TW555863B - Nonoriented electromagnetic steel sheet and method for producing the same - Google Patents
Nonoriented electromagnetic steel sheet and method for producing the same Download PDFInfo
- Publication number
- TW555863B TW555863B TW091114213A TW91114213A TW555863B TW 555863 B TW555863 B TW 555863B TW 091114213 A TW091114213 A TW 091114213A TW 91114213 A TW91114213 A TW 91114213A TW 555863 B TW555863 B TW 555863B
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- steel
- steel sheet
- iron
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 287
- 239000010959 steel Substances 0.000 title claims abstract description 287
- 238000004519 manufacturing process Methods 0.000 title claims description 25
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical group [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 228
- 229910052742 iron Inorganic materials 0.000 claims abstract description 109
- 239000000203 mixture Substances 0.000 claims abstract description 39
- 239000012535 impurity Substances 0.000 claims abstract description 12
- 238000000137 annealing Methods 0.000 claims description 58
- CWYNVVGOOAEACU-UHFFFAOYSA-N Fe2+ Chemical compound [Fe+2] CWYNVVGOOAEACU-UHFFFAOYSA-N 0.000 claims description 34
- 238000000034 method Methods 0.000 claims description 33
- 238000010438 heat treatment Methods 0.000 claims description 31
- 230000002079 cooperative effect Effects 0.000 claims description 28
- 239000013078 crystal Substances 0.000 claims description 26
- 238000011282 treatment Methods 0.000 claims description 26
- 238000005097 cold rolling Methods 0.000 claims description 25
- 238000005098 hot rolling Methods 0.000 claims description 20
- 238000007670 refining Methods 0.000 claims description 18
- 229910000565 Non-oriented electrical steel Inorganic materials 0.000 claims description 13
- 230000008569 process Effects 0.000 claims description 5
- 101000864780 Homo sapiens Pulmonary surfactant-associated protein A1 Proteins 0.000 claims description 4
- 101000651017 Homo sapiens Pulmonary surfactant-associated protein A2 Proteins 0.000 claims description 4
- 102100027773 Pulmonary surfactant-associated protein A2 Human genes 0.000 claims description 4
- 238000007639 printing Methods 0.000 claims description 3
- 229910052799 carbon Inorganic materials 0.000 claims description 2
- 230000014509 gene expression Effects 0.000 claims description 2
- 239000002184 metal Substances 0.000 claims description 2
- 229910052751 metal Inorganic materials 0.000 claims description 2
- 238000006243 chemical reaction Methods 0.000 claims 1
- 230000004907 flux Effects 0.000 abstract description 60
- 229910052698 phosphorus Inorganic materials 0.000 abstract description 7
- 229910052710 silicon Inorganic materials 0.000 abstract description 7
- 229910052748 manganese Inorganic materials 0.000 abstract description 4
- 229910052757 nitrogen Inorganic materials 0.000 abstract description 4
- 239000000126 substance Substances 0.000 abstract description 2
- 238000004080 punching Methods 0.000 description 69
- 230000000694 effects Effects 0.000 description 40
- 238000012360 testing method Methods 0.000 description 28
- 230000000052 comparative effect Effects 0.000 description 25
- 238000005096 rolling process Methods 0.000 description 19
- 230000007423 decrease Effects 0.000 description 15
- 239000002245 particle Substances 0.000 description 15
- 238000002474 experimental method Methods 0.000 description 14
- 239000000463 material Substances 0.000 description 13
- 238000005204 segregation Methods 0.000 description 10
- 238000005520 cutting process Methods 0.000 description 9
- 230000006872 improvement Effects 0.000 description 8
- 239000011162 core material Substances 0.000 description 7
- 238000005336 cracking Methods 0.000 description 7
- 239000011248 coating agent Substances 0.000 description 6
- 238000000576 coating method Methods 0.000 description 6
- 238000005452 bending Methods 0.000 description 5
- 238000002844 melting Methods 0.000 description 5
- 230000008018 melting Effects 0.000 description 5
- 238000005554 pickling Methods 0.000 description 5
- 238000001953 recrystallisation Methods 0.000 description 5
- 230000009467 reduction Effects 0.000 description 5
- 238000001816 cooling Methods 0.000 description 4
