WO2003002777A1 - Feuille en acier electromagnetique non orientee - Google Patents

Feuille en acier electromagnetique non orientee Download PDF

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Publication number
WO2003002777A1
WO2003002777A1 PCT/JP2002/006458 JP0206458W WO03002777A1 WO 2003002777 A1 WO2003002777 A1 WO 2003002777A1 JP 0206458 W JP0206458 W JP 0206458W WO 03002777 A1 WO03002777 A1 WO 03002777A1
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steel sheet
steel
oriented electrical
annealing
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PCT/JP2002/006458
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English (en)
Japanese (ja)
Inventor
Masaaki Kohno
Masaki Kawano
Atsuhito Honda
Akio Fujita
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Jfe Steel Corporation
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Application filed by Jfe Steel Corporation filed Critical Jfe Steel Corporation
Priority to EP02738812A priority Critical patent/EP1411138A4/fr
Priority to US10/481,919 priority patent/US20040149355A1/en
Priority to JP2003508741A priority patent/JP4329538B2/ja
Priority to KR1020037002839A priority patent/KR100956530B1/ko
Publication of WO2003002777A1 publication Critical patent/WO2003002777A1/fr
Priority to US11/978,406 priority patent/US20080060728A1/en

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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
    • 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
    • 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
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • 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
    • 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
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/14708—Fe-Ni based alloys
    • H01F1/14716—Fe-Ni based alloys in the form of sheets
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/14766—Fe-Si based alloys
    • H01F1/14775—Fe-Si based alloys in the form of sheets
    • 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

Definitions

  • the present invention relates to a non-oriented electrical steel sheet used as an iron core material in the Electric Sea.
  • non-oriented electrical steel sheets suitable for iron core materials such as reluctance motors or embedded magnet type DC brushless motors that require higher strength, which require high punching dimensional accuracy and high magnetic flux density, are also required. It concerns the manufacturing method.
  • Non-oriented electrical steel sheets are soft magnetic materials that are mainly used as iron core materials for electric motors and transformers. In order to improve the efficiency and reduce the size of these electrical devices, it is required that the magnetic steel sheets have low iron loss and high magnetic flux density.
  • Synchronous motors are generally surface magnet type (S PM) and embedded magnet type (I PM) DC brushless motors, and reluctance motors that use reluctance strikes generated by the magnetic saliency of the rotor and stator. are categorized. Above all, in the case of a reluctance motor, the amount of generated torque depends on the shapes of the rotor and the stator, the gap between the stator and the stator, and the magnetic flux density of the material. Therefore, as a core material for a reluctance motor, high magnetic flux density and high dimensional accuracy in punching are more important than other motors. In addition, with the progress of inverters, the number of poles tends to increase with higher speeds in order to improve motor efficiency and torque. Since these are all elements that increase the operating frequency, not only the conventional magnetic characteristics at the commercial frequency (50 to 60 Hz), but also 400 Hz It is also necessary to improve the magnetic characteristics in the high frequency range.
  • Si content In order to reduce the iron loss of non-oriented electrical steel sheets, it is common to increase the Si content.For example, about 3.5 mass% of Si is added to the highest grade non-oriented electrical steel sheets. There are ⁇ However, as the Si content increases, the iron loss decreases, but the magnetic flux density also decreases.
  • low-grade non-oriented electrical steel sheets have a relatively high magnetic flux density due to the reduced Si content, but have the problem of high iron loss.
  • Japanese Patent Application Laid-Open No. Sho 62-267421 discloses a non-directional steel sheet having an Si content of 0.6 mass% or less and an A1 content of 0.15 to 0.60 mass%.
  • the amount of impurities such as C, S, N, and O is regulated to reduce inclusions and harmlessness that hinder crystal grain growth, promote grain growth, and reduce iron loss. Techniques to achieve this have been proposed.
  • the grain growth of such a low Si steel involves a reduction in strength, there is a problem that the punching surface becomes droopy and has a large force during punching, resulting in a marked decrease in punching performance.
  • Japanese Patent Application Laid-Open No. 56-130425 discloses A technique for improving the punchability by adding less than 0.2 raass% of P is disclosed.
  • Japanese Patent Application Laid-Open No. 2-66138 discloses a technique for positively adding P to low-Si steel, in which the amount of Si is suppressed to 0.1 mass% or less and A1 is set to 0.1 to 1.0 mass%. % To the A1-added steel in the range of 0: 25% by mass, and the magnetic effect is improved by the combined effect of A1 and P. A method to improve is disclosed.
  • non-oriented electrical steel sheets are common properties desired for all applications of non-oriented electrical steel sheets such as various motors and transformers.
  • non-oriented electrical steel sheet material for reluctance motors particularly high magnetic flux density and high dimensional accuracy are important in terms of operation principle.
  • non-oriented electrical steel sheets that have been considered to be able to respond to the recent high-speed rotation of motors and the high frequencies associated with multi-polarization have been developed. Had not been found.
