WO2011105054A1 - 方向性電磁鋼板の製造方法 - Google Patents
方向性電磁鋼板の製造方法 Download PDFInfo
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
- C21D1/76—Adjusting the composition of the atmosphere
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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
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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
- 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
- C21D8/1266—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 between cold rolling steps
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- C—CHEMISTRY; METALLURGY
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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
- 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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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
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- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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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
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
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- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
Definitions
- the present invention relates to a method for producing a grain-oriented electrical steel sheet, and more particularly to a method for producing a grain-oriented electrical steel sheet having extremely low iron loss.
- Electromagnetic steel sheets are widely used as iron core materials for transformers and generators.
- grain-oriented electrical steel sheets are highly integrated in the ⁇ 110 ⁇ ⁇ 001> orientation, which is called the Goss orientation, and directly leads to reduction of energy loss in transformers and generators. It has excellent iron loss characteristics.
- As means for reducing this iron loss characteristic reduction of plate thickness, increase of Si content, improvement of orientation of crystal orientation, application of tension to steel plate, smoothing of steel plate surface, or refinement of secondary recrystallized grains Etc. are effective.
- Patent Documents 1 to 4 and others describe a method of rapid heating at the time of decarburization annealing, or a rapid reheating process immediately before decarburization annealing to form a primary recrystallized texture.
- a method for improving is disclosed.
- Patent Document 5 discloses a method for producing a grain-oriented electrical steel sheet using a component system material (hereinafter referred to as inhibitor-free system) that does not contain a precipitation type inhibitor such as AlN, MnS, and MnSe.
- JP-A-8-295937 Japanese Patent Laid-Open No. 2003-96520 Japanese Patent Laid-Open No. 10-280040 JP-A-6-49543 Japanese Patent No. 3707268
- a method for stably obtaining the iron loss reduction effect by rapid heating treatment when performing primary recrystallization annealing including rapid heating treatment, a method for stably obtaining the iron loss reduction effect by rapid heating treatment.
- the purpose is to propose.
- the directional temperature distribution was found to be an important factor. In other words, when the rapid heat treatment and primary recrystallization annealing were experimentally performed in separate facilities, refinement of secondary recrystallized grains had progressed. It is considered that the temperature distribution in the width direction caused by rapid heating has been eliminated since the temperature becomes around room temperature.
- the structure of the primary recrystallization annealing equipment is rapidly cooled, then once cooled, further heated and soaked.
- the structure for example, a rapid reheating zone, a first cooling zone, a heating zone, a soaking zone, and a recrystallization annealing facility for grain-oriented electrical steel sheets having a second cooling zone, in particular, controlling the conditions of the first cooling zone and the heating zone I have just clarified that it is important. The experimental results that led to this finding will be described below.
- a steel slab containing the components shown in Table 1 is manufactured by continuous casting. After heating the slab at 1200 ° C, it is finished into a hot-rolled sheet with a thickness of 1.8 mm by hot rolling and heated at 1100 ° C for 80 seconds. The steel sheet was annealed. Subsequently, the sheet thickness was 0.30 mm by cold rolling and primary recrystallization annealing was performed in a non-oxidizing atmosphere. During this primary recrystallization annealing, first, the direct heating method (electric heating method) is rapidly heated to 600-800 ° C at a temperature increase rate of 20-300 ° C / s, and then the indirect heating method (gas heating using a radiant tube). System) was heated to 900 ° C. at an average heating rate of 55 ° C./s and held at 900 ° C. for 100 seconds. The temperature is the temperature at the center in the plate width direction.
- the direct heating method electric heating method
- 600-800 ° C at a temperature increase rate of 20-300
- Method i First, it is rapidly heated to 800 ° C at a temperature rising rate of 600 ° C / s by an electric heating method, once at a certain temperature, that is, 800 ° C (not cooled), 750 ° C, 700 ° C, 650 ° C, 600 ° C, 550 ° C and After cooling to each temperature of 500 ° C., the mixture was heated to 850 ° C. at an average temperature increase rate of 20 ° C./s by a gas heating method using a radiant tube, and held at 850 ° C. for 200 seconds. Cooling was performed by introducing a cooling gas into the system (gas cooling).
