EP2977480A1 - Feuille d'acier magnétique non orientée ayant d'excellentes caractéristiques de perte de fer à fréquence élevée - Google Patents

Feuille d'acier magnétique non orientée ayant d'excellentes caractéristiques de perte de fer à fréquence élevée Download PDF

Info

Publication number
EP2977480A1
EP2977480A1 EP14767789.2A EP14767789A EP2977480A1 EP 2977480 A1 EP2977480 A1 EP 2977480A1 EP 14767789 A EP14767789 A EP 14767789A EP 2977480 A1 EP2977480 A1 EP 2977480A1
Authority
EP
European Patent Office
Prior art keywords
mass
iron loss
steel
steel sheet
oriented electrical
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP14767789.2A
Other languages
German (de)
English (en)
Other versions
EP2977480A4 (fr
EP2977480B1 (fr
Inventor
Shinji KOSEKI
Yoshihiko Oda
Hiroaki Toda
Tatsuhiko Hiratani
Tadashi Nakanishi
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
JFE Steel Corp
Original Assignee
JFE Steel Corp
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by JFE Steel Corp filed Critical JFE Steel Corp
Publication of EP2977480A1 publication Critical patent/EP2977480A1/fr
Publication of EP2977480A4 publication Critical patent/EP2977480A4/fr
Application granted granted Critical
Publication of EP2977480B1 publication Critical patent/EP2977480B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

Classifications

    • 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
    • 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
    • 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
    • C22C38/008—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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • 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
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the working steps
    • C21D8/1222—Hot 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the working steps
    • C21D8/1233—Cold 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the heat treatment
    • C21D8/1255—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the heat treatment with diffusion of elements, e.g. decarburising, nitriding
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the heat treatment
    • C21D8/1261—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the heat treatment following hot 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the heat treatment
    • C21D8/1272—Final recrystallisation annealing
    • 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
    • H01F1/14791—Fe-Si-Al based alloys, e.g. Sendust

