EP0084980B1 - Nicht-kornorientiertes Elektroblech mit niedrigen Wattverlusten und hoher Magnetflussdichte und Verfahren zu seiner Herstellung - Google Patents

Nicht-kornorientiertes Elektroblech mit niedrigen Wattverlusten und hoher Magnetflussdichte und Verfahren zu seiner Herstellung Download PDF

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Publication number
EP0084980B1
EP0084980B1 EP83300393A EP83300393A EP0084980B1 EP 0084980 B1 EP0084980 B1 EP 0084980B1 EP 83300393 A EP83300393 A EP 83300393A EP 83300393 A EP83300393 A EP 83300393A EP 0084980 B1 EP0084980 B1 EP 0084980B1
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EP
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Prior art keywords
oriented electrical
hot
annealing
electrical steel
steel sheet
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Expired
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EP83300393A
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English (en)
French (fr)
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EP0084980A2 (de
EP0084980A3 (en
Inventor
Kunisuke Process Technology R&D Labs. Miyoshi
Yoshiaki Yawata Works Shimoyama
Takeshi Process Technology R&D Labs. Kubota
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Nippon Steel Corp
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Nippon Steel Corp
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Priority claimed from JP57010211A external-priority patent/JPS58151453A/ja
Priority claimed from JP58009398A external-priority patent/JPS59157259A/ja
Application filed by Nippon Steel Corp filed Critical Nippon Steel Corp
Publication of EP0084980A2 publication Critical patent/EP0084980A2/de
Publication of EP0084980A3 publication Critical patent/EP0084980A3/en
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
    • C21D8/1261—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 following hot rolling
    • 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
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/14766—Fe-Si based alloys
    • H01F1/14775—Fe-Si based alloys in the form of sheets