  • the present invention has been developed in view of the above-mentioned current situation, and is provided with iron core materials such as motors and transformers,
  • Electromagnetic steel sheet that combines high magnetic flux density, high-strength characteristics that are important from the viewpoint of high-speed rotation of the rotor and prevention of scattering of embedded magnets, along with dimensional accuracy
  • the sum of Si and A1 is about 0.03raass% or more and 0.5raass% or less for low Si steel, and those for which the sum of Si and A1 exceeds 0.5mass% are medium to high. It is called Si steel.
  • the inventors of the present invention have conducted intensive studies to achieve the above object, and as a result, the amount of Si and A1 has been reduced to a low Si steel level, and the saturation magnetic flux density has been essentially reduced.
  • the average crystal grain size By adjusting the average crystal grain size to a predetermined range and adding an appropriate amount of P, it is possible to obtain excellent magnetic properties such as high magnetic flux density, low force, and low iron loss. It was found that the punching dimensional accuracy was significantly improved.
  • the addition of an appropriate amount of P has the effect of improving the punching dimensional accuracy.
  • the present invention is based on the above findings. That is, the gist configuration of the present invention is as follows. 1. in mass percentage
  • Si and Z or Al 0.03% or more, 0.5% or less in total
  • Average grain size ⁇ ⁇ or more, 80 m or less
  • Non-oriented electrical steel sheet with excellent magnetic properties and punching accuracy.
  • the steel sheet further increases by mass percentage.
  • the steel sheet further increases by mass percentage.
  • a non-oriented electrical steel sheet excellent in magnetic properties and punching accuracy characterized by containing:
  • a non-oriented electrical steel sheet according to 1, 2, or 3 above characterized in that the steel sheet has a thickness of 0.35 or less or less, and is excellent in magnetic properties and punching accuracy.
  • PA -0.2XSi + 0.12XMn- 0.32XA1 + 0.05XNi 2 +0.10 Ni + 0.36
  • the balance consists of Fe and inevitable impurities, and is a magnetic steel sheet with excellent magnetic properties and excellent punching accuracy.
  • a non-oriented electrical steel sheet with excellent strength, magnetic properties, and excellent punching accuracy In the above-mentioned steel types, as the secondary contained elements, Ca: 0.01% or less, B: 0.005% or less, Cr: 0.1% or less, Cu: 0.1% or less, Mo: 0.1% or less. It may contain at least one of 1% or less.
  • Hot rolling is performed on the steel slab having the composition described in any one of 1 to 3 above under the condition that the heating temperature is in the austenite single-phase region and the coil winding temperature is 650 or less. After descaling, after cold rolling once or twice including intermediate annealing, finish annealing in ferrite single phase region with 700 or more. Manufacturing method of excellent non-oriented electrical steel sheet.
  • Hot rolling was performed on the steel slab having the composition described in any of the above 1 to 3 under the following conditions: the heating temperature was in the austenite single phase region, and the coil winding temperature was 650: Then, when the Ni content is 0% (no addition) to 1.0 mass%, the hot-rolled sheet is annealed in a ferrite single-phase region of 900 or more or an austenite single-phase region of more than 3 points of Ac. Ni content exceeds 1.0 mass%, 2.3 mass 0 /.
  • Hot rolling is performed on the slab of 5 or 6 above at a hot rolling heating temperature of 100 000 ⁇ to 120 000 ° and a hot rolling coiling temperature of 65 O or less.
  • a method for producing a non-oriented electrical steel sheet having excellent strength, magnetic properties, and punching precision comprising performing cold rolling once or twice including intermediate annealing, and then performing finish annealing.
  • hot-rolled sheet annealing may be performed after hot-rolling.
  • a treatment for providing an insulating film may be performed.
  • FIG. 2 is a graph showing the effect of Si content and P content on the relationship between yield strength and punching anisotropy.
  • FIG. 3 is a graph showing the influence of the Si content and the P content on the relationship between the average crystal grain size and the punched diameter.
  • FIG. 4 is a graph showing the influence of the Si content and the P content on the relationship between the average grain size and the punching anisotropy.
  • FIG. 5 is a graph showing the effect of the Si content and the P content on the relationship between the average crystal grain size and iron loss.
  • FIG. 6 is a graph showing the influence of the Si content and the P content on the relationship between the average crystal grain size and the magnetic flux density.
  • FIG. 7 is a graph showing the effect of Si content and P content on the relationship between iron loss and magnetic flux density.
  • Figure 8 is a graph showing the effect of Si and P contents on the occurrence of layered cracks.
  • Figure 9 is a graph showing the effect of Si and Ni contents on the occurrence of layered cracks.
  • FIG. 10 is a graph showing the effect of Si content and Ni addition on the relationship between P content and punched diameter.
  • FIG. 11 is a graph showing the effect of Si content and Ni addition on the relationship between P content and punching anisotropy.
  • FIG. 12 is a graph showing the effect of the P content on the relationship between the tensile strength and the magnetic flux density.
  • FIG. 13 is a graph showing the relationship between and and high-frequency iron loss.
  • FIG. 14 is a graph showing the relationship between the plate thickness and the magnetic flux density.