Definitions

  • This invention relates to a non-oriented electrical steel sheet having an excellent high-frequency iron loss property.
  • a motor for a hybrid car or an electric car is driven at a high frequency region of 400-2 kHz from a viewpoint of miniaturization and high efficiency.
  • a non-oriented electrical steel sheet used in a core material for such a high-frequency motor is desired to be low in the iron loss at a high frequency.
  • Si is an element having a large solid-solution strengthening ability, so that there is a problem that the material is hardened with the increase of Si addition amount to deteriorate the rolling property.
  • Mn is small in the solid-solution strengthening ability as compared to Si, the high-frequency iron loss can be reduced while suppressing the deterioration of the productivity.
  • Patent Document 1 discloses a non-oriented electrical steel sheet containing Si: 0.5-2.5 mass%, Mn: 1.0-3.5 mass% and Al: 1.0-3.0 mass%.
  • Patent Document 2 discloses a non-oriented electrical steel sheet containing Si: not more than 3.0 mass%, Mn: 1.0-4.0 mass% and Al: 1.0-3.0 mass%.
  • Patent Documents 1 and 2 have a problem that hysteresis loss is increased with the increase of Mn addition amount and hence the desired effect of reducing the iron loss may not be obtained.
  • the invention is made in consideration of the above problems inherent to the conventional art, and an object thereof is to provide a non-oriented electrical steel sheet having a stable and excellent high-frequency iron loss property even if a great amount of Mn is contained.
  • the inventors have noted impurity ingredients contained in the steel sheet and made various studies for solving the above task. As a result, it has been found out that the deterioration of high-frequency iron loss property in high Mn-added steels is based on the presence of Bi included as an impurity and hence the high frequency iron loss can be reduced stably by suppressing Bi content even at a high Mn content, and the invention has been accomplished.
  • the invention is based on the above knowledge and is a non-oriented electrical steel sheet having a chemical composition comprising C: not more than 0.005 mass%, Si: 1.5-4 mass%, Mn: 1.0-5 mass%, P: not more than 0.1 mass%, S: not more than 0.005 mass%, Al: not more than 3 mass%, N: not more than 0.005 mass%, Bi: not more than 0.0030 mass% and the remainder being Fe and inevitable impurities.
  • the non-oriented electrical steel sheet according to the invention is characterized by containing one or two of Ca: 0.0005-0.005 mass% and Mg: 0.0002-0.005 mass% in addition to the above chemical composition.
  • non-oriented electrical steel sheet according to the invention is characterized by further containing one or two of Sb: 0.0005-0.05 mass% and Sn: 0.0005-0.05 mass% in addition to the above chemical composition.
  • non-oriented electrical steel sheet according to the invention is characterized by further containing Mo: 0.0005-0.0030 mass% in addition to the above chemical composition.
  • non-oriented electrical steel sheet according to the invention is characterized by containing Ti: not more than 0.002 mass%.
  • a steel containing C: 0.0016 mass%, Si: 3.35 mass%, P: 0.013 mass%, S: 0.0004 mass%, Al: 1.4 mass% and N: 0.0018 mass% and added with Mn changed within a range of 0.1-5.2 mass% is melted in a laboratory to form a steel ingot, which is hot rolled, subjected to a hot band annealing at 1000°C in an atmosphere of 100 vol% N 2 for 30 seconds, cold rolled to a cold rolled sheet of 0.30 mm in thickness and subjected to a final annealing at 1000°C in an atmosphere of 20 vol% H 2 - 80 vol% N 2 for 30 seconds.
  • symbol ⁇ shows the above experimental results as a relation between Mn addition amount and iron loss W 10/400 .
  • Mn is less than 1 mass%
  • the iron loss is decreased with the increase of Mn addition amount, but the decrease of the iron loss become gentle at an amount of not less than 1 mass%, and rather the iron loss is increased at an amount exceeding 4 mass%.
  • granular Bi is found in grain boundaries.
  • a steel prepared by adding Mn variously changed within a range of 0.1-5.2 mass% to a high-purity steel containing C: 0.0014 mass%, Si: 3.33 mass%, Al: 1.2 mass%, P: 0.014 mass%, S: 0.0006 mass%, N: 0.0020 mass% and Bi: not more than 0.0010 mass% is melted in a laboratory and shaped into a cold rolled and annealed sheet in the same manner as in the above experiment to measure an iron loss W 10/400 .
  • Bi is an impurity incorporated from the scrap, so that not only the amount incorporated but also the deviation thereof becomes gradually large associated with the increase of the scrap use ratio in recent years.
  • Such an increase of Bi content is not a big problem in the electrical steel sheets having a low Mn content, but the steels having a high Mn content are considered to be largely influenced by a slight amount of Bi because the grain growth is lowered by solute drag of Mn.
  • FIG. 2 are shown the above experimental results as a relation between Bi content and iron loss W 10/400 .
  • the iron loss is largely decreased when the Bi content is not more than 0.0030 mass% (not more than 30 massppm). This is considered due to the fact that the grain growth is improved by decreasing Bi. From this fact, it is confirmed that the Bi content is necessary to be decreased to not more than 0.0030 mass% for suppressing the bad influence of Bi upon the grain growth.
  • the invention is based on the above new knowledge.
  • C is an element forming a carbide with Mn.
  • the amount of Mn-based carbide is increased to block the grain growth, so that an upper limit is 0.005 mass%.
  • it is not more than 0.002 mass%.
  • Si is an element effective for increasing a specific resistance of steel and reducing an iron loss and is added in an amount of not less than 1.5 mass%. While when it is added in an amount exceeding 4 mass%, the magnetic flux density is lowered, so that an upper limit is 4 mass%.
  • the lower limit of Si is 2.0 mass% and the upper limit thereof is 3.0 mass%.
  • Mn is effective for increasing a specific resistance of steel and reducing an iron loss without largely damaging the workability and is an important ingredient in the invention, which is added in an amount of not less than 1.0 mass%. In order to further obtain an effect of reducing the iron loss, it is preferable to be added in an amount of not less than 1.6 mass%. While when it is added in an amount exceeding 5 mass%, the magnetic flux density is lowered, so that an upper limit is 5 mass%.
  • the lower limit of Mn is 2 mass% and the upper limit thereof is 3 mass%.
  • P is an element having a large solid-solution strengthening ability, but when it is added in an amount exceeding 0.1 mass%, the steel sheet is significantly hardened to deteriorate the productivity, so that it is limited to not more than 0.1 mass%. Preferably, it is not more than 0.05 mass%.