Definitions

  • the present invention relates to a non-oriented electrical steel material having a low watt loss and a high magnetic flux density, and to a process for producing the same.
  • a non-oriented electrical steel sheet is used as core material for electrical machinery and apparatuses, such as motors and transformers.
  • the magnetic properties of a non-oriented electrical steel sheet must be improved so that the watt loss in-terms of W 15/50 is 4.5 w/kg or less, while the magnetic flux density in terms of B 50 is 1.71 Tesla or more.
  • non-oriented electrical steel sheets are graded in accordance with the watt loss and magnetic flux density from S60- to S9-grades according to a JIS standard.
  • the content of silicon which appreciably increases resistivity is high so as to decrease the watt loss.
  • the silicon content of a grade S60 is virtually 0%, and the silicon contents of S23, S18, and S9 grades are approximately 1.5%, approximately 2.0%, and approximately 3.0%, respectively.
  • a high silicon content results in a decrease in the magnetic flux density.
  • Figure 1 illustrates relationships between the watt loss in terms of W 15/50 and the magnetic flux density B 50 with regard to conventional non-oriented electrical steel sheets as well as a non-oriented electrical steel sheet according to the present invention.
  • the curves 1, and 1' in Fig. 1 represent the upper and lower limits of the 8 50 and W '5/50 of conventional non-oriented electrical steel sheets which are explained hereinafter, and illustrate that the watt loss is decreased in accordance with an increase in the magnetic flux density.
  • Symbol 2 in Fig. 1 is the lines connecting the magnetic properties of non-oriented electrical steel sheets stipulated in JIS Standard C2552.
  • 56-102520 proposes a method for producing non-oriented silicon steel sheet with low watt loss due to adding Sn.
  • tin in order for tin to effectively decrease the watt loss, it is necessary to carry out slow cooling during the annealing of a hot-rolled steel strip or employ a slow heating rate during the final annealing, which procedure disadvantageously limits to the process for producing a non-oriented electrical steel sheet.
  • tin disclosed in Japanese Unexamined Patent Publication (Kokai) No. 56-102520 results in decrease in a watt loss, the relationship between the watt loss and magnetic flux density falls within the curves 1 and 1' of Fig. 1.
  • the addition of tin is unsatisfactory for meeting the above-mentioned recent demands for improving the magnetic properties of a non-oriented electrical steel sheet.
  • an increase in the magnetic flux density is non-oriented electrical steel sheets as compared with conventional non-oriented electrical steel sheets containing either tin or boron can be achieved by: adding boron into silicon steel in such an amount that the weight ratio of the boron content/nitrogen content be maintained within a predetermined range; adding tin into silicon steel in a small amount; and, subjecting a hot-rolled steel strip to an annealing or carrying out a self-annealing by means of coiling a hot-rolled steel strip at a high temperature. That is, although the known addition of either boron or tin alone does not provide the magnetic flux density increased but only provides the watt loss to be decreased, the combined addition of boron and tin can simultaneously attain both low watt loss and high magnetic flux density.
  • the boron can be totally or partially replaced with aluminum when content of manganese in a silicon steel is appreciably high.
  • the annealing mentioned above of a hot-rolled steel strip as well as a finishing annealing of a cold rolled steel strip can be carried out continuously in a short period of time.
  • the present invention was completed based on this discovery.
  • a non-oriented electrical steel sheet, according to the present invention having a low watt loss and a high magnestic flux density consists of 0.015% of carbon at the highest, from 0.3% to 2.0% of silicon, from 0.005% to 0.10% of acid-soluble aluminum (hereinafter referred to as sol. Al), from 0.02% to 0.20% of tin, 0.007% of nitrogen at the highest, and 0.005% of boron at the highest, the weight ratio of boron content/nitrogen content being from 0.5 to 1.5, the balance being iron and unavoidable impurities, said non-oriented electrical sheet being produced by a process comprising an annealing of a hot-rolled steel strip.
  • This non-oriented electrical steel sheet of the present invention is hereinafter referred to as the Sn-B non-oriented electrical steel sheet.
  • Another non-oriented electrical steel sheet, according to the present invention, having a low watt loss and a high magnetic flux density consists of 0.015% of carbon at the highest, from 0.3% to 2.0% of silicon, from more than 1.0% to 1.5% of manganese, from 0.02% to 0.20% of tin, and either (a) or (b): (a) from 0.005% to 0.10% of sol. AI and 0.007% of nitrogen at the highest, and 0.005% of boron at the highest, the weight ratio of boron content/nitrogen content being from 0.5 to 1.5; or, (b) from more than 0.1 % to 0.2% of sol.
  • This sheet is hereinafter referred to as the Sn-Al (B) nonoriented electrical steel sheet.
  • a process for producing the Sn-B non-oriented electrical steel sheet or the Sn-AI(B) non-oriented electrical steel sheet according to the present invention successively comprises the steps of: hot-rolling a silicon steel which having the composition as specified above; annealing the hot-rolled steel strip; cold rolling the hot-rolled steel strip once, or twice or more with an intermediate annealing; and, continuously annealing the cold-rolled steel strip.
  • the annealing of the hot-rolled steel strip may be carried out by means of coiling a hot-rolled steel strip at a temperature of 700°C at the lowest and then self-annealing the coiled hot-rolled steel strip.
  • annealing of the hot-rolled strip may be completed in the hot-rolling step.
  • the annealing temperature is 850°C at the lowest.
