WO2011065023A1 - Low-carbon steel sheet and process for producing same - Google Patents
Low-carbon steel sheet and process for producing same Download PDFInfo
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- WO2011065023A1 WO2011065023A1 PCT/JP2010/006958 JP2010006958W WO2011065023A1 WO 2011065023 A1 WO2011065023 A1 WO 2011065023A1 JP 2010006958 W JP2010006958 W JP 2010006958W WO 2011065023 A1 WO2011065023 A1 WO 2011065023A1
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C10/00—Solid state diffusion of only metal elements or silicon into metallic material surfaces
- C23C10/06—Solid state diffusion of only metal elements or silicon into metallic material surfaces using gases
- C23C10/08—Solid state diffusion of only metal elements or silicon into metallic material surfaces using gases only one element being diffused
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
- C21D8/1255—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest with diffusion of elements, e.g. decarburising, nitriding
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
- C21D8/1272—Final recrystallisation annealing
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
- H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
- H01F1/16—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys in the form of sheets
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- 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
- 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
- C21D2211/005—Ferrite
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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
- C21D2251/00—Treating composite or clad material
- C21D2251/02—Clad material
Definitions
- the present invention relates to a low-carbon steel sheet suitable as a high-frequency transformer, a reactor, and a motor core for power electronics, and particularly aims to improve high-frequency characteristics and reduce iron loss deterioration due to external stress.
- the iron loss of an electrical steel sheet is composed of a hysteresis loss that strongly depends on precipitates in the steel, crystal grain size, texture, and the like, and an eddy current loss that strongly depends on the plate thickness, specific resistance, magnetic domain structure, and the like.
- a general electromagnetic steel sheet increases crystal grain growth by reducing impurities in the steel as much as possible, thereby reducing hysteresis loss.
- eddy current loss is reduced by adding 0.5 to 3.5% by mass of Si to increase the specific resistance or to reduce the plate thickness.
- the ratio of the hysteresis loss to the iron loss of the electrical steel sheet is large at the commercial frequency (50/60 Hz).
- the frequency becomes several kHz or higher, the ratio of eddy current loss increases.
- high frequency switching elements have been developed in the field of power electronics, and it has been strongly desired to reduce high-frequency iron loss even for electrical steel sheets used as iron core materials for transformers, reactors, motors, etc. It was.
- Patent Document 1 describes a Si enrichment method for a steel sheet surface by a siliconization method.
- This Si enrichment technology for example, as described in Patent Document 2, reacts a 3 mass% Si steel sheet with a thickness of 0.1 to 0.35 mm with silicon tetrachloride gas at a high temperature to reduce the Si concentration in the steel. It is a process of enhancing.
- a 6.5 mass% Si steel sheet has a specific resistance approximately twice that of a 3 mass% Si steel sheet, and can effectively reduce eddy current loss. At the same time, since the magnetostriction is substantially zero, it exhibits an excellent effect in reducing the noise of the iron core.
- Patent Document 2 further shows that, in the silicidation process, sufficient magnetic properties can be obtained by adjusting the surface Si concentration without making the Si concentration uniform in the thickness direction from the viewpoint of shortening the diffusion time. ing.
- Patent Document 3 regarding a silicon steel plate having a Si concentration gradient in the plate thickness direction, in order to reduce high-frequency iron loss, the Si concentration difference (maximum-minimum) in the plate thickness direction, the surface Si concentration, and the Si on the front and back surfaces of the steel plate It defines the difference in concentration.
- the lowest iron loss is obtained when the surface Si concentration is 6.5 mass%.
- Patent Document 4 discloses an electromagnetic steel sheet having excellent high-frequency characteristics by subjecting the electromagnetic steel sheet to a silicidation treatment with a ferrite phase and forming an electromagnetic steel sheet having a high Si concentration in the surface layer and a low Si concentration in the central portion of the plate thickness. Are listed.
- Patent Document 5 discloses that a low carbon steel is subjected to a siliconization treatment in a temperature range of 900 to 1000 ° C. where the austenite phase is small to obtain a steel sheet having a high Si concentration in the surface layer, thereby improving workability and excellent high frequency characteristics.
- a silicon steel sheet for motors is described.
- the iron loss is represented by the sum of hysteresis loss and eddy current loss. It is known that the higher the excitation frequency, the higher the ratio of eddy current loss to the total iron loss. Since the eddy current is more difficult to flow as the specific resistance of the material is larger, a material having a higher specific resistance is used for the high-frequency magnetic core. In general, in a magnetic steel sheet, the specific resistance increases as the Si concentration increases. Therefore, a high frequency magnetic core material containing 3% by mass or more of Si is suitable.
- the steel tends to become harder and more brittle, making cold rolling difficult.
- the transformation from austenite to ferrite during slab cooling (hereinafter referred to as ⁇ / ⁇ transformation) does not occur, and ferrite forms a coarse structure as it is, so slab cracks and surface defects are likely to occur. Become. Therefore, in the actual electrical steel sheet manufacturing process, the upper limit of the Si concentration in the steel is 4% by mass.
- the 6.5% by mass Si steel sheet has the highest magnetic permeability and the lowest magnetostriction among the electromagnetic steel sheets.
- secondary processing such as slitting, punching, and bending.
- 6.5 mass% Si steel sheet is brittle and easily cracked as compared with a normal electromagnetic steel sheet, advanced processing technology is required in the secondary processing as described above.
- the Vickers hardness Hv of the 6.5 mass% Si steel sheet is about 390, which is very hard as compared with the conventional magnetic steel sheet Hv: about 200. For this reason, there also existed a fault that a press metal mold
- the ratio of eddy current loss is higher than hysteresis loss, so even if the hysteresis loss is bad, another material such as an inexpensive dust core with low eddy current loss (high specific resistance) can be used. Widely used.
- a 6.5% by mass Si steel plate can be manufactured by a siliconization process in which a silicon tetrachloride is sprayed at a high temperature after rolling a 3% by mass Si steel plate to a final thickness.
- a siliconization process in which a silicon tetrachloride is sprayed at a high temperature after rolling a 3% by mass Si steel plate to a final thickness.
- FIG. 13 when the Si concentration is too nonuniform, the iron loss is greatly increased.
- the Si concentration nonuniformity is suppressed to a certain level, the Si concentration is uniform.
- An example in which a low iron loss comparable to a simple steel plate is obtained is described. However, no case is shown in which when the Si concentration is not uniform, the iron loss is even lower than that of a steel plate with a uniform Si concentration. Moreover, no specific numerical value is described
- Patent Document 3 describes a steel plate that leaves a Si concentration gradient in the thickness direction as a material that is further superior in high-frequency characteristics than a 6.5 mass% Si steel plate. Even if the surface layer has a high Si concentration, since the Si concentration in the central portion in the thickness direction of the plate is about 3% by mass, the average of the entire steel material is a material having a lower Si than the 6.5% by mass Si steel plate described above. it is conceivable that. However, in this case, the ⁇ / ⁇ transformation does not occur because the lower limit of the Si concentration in the steel is about 3% by mass. For this reason, the steel sheet structure when cooled to room temperature is composed of coarse ferrite grains that longitudinally cut the plate thickness, and the problem remains that cracks and chips are likely to occur when slitting or pressing.
- a grain oriented electrical steel sheet having a large magnetic domain width and a large abnormal eddy current loss due to a coarse secondary recrystallized structure is inherently tensile on the surface layer of the steel sheet and compressed internally.
- the cost is higher than other high-frequency iron core materials.
- siliconization is used as a means for imparting stress distribution.
- silicon is immersed from the surface layer until the average Si concentration reaches 4% by mass or more. It was necessary to increase the surface layer Si concentration to 5% by mass or more.
- Patent Document 5 low carbon steel having an austenite phase is subjected to siliconizing treatment.
- siliconizing treatment is performed in a temperature range exceeding 1000 ° C.
- Silica treatment is performed at a relatively low temperature range of ⁇ 1000 ° C.
- a method was desired.
- the steel material described in Patent Document 5 has a high surface layer Si concentration of 5 to 6.5% by mass and a coarse secondary recrystallized structure, it is still cracked or chipped when slitting or pressing. The problem that often occurs was left.
- High frequency magnetic core materials include a dust core formed by compacting iron powder, a ferrite core of iron oxide powder, and an Fe-based amorphous alloy. These are characterized by low eddy current loss because of their higher specific resistance than 6.5 mass% Si steel sheet. However, since the ferrite core has a low saturation magnetic flux density, the ferrite core is normally used only for high-frequency applications with a low output and several hundred kHz or more. On the other hand, the dust core and the Fe-based amorphous alloy have a slightly lower saturation magnetic flux density than the magnetic steel sheet, but have a low eddy current loss.
- any of the above-described materials has a problem that iron loss increases remarkably when an external stress such as compression is applied.
- many magnetic materials having excellent high-frequency characteristics are inferior in workability, and react sensitively to external stress, and particularly when compressive stress is applied, iron loss increases remarkably. .
- examples of the material excellent in workability include low-carbon steel plates that are widely used as structural materials or exterior materials. Further, the magnetism of low carbon steel is not as sensitive to external stress as a general magnetic material, and iron loss does not increase remarkably even when compressive stress is applied. However, since the structure of a general low carbon steel sheet is composed of a fine ferrite mixed structure including a pearlite phase, a bainite phase, and a martensite phase, the DC magnetic characteristics are extremely poor. Therefore, a low-carbon steel plate was rarely used for a commercial frequency magnetic core mainly composed of hysteresis loss.