  • these steel materials were heated at 1100 for 60 rains, hot-rolled to a plate thickness of 2 ram, kept at a uniform temperature equivalent to coil winding of 2 h at 600, and allowed to cool. Then, after hot-rolled sheet annealing at 900 for 60 s, pickling and then cold-rolled to a sheet thickness of 0.5 ram, finish annealing at various temperatures of 700 to 900 ⁇ , and recrystallized grains The particle size of was varied. Thereafter, a sample prepared by applying and baking semi-organic insulating material having an average film thickness of 0.6; / m to the finish annealed plate was prepared and subjected to a punching test. The average crystal grain size was defined as the equivalent circle diameter determined by the Jeffries method by observing a cross section in the thickness direction parallel to the rolling direction.
  • the punching test was performed using a circular mold having a diameter of 21 ⁇ , and the clearance was set to 8% of the plate thickness. Measure the diameter (inner diameter) of the punched circle in four directions with angles of 0 °, 45 °, 90 °, and 135 ° to the rolling direction, determine the average diameter of the four points, and determine the maximum diameter among the four points. The difference between the diameter and the minimum diameter was measured and used as an index of punching anisotropy.
  • Figures 1 and 2 summarize the results obtained in relation to the yield strength (YP) obtained from tensile test pieces (JIS No. 5) cut out in the rolling direction.
  • Figures 3 and 4 summarize these relationships in relation to the average grain size of the finish annealed sheet.
  • the steel with the varied amount of Si has poor punching dimensional accuracy and punching anisotropy as the grain size increases, while P is 0.13% or more.
  • the added steel has a good level of punching dimensional accuracy and punching anisotropy even if the grain size is large.
  • the inventors made the steel whose magnetic flux density was essentially high as a material, and examined the manufacturing conditions and magnetic properties. The relationship was discussed in detail.
  • Figure 5 shows the crystal grain size of the finished annealed sheet and iron loss in the commercial frequency range for samples with a steel thickness of 0.5 ram (Wis / 50: value at a frequency of 50 Hz and maximum magnetic flux density of 1.5 T). The results of an investigation on the relationship between and are shown.
  • low Si is disadvantageous for iron loss due to reduced electrical resistance, but iron loss varies greatly depending on the crystal grain size, so the grain size should be about 30 / zm or more. It can be seen that low iron loss can be obtained stably. Similarly, when the electric resistance was reduced to a low value of A1, it was also confirmed that setting the particle size to about 30 ⁇ or more was effective in reducing iron loss.
  • the average grain size of the finish-annealed sheet is limited to about 15 to 25 / z ra. It was customary. The reason for this is that, as shown in the example of 0.1% Si-0.07% P steel (marked in the figure) in Figs. .
  • Fig. 6 shows the relationship between the average crystal grain size and the magnetic flux density of each steel type
  • Fig. 7 shows the iron loss. The result of examining the relationship between and magnetic flux density is shown.
  • B 50 is a magnetic flux density at a magnetization force of 5000 A / m.
  • the slab heating temperature for hot rolling in the production of the steel sheet of the present invention should be in the austenite single phase region (or, if possible, the ferrite single phase). is important.
  • the austenite single phase region is further reduced due to the large amount of Si and A1, which are ferrite forming elements, and as a result, the ferrite austenite two phase region tends to be formed at the conventional heating temperature.
  • the problem became clear.
  • P exceeded 0.26% laminar cracking occurred under any composition conditions. Therefore, steels with various Si, Mn, AI, and P contents were manufactured at the research facility, and in the temperature range of about 100 to 1200 ⁇ 0, unbalanced P caused rolling failure.
  • the slab ripening temperature described above is a suitable temperature from the viewpoint of stabilizing the precipitation of carbon dioxide, nitride, sulfide and the like existing in the steel.
  • the amount of P added needs to be about 0.26% or less.
  • the amount of P added is within about 0.26% and the steel sheet is heated to the austenite single-phase or ferrite single-phase region during hot-rolling heating, layer cracks after cold rolling, etc.
  • the ferrite / austenite two-phase force B reduces the amount of P distribution to the ferrite phase even under heat conditions.
  • Ni which is an element suitable for improving magnetic properties and ensuring strength, is also effective in expanding the austenite region near the hot rolling temperature in P-added steel.
  • P F -0.34Si + 0.20Mn-0.54A1 + 0.24Ni 2 + 0.28Ni +0.76 ⁇ P (2) It was found that the degree of enrichment was small, and in each case, embrittlement due to P could be avoided.
  • Fig. 12 shows the relationship between the magnetic flux density B50 and the tensile strength TS of these samples.
  • TS was determined by the same tensile test as in Experiment 1, and the magnetic flux density was also measured by the method in Experiment 1.
  • the conditions for achieving both excellent magnetic flux density and punching dimensional accuracy include the amounts of Si, Al, P, and Ni in the steel, and the average crystal grain of the finish-annealed sheet for low-Si steel.