- Method ii Further, by a gas heating method using a radiant tube, heating was performed at an average temperature increase rate of 35 ° C./s up to 700 ° C., and then at an average temperature increase rate of 5 ° C./s up to 850 ° C., and held at 850 ° C. for 200 seconds.
- an annealing separator containing MgO as a main component was applied and finish annealing was performed. Finish annealing was performed in a dry hydrogen atmosphere at 1200 ° C. for 5 hours. After finish annealing, after removing the unreacted annealing separator, a tension coat composed of 50% colloidal silica and magnesium phosphate was applied to obtain a product. The temperature is the temperature at the center in the plate width direction.
- FIG. 2 shows the relationship between the maximum temperature difference in the plate width direction and the iron loss characteristics of the outer winding portion of the product coil.
- the temperature difference in the width direction during soaking is iron. It has a particularly great influence on the loss characteristics, and in order to obtain good iron loss characteristics, it is necessary to set the temperature difference in the width direction during soaking to 5 ° C. or less. From this, it was found that it is essential that the ultimate plate temperature be once 700 ° C. or less after rapid heating. Moreover, in the case where rapid heating was not performed (Method ii), the temperature distribution in the width direction during soaking was very good, but the iron loss characteristics were greatly inferior. Incidentally, in the case of component system B containing an inhibitor, as shown in FIG. 3, the temperature difference in the width direction during soaking does not significantly affect the iron loss characteristics.
- an annealing separator mainly composed of MgO was applied and finish annealing was performed. Finish annealing was performed in a dry hydrogen atmosphere at 1250 ° C. for 5 hours. After finish annealing, after removing the unreacted annealing separator, a tension coat composed of 50% colloidal silica and magnesium phosphate was applied to obtain a product. The temperature is the temperature at the center in the plate width direction.
- Table 5 shows the temperature distribution in the width direction in each step.
- Rapid heating is not performed (Method iv)
- the temperature distribution during soaking is 5 ° C. or less under all conditions.
- the heating rate of the heating zone is 40 ° C./s. If it is not set below, the temperature distribution in the width direction caused by rapid heating is not eliminated, and desired iron loss characteristics are not obtained at a heating rate exceeding 40 ° C./s. From this, it can be said that the heating rate of the heating zone needs to be 40 ° C./s or less.
- the present invention is based on the above-described knowledge, and the gist configuration is as follows.
- the steel slab having a composition of the remaining Fe and unavoidable impurities is rolled to the final plate thickness after reducing the content of Al as an inhibitor component to 100 ppm or less, N, S and Se to 50 ppm or less, respectively,
- the primary recrystallization annealing is performed by heating to a temperature range of 700 ° C.
- a method for producing a grain-oriented electrical steel sheet characterized by heating to a soaking temperature under the following conditions.
- the steel slab is further comprised of Ni: 0.03 to 1.50% by mass, Sn: 0.01-1.50% by mass, Sb: 0.005-1.50 mass%, Cu: 0.03-3.0 mass%, P: 0.03-0.50 mass%, Mo: 0.005-0.10% by mass and Cr: 0.03-1.50% by mass 1 or 2 types or more chosen from among these,
- the steel slab is hot-rolled and then subjected to one or more cold rollings or two or more cold rollings sandwiching intermediate annealing to obtain a final sheet thickness (1)
- Recrystallization annealing equipment for grain-oriented electrical steel sheets having a rapid heating zone, a first cooling zone, a heating zone, a soaking zone, and a second cooling zone.
- Si 2.0-8.0% Si is an element effective in increasing the electrical resistance of steel and improving iron loss. However, if the content is less than 2.0%, the effect of addition is poor. On the other hand, if it exceeds 8.0%, the workability is remarkable. The amount of Si was limited to the range of 2.0 to 8.0% because the magnetic flux density also decreased.
- Mn 0.005 to 1.0%
- Mn is an element necessary for improving the hot workability, but if it is less than 0.005%, there is no effect, and if it exceeds 1.0%, the magnetic flux density of the product plate decreases, so 0.005 to 1.0% is set. .
