EP2679695A1 - Nicht orientiertes elektromagnetisches stahlblech sowie verfahren zu seiner herstellung - Google Patents

Nicht orientiertes elektromagnetisches stahlblech sowie verfahren zu seiner herstellung Download PDF

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EP2679695A1
EP2679695A1 EP11859212.0A EP11859212A EP2679695A1 EP 2679695 A1 EP2679695 A1 EP 2679695A1 EP 11859212 A EP11859212 A EP 11859212A EP 2679695 A1 EP2679695 A1 EP 2679695A1
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steel
steel sheet
strength
oriented electrical
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EP2679695B1 (de
EP2679695A4 (de
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Masaaki Kohno
Yoshiaki Zaizen
Yoshihiko Oda
Akira Fujita
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JFE Steel Corp
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JFE Steel Corp
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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
    • 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
    • C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
    • 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
    • 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
    • C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
    • C21D8/1227—Warm rolling
    • 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
    • C21D8/1266—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
    • 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
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • 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, and in particular, to a non-oriented electrical steel sheet having high strength and excellent fatigue properties, and furthermore, excellent magnetic properties that is suitably used for components that are subject to high stress, typically, drive motors for turbine generators, electric vehicles and hybrid vehicles, or rotors for high-speed rotating machinery, such as servo motors for robots, machine tools or the like, and a method for manufacturing the same. Additionally, the present invention provides the above-described non-oriented electrical steel sheet at low cost as compared to the conventional art.
  • IPM internal permanent magnet
  • IPM-type DC inverter control motors which have been increasingly employed for motors in hybrid vehicles, such as drive motors or compressor motors
  • stress is concentrated on portions between grooves for embedding magnets in a rotor and the outer circumference of the rotor, or at narrow bridge portions of several millimeters width between the grooves for embedding magnets.
  • motors can be reduced in size with increasing rotational speed, there is a growing demand for increasing the rotational speed of motors, such as in drive motors for hybrid vehicles with space and weight constraints.
  • high strength materials are advantageously used as core materials for use in rotors of high speed motors.
  • Steel-strengthening mechanisms include solid solution strengthening, precipitation strengthening, crystal grain refinement, work hardening, and so on.
  • solid solution strengthening a number of high-strength non-oriented electrical steel sheets have been considered and proposed to meet the needs, such as those of rotors of high speed motors.
  • JP 60-238421 A (PTL 1) proposes a method for increasing the strength of steel by adding elements such as Ti, W, Mo, Mn, Ni, Co or Al to the steel for the purposes of primarily increasing Si content from 3.5 % to 7.0 %, and furthermore, achieving solid solution strengthening.
  • JP 62-112723 A proposes a method for improving magnetic properties by controlling the crystal grain size in the range of 0.01 mm to 5.0 mm through manipulation of the final annealing conditions.
  • JP 06-330255 A proposes a technique that makes use of strengthening by precipitation and grain refining effects provided by carbonitrides in steel, the steel containing Si in the range of 2.0 % or more and less than 4.0 %, C in the range of 0.05 % or less, and one or two of Nb, Zr, Ti and V in the range of 0.1 ⁇ (Nb + Zr) / 8(C + N) ⁇ 1.0, and 0.4 ⁇ (Ti + V) / 4(C + N) ⁇ 4.0.
  • JP 02-008346 A proposes a technique, in addition to the features described in PTL 3, to add Ni and Mn in a total amount of 0.3 % or more and 10 % or less to steel for solid solution strengthening, and further add Nb, Zr, Ti and V in the same ratios as those described in PTL 3 to the steel, thereby balancing high strength with magnetic properties.
  • JP 2005-113185 A proposes a technique for enhancing the strength of steel containing Si in the range of 0.2 % to 3.5 % by allowing worked microstructures to remain in the steel material.
  • PTL 5 discloses means that does not perform heat treatment after cold rolling, or, if it does, retains the steel material at 750 °C for 30 seconds at most, preferably at 700 °C or lower, more preferably at 650 °C or lower, 600 °C or lower, 550 °C or lower, and 500 °C or lower.
