WO2016111088A1 - Tôle d'acier électromagnétique à grains non orientés et son procédé de fabrication - Google Patents

Tôle d'acier électromagnétique à grains non orientés et son procédé de fabrication Download PDF

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Publication number
WO2016111088A1
WO2016111088A1 PCT/JP2015/082191 JP2015082191W WO2016111088A1 WO 2016111088 A1 WO2016111088 A1 WO 2016111088A1 JP 2015082191 W JP2015082191 W JP 2015082191W WO 2016111088 A1 WO2016111088 A1 WO 2016111088A1
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Prior art keywords
mass
cao
hot
less
steel sheet
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PCT/JP2015/082191
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English (en)
Japanese (ja)
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中西　匡
宏章 中島
智幸 大久保
尾田　善彦
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Ｊｆｅスチール株式会社
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Priority claimed from JP2015204268A external-priority patent/JP6020863B2/ja
Application filed by Ｊｆｅスチール株式会社 filed Critical Ｊｆｅスチール株式会社
Priority to RU2017127961A priority Critical patent/RU2682727C2/ru
Priority to US15/541,964 priority patent/US10822678B2/en
Priority to EP15876961.2A priority patent/EP3243921B1/fr
Priority to MX2017008930A priority patent/MX2017008930A/es
Priority to BR112017014286-4A priority patent/BR112017014286B1/pt
Priority to KR1020177018621A priority patent/KR101940084B1/ko
Priority to CN201580072499.XA priority patent/CN107109570A/zh
Priority to CA2971682A priority patent/CA2971682C/fr
Publication of WO2016111088A1 publication Critical patent/WO2016111088A1/fr

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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • 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
    • C22C38/06—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
    • H01F1/16—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
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/04—Removing impurities by adding a treating agent
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/20—Recycling