- the low-carbon steel sheet can reduce the eddy current loss and take advantage of the low iron loss rise against compressive stress, the high-frequency iron loss is low and the iron loss is low against external stress. An excellent magnetic core material can be obtained.
- the present invention has been developed in view of the above-mentioned present situation, and an object thereof is to provide a low carbon steel sheet having excellent high frequency characteristics and less iron loss deterioration due to external stress, together with its manufacturing method.
- Patent Document 3 an Si concentration gradient is formed in the plate thickness direction in the siliconization process, and the Si concentration difference between the front and back surfaces of the steel plate is controlled to reduce eddy current loss. This technique is considered to be applied to low carbon steel in the same manner to reduce eddy current loss.
- Table 1 shows the compositions of the A to D4 low carbon steels used in this experiment.
- Steel treatment I Thoroughly diffused Si after siliconizing at 1200 ° C (siliconized + long-time diffusion) ...
- Steel treatment II 3 minutes of siliconization + Si diffusion at 1200 ° C (siliconization + short-time diffusion) ...
- the sample used for this experiment was produced by performing these three types of treatments.
- sample average Si concentration after treatment was 3 mass% Si.
- These samples are magnetized by direct current and alternating current using a 30 ⁇ 100mm single plate measurement frame, and the iron loss under the condition of magnetic flux density 0.05T and frequency 20kHz is separated into hysteresis loss and eddy current loss. And compared the results.
- the result of sample No. (C) is shown in FIG. In the figure, the iron loss values of electromagnetic steel sheets (3 mass% Si steel sheet and 6.5 mass% Si steel sheet) having the same thickness are also shown.
- the steel treatment II sample Compared with the steel treatment I sample, the steel treatment II sample has a lower eddy current loss due to an increase in specific resistance due to an increase in Si, and in the process of homogenizing Si, a ⁇ / ⁇ transformation is performed over the entire plate thickness, resulting in coarseness. Due to the formation of a proper ferrite structure, the hysteresis loss is also reduced.
- the iron loss of the steel treatment II sample (representing hysteresis loss + eddy current loss, hereinafter the same for the present invention) is a large value compared to the iron loss of the electrical steel sheet (3 mass% Si) having the same Si concentration. It was.
- the iron loss of the steel treatment III sample is surprisingly lower than that of the 3 mass% Si electrical steel sheet as well as the 6.5 mass% Si electrical steel sheet, and in particular, reduced eddy current loss. Admitted. It was expected that by adding a Si concentration gradient in the plate thickness direction, the magnetic flux could be concentrated on the surface layer, and eddy current loss could be reduced. It was only estimated that the eddy current loss could be reduced by 20 to 30% compared to the sample of which the Si concentration was made uniform. That is, the result of this experiment was an effect of reducing eddy current loss exceeding 50%, which was far beyond expectations.
- FIGS. 3A to 3D show photographs of the cross-sectional structures of the samples after the steel treatment III was applied to the sample Nos. (A) to (D), respectively.
- FIG. 3A although a boundary is observed between the surface layer and the plate thickness center layer, each has a coarse grain structure of a ferrite single phase.
- FIGS. 3B and 3C include a bainite structure, a pearlite structure, and a martensite structure that are found when air cooling is performed after annealing a low carbon steel at a temperature at which an austenite phase is generated in the center thickness layer. A ferrite mixed structure is observed, which is clearly different from the ferrite single-phase structure of the surface layer.
- FIG. 3D shows a martensite structure including a small amount of ferrite structure in the center layer of the plate thickness.
- the plate warpage was observed when the sample was removed from one side of the surface of the sample to the center of the plate thickness by chemical polishing. As a result, the warp was convex on the thickness center side. As a result, it was found that a tensile stress was generated in the surface layer and a compressive stress was generated in the center before the removal by polishing.
- the internal stress means that the original plate thickness is d (mm) and the curvature radius at the time of the above-described plate warp is r (mm).
- samples having the compositions to be Sample A and Sample C in Table 1 were used, and the samples were prepared by variously changing the Si diffusion time under the above-described steel treatment III conditions. About these samples, while measuring internal stress by said method, the eddy current loss was measured. The result is shown in FIG. From FIG.
- Mn is an element that stabilizes the austenite phase. Therefore, when the amount of Mn increases, the phase transformation point of ⁇ / ⁇ shifts to the low temperature side. Therefore, it is considered that the internal stress generated during cooling further increases.
- the plate thickness center layer has a fine mixed structure and is in a state where compressive stress is applied, so it is difficult to magnetize, whereas the surface layer is coarse ferrite crystal grains and tensile stress is applied. Since it is in a state, it tends to be easily magnetized. Therefore, when such a steel plate is magnetized in the in-plane direction of the plate, the magnetic flux concentrates on the surface layer, and as a result, it is considered that the eddy current loss of the steel plate is reduced.
- the iron loss value does not increase even when an external stress is applied if the sample has a large internal stress as in the sample described above.
- the external stress is zero, if the internal stress of about 70 to 160 MPa is generated like the sample, the tensile state of the surface layer is maintained even if a compressive stress of about several tens of MPa is applied from the outside. Is done.
- the compressive stress further increases in the center portion of the plate thickness, but it is a portion that is originally difficult to be magnetized, and its influence is negligible. As a result, there is no change in the situation where the magnetic flux tends to concentrate on the surface layer, and it is considered that the effect of reducing the eddy current loss of the sample is not lost.
- the Si concentration distribution of the steel sheet is relaxed, or the internal stress is relaxed, the above-described effect of reducing the eddy current loss and the deterioration of the iron loss with respect to the external compressive stress.
- the prevention effect is reduced, and the superiority over electrical steel sheets having the same Si concentration is lost. Accordingly, it has been found that it is preferable to take into consideration the time of heat treatment performed before the completion of the magnetic core including the diffusion time from the siliconization treatment.
- the present invention is based on the above findings.
- the gist configuration of the present invention is as follows. 1. Si: 1.0% by mass or less, C: 0.02 to 0.16% by mass, Mn: 0.3 to 2.0% by mass, P: 0.03% by mass or less and S: 0.01% by mass or less, the balance is Fe and inevitable impurities.
- a plate thickness central layer which is a ferrite mixed structure containing one or more of pearlite phase, bainite phase and martensite phase, Si: 3 to 5 mass%, C: 0.02 to 0.16 mass%, Mn: It is a clad-type low-carbon steel plate comprising 0.3 to 2.0% by mass, P: 0.03% by mass or less and S: 0.01% by mass or less, the composition of the balance Fe and inevitable impurities, and a surface layer that is a ferrite single phase.
- a low carbon steel sheet, wherein the surface layer has an in-plane tensile stress of 70 to 160 MPa as an internal stress.
- the sheet thickness center layer and the surface layer of the low-carbon steel plate are further Al: 0.002-0.6 mass%, Cr: 0.01-1.5 mass%, V: 0.0005-0.1 mass%, Ti: 0.0005-0.1 mass%, Nb: 0.0005. -1 mass%, Zr: 0.0005-0.1 mass%, B: 0.0005-0.01 mass%, and N: 0.002-0.01 mass%, one or more elements selected from the above, 4.
- the low carbon steel plate according to any one of 3 to 3.
- the Si-based gas is one or more gases selected from silicon tetrachloride, trichlorosilane, dichlorosilane, monosilane, and disilane.
- the steel sheet is further made of Al: 0.002-0.6% by mass, Cr: 0.01-1.5% by mass, V: 0.0005-0.1% by mass, Ti: 0.0005-0.1% by mass, Nb: 0.0005-0.1% by mass, Zr: 0.0005- 7.
- a low-carbon steel sheet having excellent high-frequency characteristics and less iron loss deterioration due to external stress can be obtained together with its manufacturing method, so that an iron core material excellent in workability can be provided.
- the present invention will be specifically described. First, the reasons for limiting the structure and composition of the steel sheet will be described. In addition, unless otherwise indicated, the% display in a steel plate component composition represents the mass%.
- ⁇ phase austenite phase
- a plate thickness center layer composed of a ferrite mixed structure containing at least one of a pearlite phase, a bainite phase and a martensite phase, and a ferrite having a high Si concentration
- a steel sheet having a so-called “clad type” three-layer structure having two surface layers on the front and back surfaces of a steel sheet having a single-phase structure is obtained. Since there is a difference in Si concentration between each surface layer and the plate thickness center layer, as described above, internal stress is generated due to the Si concentration gap, and tensile stress is applied to the surface layer.
- a pearlite phase, a bainite phase, and a martensite phase are included in total 30% (area%) or more, and the remainder is It is preferable that it is substantially a ferrite phase.
- the Si content in the surface layer is set to 3 to 5%.
- the Si concentration of the plate thickness center layer is set to 1.0% or less.
- the lower limit of the Si concentration is not particularly limited, but is preferably about 0.1% in order to remove oxygen in the steel during steelmaking.
- the surface layer Si increased by the silicon immersion penetrates to the inside by sufficient diffusion, and before the Si concentration in the surface layer and the central layer becomes uniform. Meaning. Accordingly, there is a Si concentration gradient in the surface depth portion (center) direction in both the surface layer portion and the plate thickness central layer portion, but this gradient is extremely small and can be almost ignored. Accordingly, the surface Si concentration (amount) in the present invention means the average Si concentration (amount) of the surface layer portion.
- the surface layer may have a dot-like or linear carbide, there is no particular problem in this case, and the ferrite single phase may be substantially formed.