  • PTL 5 reports the actual results indicating that the worked microstructure ratio is 5 % with annealing at 750 °C for 30 seconds, 20 % with annealing at 700 °C for 30 seconds, and 50 % with annealing at 600 °C for 30 seconds.
  • the worked microstructure ratio is 5 % with annealing at 750 °C for 30 seconds, 20 % with annealing at 700 °C for 30 seconds, and 50 % with annealing at 600 °C for 30 seconds.
  • Improperly-shaped steel sheets have a problem that would lead to a lower stacking factor after worked into a motor core in a stacked fashion, a non-uniform stress distribution when rotating at high speed as a rotor, and so on.
  • a non-oriented electrical steel sheet is generally subjected to final annealing using a continuous annealing furnace, which is usually maintained in an atmosphere containing at least several percent of hydrogen gas in order to reduce oxidation of surfaces of the steel sheet.
  • a continuous annealing furnace which is usually maintained in an atmosphere containing at least several percent of hydrogen gas in order to reduce oxidation of surfaces of the steel sheet.
  • JP 2007-186790 A (PTL 6) a high strength electrical steel sheet balancing the ability of shape correction of the steel sheet with the ability of strengthening by non-recrystallized microstructures during final annealing, which steel sheet is obtained by adding Ti sufficiently and excessively in relation to C and N to a silicon steel with reduced C and N contents and thereby raising the recrystallization temperature of the silicon steel.
  • This method still has a difficulty in that it may increase alloy cost due to a relatively high Ti content, cause variations in mechanical properties due to the remaining recrystallized microstructures, and so on.
  • the high-strength electrical steel sheets that have so far been provided for rotors of high speed motors are in a situation where the resulting rotors will be subject to unavoidable heat generation due to their magnetic property, i.e., high iron loss at high frequency, which necessarily poses limitations on the design specification of the motors.
  • an object of the present invention is to provide a high-strength non-oriented electrical steel sheet at low cost, having excellent magnetic properties and quality of steel sheet, and a method for manufacturing the same.
  • an object of the present invention is to provide means for manufacturing such a non-oriented electrical steel sheet in an industrially stable manner and yet at low cost that has both a tensile strength of 650 MPa or more, desirably 700 MPa or more, and good low iron loss properties at high frequency such that, for example, a steel material having a sheet thickness of 0.35 mm has a value of W 10/400 of 40 W/kg or lower, desirably 35 W/kg or lower.
  • the inventors of the present invention made intensive studies on high-strength electrical steel sheets that can achieve the above-described objects at a high level and methods for manufacturing the same. As a result, the inventors have revealed that the amount and ratio of Ti and C to be added to steel are deeply concerned with the balance between the strength properties and the magnetic properties of an electrical steel sheet, and that a high-strength electrical steel sheet having excellent properties may be manufactured in an stable manner and at low cost by optimizing the amount of precipitation of Ti carbides. That is, the present invention relies upon the following findings:
  • the inventors of the present invention found that a properly balanced utilization of solid solution strengthening with the use of the substitutional alloy elements mainly composed of Si, crystal grain refinement with Ti carbides, and solid solution strengthening with an interstitial element of C may provide a non-oriented electrical steel sheet that has high strength, excellent fatigue properties under the conditions of use, and furthermore, excellent magnetic properties and quality of steel sheet, without substantially adding extra constraints on manufacture of steel sheets or additional steps to the normal production of non-oriented electrical steel sheets, and also found a method necessary for manufacturing the same. As a result, the inventors accomplished the present invention.
  • a method for manufacturing a non-oriented electrical steel sheet comprising:
  • a non-oriented electrical steel sheet may be provided that is excellent in both mechanical properties and magnetic properties required for a rotor material of motors rotating at high speed, and that has excellent quality of steel sheet in terms of scab, sheet shape, and so on.
  • the present invention also allows stable production of such non-oriented electrical steel sheets with high yield, without incurring a significant increase in cost or imposing severe constraints on manufacture or requiring extra steps, as compared to the normal production of non-oriented electrical steel sheets. Therefore, the present invention is applicable in the field of motors, such as drive motors of electric vehicles and hybrid vehicles or servo motors of robots and machine tools, where demand for higher rotational speed is expected to grow in the future.