- the inhibitor component is contained, high temperature slab heating at about 1400 ° C. is essential and the production cost increases, so the inhibitor component needs to be reduced as much as possible. Therefore, in order to enable production at a low temperature slab heating of about 1200 ° C., the inhibitor components are Al: 100 ppm (0.01%), N: 50 ppm (0.005%), S: 50 ppm (0.005%) and Se: 50 ppm, respectively. (0.005%) is the upper limit. Although it is desirable to reduce such components as much as possible from the viewpoint of magnetic properties, it is not a problem to remain within the above range.
- Ni 0.03-1.50%
- Sn 0.01-1.50%
- Sb 0.005-1.50%
- Cu 0.03-3.0%
- P 0.03-0.50%
- Mo 0.005-0.10%
- Cr 0.03-1.50%
- At least one selected from Ni is a useful element that improves the hot rolled sheet structure and improves the magnetic properties.
- the content is less than 0.03%, the effect of improving the magnetic properties is small.
- the content exceeds 1.50%, secondary recrystallization becomes unstable and the magnetic properties deteriorate, so the Ni content is 0.03 to 1.50%.
- Sn, Sb, Cu, P, Cr, and Mo are elements that are useful for improving the magnetic properties, but if any of them is less than the lower limit of each component described above, the effect of improving the magnetic properties is small.
- Exceeding the upper limit of each component described above inhibits the development of secondary recrystallized grains, so Sn: 0.01 to 1.50%, Sb: 0.005 to 1.50%, Cu: 0.03 to 3.0%, P: 0.03 to It is necessary to make it contain in the range of 0.50%, Mo: 0.005-0.10% and Cr: 0.03-1.50%.
- a particularly preferred element is at least one selected from Sn, Sb and Cr.
- unavoidable impurities include O, B, Ti, Nb, V, and Ni, Sn, Sb, Cu, P, Mo, Cr, and the like, which are less than the above addition amount.
- a slab may be produced from the molten steel having this component composition by a normal ingot-making method or a continuous casting method, or a thin slab having a thickness of 100 mm or less may be produced by a direct continuous casting method.
- the slab is heated by a normal method and subjected to hot rolling, but may be immediately hot rolled without being heated after casting.
- hot rolling may be performed, or the hot rolling may be omitted and the process may proceed as it is.
- the hot-rolled sheet annealing temperature is preferably 800 ° C. or higher and 1100 ° C. or lower in order to develop a goth structure on the product plate. If the hot-rolled sheet annealing temperature is less than 800 ° C, the band structure in hot rolling remains, making it difficult to achieve a primary recrystallized structure of sized particles, which hinders the development of secondary recrystallization. . When the hot-rolled sheet annealing temperature exceeds 1100 ° C., the grain size after the hot-rolled sheet annealing is too coarse, which is extremely disadvantageous in realizing a primary recrystallized structure of sized particles.
- the upper limit of the heating rate is preferably 600 ° C./s from the viewpoint of cost.
- the rapid heating method is preferably a direct heating method such as induction heating or current heating. In rapid heating, heating is performed until the coldest point in the plate width direction reaches 700 ° C or higher. A preferable upper limit is 820 ° C. from the viewpoint of cost. Furthermore, it is preferable to set it as the soaking temperature or less. The reason why the temperature is once cooled to a temperature range of 700 ° C.
- Cooling is performed so that the hottest point in the plate width direction is 700 ° C or lower.
- a preferred lower limit is 500 ° C. from the viewpoint of cost.
- the cooling method is preferably gas cooling.
- the subsequent heating to the soaking temperature is limited to a heating rate of 40 ° C./s or less.
- the lower limit is preferably 5 ° C./s or more from the viewpoint of cost. This heating is preferably an indirect heating method in which temperature distribution is less likely to occur.
- the indirect heating method includes, for example, atmosphere heating and radiation heating, but atmosphere heating (such as a gas heating method using a radiant tube) generally employed in a continuous annealing furnace is preferable in terms of cost and maintenance.