  • the diameter was specified in the following range. Low Si steel ⁇ ⁇ Si, Al 1 or 2 types total: about 0.03 ⁇ 0.5%
  • Si and Al have a deoxidizing effect when added to steel, they are used alone or in combination as deoxidizing agents. To achieve this effect, Si and Al must be used alone or in a total of about 0.03% or more. Also, Si and Al have the effect of increasing the specific resistance and improving the iron loss, but on the other hand, they lower the saturation magnetic flux density, so the upper limit was set to 0.5%. For medium to high Si steels, the sum of one or two types of Si and Al: more than 0.5% to about 2.5%
  • the total amount of Si + Al can be more than 0.5%.
  • the effect of the addition of P makes it possible to obtain a material with higher punching accuracy and strength / magnetic flux density compared to the conventional low P medium to high Si steel. can get.
  • the total amount of Si + Al exceeds 2.5%, ordinary cold rolling becomes difficult even by the method of the present invention, so the range is more than 0.5% to about 2.5%. %.
  • P is a particularly important element in the present invention.
  • P has a function of adjusting the material hardness by its high solid solution strengthening ability.
  • low-Si and low-Al steel sheets are relatively soft by nature, but in the present invention, the average grain size needs to be about 30 / m or more to reduce iron loss. There is a possibility that.
  • P is an essential element for improving the punching property of the steel sheet of the present invention, that is, for suppressing an increase in sagging and burrs due to insufficient strength of the steel sheet.
  • the effect of suppressing the total amount of deformation at the time of punching by increasing the breaking limit at the time of punching, and the effect of ⁇ 100 ⁇ w> Improve the punching dimensional accuracy by the combined effect of increasing the orientation and improving the anisotropy.
  • the strength of the steel sheet is increased, it does not lower the magnetic flux density. This effect is also exhibited in medium to high Si steel.
  • P In order to exhibit these effects, P must be contained in an amount of about 0.10% or more.
  • P is originally a brittle element to steel, and if added excessively, it tends to cause ear cracks and layer cracks, which lowers the manufacturability.
  • the content exceeds about 0.26%, the production of P-added steel becomes difficult even if the production method of the present invention is used, so the P content is limited to the range of about 0.10 to about 0.26%. did.
  • Ni about 2.3% or less (can be added as an option)
  • Ni not only has the effect of improving the texture of the steel to increase the magnetic flux density, but also has the effect of increasing the electrical resistance of the steel to reduce iron loss, and has the effect of increasing the strength of the steel by solid solution strengthening. Since it also has the effect of suppressing drooling during punching, it can be added positively.
  • Ni is an austenite-forming element, it has the effect of expanding the austenite region ( ⁇ loop in the phase diagram) in the vicinity of the preferred slab heating temperature of 1000 to 1200. In particular, it is effective to increase the operation stability for steels with a composition of Si + Al greater than 0.5%. By utilizing this effect, the rolling instability that can occur when the brittle element P is positively added as in the present invention can be significantly improved. In other words, the point of stable production of high-P steel is to suppress excessive P bias during hot rolling, and to prevent the slab heating temperature from being in the ferrite-no-austenite two-phase region as an effective means. If the sum of the Si content and the A1 content exceeds 0.5%, it is easy to separate into two phases at the slab heating temperature.
  • the average grain size of the finish annealed sheet In low Si steel, the average grain size of the finish annealed sheet: about 30; zm or more, about 80 ⁇ or less In order to obtain good iron loss characteristics in the low Si, low A1 non-oriented electrical steel sheet of the present invention, As shown in Fig. 5, the average grain size of the finish-annealed sheet must be about 30 // m or more. However, even if the grain size exceeds about 80 / m, no further improvement in iron loss can be expected.
  • the steel according to the present invention is a transformed steel, and its slip single phase region is suitable for recrystallization annealing. Since the temperature is lower than that of ferritic single-phase steel with a high Si composition, excessive grain growth is disadvantageous in terms of productivity in continuous short-time annealing equipment. / im is the upper limit.
  • the alloy has an effect of improving electric resistance by the alloy and the like, and relatively low iron loss is easily obtained. Therefore, the grain size is not particularly limited and may be in a normal range. Generally, it is 20 to 200 / m.
  • the inventors studied a technique for improving magnetic characteristics in a high-frequency range, which has been gaining importance in recent years with the increase in the rotation speed and the number of poles of the motor. As a result, it was found that thickness reduction was effective, and the effect was particularly remarkable in low Si steel. The experiment which led to the result is shown below.
  • Figure 13 shows the loss of iron at 400Hz for 0.11% Si—0.18% P steel, 0.95% Si—0.02% P steel and 2.0% Si—0.5 ° / ⁇ 1 steel. The result of examining the thickness dependency is shown.
  • the high frequency iron loss tends to be improved because the eddy current loss of all samples decreases due to the reduction of the plate thickness. It can be seen that the effect is greater for the low Si steel.
  • non-oriented electrical steel sheets has so far been 0.50 mra, and further reductions in thickness are only applicable to some high-grade grades with high contents of Si and A1, which are specific resistance elements. As a result, there was no product example applied to non-oriented electrical steel sheets with low contents of Si and A1.
