is less than 50% and / or the elongation at break is less than 10%. It was outside the range defined by the invention.
- Example 6 In a vacuum melting furnace, in mass%, C: 0.027%, Si: 3.6%, Mn: 0.1%, Al: 1.8%, N: 0.005%, Ni: 2.0 %, Nb: 0.003%, Zr: 0.004%, Ti: 0.03%, and V: 0.01%. These steel slabs were heated at 1170 ° C. for 90 minutes and immediately hot rolled to obtain hot rolled sheets having a plate thickness of 2.5 mm. During the production of this hot-rolled sheet, the winding temperature was changed. Furthermore, the produced hot rolled sheet was annealed at 1000 ° C. for 60 seconds to obtain an annealed sheet. During this annealing, the cooling rate from 900 ° C. to 500 ° C. was changed. Charpy test pieces were produced from these hot-rolled plates and annealed plates, and the transition temperature was measured by an impact test. The results are shown in Table 10.
- a non-oriented electrical steel sheet having excellent strength can be provided at a low cost without sacrificing the yield and productivity in manufacturing the motor core and the steel sheet.
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Abstract
Description
C:0.002%以上0.05%以下、
Si:2.0%以上4.0%以下、
Mn:0.05%以上1.0%以下、
N:0.002%以上0.05%以下、及び
Cu:0.5%以上3.0%以下を含有し、
Alの含有量が3.0%以下であり、
Nbの含有量(%)を[Nb]、Zrの含有量(%)を[Zr]、Tiの含有量(%)を[Ti]、Vの含有量(%)を[V]、Cの含有量(%)を[C]、Nの含有量(%)を[N]としたとき、式(1)及び式(2)が満たされ、
残部がFe及び不可避的不純物からなり、
再結晶面積率が50%以上であり、
引張試験の降伏応力が700MPa以上であり、
破断伸びが10%以上であり、
渦電流損We10/400(W/kg)が鋼板の板厚t(mm)との関係において、式(3)を満足することを特徴とする高強度無方向性電磁鋼板。
2.0×10-4≦[Nb]/93+[Zr]/91+[Ti]/48+[V]/51 ・・・(1)
1.0×10-3≦[C]/12+[N]/14-([Nb]/93+[Zr]/91+[Ti]/48+[V]/51)≦3.0×10-3 ・・・(2)
We10/400≦70×t2 ・・・(3)
C:0.002%以上0.05%以下、
Si:2.0%以上4.0%以下、
Mn:0.05%以上1.0%以下、
N:0.002%以上0.05%以下、及び
Cu:0.5%以上3.0%以下を含有し、
Alの含有量が3.0%以下であり、
Nbの含有量(%)を[Nb]、Zrの含有量(%)を[Zr]、Tiの含有量(%)を[Ti]、Vの含有量(%)を[V]、Cの含有量(%)を[C]、Nの含有量(%)を[N]としたとき、式(1)及び式(2)が満たされ、
残部がFe及び不可避的不純物からなるスラブを作製する工程と、