  • MnS is an inevitable impurity.
  • MnS is precipitated to block the grain growth and increase the iron loss, so that an upper limit is 0.005 mass%.
  • it is not more than 0.001 mass%.
  • A1 is an element effective for increasing a specific resistance of steel and reducing an iron loss like Si.
  • the magnetic flux density is lowered, so that an upper limit is 3 mass%.
  • it is not more than 2 mass%.
  • Al content is less than 0.1 mass%, fine AlN is precipitated to block the grain growth and increase the iron loss, so that a lower limit is preferable to be 0.1 mass%.
  • N is an inevitable impurity penetrated from air into steel.
  • the content is large, grain growth is blocked due to the precipitation of AlN to increase the iron loss, so that an upper limit is restricted to 0.005 mass%.
  • it is not more than 0.003 mass%.
  • Bi is an important element to be controlled in the invention because it badly affects the high-frequency iron loss property.
  • Bi content exceeds 0.0030 mass% as seen from FIG. 2 , the iron loss violently increases. Therefore, Bi is restricted to not more than 0.0030 mass%. Preferably, it is not more than 0.0010 mass%.
  • the non-oriented electrical steel sheet according to the invention is preferable to contain one or two of Ca and Mg in addition to the above chemical composition.
  • Ca is an element effective for forming a sulfide and coarsening by compositely precipitating with Bi to suppress the adverse effect of Bi and reduce the iron loss.
  • it is preferable to be added in an amount of not less than 0.0005 mass%.
  • an upper limit is preferable to be 0.005 mass%. More preferably, the lower limit of Ca is 0.001 mass% and the upper limit thereof is 0.004 mass%.
  • Mg is an element effective for forming an oxide and coarsening by compositely precipitating with Bi to suppress the adverse effect of Bi and reduce the iron loss. In order to obtain such an effect, it is preferable to be added in an amount of not less than 0.0002 mass%. However, the addition exceeding 0.005 mass% is difficult and brings about the increase of the cost, so that an upper limit is preferable to be 0.005 mass%. More preferably, the lower limit of Mg is 0.001 mass% and the upper limit thereof is 0.004 mass%.
  • non-oriented electrical steel sheet according to the invention is preferable to further contain the following ingredients in addition to the above chemical composition.
  • Sb and Sn have an effect of improving the texture to increase the magnetic flux density, so that they can be added in an amount of not less than 0.0005 mass% alone or in admixture. More preferably, it is not less than 0.01 mass%. However, the addition exceeding 0.05 mass% brings about the embrittlement of the steel sheet, so that an upper limit is preferable to be 0.05 mass%. More preferably, the lower limit of each of Sb and Sn is 0.01 mass% and the upper limit thereof is 0.04 mass%.
  • Mo has an effect of coarsening the resulting carbide to reduce the iron loss and is preferable to be added in an amount of not less than 0.0005 mass%. However, when it is added in an amount exceeding 0.0030 mass%, the amount of the carbide becomes too large and the iron loss is rather increased, so that an upper limit is preferable to be 0.0030 mass%. More preferably, the lower limit of Mo is 0.0010 mass% and the upper limit thereof is 0.0020 mass%.
  • Ti is an element forming a carbonitride.
  • the content is large, the amount of the carbonitride precipitated becomes too large, so that the grain growth is blocked and the iron loss is increased.
  • Ti is preferable to be restricted to not more than 0.002 mass%. More preferably, it is not more than 0.001 mass%.
  • the remainder other than the aforementioned ingredients is Fe and inevitable impurities.
  • other elements may be included within a range not damaging the function effect of the invention.
  • conditions are not particularly limited except that the chemical composition of the steel sheet is controlled within a range defined in the invention, so that the production may be performed under the same conditions as in the normal non-oriented electrical steel sheet.
  • the steel sheet can be produced by a method wherein a steel having a chemical composition adapted to the invention is melted, for example, in a converter, a degassing device or the like and shaped into a raw steel material (slab) by a continuous casting method or an ingot making-blooming method, which is hot rolled, subjected to a hot band annealing as required and further to a single cold rolling or two or more cold rollings including an intermediate annealing therebetween to a predetermined sheet thickness and subsequently to a final annealing.
  • a steel having a chemical composition adapted to the invention is melted, for example, in a converter, a degassing device or the like and shaped into a raw steel material (slab) by a continuous casting method or an ingot making-blooming method, which is hot rolled, subjected to a hot band annealing as required and further to a single cold rolling or two or more cold rollings including an intermediate annealing therebetween to a
  • a steel having a chemical composition shown in Table 1 is melted in a converter, degassed by blowing and continuously cast into a slab, which is heated at 1100°C for 1 hour, hot rolled at a final rolling temperature of 800°C and wound into a coil at a temperature of 610°C to obtain a hot rolled sheet of 1.8 mm in thickness.
  • the hot rolled sheet is subjected to a hot band annealing at 1000°C in an atmosphere of 100 vol% N 2 for 30 seconds and cold rolled to obtain a cold rolled sheet having a sheet thickness of 0.35 mm, which is subjected to a final annealing at 980°C in an atmosphere of 20 vol% H 2 - 80 vol% N 2 for 15 seconds to form a cold rolled and annealed sheet.
  • the steel sheets satisfying the chemical composition of the invention, particularly the steel sheets decreasing Bi content are excellent in the high-frequency iron loss property irrespectively of a high Mn content.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Dispersion Chemistry (AREA)
  • Power Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Soft Magnetic Materials (AREA)
  • Electromagnetism (AREA)
  • Manufacturing & Machinery (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)
EP14767789.2A 2013-03-22 2014-03-12 Feuille d'acier électrique non orientée ayant d'excellentes caractéristiques de perte de fer à fréquence élevée Active EP2977480B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2013060537A JP2014185365A (ja) 2013-03-22 2013-03-22 高周波鉄損特性に優れる無方向性電磁鋼板
PCT/JP2014/056430 WO2014148328A1 (fr) 2013-03-22 2014-03-12 Feuille d'acier magnétique non orientée ayant d'excellentes caractéristiques de perte de fer à fréquence élevée