  • Fig. 14 shows the results of examining the dependence of the magnetic flux density of these materials on the plate thickness.
  • the magnetic flux density tends to decrease slightly, but the decrease is negligible, and the low Si steel is much higher at all sheet thicknesses. It has a magnetic flux density.
  • EV electric vehicle
  • HEV hybrid electric vehicle
  • high-speed rotation type reluctance motors are being studied.
  • high magnetic flux density and high frequency Low iron loss property is emphasized, but this can be dealt with by reducing the thickness of a steel sheet of low Si and low A1, which is essentially high in magnetic flux density as shown in the present invention.
  • the effect of reducing the thickness becomes significant when the thickness is about 0.35 or less, and becomes even more significant when the thickness is about 0.30 mm or less. Since the thinner the sheet, the more effective it is at reducing eddy current loss, no lower limit is set, but the number of man-hours for stacking the core increases and the cost increases, and it is difficult to caulk the laminated core. In the case of general production, the lower limit is preferably about 0.10 mm.
  • C is an element that deteriorates the magnetic properties (iron loss) with the passage of time after the steel machine due to the aging effect, and the degree becomes significant when the C content exceeds about 0.010%. Therefore, the C content was limited to 0.010% or less. In addition, as for the aging deterioration characteristics, the smaller the C content, the better. Therefore, in the present invention, the C content is substantially zero. Mouth (analysis limit full) shall be included.
  • Mn about 0.5% or less
  • n has the effect of fixing S as n S and suppressing embrittlement during hot rolling caused by Fe S.
  • the specific resistance increases and iron loss is improved.
  • an increase in the Mn content causes a decrease in the magnetic flux density, so the upper limit of the Mn content was set to about 0.5%.
  • S is an unavoidable impurity, and when precipitated as FeS as described above, it not only causes hot embrittlement but also deteriorates grain growth of finely precipitated ⁇ , reducing iron loss. From the viewpoint of, it is advantageous to reduce as much as possible.
  • the amount of S exceeds about 0.015%, the cost of iron loss deterioration becomes extremely large, so the upper limit was set to about 0.015%.
  • S also has the effect of improving the shear profile at the time of punching, so the extent of reduction is determined according to the application.
  • N is an inevitable contaminant impurity, and when finely precipitated as A1N, it inhibits grain growth and degrades iron loss. Therefore, N was restricted to about 0.010% or less.
  • the essential component and the suppressing component have been described.
  • the following elements can be appropriately contained as magnetic property improving components.
  • Sb and Sn are unevenly distributed at grain boundaries, and have the effect of improving magnetic flux density and iron loss by suppressing the generation of ⁇ 111 ⁇ oriented recrystallization nuclei from crystal grain boundaries during steel recrystallization.
  • Ca may be contained in a range of about 0.01% or less as an element for effectively trapping S present as an impurity together with Mn as a deoxidizing agent.
  • about 0.005% or less of B and about 0.1% or less of Cr can be added.
  • the effect of the present invention is not impaired by adding a known element such as Cu or Mo as an element which does not impair the magnetic properties, but the effect of the present invention is not impaired.
  • the content is about 0.1% or less.
  • the component is designed to be a single phase of either the austenite phase or the ferrite phase at the slab heating temperature, or it is in the two-phase state of austenite ferrite.
  • the composition is designed so that the amount of P enriched in the ferrite phase, which tends to enrich P more easily, is suppressed, excessive local segregation of P is suppressed, and a high-P-added steel is produced stably. It can be so.
  • the excess of P at the slab heating temperature (about 100 to 1200) that is suitable for the precipitation stability of carbides, nitrides, sulfides, etc. present in steel.
  • the slab heating temperature about 100 to 1200
  • P A -0. 2Si +0. 12Mn-0. 32A1 +0. Relationship between 05Ni 2 + 0. 10Ni + 0. 36 (1) and P content,
  • P F -0. 34Si +0. 20Mn-0. 54A1 + 0. 24Ni 2 + 0. 28Ni + 0. 76 (2) is,
  • PA was obtained by experimentally determining the upper limit of the P content of the austenitic single phase in the temperature range of about 1000 to 1200 for various Si, Mn, Al, and Ni compositions.
  • P F are those the P content is the lower limit that the ferrite single phase was determined experimentally.
  • this slab is subjected to hot rolling after heating.
  • the slab heating is preferably about 100 to 1200. Also, as mentioned above, the phase state during slab heating is extremely important for suppressing excessive local segregation of P.
  • P is a ferrite-forming element, it has the effect of reducing the austenite single-phase region near the slab heating temperature.However, in the case of low-Si steel, within the component range of the present invention, even if the slab heating temperature is about 1000 to 1200, For example, it can be a single phase of austenite. In the case of medium to high Si steel Further, if the component system satisfying the P ⁇ P A, the slab heating temperature is from about 1000: it can be single-phase austenite in the range of 1200O.
  • the segregation of P in the ferrite phase remains at a level that can avoid embrittlement even in the region where ferrite and austenite coexist. Further, even when the ferrite is heated in the single phase region of ferrite, if the P content is within about 0.26%, it can be produced without layer cracks or the like.