前記鋼の熱間圧延を行うことにより、熱間圧延板を得る工程と、
前記熱延圧延板の酸洗を行う工程と、
次に、前記熱延圧延板の冷間圧延を行うことにより、冷間圧延板を得る工程と、
前記冷間圧延板の仕上焼鈍を行う工程と、
を有し、
前記仕上焼鈍の均熱温度T(℃)と前記冷間圧延板のCu含有量a(質量%)が式(4)を満たすことを特徴とする高強度無方向性電磁鋼板の製造方法。
T≧200×a+500 ・・・(4)
C:0.002%以上0.05%以下、
Si:2.0%以上4.0%以下、
Mn:0.05%以上1.0%以下、
N:0.002%以上0.05%以下、及び
Cu:0.5%以上3.0%以下を含有し、
Alの含有量が3.0%以下であり、
Nbの含有量(%)を[Nb]、Zrの含有量(%)を[Zr]、Tiの含有量(%)を[Ti]、Vの含有量(%)を[V]、Cの含有量(%)を[C]、Nの含有量(%)を[N]としたとき、式(1)及び式(2)が満たされ、
残部がFe及び不可避的不純物からなるスラブを作製する工程と、
前記鋼の熱間圧延を行うことにより、熱間圧延板を得る工程と、
次に、前記熱延圧延板の酸洗を行う工程と、
次に、前記熱延圧延板の冷間圧延を行うことにより、冷間圧延板を得る工程と、
前記冷間圧延板の仕上焼鈍を行う工程と、
を有し、
前記熱間圧延の巻取温度が550℃以下で、かつ、前記熱間圧延板のシャルピー衝撃試験における延性脆性破面遷移温度が70℃以下であることを特徴とする高強度無方向性電磁鋼板の製造方法。
2.0×10-4≦[Nb]/93+[Zr]/91+[Ti]/48
C:0.002%以上0.05%以下、
Si:2.0%以上4.0%以下、
Mn:0.05%以上1.0%以下、
N:0.002%以上0.05%以下、及び
Cu:0.5%以上3.0%以下を含有し、
Alの含有量が3.0%以下であり、
Nbの含有量(%)を[Nb]、Zrの含有量(%)を[Zr]、Tiの含有量(%)を[Ti]、Vの含有量(%)を[V]、Cの含有量(%)を[C]、Nの含有量(%)を[N]としたとき、式(1)及び式(2)が満たされ、
残部がFe及び不可避的不純物からなるスラブを作製する工程と、
前記鋼の熱間圧延を行うことにより、熱間圧延板を得る工程と、
次に、前記熱延圧延板の焼鈍を行う工程と、
次に、前記熱延圧延板の酸洗を行う工程と、
次に、前記熱延圧延板の冷間圧延を行うことにより、冷間圧延板を得る工程と、
前記冷間圧延板の仕上焼鈍を行う工程と、
を有し、
前記焼鈍の900℃から500℃までの冷却速度が50℃/sec以上で、かつ、前記熱間圧延板のシャルピー衝撃試験における延性脆性破面遷移温度が70℃以下であることを特徴とする高強度無方向性電磁鋼板の製造方法。
実験室の真空溶解炉にて、質量%で、Si:3.1%、Mn:0.2%,Al:0.5%、Cu:2.0%を含有し、C、N、Nb、Zr、Ti、及びVの質量%が表1の鋼を作製し、1100℃で60分加熱した後、直ちに熱間圧延して、板厚が2.0mmの熱間圧延板を得た。その後、この熱間圧延板に酸洗を施し、一回の冷間圧延にて、板厚が0.35mmの冷間圧延板を得た。この冷間圧延板に対し、800℃~1000℃で30秒の仕上焼鈍を施した。表2に、仕上焼鈍後の諸特性の測定結果を示す。
実験室の真空溶解炉にて、質量%で、Si:2.8%、Mn:0.1%、Al:1.0%、Cu:1.8%を含有し、C、N、Nb、Zr、Ti、及びVの質量%が表3の鋼を作製し、1150℃で60分加熱した後、直ちに熱間圧延して、板厚が2.2mmの熱間圧延板を得た。その後、この熱間圧延板に酸洗を施し、一回の冷間圧延にて、板厚が0.35mmの冷間圧延板を得た。この冷間圧延板に対し、800℃~1000℃で30秒の仕上焼鈍を施した。表4に、仕上焼鈍後の諸特性の測定結果を示す。
2.0×10-4≦[Nb]/93+[Zr]/91+[Ti]/48+[V]/51 ・・・(1)
1.0×10-3≦[C]/12+[N]/14-([Nb]/93+[Zr]/91+[Ti]/48+[V]/51)≦3.0×10-3 ・・・(2)
We10/400≦70×t2 ・・・(3)
T≧200×a+500 ・・・(4)