- the tensile stress of the surface layer described above must be in-plane tensile stress of 70 to 160 MPa. This is because if the tensile stress of the surface layer is less than 70 MPa, there is a problem that the effect of reducing eddy current loss is weakened. On the other hand, if it exceeds 160 MPa, the hysteresis loss increases too much and the effect of reducing eddy current loss is reduced. The problem of canceling out occurs. Therefore, in the present invention, the tensile stress of the surface layer is limited to 70 to 160 MPa.
- the thickness of the surface layer described above is preferably about 30 to 60% of the total thickness of the two steel layers. This is because the hysteresis loss increases if the total thickness of the steel sheet is less than 30%. On the other hand, if it exceeds 60%, the effect of reducing eddy current loss is reduced, resulting in an increase in iron loss.
- the surface layer described above is not necessarily the same for each of the upper and lower surfaces, such as the thickness and the component composition, but it is desirable that the surface layer be the same level.
- the thickness of the steel sheet used in the present invention is desirably about 0.05 to 0.35 mm. This is because if the thickness of the steel sheet is less than 0.05 mm, the production efficiency is lowered and the manufacturing cost is increased. On the other hand, if it exceeds 0.35 mm, the eddy current loss increases and it is not suitable as a magnetic core material for high frequency. However, even if the thickness is not satisfied, the iron loss reduction effect in the present invention is not lost.
- C 0.02 to 0.16%
- C is an element necessary for increasing the internal stress of the steel material and obtaining a sufficient eddy current loss reduction effect, and needs to contain at least 0.02%.
- C is limited to the range of 0.02 to 0.16%. More preferably, C is set in the range of 0.03 to 0.10% from the viewpoint of obtaining a lower iron loss than the 6.5% Si electromagnetic steel sheet even at high frequencies.
- Mn 0.3-2.0%
- Mn is an element necessary for obtaining a sufficient eddy current loss reduction effect, and needs to be contained at least 0.3%.
- Mn is limited to a range of 0.3 to 2.0%.
- P 0.03% or less P is an embrittlement element, and cracking is likely to occur at the interface between the surface layer of the steel sheet and the thickness center layer. Therefore, it is desirable to reduce as much as possible, but 0.03% is acceptable.
- S 0.01% or less S is an element that causes hot brittleness. Since productivity decreases as the concentration increases, it is desirable to reduce it as much as possible, but it is acceptable up to 0.01%.
- the basic component of the steel plate has been described, in the present invention, in addition, one or more selected from the elements described below are contained in common in both the surface layer and the center layer of the plate thickness. can do.
- Al 0.002 to 0.6%
- the addition of Al increases the specific resistance and is therefore an effective element for reducing eddy current loss. If it is less than the lower limit, the effect of addition is poor. On the other hand, if it exceeds the upper limit, the ⁇ phase is present at a high temperature before silicidation, making it impossible to produce the clad steel sheet proposed by the present invention.
- V 0.0005 to 0.1%
- Ti 0.0005 to 0.1%
- Nb 0.0005 to 0.1%
- Zr 0.0005 to 0.1%
- the addition of V, Ti, Nb, and Zr is effective in reducing eddy current loss because it lowers the magnetic permeability by forming carbide and nitride at the center of the plate thickness and enhances the effect of concentrating the magnetic flux on the surface layer.
- the content is less than the lower limit, the effect of addition is poor.
- carbide and nitride precipitated in the grains and at the grain boundaries are the starting points, and brittle fracture is likely to occur.
- B 0.0005 to 0.01%
- N 0.002 to 0.01%
- B and N increases the hardenability of the central thickness layer in the cooling process after the siliconization treatment, so that the permeability of that portion is reduced and the effect of concentrating the magnetic flux on the surface layer is increased, thereby reducing eddy current loss.
- Each is effective. If each is less than the lower limit, the effect of addition is poor, whereas if the upper limit is exceeded, embrittlement tends to occur.
- the suitable manufacturing method of the low carbon steel plate of this invention is demonstrated.
- Any conventionally well-known method can be used conveniently.
- the slab having the composition of the plate thickness center layer of the steel plate is heated and then subjected to hot rolling, and cold rolling or cold rolling with one or more intermediate annealings is repeated to obtain a predetermined slab.
- a thick steel plate may be used.
- the steel plate obtained as described above is subjected to a siliconization treatment to increase the Si concentration of the surface layer. After forming a ferrite phase having a Si content of 3 to 5% on the surface layer of the steel plate, the Si in the steel is reduced.
- the low carbon steel sheet of the present invention can be produced by cooling before homogenization.
- any conventionally known method can be applied as a method of infiltrating (siliciding) Si.
- a vapor phase siliconization method, a liquid phase siliconization method, a solid phase siliconization method, or the like can be used. Can be mentioned.
- the Si-based gas used at that time is not particularly limited, but is a silane gas such as one or more gases selected from silicon tetrachloride, trichlorosilane, dichlorosilane, monosilane, and disilane. It is desirable to be.
- a silane gas such as one or more gases selected from silicon tetrachloride, trichlorosilane, dichlorosilane, monosilane, and disilane. It is desirable to be.
- a method of infiltrating Si by vapor phase siliconization will be described.
- the temperature history (temperature of each zone in the furnace and the residence time of the steel plate) from the start to the end of the siliconization and further cooling is determined.
- the Si concentration distribution in the plate thickness direction is determined almost uniquely.
- any conventionally known blast furnace can be suitably used.
- T k is the temperature of each zone in the furnace through which the steel plate passes after the start of the siliconization treatment
- t k is the residence time of the steel plate in each zone
- d is the plate thickness (mm)
- [mass% Si] add Represents the amount of Si added to the steel sheet during the siliconization treatment (increase in the average Si concentration in the thickness direction).
- the heat treatment is performed at a constant temperature and a constant time so that the value of ⁇ t k ⁇ exp ( ⁇ 25000 / T k ) is the same. For example, when cooling from 1200 ° C. to 700 ° C.
- the cooling can be regarded as the same as that subjected to a heat treatment at 1200 ° C. for 45 seconds.
- Equation 1 when performing the siliconization treatment in a continuous line, when the temperature is 700 ° C. or lower, the Si concentration of the steel sheet does not change in a realistic time, so the calculation of Equation 1 may be up to 700 ° C.
- the silicidation temperature in the present invention is 1050 to 1250 ° C. This is because if the temperature is less than 1050 ° C., internal stress may not be sufficiently generated when it is cooled, while if it exceeds 1250 ° C., the surface layer with high Si concentration becomes a semi-molten state during the siliconization treatment, and the steel plate It is because there is a possibility of breaking.
- the low carbon steel sheet that has been subjected to the siliconization treatment is subjected to a drying / baking process after the insulating coating is applied.
- a drying / baking process After the above-described steps, if the heat treatment is performed at a temperature lower than 600 ° C., stress relaxation of the steel sheet does not occur, and high-frequency iron loss does not increase. However, when the heat treatment is performed at 600 ° C. or higher, the internal stress is relaxed with time, so that the high-frequency iron loss is increased.
- T'k is the temperature of the heat treatment process steel sheet is passed after the siliconizing treatment
- t'k residence time of the steel sheet in each heat treatment step d is the thickness (mm)
- [mass% Si ] add Represents the amount of Si added to the steel sheet during the siliconization treatment (increase in the average Si concentration in the thickness direction).
- Equation 1 when the furnace temperature changes, heat treatment is performed at a constant temperature and a constant time so that the value of ⁇ t ′ k ⁇ exp ( ⁇ 25000 / T ′ k ) is the same. It can be regarded as a thing.
- the low-carbon steel sheet that has been subjected to the siliconization treatment is assembled as an iron core through various processing steps such as slitting, shearing, pressing, and the like, and may be subjected to strain relief annealing. Also in this case, since the internal stress is relieved by annealing at 600 ° C. or higher, it is preferable to set the strain relief annealing temperature and time so as to satisfy the above-mentioned formula 2. In addition, when the insulating coating is dried and baked at 400 ° C. or more and subjected to strain relief annealing after processing, the heat treatment step and strain relief annealing step of the coating are totaled, and the temperature and It is preferable to set the time. From the above, it is possible to set the manufacturing conditions in consideration of the time for the heat treatment performed until the completion of the magnetic core.
- Example 1 A sample having the component composition shown in Table 2 was rolled to a sheet thickness of 0.2 mm, heated to 1200 ° C., and subjected to siliconizing treatment equivalent to 3% Si and Si diffusion treatment in a SiCl 4 + N 2 atmosphere. After 3 minutes, it was cooled to room temperature at 10 ° C./min. The high frequency iron loss of these samples was measured by the Epstein test method (JIS C 2550). The results are shown in Table 3 together with the Si concentrations of the surface layer and the plate thickness center layer.
- Example 2 The samples shown as Nos. 2 to 5 in Table 2 were subjected to a change in iron loss by applying a compressive stress of ⁇ 50 MPa parallel to the magnetization direction. These high-frequency iron losses were measured by the Epstein test method (JIS C 2550). Table 4 shows the obtained results.
- the conventional 3% Si electrical steel sheet showed a significant increase in iron loss by more than twice due to external compressive stress, whereas the steel sheets according to the present invention (sample Nos. 3 to 5) However, it has stopped at a slight rise (up to 14W / kg iron loss). It can also be seen that the steel sheet according to the present invention has a sufficiently low iron loss even when subjected to an external tensile stress, and remains at a maximum of 12 W / kg.
- the present invention it is possible to obtain a low-carbon steel sheet having excellent high-frequency characteristics and less iron loss deterioration due to external stress. As a result, it is possible to obtain a high-frequency iron core with low iron loss, and thus it is possible to manufacture a highly energy efficient transformer and other electric devices.