  • the present invention has a high industrial value and makes a significant contribution to the industry.
  • Steel samples which have steel compositions mainly composed of silicon (Si): 4.0 % to 4.1 %, manganese (Mn): 0.03 % to 0.05 %, aluminum (Al): 0.001 % or less, phosphorus (P): 0.007 % to 0.009 %, and sulfur (S): 0.001 % to 0.002 %, containing substantially constant amounts of carbon (C): 0.024 % to 0.026 % and nitrogen (N): 0.001 % to 0.002 %, and different amounts of titanium (Ti) in the range of 0.001 % to 0.36 %, were obtained by steelmaking in a vacuum melting furnace.
  • FIGS. 1, 2 and 3 The research results of tensile strength, magnetic property and occurrence of surface scab defect are depicted in FIGS. 1, 2 and 3 as a function of Ti content, respectively.
  • Range B the steel structure contains homogeneous microstructures with a crystal grain size of 10 ⁇ m or less
  • Range A it involves crystal grains grown more than in Range B, particularly, mixed-grain-size microstructures with partial grain growth.
  • Range C the steel structure assumes a multi-phase of non-recrystallized grains and recrystallized grains.
  • FIG. 2 illustrates the relationship between Ti content and iron loss W 10/400 . While good iron loss properties are obtained in Range A with the lowest iron loss, as illustrated in FIG. 1 , Range A shows lower strength levels. On the other hand, while high strength materials are obtained in Range C and D in FIG. 2 , iron loss is also high in these ranges. In contrast, Range B offers materials that have iron loss properties almost as good as in Range A, while yielding strength results comparable to those obtained in Range C.
  • the scab defect rate starts to increase when Ti content exceeds 0.04 %, and continues to rise up to around a point at which the equivalent ratio of elements of Ti to C and N is equal to 1, where a substantially constant rate of scab generation is reached.
  • the amount of Ti carbonitride precipitates continues to increase up to around a point at which this equivalent ratio of elements is equal to 1, and then remains constant.
  • the amount of Ti carbonitride precipitates is related to the amount of scab generation.
  • steel samples having compositions shown in Table 1 were prepared by steelmaking in a vacuum melting furnace to obtain steel sheets, each having a sheet thickness of 0.35 mm, following the same procedure as in Experiment 1.
  • C and N contents of steel samples were varied using steel sample "a,” which has small C and N contents, as a reference.
  • Steel samples "c” and “d” contain C and N so that the total content thereof is within a predetermined range.
  • the surface scab defect rate, iron loss and tensile strength of the resulting samples are shown in Table 2.
  • steel samples “b,” “c” and “d” show an increase in strength in relation to steel sample “a,” comparing steel samples “c” and “d” having substantially the same total amount of C and N to evaluate the effect of addition of C and N, it can be seen that steel sample “c” having a lower N content has higher strength.
  • the steel samples are listed as a > d > b > c in descending order of crystal grain size, as is the case with in descending order of tensile strength.
  • Table 1 (mass%) Steel Si Mn Al P C N Ti a 4.33 0.07 0.0005 0.010 0.0019 0.0021 0.0302 b 4.32 0.05 0.0010 0.010 0.0240 0.0009 0.0295 c 4.29 0.03 0.0007 0.010 0.0293 0.0009 0.0298 d 4.25 0.08 0.0018 0.020 0.0249 0.0052 0.0301
  • Table 2 Steel W 10/400 (W/kg) Tensile Strength TS (MPa) Fatigue Limit Strength FS (MPa) Strength Ratio FS/TS Surface Scab Defect Rate (m/m 2 ) a 26.9 641 535 0.83 0.000 b 33.0 722 630 0.87 0.003 c 32.5 730 665 0.91 0.003 d 31.0 676 540 0.80 0.004
  • steel sample “c” gives better results in terms of tensile strength and fatigue limit strength, and is particularly characterized by its relatively high fatigue limit strength and high strength ratio FS/TS. Since steel samples “b” and “c” have substantially the same Ti and N contents, they exhibit similar precipitation behavior of Ti nitrides and Ti carbides. It is thus believed that the difference between them is attributed to the difference in the amount of solute carbon. Accordingly, it is estimated that the presence of solute carbon reduced the occurrence and propagation of cracks and increased fatigue limit strength by locking dislocations introduced during repeated stress cycles such as found in fatigue test. Therefore, it is also important to ensure formation of solute carbon.