真空溶解炉にて、質量%で、Si:2.9%、Mn:0.2%、Al:0.7%、及びCu:1.5%を含有し、C、N、Nb、Zr、Ti、及びVの質量%が異なる鋼を作製し、1150℃で60分加熱した後、直ちに熱間圧延して、板厚が2.3mmの熱間圧延板を得た。その後、この熱間圧延板に酸洗を施し、一回の冷間圧延にて、板厚が0.5mmの冷間圧延板を得た。この冷間圧延板に、900℃で60秒の仕上焼鈍を施した。表5に、成分と諸特性の測定結果を示す。
真空溶解炉にて、質量%で、Si:3.7%、Mn:0.1%、Al:0.2%、及びCu:1.4%を含有し、C、N、Nb、Zr、Ti、及びVの質量%が異なる鋼を作製し、1150℃で60分加熱した後、直ちに熱間圧延して、板厚が2.3mmの熱間圧延板を得た。その後、この熱間圧延板に酸洗を施し、一回の冷間圧延にて、板厚が0.5mmの冷間圧延板を得た。この冷間圧延板に、900℃で60秒の仕上焼鈍を施した。表6に、成分と諸特性の測定結果を示す。
真空溶解炉にて、質量%で、C:0.022%、Mn:0.5%、Al:2.0%、N:0.003%、Ni:1.0%、Nb:0.031%、Zr:0.004%、Ti:0.003%、及びV:0.004%を含有し、Si量とCu量を変化させた鋼を作製し、1120℃で120分加熱した後、直ちに熱間圧延して、板厚が2.0mmの熱間圧延板を得た。その後、この熱間圧延板に酸洗を施し、一回の冷間圧延にて、板厚が0.25mmの冷間圧延板を得た。この冷間圧延板に、1000℃で45秒の仕上焼鈍を施した。表7に、Si量、Cu量、及び諸特性の測定結果を示す。
真空溶解炉にて、質量%で、C:0.003%、Si:3.3%、Mn:0.2%、Al:0.7%、N:0.022%、Ni:1.5%、Nb:0.032%、Zr:0.004%、Ti:0.003%、及びV:0.003%を含有し、B量及びSn量を変化させた鋼を作製し、1110℃で80分加熱した後、直ちに熱間圧延して、板厚が2.7mmの熱間圧延板を得た。この熱間圧延における巻取温度は530℃とした。その後、この熱間圧延板に、1050℃で60秒の焼鈍(中間焼鈍)を施し、更に酸洗を施し、一回の冷間圧延にて、板厚が0.35mmの冷間圧延板を得た。この冷間圧延板に、950℃で60秒の仕上焼鈍を施した。表8に、B量、Sn量、中間焼鈍後の遷移温度、及び仕上焼鈍後の磁束密度を示す。
真空溶解炉にて、質量%で、C:0.028%、Si:2.9%、Mn:0.8%、Al:1.4%、N:0.012%、Ni:1.4%、Nb:0.003%、Zr:0.04%、Ti:0.003%、及びV:0.003%を含有し、Cu量を変化させた鋼を作製し、1120℃で90分加熱した後、直ちに熱間圧延して、板厚が2.0mmの熱間熱延板を得た。その後、この熱間圧延板に、950℃で60秒の熱延板焼鈍を施し、更に酸洗を施し、一回の冷間圧延にて、板厚が0.35mmの冷間圧延板を得た。この冷間圧延板に、均熱温度を変化させて、仕上焼鈍を施した。表9に、Cu量、仕上焼鈍の温度及び諸特性の結果を示す。
真空溶解炉にて、質量%で、C:0.027%、Si:3.6%、Mn:0.1%、Al:1.8%、N:0.005%、Ni:2.0%、Nb:0.003%、Zr:0.004%、Ti:0.03%、及びV:0.01%を含有する複数の鋼片を作製した。これらの鋼片を、1170℃で90分加熱した後、直ちに熱間圧延して、板厚が2.5mmの熱間圧延板を得た。この熱間圧延板の作製に際し、巻取温度を変化させた。更に、作製した熱間圧延板に、1000℃で60秒の焼鈍を施して、焼鈍板を得た。この焼鈍に際し、900℃から500℃までの冷却速度を変化させた。これらの熱間圧延板及び焼鈍板から、シャルピー試験片を製作し、衝撃試験によって、遷移温度を測定した。この結果を表10に示す。
Claims (12)
- 質量%で、
C:0.002%以上0.05%以下、
Si:2.0%以上4.0%以下、
Mn:0.05%以上1.0%以下、
N:0.002%以上0.05%以下、及び
Cu:0.5%以上3.0%以下を含有し、
Alの含有量が3.0%以下であり、
Nbの含有量(%)を[Nb]、Zrの含有量(%)を[Zr]、Tiの含有量(%)を[Ti]、Vの含有量(%)を[V]、Cの含有量(%)を[C]、Nの含有量(%)を[N]としたとき、式(1)及び式(2)が満たされ、
残部がFe及び不可避的不純物からなり、
再結晶面積率が50%以上であり、
引張試験の降伏応力が700MPa以上であり、
破断伸びが10%以上であり、
渦電流損We10/400(W/kg)が鋼板の板厚t(mm)との関係において、式(3)を満足することを特徴とする高強度無方向性電磁鋼板。