- atmosphere heating such as a gas heating method using a radiant tube
- the soaking temperature is preferably 800 to 950 ° C. from the viewpoint of optimizing the driving force of secondary recrystallization in the subsequent secondary recrystallization annealing.
- the equipment for performing the primary recrystallization annealing as described above includes, for example, a continuous annealing furnace composed of a rapid heating zone, a first cooling zone, a heating zone, a soaking zone, and a second cooling zone. Heating to reach 700 ° C or higher at a heating rate of 150 ° C / s or higher in the tropics, cooling to a temperature range of 700 ° C or lower in the first cooling zone, and heating at a heating rate of 40 ° C / s or lower in the heating zone are preferably performed respectively.
- the degree of atmospheric oxidation in the primary recrystallization annealing is not particularly limited, PH 2 O / PH 2 ⁇ 0.05, more preferably PH 2 O / PH, is desired in order to further stabilize the iron loss characteristics in the width direction and the longitudinal direction. 2 ⁇ 0.01 is preferable. This is because by suppressing the formation of subscales during primary recrystallization annealing, fluctuations in the width direction and longitudinal direction of the steel sheet nitriding behavior during secondary recrystallization performed by tight annealing are suppressed.
- secondary recrystallization annealing is performed.
- an annealing separator mainly composed of MgO is applied to the surface of the steel sheet.
- a known annealing separator such as silica powder or alumina powder that does not react with the steel sheet (does not form subscale on the steel sheet surface) is applied.
- a tension film is formed on the surface of the steel sheet thus obtained. This formation may be performed by a known method, and need not be limited to a specific method.
- a ceramic film made of nitride, carbide or carbonitride can be formed by using a vapor deposition method such as a CVD method or a PVD method.
- a vapor deposition method such as a CVD method or a PVD method.
- the iron loss characteristics were evaluated by collecting samples from three locations in the coil longitudinal direction.
- the coil outer winding and the inner winding are the end portions in the longitudinal direction, and the coil inner winding is the center portion in the longitudinal direction.