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Abstract
Description
一般的な電磁鋼板は、鋼中不純物を極力減らすことで、結晶粒の成長性を高め、履歴損の低減化を図っている。また、Siを0.5~3.5質量%添加して比抵抗を高めたり、板厚を薄肉化することで、渦電流損の低減化を図っている。 The iron loss of an electrical steel sheet is composed of a hysteresis loss that strongly depends on precipitates in the steel, crystal grain size, texture, and the like, and an eddy current loss that strongly depends on the plate thickness, specific resistance, magnetic domain structure, and the like.
A general electromagnetic steel sheet increases crystal grain growth by reducing impurities in the steel as much as possible, thereby reducing hysteresis loss. Moreover, eddy current loss is reduced by adding 0.5 to 3.5% by mass of Si to increase the specific resistance or to reduce the plate thickness.
近年、パワーエレクトロニクス分野でスイッチング素子の高周波化が進んでいるため、トランスやリアクトル、モーター等の鉄芯材料として用いられる電磁鋼板に対しても、高周波鉄損の低減が強く望まれるようになってきた。 Here, since the hysteresis loss is proportional to the frequency and the eddy current loss is proportional to the square of the frequency, the ratio of the hysteresis loss to the iron loss of the electrical steel sheet is large at the commercial frequency (50/60 Hz). When the frequency becomes several kHz or higher, the ratio of eddy current loss increases.
In recent years, high frequency switching elements have been developed in the field of power electronics, and it has been strongly desired to reduce high-frequency iron loss even for electrical steel sheets used as iron core materials for transformers, reactors, motors, etc. It was.
このSi富化技術は、例えば、特許文献2に記載のように、板厚:0.1~0.35mmの3質量%Si鋼板を、高温で四塩化珪素ガスと反応させて、鋼中のSi濃度を高めるプロセスである。
また、古くから知られているように、6.5質量%Si鋼板は、3質量%Si鋼板の約2倍の固有抵抗を有し、渦電流損失を効果的に低減できるため、高周波用材として有利であると同時に、磁歪が実質的にゼロであるため、鉄心の低騒音化に優れた効果を発揮するものである。 As means for reducing high-frequency iron loss of an electromagnetic steel sheet, Patent Document 1 describes a Si enrichment method for a steel sheet surface by a siliconization method.
This Si enrichment technology, for example, as described in
In addition, as is known for a long time, a 6.5 mass% Si steel sheet has a specific resistance approximately twice that of a 3 mass% Si steel sheet, and can effectively reduce eddy current loss. At the same time, since the magnetostriction is substantially zero, it exhibits an excellent effect in reducing the noise of the iron core.
一般に、電磁鋼板では、Si濃度が高くなるほど比抵抗が増加するため、高周波用磁芯材料としては、3質量%以上のSiを含むものが適している。 As described above, the iron loss is represented by the sum of hysteresis loss and eddy current loss. It is known that the higher the excitation frequency, the higher the ratio of eddy current loss to the total iron loss. Since the eddy current is more difficult to flow as the specific resistance of the material is larger, a material having a higher specific resistance is used for the high-frequency magnetic core.
In general, in a magnetic steel sheet, the specific resistance increases as the Si concentration increases. Therefore, a high frequency magnetic core material containing 3% by mass or more of Si is suitable.
しかしながら、実際に磁芯として使用するには、浸珪後の6.5質量%Si鋼板をスリット、プレスまたは曲げ加工をする必要があり、その際に割れや欠けが生じることが多いという問題を残していた。
さらに特許文献2には、その図13に、Si濃度が不均一すぎた場合、鉄損が大幅に増加する一方、Si濃度の不均一性がある程度以下に抑えられた場合は、Si濃度が均一な鋼板と遜色ない低鉄損が得られる例が記載されている。しかしながら、Si濃度が不均一な場合に、Si濃度が均一な鋼板よりもさらに低鉄損となる事例は示されていない。また、高周波鉄損について、具体的な数値が何ら記載されていない。 According to
However, in order to actually use it as a magnetic core, it is necessary to slit, press or bend the 6.5% by mass Si steel sheet after siliconization, which often causes cracking and chipping. It was.
Further, in
しかしながら、この場合は、鋼中のSi濃度の下限が3質量%程度のために、γ/α変態が生じない。そのため、室温に冷却した時の鋼板組織は、板厚を縦断する粗大フェライト粒から構成されることとなり、やはりスリットやプレスを行う際に割れや欠けが生じやすいという問題を残していた。 Patent Document 3 describes a steel plate that leaves a Si concentration gradient in the thickness direction as a material that is further superior in high-frequency characteristics than a 6.5 mass% Si steel plate. Even if the surface layer has a high Si concentration, since the Si concentration in the central portion in the thickness direction of the plate is about 3% by mass, the average of the entire steel material is a material having a lower Si than the 6.5% by mass Si steel plate described above. it is conceivable that.
However, in this case, the γ / α transformation does not occur because the lower limit of the Si concentration in the steel is about 3% by mass. For this reason, the steel sheet structure when cooled to room temperature is composed of coarse ferrite grains that longitudinally cut the plate thickness, and the problem remains that cracks and chips are likely to occur when slitting or pressing.
しかしながら、渦電流損を低減するには1000℃以上で浸珪処理をおこなうことが好ましく、上記した界面において、1000℃以上の浸珪処理を施した場合でも割れの生じない鋼板材料および鋼板の製造方法が望まれていた。また、特許文献5に記載の鋼材は、表層Si濃度が5~6.5質量%と高く、かつ粗大な二次再結晶組織を有しているため、やはり、スリットやプレスを行う際に割れや欠けが生じることが多いという問題を残していた。 In
However, in order to reduce eddy current loss, it is preferable to perform a silicidation treatment at 1000 ° C. or higher, and in the above-described interface, manufacturing of a steel plate material and a steel plate that does not cause cracking even when a silicon carbide treatment at 1000 ° C. or higher is performed. A method was desired. In addition, since the steel material described in
ただし、フェライトコアは、飽和磁束密度が低いため、通常使用されるのは低出力で数百kHz以上の高周波用途に限定される。他方、ダストコア、Fe基アモルファス合金は、電磁鋼板と比べて飽和磁束密度がやや低いものの渦電流損が低いため、高出力の高周波用途に対しては電磁鋼板と同様に使用されることもある。 Other high frequency magnetic core materials include a dust core formed by compacting iron powder, a ferrite core of iron oxide powder, and an Fe-based amorphous alloy. These are characterized by low eddy current loss because of their higher specific resistance than 6.5 mass% Si steel sheet.
However, since the ferrite core has a low saturation magnetic flux density, the ferrite core is normally used only for high-frequency applications with a low output and several hundred kHz or more. On the other hand, the dust core and the Fe-based amorphous alloy have a slightly lower saturation magnetic flux density than the magnetic steel sheet, but have a low eddy current loss.
以上述べたように、高周波特性に優れた磁性材料は、加工性に劣るものが多く、また外部応力に対して敏感に反応し、特に圧縮応力がかかると、鉄損が著しく増加するものが多い。 However, any of the above-described materials has a problem that iron loss increases remarkably when an external stress such as compression is applied.
As described above, many magnetic materials having excellent high-frequency characteristics are inferior in workability, and react sensitively to external stress, and particularly when compressive stress is applied, iron loss increases remarkably. .
ただし、一般的な低炭素鋼板の組織は、パーライト相、ベイナイト相およびマルテンサイト相を含む微細なフェライト混合組織で構成されているため、その直流磁気特性は極めて悪い。したがって、履歴損が主体となる商用周波数の磁芯に低炭素鋼板が使われることはほとんどなかった。 On the other hand, examples of the material excellent in workability include low-carbon steel plates that are widely used as structural materials or exterior materials. Further, the magnetism of low carbon steel is not as sensitive to external stress as a general magnetic material, and iron loss does not increase remarkably even when compressive stress is applied.
However, since the structure of a general low carbon steel sheet is composed of a fine ferrite mixed structure including a pearlite phase, a bainite phase, and a martensite phase, the DC magnetic characteristics are extremely poor. Therefore, a low-carbon steel plate was rarely used for a commercial frequency magnetic core mainly composed of hysteresis loss.
この技術は、低炭素鋼に対しても、同様に適用されて渦電流損の低減化を図ることができると考えられる。 According to Patent Document 3, an Si concentration gradient is formed in the plate thickness direction in the siliconization process, and the Si concentration difference between the front and back surfaces of the steel plate is controlled to reduce eddy current loss.
This technique is considered to be applied to low carbon steel in the same manner to reduce eddy current loss.
すなわち、低炭素鋼を浸珪処理してSi濃度勾配を付与したものは、γ/α変態を生じることのない特許文献3に記載の技術とは、その構成が大きく異なっている。 However, in the case of low carbon steel, the γ / α transformation occurs. Therefore, when the siliconizing treatment is performed in the high-temperature austenite phase region, a phenomenon occurs in which the surface layer where the Si concentration increases is transformed into the ferrite phase. At this time, a Si concentration gap exists between the low Si concentration austenite phase and the high Si concentration ferrite phase, and therefore, the Si concentration gradient at the heterophase interface becomes discontinuous. When cooling with such a Si concentration gradient remaining, the high Si concentration ferrite phase in the surface layer does not transform, as shown in FIG. 1, whereas the low Si concentration austenite phase in the center layer of the plate thickness is the pearlite phase. And a fine ferrite mixed structure containing a bainite phase and a martensite phase.