  • the inventors of the present invention made further studies on how these factors including Ti carbides, Ti nitrides and solute carbon, with the addition of a relatively small amount of Ti, affect the steel structure, quality of steel sheet surface, as well as mechanical properties and magnetic properties of steel sheets. As a result, the inventors discovered the rules comprehensively applicable to these factors and accomplished the present invention.
  • Steel of the present invention contains Si: 5.0 % or less, Mn: 2.0 % or less, Al: 2.0 % or less, and P: 0.05 % or less in a range satisfying formula (1): 300 ⁇ 85 Si % + 16 Mn % + 40 Al % + 490 P % ⁇ 430
  • An object of the present invention is to provide an electrical steel sheet having high strength and excellent magnetic properties at low cost. To this end, it is necessary to achieve solid solution strengthening above a certain level by means of the above-described four major alloy components. Thus, it is important to specify the contents of the four major alloy components as described later, and to add these components to the steel so that the total amount of these alloy components is within a range satisfying the above formula (1), considering individual contributions to solid solution strengthening. That is, if formula (1) gives a result less than 300, the strength of the resulting material is insufficient, whereas if formula (1) gives a result more than 430, there are more troubles with sheet cracking at the time of manufacture of steel sheets, leading to a deterioration in productivity and a significant increase in manufacturing cost.
  • Si is generally used as a deoxidizer and one of the major elements that are contained in a non-oriented electrical steel sheet and have an effect of increasing the electrical resistance of steel to reduce its iron loss. Further, Si has high solid solution strengthening ability. That is, Si is an element that is positively added to the non-oriented electrical steel sheet because it is capable of achieving higher tensile strength, higher fatigue strength and lower iron loss at the same time in a most balanced manner as compared to other solid-solution-strengthening elements, such as Mn, Al or Ni, that are added to the non-oriented electrical steel sheet. To this end, it is advantageous to contain Si in steel in an amount of 3.0 % or more, more preferably exceeding 3.5 %. However, above 5.0 %, toughness degradation will be pronounced, which should necessitate highly-sophisticated control during sheet passage and rolling processes, resulting in lower productivity. Therefore, the upper limit of the Si content is to be 5.0 % or less.
  • Manganese (Mn) is effective in improving hot shortness properties, and also has effects of increasing the electrical resistance of steel to reduce its iron loss and enhancing the strength of steel by solid solution strengthening.
  • Mn is preferably contained in steel in an amount of 0.01 % or more.
  • addition of Mn is less effective in improving the strength of steel as compared to Si and excessive addition thereof leads to embrittlement of the resulting steel. Therefore, the Mn content is to be 2.0 % or less.
  • Aluminum (Al) is an element that is generally used in steel refining as a strong deoxidizer. Further, as is the case with Si and Mn, Al also has effects of increasing the electrical resistance of steel to reduce its iron loss and enhancing the strength of steel by solid solution strengthening. Therefore, Al is preferably contained in steel in an amount of 0.0001 % or more. However, addition of Al is less effective in improving the strength of steel as compared to Si and excessive addition thereof leads to embrittlement of the resulting steel. Therefore, the Al content is to be 2.0 % or less.
  • Phosphorus (P) is extremely effective in enhancing the strength of steel because it offers a significantly high solid solution strengthening ability even when added in relatively small amounts.
  • P is preferably contained in steel in an amount of 0.005 % or more.
  • excessive addition of P leads to embrittlement of steel due to segregation, causing intergranular cracking or a reduction in rollability. Therefore, the P content is limited to 0.05 % or less.
  • a Si-based alloy design is advantageous for balancing solid solution strengthening/low iron loss and productivity in a most efficient way. That is, it is advantageous to contain Si in steel in an amount of more than 3.5 % for optimizing the balance of properties of the non-oriented electrical steel sheet, where the contents of the remaining three elements are preferably controlled as follows: Mn: 0.3 % or less, Al: 0.1 % or less, and P: 0.05 % or less.