  • the Sn-B non-oriented electrical steel sheet is described with regard to how tin and boron synergistically improve the magnetic properties thereof.
  • a non-oriented electrical steel sheet contains boron only, the boron fixes nitrogen which is detrimental to the magnetic properties and boron nitrides precipitate in the crystal grains.
  • the tin segregates at the grain boundaries and suppresses during recrystallization the generation of a (111) orientation which orientation is detrimental to the magnetic properties thereof.
  • the segregated tin suppresses the recrystallization to initiate at the grain boundaries and promotes recrystallization to initiate in the crystal grains.
  • the boron nitrides which are precipitated in the crystal grains behave as nuclei during recrystallization and promotes the generation of (110) and (100) textures which are advantageous for the magnetic properties thereof. Therefore, the magnetic properties of the Sn-B non-oriented electrical steel sheet are considerably improved over the magnetic properties of a non-oriented electrical steel sheet containing either boron or tin alone.
  • the Sn-AI(B) non-oriented electrical steel sheet is described with regard to how manganese, tin and aluminum or boron synergistically improve the magnetic properties thereof. Manganese lowers the recrystallization temperature and substantially facilitates the recrystallization.
  • the synergistic effect of tin and boron is explained with reference to the Sn-B non-oriented electrical steel sheet is also attained and promoted since manganese substantially promotes recrystallization.
  • the improvement in magnetic properties is attained by even partially or totally replacing boron with sol. Al
  • Aluminum added to a silicon steel and alloyed in the silicon steel as sol. AI in an appreciable amount prevents the precipitation of AIN, which is detrimental to the magnetic properties thereof.
  • aluminum increases the resistivity and decreases the watt loss of silicon steels.
  • Tin segregates at the grain boundaries and suppresses during recrystallization the generation of (111) orientation which is detrimental to the magnetic properties of a silicon steel.
  • Manganese, sol. Al, and tin which are advantageous for the magnetic properties as understood from the above description synergistically promotes the generation of (110) and (100) orientations so that the Sn-AI(B) non-oriented electrical steel sheet has predominantly (110) and (100) textures.
  • nitrogen and sol. AI that: nitrogen does not form compounds or precipitates which behave as nuclei during recrystallization; AIN which is detrimental to the magnetic properties of a silicon steel is not formed due to an appreciable Sol. AI content of; and, sol. AI not only removes the detrimental effects of nitrogen but also increases resistivity, thereby decreasing the watt loss.
  • the concept which are common to both the Sn-B nonoriented electrical steel sheet and the Sn-AI(B) non-oriented electrical steel sheet is to controlling the recrystallization so that it is advantageous with regard to the magnetic properties thereof.
  • this concept is explained in more metallurgical terms, it can be said that the combined addition of tin together with boron and or sol. Al renders recrystallization liable to occur predominantly in the crystal grains, and (110) and (100) textures which are desirable for the magnetic are formed during recrystallization.
  • conventional addition of tin only and addition of boron and/or sol. AI only are not very effective for suppressing the formation of (111) texture which is detrimental to the magnetic properties of a non-oriented electrical steel sheet.
  • compositions of the Sn-B nonoriented electrical steel sheet and the SnB(AI) non-oriented electrical steel sheet are now described.
  • Carbon is a harmful element which increases the watt loss. Therefore, a low carbon content, i.e. 0.015% or less, is desirable so as to reduce the watt loss and prevent deterioration of the magnetic properties due to aging or the so-called magnetic aging. A carbon content of not more than 0.005% is desirable for promoting the synergistic effects which are attained by combined addition of tin with boron and/or sol. Al.
  • Silicon increases the resistivity and decreases the watt loss of a steel as is well known. Silicon content which is effective for decreasing the watt loss is 0.3% at the lowest. However, when the silicon content is more than 2.0%, the rolling workability of silicon steel is impaired and the nonoriented electrical steel sheet becomes expensive.
  • Aluminum is necessary for deoxidizing steels.
  • a sol. AI content of 0.005% is necessary for effectively deoxidizing silicon steels.
  • sol. AI In the case of the Sn-B non-oriented electrical steel sheet and the Sn-AI(B) non-oriented silicon steel sheet containing boron, the maximum content of sol. AI should be so controlled that sol. AI does not excessively fix the nitrogen. If the sol. AI content is more than 0.1%, the sol. AI fixes the nitrogen excessively, and thus the amount of solute boron is increased with the result that the watt loss is increased and the magnetic flux density is decreased. In other words, when the sol. AI content is more than 0.1 %, sol. AI renders the boron ineffective for improving the magnetic properties of the non-oriented electrical steel sheet.
  • boron can be partially or totally replaced with sol. AI as described above. If boron is totally replaced with sol. Al, the sol. AI content must be more than 0.1% so as to prevent the precipitation of AIN. If boron is partially replaced with sol. AI and if the content of sol. AI is 0.1 % at the highest, the weight ratio of the boron content/nitrogen content should be from 0.5 to 1.5 (0.5 ⁇ B/N ⁇ 1.5). When the content of sol. AI is more than 0.20%, the magnetic flux density is low.
  • the weight ratio of the boron content/nitrogen content must be from 0.5 to 1.5. If the weight ratio is less than 0.5, it is difficult to eliminate the detrimental effect of nitrogen. On the other hand, when such ratio is more than 1.5, an amount of solute boron is so increased that the magnetic properties of the non-oriented electrical steel sheet cannot be improved.