Publications (3)

Publication Number Publication Date
EP2977480A1 true EP2977480A1 (fr) 2016-01-27
EP2977480A4 EP2977480A4 (fr) 2016-04-13
EP2977480B1 EP2977480B1 (fr) 2017-07-05

Family

ID=51580015

Family Applications (1)

Application Number Title Priority Date Filing Date
EP14767789.2A Active EP2977480B1 (fr) 2013-03-22 2014-03-12 Feuille d'acier électrique non orientée ayant d'excellentes caractéristiques de perte de fer à fréquence élevée

Country Status (8)

Country Link
US (1) US20160076125A1 (fr)
EP (1) EP2977480B1 (fr)
JP (1) JP2014185365A (fr)
KR (1) KR101700694B1 (fr)
CN (1) CN105074032B (fr)
RU (1) RU2650469C2 (fr)
TW (1) TWI551694B (fr)
WO (1) WO2014148328A1 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3633059A4 (fr) * 2017-05-31 2020-04-29 JFE Steel Corporation Tôle d'acier électromagnétique non orienté et son procédé de production

Families Citing this family (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP7172100B2 (ja) * 2018-04-02 2022-11-16 日本製鉄株式会社 無方向性電磁鋼板
KR102105530B1 (ko) * 2018-09-27 2020-04-28 주식회사 포스코 무방향성 전기강판 및 그 제조방법
JP7328491B2 (ja) * 2018-11-09 2023-08-17 日本製鉄株式会社 無方向性電磁鋼板
KR102175065B1 (ko) * 2018-11-30 2020-11-05 주식회사 포스코 무방향성 전기강판 및 그 제조방법
KR102176351B1 (ko) 2018-11-30 2020-11-09 주식회사 포스코 무방향성 전기강판 및 그 제조방법
KR102348508B1 (ko) * 2019-12-19 2022-01-07 주식회사 포스코 무방향성 전기강판 및 그 제조방법
KR102325008B1 (ko) * 2019-12-20 2021-11-10 주식회사 포스코 무방향성 전기강판 및 그 제조방법