Definitions

  • the present invention relates to a non-oriented electrical steel sheet used as an iron core material for electrical equipment and a method for manufacturing the same.
  • Patent Document 1 discloses a slab containing wt%, C: 0.02% or less, Si or Si + Al: 4.0% or less, Mn: 1.0% or less, and P: 0.2% or less.
  • a technique for increasing the magnetic flux density by adding Sb or Sn has been proposed. However, this technique cannot sufficiently reduce the variation in magnetic properties, and further requires two cold rollings with short-time annealing after hot rolling, resulting in high manufacturing costs. is there.
  • Patent Document 2 discloses that wt%, C ⁇ 0.008%, Si ⁇ 4%, Al ⁇ 2.5%, Mn ⁇ 1.5%, P ⁇ 0.2%, S ⁇ 0.005.
  • MnO %, N ⁇ 0.003% by controlling the MnO composition ratio (MnO / (SiO 2 + Al 2 O 3 + CaO + MnO)) of the oxide inclusions present in the hot rolled sheet containing 0.33% or less.
  • iron scrap is reused as a raw material for casting iron. Therefore, when the Al content is reduced, there is no need for new facilities and process management, and high magnetic flux density and low iron loss.
  • the reality is that it is difficult to manufacture non-oriented electrical steel sheets at low cost with high productivity.
  • the present invention has been made in view of the above-mentioned problems of the prior art, and the object thereof is a non-oriented electrical steel sheet having a low Al content, excellent recyclability, a high magnetic flux density and a low iron loss. And providing a method for manufacturing the steel sheet at low cost and high productivity.
  • the inventors made extensive studies by paying attention to the relationship between the component composition of the oxide inclusions present in the steel sheet and the magnetic properties.
  • sol in order to increase the magnetic flux density of the non-oriented electrical steel sheet and reduce the iron loss, sol.
  • the composition ratio of CaO and / or Al 2 O 3 in the oxide inclusions present in the steel material is controlled to an appropriate range, and grain growth in hot-rolled sheet annealing and finish annealing As a result, it has been found that it is effective to improve the above, and the present invention has been developed.
  • the present invention relates to C: 0.0050 mass% or less, Si: 1.5 to 5.0 mass%, Mn: 0.20 to 3.0 mass%, sol.
  • the following formula (1) CaO / (SiO 2 + Al 2 O 3 + CaO) (1)
  • the composition ratio of CaO defined by the formula (0.4) or more and / or the following formula (2): Al 2 O 3 / (SiO 2 + Al 2 O 3 + CaO) (2) Is a non-oriented electrical steel sheet in which the composition ratio of Al 2 O 3 defined by is 0.3 or more.
  • the non-oriented electrical steel sheet of the present invention is characterized by further containing at least one component of the following groups A to D in addition to the above component composition.
  • the present invention is to hot-roll a slab having any of the above-described component compositions into a hot-rolled sheet, and then cold-roll the hot-rolled sheet without subjecting the hot-rolled sheet to a finish.
  • the following formula (1) in the oxide inclusions present in the slab CaO / (SiO 2 + Al 2 O 3 + CaO) (1)
  • the composition ratio of Al 2 O 3 defined by the above is set to 0.3 or more, and the coil winding temperature in the hot rolling is set to 650 ° C. or more, and a method for producing a non-oriented electrical steel sheet is proposed.
  • the present invention is a non-directional property in which a slab having any of the above-described component compositions is hot-rolled into a hot-rolled sheet, subjected to hot-rolled sheet annealing, cold-rolled, and subjected to finish annealing.
  • the inventors reduced the Al content as much as possible based on the component composition of steel disclosed in Patent Document 3 described above in order to improve the texture and to investigate measures for improving magnetic properties.
  • P and Sn added component system specifically, C: 0.0030 mass%, Si: 1.6 mass%, Mn: 0.08 mass%, P: 0.06 mass%, S: 0.0020 mass%, sol.
  • Mn or added Ca to fix S as high melting point MnS or CaS, thereby preventing the formation of low melting point FeS and brittleness in hot rolling.
  • Mn is increased and Ca is added (C: 0.0030 mass%, Si: 1.6 mass%, Mn: 0.40 mass%, P: 0.07 mass%, S: 0.0020 mass%, sol.Al: 0.0008 mass%, N: 0.0015 mass%, Sn: 0.04 mass%, and Ca: 0.0030 mass%) are manufactured and re-adjusted to a temperature of 1100 ° C. After heating, when hot rolled to a thickness of 2.3 mm, no cracks or breaks were observed. From the above, it was confirmed that the increase in Mn and the addition of Ca are effective for preventing cracking and fracture in hot rolling in low Al steel.