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Abstract
Description
表1に示す成分を含む鋼スラブを連続鋳造にて製造し、該スラブを1200℃にて加熱した後に、熱間圧延により板厚1.8mmの熱延板に仕上げ、1100℃で80秒の熱延板焼鈍を施した。ついで、冷間圧延により板厚0.30mmとし、非酸化性雰囲気にて一次再結晶焼鈍を施した。この一次再結晶焼鈍時は、まず、直接加熱方式(通電加熱方式)によって20~300℃/sの昇温速度で600~800℃まで急速加熱し、その後、間接加熱方式(ラジアントチューブによるガス加熱方式)によって、900℃まで55℃/sの平均昇温速度で加熱し、900℃で100秒間保持した。なお、温度は、板幅方向中央部の温度である。
表2に示す成分を含む鋼スラブを連続鋳造にて製造し、該スラブを1400℃にて加熱した後に、熱間圧延により板厚2.3mmの熱延板に仕上げ、1100℃で80秒の熱延板焼鈍を施した。ついで、冷間圧延により板厚0.27mmとし、雰囲気の水素分圧に対する水蒸気分圧の比である雰囲気酸化度:PH2O/PH2=0.35にて、一次再結晶焼鈍を施した。なお、一次再結晶焼鈍は、次の二つの方式で行った。
(方式i)
まず、通電加熱方式によって600℃/sの昇温速度で800℃まで急速加熱し、一旦ある温度、すなわち800℃(冷却せず)、750℃、700℃、650℃、600℃、550℃および500℃の各温度まで冷却し、その後、ラジアントチューブによるガス加熱方式によって、850℃まで20℃/sの平均昇温速度で加熱し、850℃で200秒間保持した。冷却は、冷却用のガスを系内に導入して行った(ガス冷却)。
(方式ii)
また、ラジアントチューブによるガス加熱方式によって、700℃までは平均昇温速度35℃/s、その後850℃までは5℃/sの平均昇温速度で加熱し、850℃で200秒間保持した。
ちなみに、インヒビターを含有する成分系Bの場合は、図3に示すように、均熱時の幅方向温度差が鉄損特性に大きな影響を与えることはない。
表4に示す成分を含む鋼スラブを連続鋳造にて製造し、スラブを1100℃にて加熱した後に、熱間圧延により板厚2.0mmの熱延板に仕上げ、950℃で120秒の熱延板焼鈍を施した。ついで、冷間圧延により板厚0.23mmの冷延板とし、雰囲気酸化度:PH2O/PH2=0.25にて一次再結晶焼鈍を施した。一次再結晶焼鈍は、次の二つの方式で行った。
(方式iii)
まず、直接加熱方式(誘導加熱方式)によって750℃/sの昇温速度で730℃まで急速加熱し、その後一度650℃までガス冷却した。次いで、間接加熱方式(ラジアントチューブによるガス加熱方式)によって、10~60℃/sの昇温速度で850℃まで加熱して、850℃で300秒間保持した。
(方式iv)
また、間接加熱方式(ラジアントチューブによるガス加熱方式)によって、700℃までは平均昇温速度60℃/s、その後850℃までは10~60℃/sの平均昇温速度で加熱し、850℃で300秒間保持した。
(1)C:0.08質量%以下、
Si:2.0~8.0質量%および
Mn:0.005~1.0質量%
を含み、かつインヒビター成分であるAlを100ppm以下、N、SおよびSeを各々50ppm以下に低減し、残部Feおよび不可避不純物の組成を有する鋼スラブを圧延して最終板厚とした後、一次再結晶焼鈍を施し、その後二次再結晶焼鈍を施す方向性電磁鋼板の製造工程において、
前記一次再結晶焼鈍は、700℃以上の温度域へ150℃/s以上の昇温速度で加熱し、その後、一旦700℃以下の温度域に冷却した後、平均昇温速度が40℃/s以下となる条件で均熱温度まで加熱することを特徴とする方向性電磁鋼板の製造方法。
Ni:0.03~1.50質量%、
Sn:0.01~1.50質量%、
Sb:0.005~1.50質量%、
Cu:0.03~3.0質量%、
P:0.03~0.50質量%、
Mo:0.005~0.10質量%および
Cr:0.03~1.50質量%
のうちから選ばれる1種または2種以上を含有することを特徴とする前記(1)または(2)に記載の方向性電磁鋼板の製造方法。
本発明の電磁鋼板を製造する際の溶鋼成分の限定理由を、以下に説明する。この成分に関する「%」および「ppm」表示は特に断らない限り質量%および質量ppmを意味する。
C:0.08%以下
Cは、0.08%を超えると製造工程中に磁気時効の起こらない50ppm以下までCを低減することが困難になるため、0.08%以下に限定する。また、下限に関しては、Cを含まない素材でも二次再結晶可能であるので特に設ける必要はないが、工業的には0%超えで含まれることがある。
Siは、鋼の電気抵抗を高め、鉄損を改善するのに有効な元素であるが、含有量が2.0%に満たないとその添加効果に乏しく、一方、8.0%を超えると加工性が著しく低下し、また磁束密度も低下するため、Si量は2.0~8.0%の範囲に限定した。
Mnは、熱間加工性を良好にするために必要な元素であるが、0.005%未満であると効果がなく1.0%を超えると製品板の磁束密度が低下するため、0.005~1.0%とする。