  • the boron content must be 0.005% at the highest so as to prevent that cracks are formed on slabs during hot rolling.
  • AI synergistically improve the magnetic properties of the non-oriented electrical steel sheet.
  • the content of tin must be 0.02% at the lowest.
  • the effect of tin is saturated and the production cost is increased.
  • Manganese is not conventionally used to enhance the magnetic properties of a non-oriented electrical steel sheet because manganese is liable to form nonmetallic inclusions, such as sulfides and oxides. However, it is possible to use manganese to enhance the magnetic properties of an electrical steel sheet since the steelmaking technique is advanced enough so that high-purity steels can be produced. According to a discovery made by the present inventors manganese is effective for developing (100) and (110) textures, which textures result in desirable magnetic properties, and for suppressing a (111) texture, which texture is detrimental to the magnetic properties thereof. In the Sn-AI(B) nonoriented electrical steel sheet the manganese content is more than 1.0% so as to promote development of (100) and (110) textures.
  • the manganese content in the Sn-B non-oriented electrical steel sheet is not specified and may be less than 1.0%, e.g. approximately 0.3%.
  • the elements other than those described above are iron and unavoidable impurities.
  • Steels having the composition as described above are melted in a converter, an electric furnace, or the like, and are continuously cast or cast as an ingot, followed by rough rolling to obtain a slab.
  • the slab is hot-rolled at a predetermined temperature so as to produce a hot-rolled steel strip.
  • Annealing of a hot-rolled steel strip can improve the texture of the strip, thereby enhancing the magnetic properties thereof as compared with those without annealing of a hot-rolled strip. If the hot-rolled strip is annealed at a temperature less than 850°C, the annealing is not very effective for improving the texture of the strip.
  • Annealing of the hot-rolled steel strip may be carried out by means of self-annealing, in which the strip is annealed by the heat retained therein.
  • the self-annealing can be attained by coiling a hot-rolled steel strip at a temperature of 700°C at the lowest. If the coiling temperature is less than 700°C, fine precipitates form during a subsequent annealing, i.e. the annealing of a hot-rolled steel strip, and suppress the growth of crystal grains.
  • a coiled hot-rolled strip is advantageously covered with a heat-insulation cover which reduces the amount of heat which radiates from the strip.
  • the hot-rolled steel strip is subsequently annealed, e.g. by means of the batch annealing or continuous annealing. Since the magnetic properties obtained by both rapid heating- and cooling-rates of annealing are excellent, the continuous annealing is advisable for annealing a hot-rolled steel strip.
  • a hot-rolled steel strip is then cold-rolled once or twice or more with an intermediate annealing, thereby obtaining a final thickness.
  • the intermediate annealing is carried out between successive cold-rollings.
  • Finishing annealing of a cold-rolled steel strip is then carried out. Slow heating during the finishing annealing is not very advantageous for the magnetic properties, since the combined addition of tin with boron and/or sol. AI changes the influences of the heating rate upon the magnetic properties in such a manner that a rapid heating is rather desirable for the magnetic properties.
  • the annealing temperature is varied in accordance with the magnetic properties to be attained. Since the continuous finishing annealing is more advisable than the batch finishing annealing, the production efficiency of the Sn-B non-oriented electrical steel sheet and Sn-AI(B) non-oriented electrical steel sheet is high, which is one of the synergistic effects attained by the combined addition of tin with boron and/or sol. Al.
  • the process for producing the Sn-B non-oriented electrical steel sheet and the Sn-AI(B) non-oriented electrical steel sheet may be further subjected to stress-relief annealing or skin pass rolling.
  • the reduction rate (draft) at skin pass rolling depends on the intermediate annealing temperature.
  • reduction rate at skin-pass rolling is from 2% to 10%.
  • a skin-pass rolled steel strip is then subjected to blanking to obtain a predetermined sheet section and is then stress-relief annealed. In this case, the so-called semi-processed non-oriented electrical steel sheet is produced.
  • the reduction rate at skin pass rolling is less than 2%, stress-relief annealing is ineffective for improving the watt loss.
  • a reduction rate at skin pass rolling of more than 10% results in deterioration the magnetic properties.
  • Non-oriented electrical steel sheets were produced under the conditions of process for treating steels given in Table 2.
  • both a low watt loss and a high magnetic flux density are attained when steels: contain both boron and tin or has high manganese and sol. AI contents and contains tin, and at the same time these steels are self-annealed or annealed after the hot-rolling step.
  • Example 1 Steel Nos. 5, 6, 7, 14, and 15, were subjected to the same production procedure as in Example 1, except that virtually 0.5 mm thick cold-rolled steel strips were continuously annealed at 750°C for the period of 60 seconds (1 minute) and then skin-passes rolled at the reduction rate of 4%.
  • An Epstein specimen was cut from the skin-pass rolled strip and the magnetic properties were measured after carrying out a stress-relief annealing at 790°C for the period of 1 hour (60 minutes).
  • a manganese content of more than 1% is effective for improving the magnetic properties of non-oriented electrical steel sheets containing tin and boron at such contents as providing 0.5 ⁇ B/N ⁇ 1.5 and a decrease in the watt-loss and an increase in magnetic flux density are simultaneously attained.