That is, the low carbon steel that has been subjected to a siliconization treatment to give a Si concentration gradient is greatly different from the technique described in Patent Document 3 in which no γ / α transformation occurs.
同表中、記号(C)で示した鋼材に、
窒素ガス中、1200℃で焼鈍したもの(浸珪無し)…鋼処理I
1200℃で浸珪後、Siを十分に均一拡散したもの(浸珪+長時間拡散)…鋼処理II
1200℃での浸珪+Si拡散を合わせて3分間実施したもの(浸珪+短時間拡散)…鋼処理III
の3種類の処理を施して、本実験に用いる試料を作製した。 Hereinafter, the experiment that led to the completion of the present invention will be described. Table 1 shows the compositions of the A to D4 low carbon steels used in this experiment.
In the table, the steel indicated by the symbol (C)
Annealed at 1200 ° C in nitrogen gas (no siliconization) ... Steel treatment I
Thoroughly diffused Si after siliconizing at 1200 ° C (siliconized + long-time diffusion) ... Steel treatment II
3 minutes of siliconization + Si diffusion at 1200 ° C (siliconization + short-time diffusion) ... Steel treatment III
The sample used for this experiment was produced by performing these three types of treatments.
試料No.(C)の結果を図2に示す。なお、図中には、同じ板厚の電磁鋼板(3質量%Si鋼板と6.5質量%Si鋼板)の鉄損値も併せて示した。 Here, the silicon treatment of steel treatments II and III was adjusted such that the sample average Si concentration after treatment was 3 mass% Si. These samples are magnetized by direct current and alternating current using a 30 × 100mm single plate measurement frame, and the iron loss under the condition of magnetic flux density 0.05T and frequency 20kHz is separated into hysteresis loss and eddy current loss. And compared the results.
The result of sample No. (C) is shown in FIG. In the figure, the iron loss values of electromagnetic steel sheets (3 mass% Si steel sheet and 6.5 mass% Si steel sheet) having the same thickness are also shown.
また、鋼処理IIの試料の鉄損(履歴損+渦電流損を表す、以下本発明について同じ)は、同じSi濃度の電磁鋼板(3質量%Si)の鉄損と比較すると大きな値であった。この理由は、同じ3質量%Siのフェライト粗大組織同士であっても、電磁鋼板の場合はC量が50ppm未満であるのに対し、低炭素鋼の場合は、C量が500ppm以上含まれているため、履歴損が増大してしまうためと考えられる。 Compared with the steel treatment I sample, the steel treatment II sample has a lower eddy current loss due to an increase in specific resistance due to an increase in Si, and in the process of homogenizing Si, a γ / α transformation is performed over the entire plate thickness, resulting in coarseness. Due to the formation of a proper ferrite structure, the hysteresis loss is also reduced.
In addition, the iron loss of the steel treatment II sample (representing hysteresis loss + eddy current loss, hereinafter the same for the present invention) is a large value compared to the iron loss of the electrical steel sheet (3 mass% Si) having the same Si concentration. It was. The reason for this is that even in the same coarse ferrite structure of 3 mass% Si, the amount of C is less than 50 ppm in the case of electrical steel sheets, whereas the amount of C is included in the case of low carbon steel is 500 ppm or more. Therefore, it is considered that the history loss increases.
板厚方向にSi濃度勾配を付することで、表層に磁束を集中させ、渦電流損の低減化を図ることができるものと予想はしていたが、その場合の効果は、同じ浸珪量の試料でSi濃度を均一化させたものよりも、渦電流損で2~3割の低減化が図れる程度との推定に止まっていた。すなわち、本実験の結果は、5割を超えるほどの渦電流損の低減化効果であって、予想をはるかに上回るものであった。 On the other hand, the iron loss of the steel treatment III sample is surprisingly lower than that of the 3 mass% Si electrical steel sheet as well as the 6.5 mass% Si electrical steel sheet, and in particular, reduced eddy current loss. Admitted.
It was expected that by adding a Si concentration gradient in the plate thickness direction, the magnetic flux could be concentrated on the surface layer, and eddy current loss could be reduced. It was only estimated that the eddy current loss could be reduced by 20 to 30% compared to the sample of which the Si concentration was made uniform. That is, the result of this experiment was an effect of reducing eddy current loss exceeding 50%, which was far beyond expectations.
図3(a)は、表層と板厚中央層に境界は認められるものの、いずれもフェライト単相の粗大粒組織となっている。これに対し、図3(b)及び(c)は、板厚中央層において低炭素鋼をオーステナイト相が生じる温度で焼鈍後、空冷したときに見られるベイナイト組織、パーライト組織、マルテンサイト組織を含むフェライト混合組織が認められ、表層のフェライト単相組織と明らかに異なる組織となっている。図3(d)は板厚中央層で少量のフェライト組織を含むマルテンサイト組織となっている。 FIGS. 3A to 3D show photographs of the cross-sectional structures of the samples after the steel treatment III was applied to the sample Nos. (A) to (D), respectively.
In FIG. 3A, although a boundary is observed between the surface layer and the plate thickness center layer, each has a coarse grain structure of a ferrite single phase. On the other hand, FIGS. 3B and 3C include a bainite structure, a pearlite structure, and a martensite structure that are found when air cooling is performed after annealing a low carbon steel at a temperature at which an austenite phase is generated in the center thickness layer. A ferrite mixed structure is observed, which is clearly different from the ferrite single-phase structure of the surface layer. FIG. 3D shows a martensite structure including a small amount of ferrite structure in the center layer of the plate thickness.
そこで、各試料の成分を確認したところ、C量が200ppm以上含まれる場合であって、Mnが0.3質量%以上含まれる場合に、渦電流損の低減化効果が顕著に現れており、同時に、6.5質量%Siの電磁鋼板をしのぐ低鉄損が得られることが分かった。
また、試料Dは、通常の電磁鋼板(3質量%Si)より低鉄損を示すものの、その優位性は試料B、Cと比較すると低下する傾向にある。 From FIG. 4, it was found that not all steel materials subjected to the steel treatment III were able to obtain a low iron loss that surpassed the 6.5% by mass Si magnetic steel sheet.
Therefore, when the components of each sample were confirmed, when the amount of C was 200 ppm or more and when Mn was contained by 0.3 mass% or more, the effect of reducing eddy current loss was noticeable, It was found that low iron loss was obtained that surpassed 6.5% by mass Si magnetic steel sheet.
Moreover, although the sample D shows a lower iron loss than a normal electromagnetic steel sheet (3 mass% Si), its superiority tends to be lower than those of the samples B and C.
面内引張応力=E×d/(2r) [MPa] (Eは鋼板のヤング率を表す)
と定義される。
さらに、表1の試料Aおよび試料Cになる組成の材料を用い、前記した鋼処理IIIの条件において、Si拡散時間を種々に変更して試料を作製した。これら試料について、上記の方法で内部応力を測定するとともに、渦電流損を測定した。その結果を図6に示す。
図6より、Cが200ppm以上、Mnが0.3質量%以上含まれる試料Cの場合、上記の浸珪処理後の内部応力が、大きくなっている傾向にあった。また、内部応力(面内引張応力)が70~160MPaの範囲で渦電流損の低減が顕著となっていた。 Here, in the present invention, as shown in FIG. 5, the internal stress means that the original plate thickness is d (mm) and the curvature radius at the time of the above-described plate warp is r (mm). (Internal tensile stress) = Compressive stress acting on the thickness center
In-plane tensile stress = E x d / (2r) [MPa] (E represents Young's modulus of the steel sheet)
Is defined.
Further, samples having the compositions to be Sample A and Sample C in Table 1 were used, and the samples were prepared by variously changing the Si diffusion time under the above-described steel treatment III conditions. About these samples, while measuring internal stress by said method, the eddy current loss was measured. The result is shown in FIG.
From FIG. 6, in the case of Sample C containing 200 ppm or more of C and 0.3% by mass or more of Mn, the internal stress after the above-described siliconization treatment tended to be large. In addition, the reduction of eddy current loss was remarkable when the internal stress (in-plane tensile stress) was in the range of 70 to 160 MPa.
Fe-Si系合金では、低炭素鋼レベルで、鋼中C量が増加した場合、Fe-Siの状態図上のγ/α境界線が、高Si側にシフトし、浸珪処理が施された場合に、フェライト相に変態した部分と、オーステナイト相のままの部分のSi濃度ギャップが増大する。高温時に、Si濃度ギャップが増大すると、冷却時にγ/αの相変態が生じて膨張しようとする中央層と、もはや変態をしない表層のフェライト相との間に内部応力が発生すると考えられる。 The cause of the above-mentioned tendency is not clear at present, but the inventors speculate as follows.
In Fe-Si alloys, when the amount of C in steel increases at the low carbon steel level, the γ / α boundary line on the Fe-Si phase diagram is shifted to the high Si side, and siliconization is applied. In this case, the Si concentration gap between the portion transformed into the ferrite phase and the portion remaining in the austenite phase increases. When the Si concentration gap increases at high temperatures, it is considered that an internal stress is generated between the central layer that is about to expand due to a γ / α phase transformation during cooling and the surface ferrite phase that no longer undergoes transformation.
従って、このような鋼板を板の面内方向に向かって磁化したとき、その磁束は表層に集中するため、結果として鋼板の渦電流損を低下させると考えられる。 Furthermore, the plate thickness center layer has a fine mixed structure and is in a state where compressive stress is applied, so it is difficult to magnetize, whereas the surface layer is coarse ferrite crystal grains and tensile stress is applied. Since it is in a state, it tends to be easily magnetized.