Ni:0.03~1.50%、Sn:0.01~1.50%、Sb:0.005~1.50%、Cu:0.03~3.0%、P:0.03~0.50%、Mo:0.005~0.10%およびCr:0.03~1.50%のうちから選んだ少なくとも1種
Niは、熱延板組織を改善して磁気特性を向上させる有用な元素である。しかしながら、0.03%未満では磁気特性の向上効果が小さく、一方1.50%を超えると二次再結晶が不安定になり磁気特性が劣化するため、Ni量は0.03~1.50%とする。
また、Sn、Sb、Cu、P、CrおよびMoはそれぞれ磁気特性の向上に有用な元素であるが、いずれも上記した各成分の下限に満たないと、磁気特性の向上効果が小さく、一方、上記した各成分の上限量を超えると、二次再結晶粒の発達が阻害されるため、それぞれSn:0.01~1.50%、Sb:0.005~1.50%、Cu:0.03~3.0%、P:0.03~0.50%、Mo:0.005~0.10%およびCr:0.03~1.50%の範囲で含有させる必要がある。
とくに好ましい元素は、Sn、SbおよびCrから選ばれる少なくとも1種である。
この急速加熱後に一旦700℃以下の温度域に冷却するのは、急速加熱時に発生した板幅方向温度分布を均熱過程までに解消させるためである。冷却は板幅方向の最も高温の点が700℃以下となるよう行う。好ましい下限は、コストの観点から500℃である。冷却方式は、ガス冷却が好ましい。同様の目的で、その後の均熱温度までの加熱は、昇温速度40℃/s以下に限定する。一方、下限は、コストの観点から5℃/s以上が好ましい。この加熱は温度分布が生じにくい間接加熱方式とすることが好ましい。間接加熱方式は、例えば、雰囲気加熱や輻射加熱などがあるが、連続焼鈍炉で一般的に採用されている雰囲気加熱(ラジアントチューブによるガス加熱方式など)がコストやメンテナンスの点で好ましい。なお、均熱温度は800~950℃とすることが、後続の二次再結晶焼鈍における二次再結晶の駆動力を最適化する観点から好ましい。
Claims (5)
- C:0.08質量%以下、
Si:2.0~8.0質量%および
Mn:0.005~1.0質量%
を含み、かつインヒビター成分であるAlを100ppm以下、N、SおよびSeを各々50ppm以下に低減し、残部Feおよび不可避不純物の組成を有する鋼スラブを圧延して最終板厚とした後、一次再結晶焼鈍を施し、その後二次再結晶焼鈍を施す方向性電磁鋼板の製造工程において、
前記一次再結晶焼鈍は、700℃以上の温度域へ150℃/s以上の昇温速度で加熱し、その後、一旦700℃以下の温度域に冷却した後、平均昇温速度が40℃/s以下となる条件で均熱温度まで加熱することを特徴とする方向性電磁鋼板の製造方法。 - 前記一次再結晶焼鈍における雰囲気酸化度PH2O/PH2を0.05以下とすることを特徴とする請求項1に記載の方向性電磁鋼板の製造方法。
- 前記鋼スラブは、さらに
Ni:0.03~1.50質量%、
Sn:0.01~1.50質量%、
Sb:0.005~1.50質量%、
Cu:0.03~3.0質量%、
P:0.03~0.50質量%、
Mo:0.005~0.10質量%および
Cr:0.03~1.50質量%
のうちから選ばれる1種または2種以上を含有することを特徴とする請求項1または2に記載の方向性電磁鋼板の製造方法。 - 前記鋼スラブに、熱間圧延を施し、ついで1回もしくは中間焼鈍を挟む2回以上の冷間圧延を施して最終板厚とすることを特徴とする請求項1、2または3に記載の方向性電磁鋼板の製造方法。
- 急速加熱帯、第一冷却帯、加熱帯、均熱帯および第二冷却帯を有する方向性電磁鋼板の再結晶焼鈍設備。
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Also Published As
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EP2540844A1 (en) | 2013-01-02 |
RU2532539C2 (ru) | 2014-11-10 |
CN102812133A (zh) | 2012-12-05 |
EP2540844A4 (en) | 2016-11-23 |
JP2011174138A (ja) | 2011-09-08 |
KR101445467B1 (ko) | 2014-09-26 |
TWI472626B (zh) | 2015-02-11 |
JP4840518B2 (ja) | 2011-12-21 |
EP2540844B1 (en) | 2017-11-22 |
TW201130996A (en) | 2011-09-16 |
US9574249B2 (en) | 2017-02-21 |
CN102812133B (zh) | 2014-12-31 |
BR112012021454A2 (pt) | 2016-05-31 |
KR20120118494A (ko) | 2012-10-26 |
RU2012140409A (ru) | 2014-03-27 |
BR112012021454B1 (pt) | 2018-06-19 |
US20130074996A1 (en) | 2013-03-28 |
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