  • the coil winding temperature after hot rolling is also an important point in securing the productivity of high-P steel. That is, if the coil winding temperature is high, iron phosphating (Fe 3 P) is generated during cooling of the coil, and the bendability and rollability of the hot-rolled sheet are reduced.
  • the winding it is desirable to perform the winding at a temperature as low as possible, preferably about 600 ° or less, more preferably about 550 or less. It is also effective to accelerate the cooling of the coil by immersing the coil after winding into a water tank or by ifc-ing the coil. Then, the hot-rolled coil is subjected to cold rolling after descaling by a technique such as pickling, but hot-rolled sheet annealing can be performed to further improve the magnetic properties.
  • the hot-rolled sheet annealing temperature also avoid the ferrite-no-austenite coexistence region (two-phase region). This is because the growth of crystal grains does not easily progress in the annealing in the two-phase region, and improvement in magnetic properties such as magnetic flux density cannot be expected.
  • the preferred hot-rolled sheet annealing temperature in low Si steel will be described according to the amount of Ni.
  • the non-oriented electrical steel sheet is usually about 900% or more as in the case of hot-rolled sheet annealing.
  • ⁇ ⁇ ⁇ Can be annealed in the light single phase region.
  • the temperature of the slag can be increased to a single phase region of austenite (preferably about 1050 to 1100) with three or more Ac points. In short, it is important to avoid annealing (especially around 9503 ⁇ 4) in the two-phase region, which is the intermediate region between the two.
  • the austenite formation temperature during annealing decreases, so that a two-phase region is obtained even at an annealing temperature of about 900, The magnetic flux density decreases.
  • sufficient magnetic flux density cannot be obtained by annealing in the single phase region of ferrite below 900 due to insufficient grain growth. Therefore, the annealing condition of the hot rolled sheet in this component system is limited to the austenite single phase region (preferably about ⁇ ⁇ ⁇ ) above the Ac3 point. Limited.
  • the austenite single phase region preferably about ⁇ ⁇ ⁇
  • the annealing temperature of the hot-rolled sheet is not particularly limited, but is usually preferably in the range of 700 to 110 ⁇ . Then, after descaling, the obtained coil is rolled once in a cold or warm state, or is subjected to two or more cold (or warm) rolling steps with intermediate annealing to obtain a predetermined thickness. Finish.
  • finish annealing is performed.
  • this finish annealing is performed in the ferrite single phase region of 700: or more. This is because if the final annealing temperature is less than 700, it is difficult to stably grow the average grain size to about 30 m or more, and if austenite grains are formed beyond the ferrite single phase region, the aggregated yarn! ⁇ Is formed. This is because of deterioration, leading to deterioration of magnetic flux density and iron loss.
  • the grain growth during annealing is not as important as that of low Si steel, as described above.
  • the final annealing temperature is not particularly limited, but is usually in the range of 700 to 110. It is preferable that
  • the ferrite single-phase temperature range or austenite single-phase temperature range of the hot-rolled sheet and cold-rolled sheet is obtained by heating and water-cooling steel sheets of the same composition in various temperature ranges beforehand using an optical microscope. It can be determined by observing with such as. Alternatively, as another method, it can be estimated in advance from a calculation state diagram obtained by thermodynamic calculation software such as Thermo-Calc TM. After the finish annealing, an insulating coating can be applied in the same manner as a general non-oriented electrical steel sheet.
  • the application method is not particularly limited, but a method of performing a baking treatment after applying the treatment liquid is preferable.
  • the obtained coil is slit to the required width and dimensions, and then After punching into the shape of the motor stator and rotor, they are laminated and commercialized. Alternatively, in some cases, after punching, it is commercialized after being subjected to strain relief annealing (usually 750 Xl to 2 h).
  • Molten steel having the composition shown in Table 1 was smelted and incorporated in a laboratory, and then hot rolled to form a sheet par with a sheet thickness of 30 rara. Then, after heating for 1 min at 60 ° C, the plate was hot-rolled to a thickness of 2 mm, and at 600 at 2 hours for coil winding, and then allowed to cool. Then, after hot-rolled sheet annealing at 950 for 60 s, pickling is performed, then cold-rolled to 0.50 thickness (one-time cold-rolling), and finish annealing at various temperatures of 700 to 900 ⁇ . Thus, the recrystallized grain size was variously changed. In addition, during cold rolling, steel J with a P content exceeding the range of the present invention caused many layered cracks parallel to the sheet surface during cold rolling, and the subsequent processing was stopped and evaluation was not performed .
  • Nos. 56 to 59 were cold rolled by hot rolling twice without intermediate annealing at 800 without hot strip annealing.
  • samples were prepared by applying a semi-organic insulating film having an average film thickness of 0.6 to the obtained finish-annealed sheet and subjected to various tests.
  • the punching test was performed using a circular mold having a diameter of 21 ⁇ , and the clearance was 8% of the plate thickness.
  • the angle made with the rolling direction is 0. , 45 °, 90 °, 135.