  • the inventors scan the cross section (L cross section) parallel to the rolling direction of the product plate (finished annealed plate) manufactured by using the steel slab of the component system to which Mn is added and Ca is added as described above. It observed with the electron microscope (SEM), the component composition of the oxide inclusion which exists in a steel plate was analyzed, and the relationship between the result and the magnetic characteristic of a product board was investigated. As a result, it was recognized that the magnetic properties tended to vary depending on the composition of oxide inclusions present in the steel sheet, particularly the composition ratio of CaO and the composition ratio of Al 2 O 3 .
  • the inventors further changed the component composition of the oxide inclusions in the above component steels, and specifically changed the component systems in which the addition amounts of Al and Ca used as deoxidizers were changed.
  • C 0.0015 to 0.0035 mass%
  • Si 1.6 to 1.7 mass%
  • Mn 0.40 mass%
  • P 0.07 mass%
  • S 0.0010 to 0.0030 mass%
  • the C, Si, S and N having a composition range are due to variations during melting and are not intended.
  • the cross section (L cross section) of the finish annealing plate in the rolling direction is observed with a scanning electron microscope (SEM), the component composition of the oxide inclusions is analyzed, and the following formula (1): CaO / (SiO 2 + Al 2 O 3 + CaO) (1)
  • the composition ratio (mass% ratio) of Al 2 O 3 defined by The composition ratio (mass% ratio) of CaO and Al 2 O 3 is an average value for 200 or more oxide inclusions.
  • MnO, MgO, and the like were observed in addition to the above SiO 2 , Al 2 O 3 , and CaO. However, since they were small amounts, they were not considered in the calculation of the composition ratio.
  • FIG. 1 shows the relationship between the CaO composition ratio of oxide inclusions and the composition ratio of Al 2 O 3 and the iron loss W 15/50 . From this figure, the composition ratio of CaO (CaO / (SiO 2 + Al 2 O 3 + CaO)) is less than 0.4, and the composition ratio of Al 2 O 3 (Al 2 O 3 / (SiO 2 + Al 2 O 3 + CaO )) Is less than 0.3, the iron loss W 15/50 is inferior.
  • CaO / (SiO 2 + Al 2 O 3 + CaO) is 0.4 or more and / or Al 2 O 3 / ( It was found that the iron loss W 15/50 was favorable when (SiO 2 + Al 2 O 3 + CaO) was in the range of 0.3 or more.
  • Inclusions elongated in the rolling direction inhibit the grain growth in self-annealing immediately after hot rolling, hot-rolled sheet annealing, and finish annealing, thereby reducing the crystal grain size and inhibiting the domain wall movement. Loss deteriorates. Therefore, in order to improve the magnetic properties of the steel plate (product plate) after the finish annealing, the component composition of oxide inclusions present in the steel is controlled within an appropriate range and stretched in the rolling direction during hot rolling. It is considered effective to prevent this and improve the grain growth.
  • the present invention has been developed based on the above findings.
  • C 0.0050 mass% or less
  • C is an element that causes magnetic aging and increases iron loss. Particularly, if it exceeds 0.0050 mass%, an increase in iron loss becomes significant, so 0.0050 mass% or less. Restrict to. Preferably it is 0.0030 mass% or less. In addition, about a minimum, since it is so preferable that there is little, it does not prescribe
  • Si 1.5 to 5.0 mass%
  • Si is an element effective for increasing the electric resistance of steel and reducing iron loss.
  • Si since Al having the same effect as Si is reduced, Si is added by 1.5 mass% or more.
  • the upper limit is set to 5.0 mass%. The range is preferably 1.6 to 3.5 mass%.
  • Mn 0.20 to 3.0 mass% Mn combines with S to form MnS and has the effect of preventing hot brittleness due to FeS. Moreover, like Si, it is an element effective in increasing the electrical resistance of steel and reducing iron loss. Therefore, in the present invention, Mn is contained in an amount of 0.20 mass% or more. On the other hand, since magnetic flux density will fall if it exceeds 3.0 mass%, an upper limit shall be 3.0 mass%. Preferably, it is in the range of 0.25 to 1.0 mass%.
  • P 0.2 mass% or less
  • P is a useful element that has a large effect of increasing the hardness of steel with a small amount of addition, and is appropriately added according to the required hardness.
  • the upper limit is made 0.2 mass%.
  • it is in the range of 0.040 to 0.15 mass%.
  • S 0.0050 mass% or less
  • S is preferably as less as it is sulfided to form precipitates and inclusions, and deteriorates manufacturability (hot rollability) and magnetic properties of the product plate.