2.0×10-4≦[Nb]/93+[Zr]/91+[Ti]/48+[V]/51 ・・・(1)
1.0×10-3≦[C]/12+[N]/14-([Nb]/93+[Zr]/91+[Ti]/48+[V]/51)≦3.0×10-3 ・・・(2)
We10/400≦70×t2 ・・・(3) - さらに、質量%で、Ni:0.5%以上3.0%以下を含有することを特徴とする請求項1に記載の高強度無方向性電磁鋼板。
- さらに、質量%で、Sn:0.01%以上0.10%以下を含有することを特徴とする請求項1に記載の高強度無方向性電磁鋼板。
- さらに、質量%で、Sn:0.01%以上0.10%以下を含有することを特徴とする請求項2に記載の高強度無方向性電磁鋼板。
- さらに、質量%で、B:0.0010%以上0.0050%以下を含有することを特徴とする請求項1に記載の高強度無方向性電磁鋼板。
- さらに、質量%で、B:0.0010%以上0.0050%以下を含有することを特徴とする請求項2に記載の高強度無方向性電磁鋼板。
- さらに、質量%で、B:0.0010%以上0.0050%以下を含有することを特徴とする請求項3に記載の高強度無方向性電磁鋼板。
- さらに、質量%で、B:0.0010%以上0.0050%以下を含有することを特徴とする請求項4に記載の高強度無方向性電磁鋼板。
- 質量%で、
C:0.002%以上0.05%以下、
Si:2.0%以上4.0%以下、
Mn:0.05%以上1.0%以下、
N:0.002%以上0.05%以下、及び
Cu:0.5%以上3.0%以下を含有し、
Alの含有量が3.0%以下であり、
Nbの含有量(%)を[Nb]、Zrの含有量(%)を[Zr]、Tiの含有量(%)を[Ti]、Vの含有量(%)を[V]、Cの含有量(%)を[C]、Nの含有量(%)を[N]としたとき、式(1)及び式(2)が満たされ、
残部がFe及び不可避的不純物からなるスラブを作製する工程と、
前記鋼の熱間圧延を行うことにより、熱間圧延板を得る工程と、
前記熱延圧延板の酸洗を行う工程と、
次に、前記熱延圧延板の冷間圧延を行うことにより、冷間圧延板を得る工程と、
前記冷間圧延板の仕上焼鈍を行う工程と、
を有し、
前記仕上焼鈍の均熱温度T(℃)と前記冷間圧延板のCu含有量a(質量%)が式(4)を満たすことを特徴とする高強度無方向性電磁鋼板の製造方法。
2.0×10-4≦[Nb]/93+[Zr]/91+[Ti]/48+[V]/51 ・・・(1)
1.0×10-3≦[C]/12+[N]/14-([Nb]/93+[Zr]/91+[Ti]/48+[V]/51)≦3.0×10-3 ・・・(2)
T≧200×a+500 ・・・(4) - 前記熱間圧延板を得る工程と前記酸洗を行う工程との間に、前記熱間圧延板の焼鈍を行う工程を有することを特徴とする請求項9に記載の高強度無方向性電磁鋼板の製造方法。
- 質量%で、
C:0.002%以上0.05%以下、
Si:2.0%以上4.0%以下、
Mn:0.05%以上1.0%以下、
N:0.002%以上0.05%以下、及び
Cu:0.5%以上3.0%以下を含有し、
Alの含有量が3.0%以下であり、
Nbの含有量(%)を[Nb]、Zrの含有量(%)を[Zr]、Tiの含有量(%)を[Ti]、Vの含有量(%)を[V]、Cの含有量(%)を[C]、Nの含有量(%)を[N]としたとき、式(1)及び式(2)が満たされ、
残部がFe及び不可避的不純物からなるスラブを作製する工程と、
前記鋼の熱間圧延を行うことにより、熱間圧延板を得る工程と、
次に、前記熱延圧延板の酸洗を行う工程と、
次に、前記熱延圧延板の冷間圧延を行うことにより、冷間圧延板を得る工程と、
前記冷間圧延板の仕上焼鈍を行う工程と、
を有し、
前記熱間圧延の巻取温度が550℃以下で、かつ、前記熱間圧延板のシャルピー衝撃試験における延性脆性破面遷移温度が70℃以下であることを特徴とする高強度無方向性電磁鋼板の製造方法。
2.0×10-4≦[Nb]/93+[Zr]/91+[Ti]/48+[V]/51 ・・・(1)
1.0×10-3≦[C]/12+[N]/14-([Nb]/93+[Zr]/91+[Ti]/48+[V]/51)≦3.0×10-3 ・・・(2) - 質量%で、
C:0.002%以上0.05%以下、
Si:2.0%以上4.0%以下、