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Claims (7)

1. Nicht-orientierter Elektrostahl mit niedrigem Wattverlust und hoher magnetischer Flußdichte, bestehend aus höchstens 0,015% Kohlenstoff, 0,3 bis 2,0% Silicium, 0,005 bis 0,10% säurelösliches Aluminium, 0,02 bis 0,20% Zinn, höchstens 0,007% Stickstoff und höchstens 0,005% Bor, wobei das Gewichtsver.häitnis des Borgehalts zum Stickstoffgehalt 0,5 bis 1,5 beträgt, Rest Eisen und unvermeidbare Verunreinigungen, wobei der nicht-orientierte Elektrostahl durch ein Verfahren hergestellt wird, das ein Glühen nach dem Warmwalzen des Stahls umfaßt.
2. Nicht-orientiertes Elektrostahlblech mit niedrigem Wattverlust und hoher magnetischer Flußdichte gemäß vorliegender Erfindung, enthaltend höchstens 0,015% Kohlenstoff, 0,3 bis 2,0% Silicium, von mehr als 1,0 bis 1,5% Mangan, von 0,02 bis 0,20% Zinn, und entweder (a) oder (b): (a) von 0,005 bis 0,10% säurelösliches Aluminium, höchstens 0,005% Bor, und höchstens 0,007% Stickstoff, wobei das Gewichtsverhältnis des Borgehalts zum Stickstoffgehalt 0,5 bis 1,5 beträgt, oder (b) von mehr als 0,1 bis 0,2% säurelösliches Aluminium, Rest Eisen und unvermeidbare Verunreinigungen, wobei das Blech durch Verfahrensstufen hergestellt wird, die ein Glühen nach dem Warmwalzen des Stahls umfassen.
3. Verfahren zur Herstellung eines nicht-orientierten Elektrostahlblechs nach den Ansprüchen 1 oder 2, umfassend nacheinander die Stufen: Warmwalzen eines Siliciumstahls mit der vorstehend angegebenen Zusammensetzung; Glühen nach dem Warmwalzen des Stahls; einmal, zweimal oder mehrmals Kaltwalzen des warmgewalzten Stahls mit einem Zwischenglühen; und Durchlaufglühen des kaltgewalzten Stahls.
4. Verfahren nach Anspruch 3, wobei das Material in Bandform vorliegt.
5. Verfahren nach Anspruch 3 oder 4, wobei das Glühen des warmgewalzten Stahlbandes durch Aufwickeln des warmgewalzten Stahlbandes bei einer Temperatur von mindestens 700°C und Glühen des aufgewickelten warmgewalzten Stahlbandes durchgeführt wird.
6. Verfahren nach Anspruch 3 oder 4, wobei das Glühen des warmgewalzten Stahlbandes nach dem Warmwalzschritt bei einer Temperatur von mindestens 850°C durchgeführt.
7. Verfahren nach Anspruch 3 oder 4, wobei das durchlaufgeglühte kaltgewalzte Stahlband ferner einem Kaltnachwalzen mit einer Dickenverminderung von 2 bis 10% unterzogen wird.
EP83300393A 1982-01-27 1983-01-26 Nicht-kornorientiertes Elektroblech mit niedrigen Wattverlusten und hoher Magnetflussdichte und Verfahren zu seiner Herstellung Expired EP0084980B1 (de)