  • the upper limit is allowed up to 0.0050 mass%.
  • it is preferably 0.0025 mass% or less.
  • a minimum is not prescribed
  • sol. Al 0.0050 mass% or less
  • Al is an element effective in increasing the electric resistance of steel and reducing iron loss.
  • Al is desired to be less than 0.05 mass%, and the lower the better.
  • Al is further reduced, and sol. It is limited to 0.0050 mass% or less with Al (acid-soluble Al). Preferably, it is 0.0020 mass% or less.
  • N 0.0040 mass% or less
  • N is an element that deteriorates the magnetic characteristics as in the case of C described above.
  • the above-described adverse effect becomes significant, so the content is limited to 0.0040 mass% or less.
  • it is 0.0030 mass% or less.
  • the content is limited to 0.0040 mass% or less.
  • it is 0.0030 mass% or less.
  • the non-oriented electrical steel sheet of the present invention may further contain at least one component of the following groups A to D in the following range in addition to the essential components.
  • Group A; Ca: 0.0005 to 0.0100 mass% Ca like Mn, has the effect of fixing S in steel and preventing the formation of low melting point FeS and improving hot rolling properties.
  • Mn is increased, The addition of is not essential.
  • Ca has an effect of suppressing the occurrence of lashes in hot rolling, it is preferable to add 0.0005 mass% or more.
  • addition exceeding 0.0100 mass% increases the amount of Ca sulfide and Ca oxide to inhibit grain growth, and on the contrary, the iron loss characteristics deteriorate, so the upper limit is preferably 0.0100 mass%. . More preferably, it is in the range of 0.0010 to 0.0050 mass%.
  • Group B Sn: 0.01-0.1 mass% and Sb: 0.01-0.1 mass%, one or two selected from both Sn and Sb both improve texture and magnetic properties Has the effect of improving.
  • the upper limit is preferably set to 0.1 mass%. More preferably, it is in the range of 0.02 to 0.05 mass%.
  • Mg and REM are more stable than MnS and Cu 2 S at high temperatures It is an element having the effect of improving the magnetic properties by improving the grain growth because it produces sulfide and coarsens and fine sulfides are reduced. In order to acquire the said effect, it is preferable to contain 0.001 mass% or more of 1 or more types of Mg and REM, respectively. On the other hand, even if Mg and REM are added in excess of 0.05 mass%, the effect is saturated and economically disadvantageous. Therefore, the upper limit is preferably 0.05 mass%.
  • Group D Cu: 0.01 to 0.5 mass%, Ni: 0.01 to 0.5 mass%, and Cr: 0.01 to 0.5 mass%, or one or more selected from Cu, Ni and Cr is an element effective for increasing the specific resistance of a steel sheet and reducing iron loss. In order to acquire the said effect, it is preferable to add 0.01 mass% or more, respectively. On the other hand, since these elements are more expensive than Si and Al, the amount of each added is preferably 0.5 mass% or less.
  • the balance other than the above components is Fe and inevitable impurities.
  • the content of other elements is not rejected.
  • the content contained as an unavoidable impurity is as follows: V is 0.004 mass% or less, and Nb is 0. 0.004 mass% or less, B is 0.0005 mass% or less, and Ti is 0.002 mass% or less.
  • the inclusion which exists in the non-oriented electrical steel sheet of this invention is demonstrated.
  • the oxide inclusions present in the hot-rolled plate or slab as the material CaO composition ratio (CaO / (SiO 2 + Al 2 O 3 + CaO)) is 0.4 or more and / or composition ratio of Al 2 O 3 (Al 2 O 3 / (SiO 2 + Al 2 O 3 + CaO)) 0 .3 or more is required.
  • the composition ratio of CaO is 0.5 or more and / or the composition ratio of Al 2 O 3 is 0.4 or more, more preferably, the composition ratio of CaO is 0.6 or more, or the composition of Al 2 O 3 The ratio is 0.5 or more.
  • the CaO composition ratio and the Al 2 O 3 composition ratio of the oxide inclusions present in the steel sheet are the same as the SEM (oxide inclusions present in the cross section (L cross section) parallel to the rolling direction of the steel sheet. It is a value calculated from an average value obtained by observing 200 or more pieces with a scanning electron microscope) and analyzing their component compositions.
  • the manufacturing method of the non-oriented electrical steel sheet of this invention is demonstrated.