Mn:0.05%以上1.0%以下、
N:0.002%以上0.05%以下、及び
Cu:0.5%以上3.0%以下を含有し、
Alの含有量が3.0%以下であり、
Nbの含有量(%)を[Nb]、Zrの含有量(%)を[Zr]、Tiの含有量(%)を[Ti]、Vの含有量(%)を[V]、Cの含有量(%)を[C]、Nの含有量(%)を[N]としたとき、式(1)及び式(2)が満たされ、
残部がFe及び不可避的不純物からなるスラブを作製する工程と、
前記鋼の熱間圧延を行うことにより、熱間圧延板を得る工程と、
次に、前記熱延圧延板の焼鈍を行う工程と、
次に、前記熱延圧延板の酸洗を行う工程と、
次に、前記熱延圧延板の冷間圧延を行うことにより、冷間圧延板を得る工程と、
前記冷間圧延板の仕上焼鈍を行う工程と、
を有し、
前記焼鈍の900℃から500℃までの冷却速度が50℃/sec以上で、かつ、前記熱間圧延板のシャルピー衝撃試験における延性脆性破面遷移温度が70℃以下であることを特徴とする高強度無方向性電磁鋼板の製造方法。
2.0×10-4≦[Nb]/93+[Zr]/91+[Ti]/48+[V]/51 ・・・(1)
1.0×10-3≦[C]/12+[N]/14-([Nb]/93+[Zr]/91+[Ti]/48+[V]/51)≦3.0×10-3 ・・・(2)
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CN2009801130902A CN102007226B (zh) | 2008-04-14 | 2009-04-13 | 高强度无方向性电磁钢板及其制造方法 |
JP2010508206A JP4659135B2 (ja) | 2008-04-14 | 2009-04-13 | 無方向性電磁鋼板及びその製造方法 |
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WO2012055223A1 (zh) | 2010-10-25 | 2012-05-03 | 宝山钢铁股份有限公司 | 一种较高磁感的高强度无取向电工钢及其制造方法 |
WO2013024894A1 (ja) | 2011-08-18 | 2013-02-21 | 新日鐵住金株式会社 | 無方向性電磁鋼板、その製造方法、モータ鉄心用積層体及びその製造方法 |
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JP2014503685A (ja) * | 2010-12-23 | 2014-02-13 | ポスコ | 低鉄損高強度無方向性電気鋼板およびその製造方法 |
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CN114657461B (zh) * | 2022-02-25 | 2023-08-08 | 东北大学 | 一种基于固溶强化的高强度无取向硅钢及其制备方法 |
Also Published As
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EP2278034A4 (en) | 2017-01-25 |
EP2278034B1 (en) | 2020-02-12 |
CN102007226A (zh) | 2011-04-06 |
JPWO2009128428A1 (ja) | 2011-08-04 |
JP4659135B2 (ja) | 2011-03-30 |
CN102007226B (zh) | 2013-11-06 |
TWI404806B (zh) | 2013-08-11 |
BRPI0910984B8 (pt) | 2018-09-25 |
TW200946695A (en) | 2009-11-16 |
BRPI0910984B1 (pt) | 2018-06-05 |
KR20100122116A (ko) | 2010-11-19 |
PL2278034T3 (pl) | 2020-06-29 |
EP2278034A1 (en) | 2011-01-26 |
BRPI0910984A2 (pt) | 2016-01-05 |
US20110056592A1 (en) | 2011-03-10 |
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