Therefore, when such a steel plate is magnetized in the in-plane direction of the plate, the magnetic flux concentrates on the surface layer, and as a result, it is considered that the eddy current loss of the steel plate is reduced.
すなわち、外部応力ゼロの状態でも、当該試料のように70~160MPa程度の内部応力が発生していれば、外部から数十MPa程度の圧縮応力が加えられたとしても、表層の引張状態は維持される。これに対し、板厚中心部では、圧縮応力が更に増えることになるが、元々磁化され難い部分であり影響はごくわずかである。
その結果、表層に磁束が集中しやすい状況に変化はなく、当該試料の渦電流損の低減化効果は失われないものと考えている。 It has also been found that the iron loss value does not increase even when an external stress is applied if the sample has a large internal stress as in the sample described above.
In other words, even when the external stress is zero, if the internal stress of about 70 to 160 MPa is generated like the sample, the tensile state of the surface layer is maintained even if a compressive stress of about several tens of MPa is applied from the outside. Is done. On the other hand, the compressive stress further increases in the center portion of the plate thickness, but it is a portion that is originally difficult to be magnetized, and its influence is negligible.
As a result, there is no change in the situation where the magnetic flux tends to concentrate on the surface layer, and it is considered that the effect of reducing the eddy current loss of the sample is not lost.
従って、浸珪処理からの拡散時間を含めて磁芯完成までに施される熱処理の時間も考慮することが好ましいことが分かった。
本発明は上記知見に立脚するものである。 In addition, as described above, when annealing is performed for a long time at a high temperature, the Si concentration distribution of the steel sheet is relaxed, or the internal stress is relaxed, the above-described effect of reducing the eddy current loss and the deterioration of the iron loss with respect to the external compressive stress. The prevention effect is reduced, and the superiority over electrical steel sheets having the same Si concentration is lost.
Accordingly, it has been found that it is preferable to take into consideration the time of heat treatment performed before the completion of the magnetic core including the diffusion time from the siliconization treatment.
The present invention is based on the above findings.
1.Si:1.0 質量%以下、C:0.02~0.16質量%、Mn:0.3~2.0質量%、P:0.03質量%以下およびS:0.01質量%以下を含み、残部Feおよび不可避的不純物の組成であり、パーライト相、ベイナイト相およびマルテンサイト相のうちいずれか1種また2種以上を含むフェライト混合組織である板厚中央層と、Si:3~5質量%、C:0.02~0.16質量%、Mn:0.3~2.0質量%、P:0.03質量%以下およびS:0.01質量%以下を含み、残部Feおよび不可避的不純物の組成であり、フェライト単相である表層とからなるクラッド型の低炭素鋼板であって、該表層が内部応力として70~160MPaの面内引張応力を有することを特徴とする低炭素鋼板。 That is, the gist configuration of the present invention is as follows.
1. Si: 1.0% by mass or less, C: 0.02 to 0.16% by mass, Mn: 0.3 to 2.0% by mass, P: 0.03% by mass or less and S: 0.01% by mass or less, the balance is Fe and inevitable impurities. A plate thickness central layer which is a ferrite mixed structure containing one or more of pearlite phase, bainite phase and martensite phase, Si: 3 to 5 mass%, C: 0.02 to 0.16 mass%, Mn: It is a clad-type low-carbon steel plate comprising 0.3 to 2.0% by mass, P: 0.03% by mass or less and S: 0.01% by mass or less, the composition of the balance Fe and inevitable impurities, and a surface layer that is a ferrite single phase. A low carbon steel sheet, wherein the surface layer has an in-plane tensile stress of 70 to 160 MPa as an internal stress.
まず、鋼板の構造、成分組成等の限定理由について述べる。なお、鋼板成分組成における%表示は、特に断らない限り質量%を表す。 Hereinafter, the present invention will be specifically described.
First, the reasons for limiting the structure and composition of the steel sheet will be described. In addition, unless otherwise indicated, the% display in a steel plate component composition represents the mass%.
そのために、高温でオーステナイト相(以下、γ相という)となっている鋼板に対して浸珪処理を施して、表層のSi量を増加させて比抵抗を上げ、さらに表層のみをフェライト相(以下、α相という)に変態させてから、鋼中Siが均一化する前に冷却することが必要である。
上記の冷却によって、図1に示したような、パーライト相、ベイナイト相およびマルテンサイト相のうちいずれか1種また2種以上を含むフェライト混合組織からなる板厚中央層と、Si濃度の高いフェライト単相組織からなる鋼板表裏面の2層の表層を有する、いわゆる「クラッド型」の3層構造の鋼板となる。これら各表層と板厚中央層との間には、Si濃度に差があるため、前述したように、Si濃度ギャップによる内部応力が発生し、表層には引張応力が付加される。
なお、板厚中央層については、フェライト単相の場合、十分な内部応力が得られないことから、パーライト相、ベイナイト相およびマルテンサイト相を、合計で30%(面積%)以上含み、残部は実質的にフェライト相であることが好ましい。 In the present invention, as described above, it is important to further apply tensile stress to the surface layer with increased specific resistance.
For this purpose, a steel sheet that is in an austenite phase (hereinafter referred to as γ phase) at high temperature is subjected to a siliconization treatment to increase the specific resistance by increasing the amount of Si in the surface layer. , It is necessary to cool before Si in steel becomes uniform.
As a result of the cooling described above, as shown in FIG. 1, a plate thickness center layer composed of a ferrite mixed structure containing at least one of a pearlite phase, a bainite phase and a martensite phase, and a ferrite having a high Si concentration A steel sheet having a so-called “clad type” three-layer structure having two surface layers on the front and back surfaces of a steel sheet having a single-phase structure is obtained. Since there is a difference in Si concentration between each surface layer and the plate thickness center layer, as described above, internal stress is generated due to the Si concentration gap, and tensile stress is applied to the surface layer.
In addition, about a plate | board thickness center layer, since sufficient internal stress is not obtained in the case of a ferrite single phase, a pearlite phase, a bainite phase, and a martensite phase are included in total 30% (area%) or more, and the remainder is It is preferable that it is substantially a ferrite phase.
しかし、表層Si量が5%を超えると、逆に磁歪が小さくなって、引張応力による磁気弾性効果が小さくなり、また表面が硬くなって加工性の低下を招く。従って、、表層のSi量は3~5%とした。 Here, when the amount of Si in the surface layer is 3% or more, the magnetostriction takes a large positive value. Therefore, when the tensile stress as described above is applied, it becomes easy to be magnetized by the magnetoelastic effect. As a result, when the steel plate is magnetized, the concentration of magnetic flux on the surface layer is promoted, and the effect of reducing eddy current is increased.
However, when the surface layer Si content exceeds 5%, the magnetostriction is conversely reduced, the magnetoelastic effect due to the tensile stress is reduced, and the surface becomes hard, resulting in a decrease in workability. Therefore, the Si content in the surface layer is set to 3 to 5%.
従って、表層部分にも、板厚中央層部分にも板厚深さ(中心)方向に向かって、Si濃度勾配が存在するが、この勾配は極めて微小であり、ほとんど無視することができる。従って、本発明における表層Si濃度(量)とは、表層部分の平均Si濃度(量)のことを意味する。また、上記表層に点状または線状の炭化物が存在することがあるが、この場合も特に問題はなく、実質的にフェライト単相としてよい。 In the present invention, before the Si in the steel is made uniform, the surface layer Si increased by the silicon immersion penetrates to the inside by sufficient diffusion, and before the Si concentration in the surface layer and the central layer becomes uniform. Meaning.
Accordingly, there is a Si concentration gradient in the surface depth portion (center) direction in both the surface layer portion and the plate thickness central layer portion, but this gradient is extremely small and can be almost ignored. Accordingly, the surface Si concentration (amount) in the present invention means the average Si concentration (amount) of the surface layer portion. Moreover, although the surface layer may have a dot-like or linear carbide, there is no particular problem in this case, and the ferrite single phase may be substantially formed.
なお、上記した表層は、厚み、成分組成等、上下面の2層各々で、必ずしも同じである必要はないが、同じ程度とすることが望ましい。 The thickness of the surface layer described above is preferably about 30 to 60% of the total thickness of the two steel layers. This is because the hysteresis loss increases if the total thickness of the steel sheet is less than 30%. On the other hand, if it exceeds 60%, the effect of reducing eddy current loss is reduced, resulting in an increase in iron loss.
The surface layer described above is not necessarily the same for each of the upper and lower surfaces, such as the thickness and the component composition, but it is desirable that the surface layer be the same level.
成分中、Siについては、上述したとおり表層は3~5%、板厚中央層は1.0%以下にする必要があるが、その他の成分については、表層および板厚中央層の両層に共通する。
C:0.02~0.16%、
Cは、鋼材の内部応力を高め、十分な渦電流損低減効果を得るために必要な元素であり、少なくとも0.02%の含有を必要とする。一方 0.16%を超えると表層と板厚中央層の界面で割れが生じやすくなる。そのため、Cは 0.02~0.16%の範囲に限定した。
より好ましくは、高周波においても6.5%Siの電磁鋼板より低い鉄損を得るという観点から、Cを0.03~0.10%の範囲とする。 Hereinafter, the reasons for limiting the components of the surface layer and the plate thickness center layer of the steel plate will be described. In addition, the remainder of the steel plate component shown below is Fe and inevitable impurities.
Among the components, for Si, as described above, the surface layer needs to be 3 to 5%, and the plate thickness center layer needs to be 1.0% or less, but the other components are common to both the surface layer and the plate thickness center layer. .