  • Mn 0.3 % or less
  • Al 0.1 % or less
  • P 0.05 % or less.
  • Carbon (C) needs to be contained in steel in an amount of 0.008 % or more. That is, a carbon content of less than 0.008 % makes it difficult to provide stable precipitation of fine Ti carbides and results in an insufficient amount of solute C, in which case a further improvement in fatigue strength is no longer possible.
  • excessive addition of C leads to a deterioration in magnetic properties, while becoming a factor responsible for an increase in cost, such as making work hardening more pronounced during cold rolling and causing sheet fracture, forcing more rolling cycles due to an increased rolling load, and so on. Therefore, the upper limit of C is limited to 0.04 %.
  • N Nitrogen (N) forms nitrides with Ti, which are, however, formed at higher temperatures than Ti carbides. Thus, N is less effective in inhibiting the growth of crystal grains and not effective so much in refining crystal grains. Rather, N sometimes causes adverse effects such as providing origins of fatigue fracture. Therefore, N content is limited to 0.003 % or less. Additionally, without limitation, the lower limit is preferably about 0.0005 % in terms of steelmaking degassing ability and for avoiding a deterioration in productivity due to a long refining duration.
  • Ti titanium carbides
  • Ti* the amount of Ti that is capable of forming carbides.
  • Ti * Ti - 3.4 N %
  • Ti content exceeds 0.04 %, as previously described with reference to FIG. 3 , more scab defects will occur and the quality of steel sheet and yield will be reduced, resulting in an increase in cost. Therefore, the upper limit of Ti content is to be 0.04 %.
  • the present invention may also contain elements other than the aforementioned elements without impairing the effects of the invention.
  • the present invention may contain: antimony (Sb) and tin (Sn), each of which has an effect of improving magnetic properties of steel, in the range of 0.0005 % to 0.1 %; boron (B), which has an effect of enhancing grain boundary strength of steel, in the range of 0.0005 % to 0.01 %; Ca and REM, each of which has an effect of controlling the form of oxide and sulfide and improving magnetic properties of steel, in the range of 0.001 % to 0.01 %; Co and Ni, each of which has an effect of improving magnetic flux density of steel, in the range of 0.05 % to 5 %; and Cu, which is expected to provide strengthening by precipitation by means of aging precipitation, in the range of 0.2 % to 4 %, respectively.
  • the manufacturing process from steelmaking to cold rolling may be performed in accordance with methods commonly used for manufacturing general non-oriented electrical steel sheets.
  • steel which was prepared by steelmaking and refined with predetermined components in a converter or electric furnace, may be subjected to continuous casting or blooming after ingot casting to obtain steel slabs, which in turn may be subjected to process steps, including hot rolling, optional hot band annealing, cold rolling, final annealing, insulating coating application and baking, and so on to manufacture steel sheets.
  • process steps including hot rolling, optional hot band annealing, cold rolling, final annealing, insulating coating application and baking, and so on to manufacture steel sheets.
  • hot band annealing may optionally be carried out after the hot rolling, and that the cold rolling may be performed once, or twice or more with intermediate annealing performed therebetween.
  • the steel slabs composed of the aforementioned chemical compositions are to be subjected to hot rolling at a slab heating temperature of 1000 °C or higher to 1200 °C or lower. That is, if the slab heating temperature is below 1000 °C, it is not possible to achieve an effect of inhibiting the growth of crystal grains during final annealing in a sufficient manner due to the precipitation and growth of Ti carbides during slab heating. Alternatively, if the slab heating temperature is above 1200 °C, this is not only disadvantageous in terms of cost, but also causes slab deformation due to a reduction in strength at high temperature, which interferes with, e.g., extraction of the steel slabs from the heating furnace, resulting in lower operability.
  • the slab heating temperature is to be within the range of 1000 °C to 1200 °C.
  • the hot rolling itself is not limited to a particular type and may be performed under the conditions of, for example, hot rolling finishing temperature in the range of 700 °C to 950 °C and coiling temperature of 750 °C or lower.