  • the non-oriented electrical steel sheet of the present invention is manufactured by omitting hot-rolled sheet annealing, it is necessary to regulate the coiling temperature after hot rolling, but it is manufactured by performing hot-rolled sheet annealing. When it does, it can manufacture with the manufacturing equipment and manufacturing process which are applied to the normal non-oriented electrical steel sheet. That is, in the method for producing a non-oriented electrical steel sheet of the present invention, first, a steel melted in a converter or an electric furnace is secondarily refined with a degassing treatment facility or the like, and prepared to a predetermined component composition. A steel material (slab) is obtained by a casting method or ingot-bundling method.
  • the component composition of oxide inclusions present in the steel is controlled within an appropriate range, that is, the composition ratio of CaO (CaO / (SiO 2 + Al 2 O 3 + CaO )) of 0.4 or more, and / or the need to control the composition ratio of Al 2 O 3 and (Al 2 O 3 / (SiO 2 + Al 2 O 3 + CaO)) to 0.3 or more Is that there is.
  • the method is as described above.
  • the slab produced as described above is subsequently hot-rolled, and the temperature (SRT) for reheating the slab is preferably in the range of 1000 to 1200 ° C. If the SRT exceeds 1200 ° C., not only energy loss increases and becomes uneconomical, but also the high temperature strength of the slab decreases, which may cause manufacturing problems such as slab sagging. On the other hand, when the temperature is lower than 1000 ° C., the hot deformation resistance increases and it is difficult to perform hot rolling. The subsequent hot rolling may be performed under normal conditions.
  • the thickness of the hot-rolled steel sheet is preferably in the range of 1.5 to 2.8 mm from the viewpoint of ensuring productivity.
  • hot-rolled sheet annealing after hot rolling may be performed or omitted, it is advantageous to omit it from the viewpoint of reducing manufacturing costs.
  • hot-rolled sheet annealing when hot-rolled sheet annealing is omitted, it is necessary to set the coiling temperature after hot rolling to 650 ° C. or higher. This is because, when the self-annealing of the hot-rolled sheet coil is insufficient and the steel sheet before cold rolling is not sufficiently recrystallized, ridging occurs or the magnetic flux density decreases.
  • it is 670 ° C. or higher.
  • the soaking temperature of hot-rolled sheet annealing is preferably in the range of 900 to 1150 ° C.
  • the steel sheet after the hot rolling or after the hot-rolled sheet annealing is made into a cold-rolled sheet having a final thickness by one or more cold rollings sandwiching the intermediate annealing.
  • the thickness of the cold-rolled sheet (final sheet thickness) is not particularly specified, but is preferably in the range of 0.10 to 0.60 mm. It is because productivity will fall if it is less than 0.10 mm, and an iron loss reduction effect is small if it exceeds 0.60 mm. In order to increase the iron loss reduction effect, the range of 0.10 to 0.35 mm is more preferable.
  • the cold-rolled steel sheet (cold rolled sheet) is then subjected to finish annealing by continuous annealing.
  • the soaking temperature of this finish annealing is preferably in the range of 700 to 1150 ° C. If the soaking temperature is less than 700 ° C., recrystallization does not proceed sufficiently and good magnetic properties cannot be obtained, and the shape correction effect by continuous annealing cannot be obtained. On the other hand, when the temperature exceeds 1150 ° C., energy loss increases and becomes uneconomical.
  • the insulating coating is preferably an organic coating containing a resin when it is desired to ensure good punchability. Moreover, when importance is attached to weldability, it is preferable to use a semi-organic or inorganic coating.
  • the steel sheet having the conditions suitable for the present invention can be produced without causing trouble in hot rolling or cold rolling, and the iron loss W 15/50 is 3.28 W / kg or less. It can be seen that the iron loss is low, the magnetic flux density B 50 is 1.722 T or higher and the magnetic flux density is high, and the magnetic properties are excellent. Conversely, it can be seen that the iron loss W 15/50 and / or the magnetic flux density B 50 are inferior in the magnetic properties of the steel sheet, which is a condition that does not conform to the present invention.
  • Steel C is an example in which the composition ratio of inclusions is outside the scope of the present invention because the amount of Al added as a deoxidizer during steel melting is small and CaSi is not added. .
  • the steel sheet having the composition suitable for the present invention has excellent magnetic properties with an iron loss W 15/50 of 3.13 W / kg or less and a magnetic flux density B 50 of 1.725 T or more. I understand that.