C: 0.02 to 0.16%,
C is an element necessary for increasing the internal stress of the steel material and obtaining a sufficient eddy current loss reduction effect, and needs to contain at least 0.02%. On the other hand, if it exceeds 0.16%, cracking is likely to occur at the interface between the surface layer and the thickness center layer. Therefore, C is limited to the range of 0.02 to 0.16%.
More preferably, C is set in the range of 0.03 to 0.10% from the viewpoint of obtaining a lower iron loss than the 6.5% Si electromagnetic steel sheet even at high frequencies.
Mnは、十分な渦電流損低減効果を得るために必要な元素であり、少なくとも 0.3%の含有を必要とする。一方2.0%を超えると、室温まで冷却した後も鋼板の板厚中央層にγ相が残留しやすくなり、鋼板の表層との内部応力が低下してしまう。そのために、Mnは0.3~2.0%の範囲に限定した。 Mn: 0.3-2.0%
Mn is an element necessary for obtaining a sufficient eddy current loss reduction effect, and needs to be contained at least 0.3%. On the other hand, if it exceeds 2.0%, the γ phase tends to remain in the thickness center layer of the steel sheet even after cooling to room temperature, and the internal stress with the surface layer of the steel sheet is reduced. Therefore, Mn is limited to a range of 0.3 to 2.0%.
Pは、脆化元素であり、鋼板の表層と板厚中央層の界面で割れが生じやすくなるため、極力低減化することが望ましいが、0.03%までは許容できる。 P: 0.03% or less P is an embrittlement element, and cracking is likely to occur at the interface between the surface layer of the steel sheet and the thickness center layer. Therefore, it is desirable to reduce as much as possible, but 0.03% is acceptable.
Sは、熱間脆性の原因となる元素であり、濃度が増すと生産性が低下するため、極力低減化することが望ましいが、0.01%までは許容できる。 S: 0.01% or less S is an element that causes hot brittleness. Since productivity decreases as the concentration increases, it is desirable to reduce it as much as possible, but it is acceptable up to 0.01%.
Al:0.002~0.6%
Alの添加は、固有抵抗を高めるので、渦電流損低減に有効な元素である。下限未満では添加効果に乏しく、一方上限を超えると浸珪前に高温でα相が存在するため本発明が提示するクラッド型鋼板の作製ができなくなる。 As mentioned above, although the basic component of the steel plate has been described, in the present invention, in addition, one or more selected from the elements described below are contained in common in both the surface layer and the center layer of the plate thickness. can do.
Al: 0.002 to 0.6%
The addition of Al increases the specific resistance and is therefore an effective element for reducing eddy current loss. If it is less than the lower limit, the effect of addition is poor. On the other hand, if it exceeds the upper limit, the α phase is present at a high temperature before silicidation, making it impossible to produce the clad steel sheet proposed by the present invention.
Crの添加は、固有抵抗を高めるので、渦電流損低減に有効な元素である。下限未満では添加効果に乏しく、一方上限を超えると粒内及び粒界に析出した炭化物が起点となり脆性破壊しやすくなる。 Cr: 0.01-1.5%
The addition of Cr increases the specific resistance and is therefore an effective element for reducing eddy current loss. If the amount is less than the lower limit, the effect of addition is poor. On the other hand, if the amount exceeds the upper limit, carbides precipitated in the grains and at the grain boundaries are the starting points, and brittle fracture is likely to occur.
V、Ti、NbおよびZrの添加は、板厚中央部で炭化物、窒化物を形成することで透磁率を下げ、表層への磁束集中効果を高めるため、渦電流損低減にそれぞれ有効である。それぞれ下限未満では添加効果に乏しく、一方上限を超えると粒内及び粒界に析出した炭化物、窒化物が起点となり脆性破壊しやすくなる。 V: 0.0005 to 0.1%, Ti: 0.0005 to 0.1%, Nb: 0.0005 to 0.1%, Zr: 0.0005 to 0.1%
The addition of V, Ti, Nb, and Zr is effective in reducing eddy current loss because it lowers the magnetic permeability by forming carbide and nitride at the center of the plate thickness and enhances the effect of concentrating the magnetic flux on the surface layer. When the content is less than the lower limit, the effect of addition is poor. On the other hand, when the content exceeds the upper limit, carbide and nitride precipitated in the grains and at the grain boundaries are the starting points, and brittle fracture is likely to occur.
BおよびNの添加は、浸珪処理後の冷却過程で板厚中央層の焼入れ性を高めるため、その部分の透磁率が低下し、表層への磁束集中効果を高めるため、渦電流損低減にそれぞれ有効である。それぞれ下限未満では添加効果に乏しく、一方上限を超えると脆化しやすくなる。 B: 0.0005 to 0.01%, N: 0.002 to 0.01%
The addition of B and N increases the hardenability of the central thickness layer in the cooling process after the siliconization treatment, so that the permeability of that portion is reduced and the effect of concentrating the magnetic flux on the surface layer is increased, thereby reducing eddy current loss. Each is effective. If each is less than the lower limit, the effect of addition is poor, whereas if the upper limit is exceeded, embrittlement tends to occur.
浸珪処理を施す前の低炭素鋼板の製造方法について、特に制限はなく、従来公知の方法いずれもが好適に使用することができる。例えば、前記した鋼板の板厚中央層の成分組成になるスラブを、加熱後、熱間圧延を施し、冷間圧延または1回もしくは2回以上の中間焼鈍を挟む冷間圧延を繰り返して所定の板厚の鋼板とすれば良い。また、必要に応じ仕上げ焼鈍を施してもよい。 Next, the suitable manufacturing method of the low carbon steel plate of this invention is demonstrated.
There is no restriction | limiting in particular about the manufacturing method of the low carbon steel plate before performing a siliconization process, Any conventionally well-known method can be used conveniently. For example, the slab having the composition of the plate thickness center layer of the steel plate is heated and then subjected to hot rolling, and cold rolling or cold rolling with one or more intermediate annealings is repeated to obtain a predetermined slab. A thick steel plate may be used. Moreover, you may give finish annealing as needed.
ここに、Siを浸透(浸珪)させる方法としては、従来公知の方法をいずれも適用することができるが、例えば、気相浸珪法、液相浸珪法、固相浸珪法等が挙げられる。また、その際に使用するSi系のガスは、特に限定はないが、シランガス、例えば、四塩化珪素、トリクロロシラン、ジクロロシラン、モノシラン、ジシランの内から選んだ1種または2種以上のガスであることが望ましい。
以下に、気相浸珪法によってSiを浸透させる方法について説明する。 The steel plate obtained as described above is subjected to a siliconization treatment to increase the Si concentration of the surface layer. After forming a ferrite phase having a Si content of 3 to 5% on the surface layer of the steel plate, the Si in the steel is reduced. The low carbon steel sheet of the present invention can be produced by cooling before homogenization.
Here, as a method of infiltrating (siliciding) Si, any conventionally known method can be applied. For example, a vapor phase siliconization method, a liquid phase siliconization method, a solid phase siliconization method, or the like can be used. Can be mentioned. In addition, the Si-based gas used at that time is not particularly limited, but is a silane gas such as one or more gases selected from silicon tetrachloride, trichlorosilane, dichlorosilane, monosilane, and disilane. It is desirable to be.
Hereinafter, a method of infiltrating Si by vapor phase siliconization will be described.
式1:1.3×10-4≦(Σtk×exp(-25000/Tk))/(d2×[mass%Si]add)≦2.2×10-4 In the present invention, when siliconizing is performed on a low carbon steel sheet having a Si concentration of 1% or less, performing the siliconizing process under a condition satisfying the following formula 1 particularly reduces the high-frequency iron loss significantly. It is preferable for obtaining a Si concentration distribution.
Formula 1: 1.3 × 10 −4 ≦ (Σt k × exp (−25000 / T k )) / (d 2 × [mass% Si] add ) ≦ 2.2 × 10 −4
なお、本発明では、炉内温度が変化する場合、Σtk×exp(-25000/Tk)の値が同じとなるような、一定温度および一定時間で熱処理したものとみなすことができる。例えば、1200℃から700℃までを5分間で冷却する場合、Σtk×exp(-25000/Tk)≒1.9×10-6であり、1200℃一定とした場合は、tkの値が45秒となる。従って、上記冷却は、1200℃で45秒間の熱処理を受けたものと同じであるとみなすことができる。 Here, T k is the temperature of each zone in the furnace through which the steel plate passes after the start of the siliconization treatment, t k is the residence time of the steel plate in each zone, d is the plate thickness (mm), [mass% Si] add Represents the amount of Si added to the steel sheet during the siliconization treatment (increase in the average Si concentration in the thickness direction).
In the present invention, when the furnace temperature changes, it can be considered that the heat treatment is performed at a constant temperature and a constant time so that the value of Σt k × exp (−25000 / T k ) is the same. For example, when cooling from 1200 ° C. to 700 ° C. in 5 minutes, Σt k × exp (-25000 / T k ) ≈1.9 × 10 −6 , and when 1200 ° C. is constant, the value of t k is 45 Second. Therefore, the cooling can be regarded as the same as that subjected to a heat treatment at 1200 ° C. for 45 seconds.
上記した工程を通る際、600℃未満で熱処理されるのであれば、鋼板の応力緩和は起こらず、高周波鉄損は上昇しない。しかしながら、600℃以上で熱処理される場合は、時間とともに内部応力が緩和していくために、その高周波鉄損は上昇することとなる。 The low carbon steel sheet that has been subjected to the siliconization treatment is subjected to a drying / baking process after the insulating coating is applied.
