EP0084980A2 - 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
EP0084980A2
EP0084980A2 EP83300393A EP83300393A EP0084980A2 EP 0084980 A2 EP0084980 A2 EP 0084980A2 EP 83300393 A EP83300393 A EP 83300393A EP 83300393 A EP83300393 A EP 83300393A EP 0084980 A2 EP0084980 A2 EP 0084980A2
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EP
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Prior art keywords
oriented electrical
hot
annealing
electrical steel
steel sheet
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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
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EP83300393A
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English (en)
French (fr)
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EP0084980B1 (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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Publication date
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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Publication of EP0084980B1 publication Critical patent/EP0084980B1/de
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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.
  • non-oriented electrical steel sheets are graded in accordance with the watt loss and magnetic flux density from S60- to 59-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 B 50 and W 15/50 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. 2 is the lines connecting the magnetic properties of non-oriented electrical steel sheets stipulated in JIS Standard C2552.
  • an increase in the magnetic flux density in 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 provides 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 totaly 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 consinuously 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 (nereinafter 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 nonoriented 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 inveniton 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. Al 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 SnB non-oriented electrical steel sheet or the Sn-Al(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 temparature 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 tehreof.
  • a nonoriented electrical steel sheet contains boron only, the boron fixes nitrogen which is detrimental to the magnetic properties and boron nitrides precepitate in the crystal grains.
  • the tin segregates at the grain boundaries and suppresses during recrystallization the generation of a (1111 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 initiates 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-Al(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. Al in an appreciable amount prevents the precipitation of AlN, which is deterimental to the magnetic properties thereof.
  • aluminum increases the resistivity and decreases the watt loss or 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.
  • nitrogen and sol. Al 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. Al content of; and, sol. Al not only removes the deterimental 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-Al(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. Al 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(Al) non-oriented electrical steel sheet are now aescribed.
  • 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 peoperties 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. Al content of 0.005% is necessary for effectively deoxidizing silicon steels.
  • the maximum content of sol. Al should be so controlled that sol. Al does not excessively ix the nitrogen. If the sol. Al content is more than 0.1%, the sol. Al 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. Al content is more than 0.1%, sol. Al 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. Al as described above. If boron is totally replaced with sol. A1, the sol. Al content must be more than 0.1% so as to prevent the precipitation of AlN. If boron is partially replaced with sol. Al and if the content of sol. Al 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 ⁇ BIN ⁇ 1.5). When the content of sol. Al 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.
  • Tin together with boron, or together with both manganese and sol Al 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 includions, 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-A1(B) nonoriented electrical steel sheet the manganese content is more than 1.0% so as to promote development of [100] and [1101 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 tnan 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. Al 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.
  • the production efficiency of the Sn-B non-orientea electrical steel sheet and Sn-Al(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-Al(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. Al 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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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Materials Engineering (AREA)
  • Electromagnetism (AREA)
  • Organic Chemistry (AREA)
  • Metallurgy (AREA)
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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 true EP0084980A2 (de) 1983-08-03
EP0084980A3 EP0084980A3 (en) 1983-09-14
EP0084980B1 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)

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2643386A1 (fr) * 1989-02-21 1990-08-24 Nippon Kokan Kk Procede de fabrication de feuillards d'acier magnetique non oriente
FR2643387A1 (fr) * 1989-02-23 1990-08-24 Nippon Kokan Kk Procede de fabrication de feuillards d'acier magnetique non-oriente
EP0418424A1 (de) * 1988-07-12 1991-03-27 Nippon Steel Corporation Hochfeste nichtkornorientierte Elektrobleche und Verfahren zu ihrer Herstellung
EP0511601A1 (de) * 1991-04-25 1992-11-04 Nippon Steel Corporation Verfahren zur Herstellung nichtorientierter Elektrostahlbleche mit ausgezeichneten magnetischen Eigenschaften
WO1993008313A1 (en) * 1991-10-22 1993-04-29 Pohang Iron & Steel Co., Ltd. Nonoriented electrical steel sheets with superior magnetic properties, and methods for manufacturing thereof
KR100345706B1 (ko) * 1996-12-09 2002-09-18 주식회사 포스코 자기적특성이우수한무방향성전기강판및그제조방법

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2249957A1 (de) * 1973-10-31 1975-05-30 Kawasaki Steel Co
GB2005718A (en) * 1977-09-29 1979-04-25 Gen Electric Method of producing silicon- iron sheet material and product
EP0019849A1 (de) * 1979-05-30 1980-12-10 Kawasaki Steel Corporation Kaltgewalztes Stahlblech mit nicht-orientierter Kornstruktur für elektrotechnische Anwendungen

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2249957A1 (de) * 1973-10-31 1975-05-30 Kawasaki Steel Co
GB2005718A (en) * 1977-09-29 1979-04-25 Gen Electric Method of producing silicon- iron sheet material and product
EP0019849A1 (de) * 1979-05-30 1980-12-10 Kawasaki Steel Corporation Kaltgewalztes Stahlblech mit nicht-orientierter Kornstruktur für elektrotechnische Anwendungen

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0418424A1 (de) * 1988-07-12 1991-03-27 Nippon Steel Corporation Hochfeste nichtkornorientierte Elektrobleche und Verfahren zu ihrer Herstellung
FR2643386A1 (fr) * 1989-02-21 1990-08-24 Nippon Kokan Kk Procede de fabrication de feuillards d'acier magnetique non oriente
FR2643387A1 (fr) * 1989-02-23 1990-08-24 Nippon Kokan Kk Procede de fabrication de feuillards d'acier magnetique non-oriente
DE4005807A1 (de) * 1989-02-23 1990-08-30 Nippon Kokan Kk Verfahren zum herstellen von nichtorientiertem magnetstahlblech
EP0511601A1 (de) * 1991-04-25 1992-11-04 Nippon Steel Corporation Verfahren zur Herstellung nichtorientierter Elektrostahlbleche mit ausgezeichneten magnetischen Eigenschaften
US5186763A (en) * 1991-04-25 1993-02-16 Nippon Steel Corporation Process for production of non-oriented electrical steel sheet having excellent magnetic properties
WO1993008313A1 (en) * 1991-10-22 1993-04-29 Pohang Iron & Steel Co., Ltd. Nonoriented electrical steel sheets with superior magnetic properties, and methods for manufacturing thereof
KR100345706B1 (ko) * 1996-12-09 2002-09-18 주식회사 포스코 자기적특성이우수한무방향성전기강판및그제조방법

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Publication number Publication date
EP0084980B1 (de) 1986-01-08
ATE17376T1 (de) 1986-01-15
AU1076583A (en) 1983-08-04
DE3361738D1 (en) 1986-02-20
AU4568185A (en) 1985-11-07
EP0084980A3 (en) 1983-09-14
AU551071B2 (en) 1986-04-17

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