  • the diameter of the circle (inner diameter) in four directions was measured, and the average diameter of the four points was determined.
  • the difference between the maximum diameter and the minimum diameter among the four points was taken as the index of punching anisotropy.
  • the magnetic properties were measured by the Epstein method using strip-shaped test pieces cut out to 180 mm x 30 mm so that the angles to the rolling direction were 0 ° and 90 °.
  • the YP As the diameter increases, the punching diameter tends to approach the die diameter.
  • steels G to H containing 0.10% or more of P as a low Si and A1 composition have good punching diameters even when YP is relatively low at 350 MPa or less. ⁇ Anisotropy of punch size is also small.
  • the average grain size of these steel grades was controlled to 30; zra or more (Nos. 37, 38, 39, 44, 45, 46, 47, 51, 52, 53, 53). 54, 59) have stable and low iron loss and high magnetic flux density.
  • Molten steel having the composition shown in Table 4 was smelted in a laboratory and made into a hot-rolled sheet with a thickness of 2 mm in the same manner as in Example 1. After annealing the hot-rolled sheet at 1100 ⁇ for 30 s After being pickled, it was cold rolled to a thickness of 0.50. Then, finish annealing was performed at various temperatures of 700 or more and in the ferrite single phase region to change the recrystallized grain size in various ways.
  • steels K to M have been subjected to deoxidation by A1 to reduce Si, and steel N, O, and steel Q, R are melted so that the effect of Ni addition can be evaluated. It was made.
  • any of the steel compositions satisfying the steel composition of the present invention and having an average crystal grain size of 30 ⁇ or more have excellent punching dimensional accuracy, low punching anisotropy, and magnetic properties.
  • steel ⁇ and steel 0 are compared, and steel Q and steel R are compared with each other, a remarkable improvement in magnetic flux density is observed in steel O and steel R to which Ni is added.
  • Example 3 Molten steel having the compositions shown in Table 1 (Steel F) and Table 4 (Steel N and Steel O) was smelted in a laboratory and made into a hot-rolled sheet with a thickness of 2 mm in the same manner as in Example 1. After the hot-rolled sheet was annealed at 1100 for 30 s, it was pickled and then cold-rolled to obtain various thicknesses of 0.50 to 0.2 rara. Next, finish annealing was performed at various temperatures of 700 ⁇ or more and in the ferrite single phase region, and the recrystallized grain size was controlled between 35 and 45 m.
  • the iron loss particularly at high frequencies tends to be remarkably improved.
  • the punching dimensional accuracy tends to improve with a decrease in the thickness, but steels N and O satisfying the composition range of the present invention are superior to comparative steel F.
  • the steel of the present invention is excellent in anisotropy of the punched size at any thickness.
  • Example 4 Molten steel having the composition shown in Table 7 was smelted in a laboratory and poured into a steel ingot, and was then soaked at 1150 X for 1 hour. And The obtained sheet bar was heated to the temperature (SRT) shown in Table 8 and held for 1 hour, then hot rolled to 2.0 mm, subjected to coil winding at 580 ° C for 1 hour, and allowed to cool. did. After that, except for some steels, hot-rolled sheet annealing was performed under the conditions shown in Table 8. Then, after pickling, they were cold rolled to 0.50 marauders.
  • the cold-rolled sheet was subjected to finish annealing at various temperatures of 700 or more, and then subjected to the same semi-organic insulation as in Example 1, and then subjected to various tests.
  • the strength was measured by cutting a JIS No. 5 test piece in the rolling direction and 5 mm, pulling it at a pulling speed of 10 ram / s, and evaluating the obtained tensile strength (TS). Table 8 shows the obtained results.
  • T Invention steel 0.0011 0.60 0.0011 0.19 0.0033 0.00 0.13 0.0032 ⁇ 0.001 ⁇ 0.001 0.262 OK 0.593 NG OK
  • the steels (Nos. 2 to 4, 7, 13, 14, 16 to 18, and 21 to 24) containing at least 0.1% of P as components within the scope of the present invention have excellent punching dimensional accuracy. Is shown. That is, for steels with less than 0.1% of P added ( ⁇ 1, 6, 10, and 15), the punching diameter tends to improve with the increase of Si + Al content, but Large anisotropy in diameter. On the other hand, it is clear that the steel of the present invention is excellent in both the punching diameter and the anisotropy of the punching diameter. Furthermore, these inventive steels have a magnetic flux density equal to or higher than that of comparative steels with a P content of less than 0.1%. Nevertheless, they have high strength, and have an excellent strength-to-magnetic flux density balance.
  • a bending test was performed on the obtained hot-rolled steel sheet at room temperature (at 23).
  • a test piece of 100 rara X 30 sq. was sampled from the hot-rolled sheet so that the rolling direction became longitudinal, and a repeated bending test with a bending radius of 15 mra was performed according to JIS-C2550.
  • Table 9 shows the number of times until the surface of the hot rolled sheet cracked.