Family Cites Families (18)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2540946B2 (ja) * 1989-06-30 1996-10-09 日本鋼管株式会社 磁気特性に優れた無方向性電磁鋼板およびその製造方法
JPH06108149A (ja) * 1992-09-29 1994-04-19 Nippon Steel Corp 需要家焼鈍後の鉄損が極めて優れた無方向性珪素鋼板の製造方法
JP2002030397A (ja) 2000-07-13 2002-01-31 Sumitomo Metal Ind Ltd 無方向性電磁鋼板とその製造方法
JP3835137B2 (ja) * 2000-07-28 2006-10-18 住友金属工業株式会社 無方向性電磁鋼板およびその製造方法
JP3835216B2 (ja) * 2001-08-09 2006-10-18 住友金属工業株式会社 無方向性電磁鋼板およびその製造方法
EP1632582B1 (fr) * 2003-05-06 2011-01-26 Nippon Steel Corporation Tole d'acier magnetique non orientee excellente du point de vue des pertes de fer, et son procede de production
JP4414727B2 (ja) * 2003-10-31 2010-02-10 新日本製鐵株式会社 磁気特性、耐変形性の優れた電磁鋼板とその製造方法
EP1816226B1 (fr) * 2004-11-04 2011-04-13 Nippon Steel Corporation Feuille d'acier electrique non orienté excellente en termes de perte de fer
JP4280224B2 (ja) * 2004-11-04 2009-06-17 新日本製鐵株式会社 鉄損に優れた無方向性電磁鋼板
RU2398894C1 (ru) * 2006-06-16 2010-09-10 Ниппон Стил Корпорейшн Лист высокопрочной электротехнической стали и способ его производства
JP5200376B2 (ja) * 2006-12-26 2013-06-05 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
JP5417689B2 (ja) * 2007-03-20 2014-02-19 Ｊｆｅスチール株式会社 無方向性電磁鋼板
KR101259233B1 (ko) * 2007-12-03 2013-05-07 신닛테츠스미킨 카부시키카이샤 고주파 철손이 낮은 무방향성 전자기 강판 및 그 제조 방법
KR101297864B1 (ko) * 2009-06-03 2013-08-19 신닛테츠스미킨 카부시키카이샤 무방향성 전자기 강판 및 그 제조 방법
JP5338750B2 (ja) * 2010-06-09 2013-11-13 Ｊｆｅスチール株式会社 無方向性電磁鋼板の製造方法
KR101353463B1 (ko) * 2011-12-28 2014-01-21 주식회사 포스코 무방향성 전기강판 및 그 제조방법
KR101353462B1 (ko) * 2011-12-28 2014-01-24 주식회사 포스코 무방향성 전기강판 및 제조 방법
CN102634742B (zh) * 2012-04-01 2013-09-25 首钢总公司 一种无Al的无取向电工钢的制备方法

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3633059A4 (fr) * 2017-05-31 2020-04-29 JFE Steel Corporation Tôle d'acier électromagnétique non orienté et son procédé de production
US11404189B2 (en) 2017-05-31 2022-08-02 Jfe Steel Corporation Non-oriented electrical steel sheet and method for manufacturing the same

Also Published As

Publication number Publication date
RU2015145284A (ru) 2017-04-25
KR20150109485A (ko) 2015-10-01
US20160076125A1 (en) 2016-03-17
EP2977480A4 (fr) 2016-04-13
CN105074032A (zh) 2015-11-18
KR101700694B1 (ko) 2017-01-31
JP2014185365A (ja) 2014-10-02
RU2650469C2 (ru) 2018-04-13
TWI551694B (zh) 2016-10-01
CN105074032B (zh) 2018-01-12
TW201443248A (zh) 2014-11-16
WO2014148328A1 (fr) 2014-09-25
EP2977480B1 (fr) 2017-07-05

Similar Documents

Publication Publication Date Title
EP2977480B1 (fr) Feuille d'acier électrique non orientée ayant d'excellentes caractéristiques de perte de fer à fréquence élevée
CN103827333B (zh) 无取向电磁钢板
EP2657355B1 (fr) Procédé de fabrication d'une feuille d'acier électrique non-orienté
EP3260567B1 (fr) Tôle d'acier électrique non orienté, son procédé de production, et noyau de moteur
EP2975152B1 (fr) Tôle d'acier électrique non orienté présentant d'excellentes propriétés magnétiques.
TWI494446B (zh) 無方向性電磁鋼板之製造方法
EP3095887B1 (fr) Feuille d'acier électrique non directionnel présentant d'excellentes propriétés magnétiques
KR101919529B1 (ko) 무방향성 전기강판 및 그 제조방법
EP2975147B1 (fr) Feuille d'acier électrique non orientée ayant une excellente propriété de perte de fer à haute fréquence
KR100872607B1 (ko) 펀칭 가공성과 왜곡 제거 소둔 후의 자기 특성이 우수한무방향성 전자 강판과 그 제조 방법
EP3889290A2 (fr) Tôle magnétique en acier non directionnelle et son procédé de production
KR102134311B1 (ko) 무방향성 전기강판 및 그 제조방법
EP2639326B1 (fr) Tige de fil métallique et fil d'acier ayant d'excellentes caractéristiques magnétiques, et procédé pour leur fabrication