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
JP10211/82 1982-01-27
JP57010211A JPS58151453A (ja) 1982-01-27 1982-01-27 鉄損が低くかつ磁束密度のすぐれた無方向性電磁鋼板およびその製造法
JP58009398A JPS59157259A (ja) 1983-01-25 1983-01-25 鉄損が低くかつ磁束密度がすぐれた無方向性電磁鋼板およびその製造法
JP9398/83 1983-01-25

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EP0084980A2 EP0084980A2 (de) 1983-08-03
EP0084980A3 EP0084980A3 (en) 1983-09-14
EP0084980B1 true EP0084980B1 (de) 1986-01-08

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EP83300393A Expired EP0084980B1 (de) 1982-01-27 1983-01-26 Nicht-kornorientiertes Elektroblech mit niedrigen Wattverlusten und hoher Magnetflussdichte und Verfahren zu seiner Herstellung

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EP (1) EP0084980B1 (de)
AT (1) ATE17376T1 (de)
AU (2) AU551071B2 (de)
DE (1) DE3361738D1 (de)

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0222442A (ja) * 1988-07-12 1990-01-25 Nippon Steel Corp 高張力電磁鋼板及びその製造方法
JPH07116509B2 (ja) * 1989-02-21 1995-12-13 日本鋼管株式会社 無方向性電磁鋼板の製造方法
JPH07116507B2 (ja) * 1989-02-23 1995-12-13 日本鋼管株式会社 無方向性電磁鋼板の製造方法
JPH086135B2 (ja) * 1991-04-25 1996-01-24 新日本製鐵株式会社 磁気特性の優れた無方向性電磁鋼板の製造方法
EP0567612A4 (de) * 1991-10-22 1994-04-05 Po Hang Iron & Steel Elektrisch nichtorientierte stahlplatten mit hohen magnetischen eigenschaften und deren herstellung.
KR100345706B1 (ko) * 1996-12-09 2002-09-18 주식회사 포스코 자기적특성이우수한무방향성전기강판및그제조방법

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JPS5432412B2 (de) * 1973-10-31 1979-10-15
DE2834035A1 (de) * 1977-09-29 1979-04-12 Gen Electric Verfahren zur herstellung von kornorientiertem siliziumeisen-flachmaterial und kaltgewalztes siliziumeisen-flachmaterial als produkt
JPS583027B2 (ja) * 1979-05-30 1983-01-19 川崎製鉄株式会社 鉄損の低い冷間圧延無方向性電磁鋼板

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DE3361738D1 (en) 1986-02-20
EP0084980A2 (de) 1983-08-03
EP0084980A3 (en) 1983-09-14
ATE17376T1 (de) 1986-01-15
AU551071B2 (en) 1986-04-17
AU1076583A (en) 1983-08-04
AU4568185A (en) 1985-11-07

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