  • the structure (phase) during slab heating and hot-rolled sheet annealing was investigated by the following method. After maintaining the sheet par and the hot rolled sheet for a predetermined time (described in Table 9) for a predetermined time (slab heating: 1 hour, annealing: 60 seconds), the structure at the time of heating is frozen by water quenching, and optical The phases were identified by microscopic observation of the yarn. The results are shown in Table 9.
  • the hot-rolled sheet was pickled and then cold-rolled to a thickness of 0.50 (one-time cold-rolling), and evaluated whether or not cold-rolling failure (lamellar cracking) due to embrittlement occurred.
  • the cold-rolled sheet with no layer cracks was subjected to finish annealing at various temperatures shown in Table 9 and then samples coated with the same semi-organic insulating coating as in Example 1 were prepared for various tests. Provided. Table 9 shows the obtained results.
  • the slab heating temperature of the present invention was in the two-phase region (Ntxl and 4), it was found that cold rolling failure due to embrittlement easily occurred and commercialization was difficult. Also, when the Koino scraping temperature was higher at 650 ( ⁇ 5), the workability of the hot rolled sheet was reduced, and the iron loss of the obtained electrical steel sheet was also reduced. Furthermore, when the hot-rolled sheet annealing temperature was in the two-phase region (Nos. 7 and 12), and in steels with more than 1.0 mass% Ni added, hot-rolled sheet annealing was performed in the ⁇ single-phase region. With ( ⁇ 13), the magnetic flux density of the obtained magnetic steel sheet decreased.
  • the non-oriented electrical steel sheet of the present invention is used as a core material for various motors, particularly a reluctance motor that requires particularly high dimensional accuracy and a high magnetic flux density, and an embedded magnet type DC brushless motor that requires further material strength. It is most suitable as iron core material.

Abstract

L'invention concerne une feuille en acier électromagnétique non orientée possédant la composition chimique suivante : entre 0 et 0,010 % en masse de C, entre 0,03 et 0,5 % en masse de Si et/ou Al ou de préférence 0,5 % en masse au maximum et 2,5 % en masse au minimum de Si et/ou Al, au maximum 0,5 % en masse de Mn, entre 0,10 et 0,26 % en masse de P, 0,015 % en masse au maximum de S, 0,010 % en masse au maximum de N, et un équilibre de Fe et d'impuretés inévitables. La feuille en acier électromagnétique non orientée présente une excellente précision dimensionnelle dans le découpage à l'emporte-pièce, et un excellent équilibre magnétique de perte de fer de faible densité d'un flux magnétique élevé dans un acier à faible teneur en Si, ainsi qu'un excellent équilibre de résistance de densité élevée d'un flux magnétique élevé dans un acier à teneur en Si moyenne et élevée.
PCT/JP2002/006458 2001-06-28 2002-06-27 Feuille en acier electromagnetique non orientee WO2003002777A1 (fr)

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EP02738812A EP1411138A4 (fr) 2001-06-28 2002-06-27 Feuille en acier electromagnetique non orientee
US10/481,919 US20040149355A1 (en) 2001-06-28 2002-06-27 Nonoriented electromagnetic steel sheet
JP2003508741A JP4329538B2 (ja) 2001-06-28 2002-06-27 無方向性電磁鋼板およびその製造方法
KR1020037002839A KR100956530B1 (ko) 2001-06-28 2002-06-27 무방향성 전자강판 및 그 제조방법
US11/978,406 US20080060728A1 (en) 2001-06-28 2007-10-29 Method of manufacturing a nonoriented electromagnetic steel sheet

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CN100334246C (zh) * 2004-05-28 2007-08-29 宝山钢铁股份有限公司 防伪造币钢及其生产方法
JP2009185357A (ja) * 2008-02-07 2009-08-20 Jfe Steel Corp 無方向性電磁鋼板およびその製造方法
JP2019504193A (ja) * 2015-12-11 2019-02-14 ポスコＰｏｓｃｏ 無方向性電磁鋼板及びその製造方法
US11299791B2 (en) 2015-12-11 2022-04-12 Posco Non-oriented electrical steel sheet and manufacturing method therefor
JP2018003049A (ja) * 2016-06-28 2018-01-11 新日鐵住金株式会社 占積率に優れる電磁鋼板およびその製造方法
WO2020188783A1 (fr) 2019-03-20 2020-09-24 日本製鉄株式会社 Tôle d'acier électromagnétique non orientée et son procédé de fabrication
KR20210125074A (ko) 2019-03-20 2021-10-15 닛폰세이테츠 가부시키가이샤 무방향성 전자 강판 및 그 제조 방법

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EP1411138A1 (fr) 2004-04-21
CN1520464A (zh) 2004-08-11
KR100956530B1 (ko) 2010-05-07
US20080060728A1 (en) 2008-03-13
CN1318627C (zh) 2007-05-30
KR20040014960A (ko) 2004-02-18
JPWO2003002777A1 (ja) 2004-10-21
US20040149355A1 (en) 2004-08-05
JP4329538B2 (ja) 2009-09-09
EP1411138A4 (fr) 2005-01-12
TW555863B (en) 2003-10-01

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