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

17P Request for examination filed

Effective date: 20150828

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

AX Request for extension of the european patent

Extension state: BA ME

A4 Supplementary search report drawn up and despatched

Effective date: 20160311

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 38/00 20060101AFI20160307BHEP

Ipc: H01F 1/16 20060101ALI20160307BHEP

Ipc: C22C 38/06 20060101ALI20160307BHEP

Ipc: C21D 8/12 20060101ALI20160307BHEP

Ipc: C22C 38/12 20060101ALI20160307BHEP

Ipc: C22C 38/60 20060101ALI20160307BHEP

Ipc: C22C 38/04 20060101ALI20160307BHEP

Ipc: C22C 38/14 20060101ALI20160307BHEP

Ipc: C22C 38/02 20060101ALI20160307BHEP

DAX Request for extension of the european patent (deleted)
RIC1 Information provided on ipc code assigned before grant

Ipc: C21D 8/12 20060101ALI20161028BHEP

Ipc: C22C 38/02 20060101ALI20161028BHEP

Ipc: C22C 38/60 20060101ALI20161028BHEP

Ipc: C22C 38/04 20060101ALI20161028BHEP

Ipc: C22C 38/12 20060101ALI20161028BHEP

Ipc: C22C 38/14 20060101ALI20161028BHEP

Ipc: C22C 38/00 20060101AFI20161028BHEP

Ipc: C22C 38/06 20060101ALI20161028BHEP

Ipc: H01F 1/147 20060101ALI20161028BHEP

Ipc: H01F 1/16 20060101ALI20161028BHEP

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

INTG Intention to grant announced

Effective date: 20161216

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAJ Information related to disapproval of communication of intention to grant by the applicant or resumption of examination proceedings by the epo deleted

Free format text: ORIGINAL CODE: EPIDOSDIGR1

GRAL Information related to payment of fee for publishing/printing deleted

Free format text: ORIGINAL CODE: EPIDOSDIGR3

INTC Intention to grant announced (deleted)
GRAR Information related to intention to grant a patent recorded

Free format text: ORIGINAL CODE: EPIDOSNIGR71

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

INTG Intention to grant announced

Effective date: 20170529

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 906666

Country of ref document: AT

Kind code of ref document: T

Effective date: 20170715

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602014011549

Country of ref document: DE

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20170705

REG Reference to a national code

Ref country code: AT

Ref legal event code: MK05

Ref document number: 906666

Country of ref document: AT

Kind code of ref document: T

Effective date: 20170705

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG4D

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: NO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20171005

Ref country code: HR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170705

Ref country code: NL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170705

Ref country code: AT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170705

Ref country code: FI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170705

Ref country code: LT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170705

Ref country code: SE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170705

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20171105

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20171006

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20171005

Ref country code: LV

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170705

Ref country code: ES

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170705

Ref country code: PL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170705

Ref country code: RS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170705

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602014011549

Country of ref document: DE

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170705

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170705

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170705

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170705

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170705

Ref country code: IT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170705

Ref country code: SM

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170705

26N No opposition filed

Effective date: 20180406

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170705

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20180312

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170705

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20180331

REG Reference to a national code

Ref country code: IE

Ref legal event code: MM4A

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180312

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180312

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180312

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180331

Ref country code: BE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180331

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180331

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FR

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180331

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180312

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170705

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170705

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: HU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO

Effective date: 20140312

Ref country code: MK

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170705

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170705

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: AL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20170705

REG Reference to a national code

Ref country code: DE

Ref legal event code: R082

Ref document number: 602014011549

Country of ref document: DE

Representative=s name: HL KEMPNER PATENTANWAELTE, SOLICITORS (ENGLAND, DE

Ref country code: DE

Ref legal event code: R082

Ref document number: 602014011549

Country of ref document: DE

Representative=s name: HL KEMPNER PATENTANWALT, RECHTSANWALT, SOLICIT, DE

Ref country code: DE

Ref legal event code: R082

Ref document number: 602014011549

Country of ref document: DE

Representative=s name: HL KEMPNER PARTG MBB, DE

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 20250128

Year of fee payment: 12