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Abstract

L'invention concerne une tôle d'acier électromagnétique à grains non orientés qui est caractérisée en ce que, lorsqu'elle est fabriquée par laminage à chaud d'une brame contenant, en % en masse, 0,0050 % ou moins de C, 1,5 à 5,0 % de Si, 0,20 à 3,0 % de Mn, 0,0050 % ou moins d'Al sol., 0,2 % ou moins de P, 0,0050 % ou moins de S et 0,0040 % ou moins de N, formant ainsi une tôle laminée à chaud, puis en soumettant la tôle laminée à chaud à un laminage à froid, sans effectuer de recuit de la tôle laminée à chaud, et à un recuit de finition, la proportion de composition de CaO dans les inclusions à base d'oxyde présentes dans la brame, ladite proportion de composition de CaO étant définie par CaO/(SiO2 + Al2O3 + CaO), est établie à 0,4 ou plus et/ou la proportion de composition d'Al2O3 dans les inclusions à base d'oxyde présentes dans la brame, ladite proportion de composition d'Al2O3 étant définie par Al2O3/(SiO2 + Al2O3 + CaO), est établie à 0,3 ou plus et la température de bobinage pendant le laminage à chaud est établie à 650 °C ou plus. Par conséquent, cette tôle d'acier électromagnétique à grains non orientés permet d'obtenir une excellente aptitude au recyclage, une haute densité de flux magnétique et une faible perte dans le fer.
PCT/JP2015/082191 2015-01-07 2015-11-17 Tôle d'acier électromagnétique à grains non orientés et son procédé de fabrication WO2016111088A1 (fr)

Priority Applications (8)

Application Number Priority Date Filing Date Title
RU2017127961A RU2682727C2 (ru) 2015-01-07 2015-11-17 Листовая неориентированная электротехническая сталь и способ ее производства
US15/541,964 US10822678B2 (en) 2015-01-07 2015-11-17 Non-oriented electrical steel sheet and method for producing the same
EP15876961.2A EP3243921B1 (fr) 2015-01-07 2015-11-17 Tôle d'acier électromagnétique à grains non orientés et son procédé de fabrication
MX2017008930A MX2017008930A (es) 2015-01-07 2015-11-17 Hoja de acero electrico no orientado y metodo para producir la misma.
BR112017014286-4A BR112017014286B1 (pt) 2015-01-07 2015-11-17 chapa de aço elétrico não orientado e método para produção da mesma
KR1020177018621A KR101940084B1 (ko) 2015-01-07 2015-11-17 무방향성 전자 강판 및 그의 제조 방법
CN201580072499.XA CN107109570A (zh) 2015-01-07 2015-11-17 无取向性电磁钢板及其制造方法
CA2971682A CA2971682C (fr) 2015-01-07 2015-11-17 Tole d'acier electromagnetique a grains non orientes et son procede de fabrication

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
JP2015001531 2015-01-07
JP2015-001531 2015-01-07
JP2015204268A JP6020863B2 (ja) 2015-01-07 2015-10-16 無方向性電磁鋼板およびその製造方法
JP2015-204268 2015-10-16

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Cited By (4)

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CN113727788A (zh) * 2019-04-22 2021-11-30 杰富意钢铁株式会社 无取向性电磁钢板的制造方法
CN114086058A (zh) * 2021-10-25 2022-02-25 马鞍山钢铁股份有限公司 一种切口耐蚀性良好的无取向硅钢及其生产方法
CN115198203A (zh) * 2021-04-09 2022-10-18 宝山钢铁股份有限公司 一种免常化中间退火的无取向电工钢板及其制造方法
EP4253574A4 (fr) * 2020-11-27 2024-01-24 Nippon Steel Corporation Tôle en acier électromagnétique non orienté ainsi que procédé de fabrication de celle-ci, et tôle en acier laminée à chaud

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CN113727788B (zh) * 2019-04-22 2023-09-01 杰富意钢铁株式会社 无取向性电磁钢板的制造方法
EP4253574A4 (fr) * 2020-11-27 2024-01-24 Nippon Steel Corporation Tôle en acier électromagnétique non orienté ainsi que procédé de fabrication de celle-ci, et tôle en acier laminée à chaud
CN115198203A (zh) * 2021-04-09 2022-10-18 宝山钢铁股份有限公司 一种免常化中间退火的无取向电工钢板及其制造方法
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CN114086058A (zh) * 2021-10-25 2022-02-25 马鞍山钢铁股份有限公司 一种切口耐蚀性良好的无取向硅钢及其生产方法

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