  • the resulting hot rolled steel materials are subjected to optional hot band annealing and cold rolling or warm rolling once, or twice or more with intermediate annealing performed therebetween to be finished to a final sheet thickness before final annealing.
  • Prior to the final annealing it is important to subject the steel materials to heat treatment at least once where the steel materials are retained at temperatures of 800 °C or higher and 950 °C or lower for 30 seconds or more. This heat treatment may allow precipitation of Ti carbides in microstructures prior to the final annealing and thereby inhibit the growth of crystal grains during final annealing.
  • the resulting precipitation may be insufficient, while above 950 °C, the effect of inhibiting the growth of crystal grains during final annealing would be insufficient due to the growth of precipitates.
  • the aforementioned heat treatment is preferably performed in combination with either hot band annealing or intermediate annealing prior to the final annealing.
  • the subsequent final annealing may be performed at 700 °C or higher and 850 °C or lower to thereby control the microstructure of recrystallized grains into a homogeneous and fine state, providing an electrical steel sheet having high strength and excellent magnetic properties. If the final annealing is performed at temperatures below 700 °C, the resulting recrystallization is insufficient, while above 850 °C, crystal grains are prone to grow even when applying the present invention, resulting in a reduction in strength of the products. Following this final annealing, the steel materials are subjected to processes for applying and baking insulating coating thereon to obtain final products.
  • Steel samples having compositions shown in Table 3 were obtained by steelmaking in a vacuum melting furnace, heated to 1100 °C, and then subjected to hot rolling to be a thickness of 2.1 mm. Then, the samples were subjected to hot band annealing at 900 °C for 90 seconds and further to cold rolling to be finished to a thickness of 0.35 mm. At this moment, an evaluation was made of the occurrence of scab defects on the surfaces of the steel sheets, using the scab size per unit area as a reference. Subsequently, the samples were subjected to final annealing for 30 seconds under two different conditions at 750 °C and 800 °C, respectively.
  • test specimens were cut parallel to the rolling direction from the steel sheet samples thus obtained for tensile test and fatigue test.
  • the magnetic properties were evaluated based on the iron loss with a magnetizing flux density of 1.0 T and frequency of 400 Hz of the Epstein test specimens that were cut from the samples in the rolling direction and transverse direction, respectively. The evaluation results are shown in Table 4.
  • Steel samples having compositions shown in Table 5 were obtained by steelmaking in a vacuum melting furnace, heated to 1050 °C, and then subjected to hot rolling to be a thickness of 2.1 mm. Then, the samples were subjected to hot band annealing at 850 °C for 120 seconds and further to cold rolling to be finished to a thickness of 0.35 mm. At this moment, an evaluation was made of the occurrence of scab defects on the surfaces of the steel sheets, using the scab size per unit area as a reference. Subsequently, the steel samples were subjected to final annealing at 800 °C for 30 seconds. Then, test specimens were cut parallel to the rolling direction from the steel sheet samples thus obtained for tensile test and fatigue test.
  • each of the steel sheets according to the present invention exhibits less scabs, good iron loss properties and high tensile strength, as well as high fatigue limit strength.

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  • Organic Chemistry (AREA)
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  • Physics & Mathematics (AREA)
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EP11859212.0A 2011-02-24 2011-02-24 Nicht orientiertes elektromagnetisches stahlblech sowie verfahren zu seiner herstellung Not-in-force EP2679695B1 (de)

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WO2019017426A1 (ja) * 2017-07-19 2019-01-24 新日鐵住金株式会社 無方向性電磁鋼板
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JP7056745B2 (ja) * 2019-10-29 2022-04-19 Ｊｆｅスチール株式会社 無方向性電磁鋼板およびその製造方法
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CN103392021A (zh) 2013-11-13
CA2822206A1 (en) 2012-08-30
RU2536711C1 (ru) 2014-12-27
KR20130087611A (ko) 2013-08-06
EP2679695A4 (de) 2014-10-29
BR112013020657A2 (pt) 2016-10-18
US20130306200A1 (en) 2013-11-21
KR101412363B1 (ko) 2014-06-25
CA2822206C (en) 2016-09-13
WO2012114383A1 (ja) 2012-08-30

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