When passing through the above-described steps, if the heat treatment is performed at a temperature lower than 600 ° C., stress relaxation of the steel sheet does not occur, and high-frequency iron loss does not increase. However, when the heat treatment is performed at 600 ° C. or higher, the internal stress is relaxed with time, so that the high-frequency iron loss is increased.
式2:(Σt´k×exp(-25000/T´k))/(d2×[mass%Si]add)≦0.2×10-4 Therefore, we investigated the optimum thermal history for heat treatment in the range of 600-800 ° C. As a result, it was confirmed that the iron loss was lower than that of a uniform material having the same plate thickness and the same Si concentration as long as the following
Formula 2: (Σt ′ k × exp (−25000 / T ′ k )) / (d 2 × [mass% Si] add ) ≦ 0.2 × 10 −4
また前記の式1の場合と同様に、炉内温度が変化する場合は、Σt´k×exp(-25000/T´k)の値が同じとなるような、一定温度および一定時間で熱処理したものとみなすことができる。 Here, T'k is the temperature of the heat treatment process steel sheet is passed after the siliconizing treatment, t'k residence time of the steel sheet in each heat treatment step, d is the thickness (mm), [mass% Si ] add Represents the amount of Si added to the steel sheet during the siliconization treatment (increase in the average Si concentration in the thickness direction).
As in the case of Equation 1, when the furnace temperature changes, heat treatment is performed at a constant temperature and a constant time so that the value of Σt ′ k × exp (−25000 / T ′ k ) is the same. It can be regarded as a thing.
また、絶縁被膜の乾燥・焼付けを400℃以上でおこない、加工後に歪取り焼鈍を施す場合には、被膜の熱処理工程と歪取り焼鈍工程とを合計して、前記式2を満たすように温度および時間を設定することが好ましい。
以上より、磁芯完成までに施される熱処理の時間も考慮した製造条件を設定することができる。 The low-carbon steel sheet that has been subjected to the siliconization treatment is assembled as an iron core through various processing steps such as slitting, shearing, pressing, and the like, and may be subjected to strain relief annealing. Also in this case, since the internal stress is relieved by annealing at 600 ° C. or higher, it is preferable to set the strain relief annealing temperature and time so as to satisfy the above-mentioned
In addition, when the insulating coating is dried and baked at 400 ° C. or more and subjected to strain relief annealing after processing, the heat treatment step and strain relief annealing step of the coating are totaled, and the temperature and It is preferable to set the time.
From the above, it is possible to set the manufacturing conditions in consideration of the time for the heat treatment performed until the completion of the magnetic core.
表2に示す成分組成になる試料を圧延して、板厚:0.2mmとした後、1200℃に加熱し、SiCl4+N2雰囲気で3%Si相当の浸珪処理およびSi拡散処理をあわせて3分間行った後、室温まで10℃/minで冷却した。
これら試料の高周波鉄損を、エプスタイン試験法(JIS C 2550)により測定した。結果を、表層および板厚中央層のSi濃度と共に、表3に示す。 <Example 1>
A sample having the component composition shown in Table 2 was rolled to a sheet thickness of 0.2 mm, heated to 1200 ° C., and subjected to siliconizing treatment equivalent to 3% Si and Si diffusion treatment in a SiCl 4 + N 2 atmosphere. After 3 minutes, it was cooled to room temperature at 10 ° C./min.
The high frequency iron loss of these samples was measured by the Epstein test method (JIS C 2550). The results are shown in Table 3 together with the Si concentrations of the surface layer and the plate thickness center layer.
表2にNo.2~5として示した試料に対して、磁化する方向と平行に±50MPaの圧縮応力を付与して鉄損の変化を調査した。これらの高周波鉄損は、エプスタイン試験法(JIS C 2550)により測定した。
得られた結果を表4に示す。 <Example 2>
The samples shown as Nos. 2 to 5 in Table 2 were subjected to a change in iron loss by applying a compressive stress of ± 50 MPa parallel to the magnetization direction. These high-frequency iron losses were measured by the Epstein test method (JIS C 2550).
Table 4 shows the obtained results.
Claims (7)
- Si:1.0 質量%以下、C:0.02~0.16質量%、Mn:0.3~2.0質量%、P:0.03質量%以下およびS:0.01質量%以下を含み、残部Feおよび不可避的不純物の組成であり、パーライト相、ベイナイト相およびマルテンサイト相のうちいずれか1種また2種以上を含むフェライト混合組織である板厚中央層と、Si:3~5質量%、C:0.02~0.16質量%、Mn:0.3~2.0質量%、P:0.03質量%以下およびS:0.01質量%以下を含み、残部Feおよび不可避的不純物の組成であり、フェライト単相である表層とからなるクラッド型の低炭素鋼板であって、該表層が内部応力として70~160MPaの面内引張応力を有することを特徴とする低炭素鋼板。 Si: 1.0% by mass or less, C: 0.02 to 0.16% by mass, Mn: 0.3 to 2.0% by mass, P: 0.03% by mass or less and S: 0.01% by mass or less, and the balance is Fe and inevitable impurities. A plate thickness central layer which is a ferrite mixed structure containing one or more of pearlite phase, bainite phase and martensite phase, Si: 3 to 5 mass%, C: 0.02 to 0.16 mass%, Mn: It is a clad-type low-carbon steel plate comprising 0.3 to 2.0% by mass, P: 0.03% by mass or less and S: 0.01% by mass or less, the composition of the balance Fe and inevitable impurities, and a surface layer that is a ferrite single phase. A low carbon steel sheet, wherein the surface layer has an in-plane tensile stress of 70 to 160 MPa as an internal stress.
- 前記表層の合計厚みが、全板厚の30~60%であることを特徴とする請求項1に記載の低炭素鋼板。 The low-carbon steel sheet according to claim 1, wherein the total thickness of the surface layer is 30 to 60% of the total sheet thickness.
- 前記低炭素鋼板の板厚が、0.05~0.35mmであることを特徴とする請求項1または2に記載の低炭素鋼板。 The low-carbon steel sheet according to claim 1 or 2, wherein a thickness of the low-carbon steel sheet is 0.05 to 0.35 mm.
- 前記低炭素鋼板の板厚中央層および表層が、さらにAl:0.002~0.6質量%、Cr:0.01~1.5質量%、V:0.0005~0.1質量%、Ti:0.0005~0.1質量%、Nb:0.0005~0.1質量%、Zr:0.0005~0.1質量%、B:0.0005~0.01質量%およびN:0.002~0.01質量%の内から選んだ1種または2種以上の元素を含むことを特徴とする請求項1~3いずれかに記載の低炭素鋼板。 The sheet thickness center layer and the surface layer of the low-carbon steel plate are further Al: 0.002-0.6 mass%, Cr: 0.01-1.5 mass%, V: 0.0005-0.1 mass%, Ti: 0.0005-0.1 mass%, Nb: 0.0005- 2. One or more elements selected from 0.1% by mass, Zr: 0.0005 to 0.1% by mass, B: 0.0005 to 0.01% by mass and N: 0.002 to 0.01% by mass are included. 4. The low carbon steel plate according to any one of 3 to 3.
- Si:1.0%質量以下、C:0.02~0.16質量%、Mn:0.3~2.0質量%、P:0.03質量%以下およびS:0.01質量%以下を含み、残部Feおよび不可避的不純物からなる鋼板を加熱し、1050~1250℃のオーステナイト域において、Si系のガスと反応させることにより、該鋼板の表層にSi含有量:3~5質量%のフェライト相を形成したのち、鋼中Siが均一化する前に冷却することを特徴とする低炭素鋼板の製造方法。 Heating a steel plate containing Si: 1.0% by mass or less, C: 0.02 to 0.16% by mass, Mn: 0.3 to 2.0% by mass, P: 0.03% by mass or less and S: 0.01% by mass or less, the balance being Fe and inevitable impurities Then, in the austenite region of 1050 to 1250 ° C., by reacting with a Si-based gas, a ferrite phase having a Si content of 3 to 5% by mass is formed on the surface layer of the steel sheet, and then Si in the steel is homogenized. A method for producing a low-carbon steel sheet, characterized by cooling before.
- 前記Si系のガスは、四塩化珪素、トリクロロシラン、ジクロロシラン、モノシラン、ジシランの内から選んだ1種または2種以上のガスであることを特徴とする請求項5に記載の低炭素鋼板の製造方法。 6. The low carbon steel sheet according to claim 5, wherein the Si-based gas is one or more gases selected from silicon tetrachloride, trichlorosilane, dichlorosilane, monosilane, and disilane. Production method.
- 前記鋼板が、さらに、Al:0.002~0.6質量%、Cr:0.01~1.5質量%、V:0.0005~0.1質量%、Ti:0.0005~0.1質量%、Nb:0.0005~0.1質量%、Zr:0.0005~0.1質量%、B:0.0005~0.01質量%およびN:0.002~0.01質量%の内から選んだ1種または2種以上の元素を含有することを特徴とする請求項5または6に記載の低炭素鋼板の製造方法。 The steel sheet is further made of Al: 0.002-0.6% by mass, Cr: 0.01-1.5% by mass, V: 0.0005-0.1% by mass, Ti: 0.0005-0.1% by mass, Nb: 0.0005-0.1% by mass, Zr: 0.0005- The low carbon according to claim 5 or 6, which contains one or more elements selected from 0.1% by mass, B: 0.0005 to 0.01% by mass and N: 0.002 to 0.01% by mass. A method of manufacturing a steel sheet.
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