- 230000006866 deterioration Effects 0.000 description 4
- 238000005516 engineering process Methods 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 230000008859 change Effects 0.000 description 3
- 238000009826 distribution Methods 0.000 description 3
- 150000001247 metal acetylides Chemical class 0.000 description 3
- 229910052759 nickel Inorganic materials 0.000 description 3
- 150000004767 nitrides Chemical class 0.000 description 3
- 150000003568 thioethers Chemical class 0.000 description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 3
- 229910000859 α-Fe Inorganic materials 0.000 description 3
- 239000008280 blood Substances 0.000 description 2
- 210000004369 blood Anatomy 0.000 description 2
- 238000005266 casting Methods 0.000 description 2
- 239000010960 cold rolled steel Substances 0.000 description 2
- 230000002301 combined effect Effects 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 238000013461 design Methods 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 238000011156 evaluation Methods 0.000 description 2
- 239000003337 fertilizer Substances 0.000 description 2
- 230000002401 inhibitory effect Effects 0.000 description 2
- 238000011835 investigation Methods 0.000 description 2
- 238000003475 lamination Methods 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 238000012552 review Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 239000002436 steel type Substances 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 230000001360 synchronised effect Effects 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- 206010012335 Dependence Diseases 0.000 description 1
- 241000270666 Testudines Species 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 230000003679 aging effect Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 238000004364 calculation method Methods 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 230000002508 compound effect Effects 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 238000007599 discharging Methods 0.000 description 1
- 235000013399 edible fruits Nutrition 0.000 description 1
- 238000007710 freezing Methods 0.000 description 1
- 230000008014 freezing Effects 0.000 description 1
- 230000035876 healing Effects 0.000 description 1
- 238000010191 image analysis Methods 0.000 description 1
- 229910052738 indium Inorganic materials 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- VAKIVKMUBMZANL-UHFFFAOYSA-N iron phosphide Chemical compound P.[Fe].[Fe].[Fe] VAKIVKMUBMZANL-UHFFFAOYSA-N 0.000 description 1
- 230000001788 irregular Effects 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 239000000696 magnetic material Substances 0.000 description 1
- 230000029052 metamorphosis Effects 0.000 description 1
- 238000005121 nitriding Methods 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
- 230000001590 oxidative effect Effects 0.000 description 1
- 230000002265 prevention Effects 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 230000001568 sexual effect Effects 0.000 description 1
- 239000007779 soft material Substances 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
- 230000008719 thickening Effects 0.000 description 1
- 229910052718 tin Inorganic materials 0.000 description 1
- 229940098465 tincture Drugs 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
-
- 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
- C22C38/06—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
- H01F1/147—Alloys characterised by their composition
-
- 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
- H01F1/14708—Fe-Ni based alloys
- H01F1/14716—Fe-Ni based alloys in the form of sheets
-
- 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
-
- 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
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Electromagnetism (AREA)
- Dispersion Chemistry (AREA)
- Power Engineering (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Soft Magnetic Materials (AREA)
- Manufacturing Of Steel Electrode Plates (AREA)
Abstract
Description
555863 Α7 Β7 五、發明説明(j) 〔技術領域〕 (請先閲讀背面之注意事項再填寫本頁) 本發明有關於使用於電氣機器之鐵芯材料之無方向性 電磁鋼板。其中特別是做爲被兼並要求高級之沖切尺寸精 度以及局fe通抬度之,電抗馬達,或進一步被要求其強度 之埋入磁鐵型之D C無電刷馬達之鐵芯材料之無方向性電 磁鋼板及其製造方法。 (背景技術) 按無方向性電磁鋼板乃,主要使用於馬達或變壓器等 之電氣機器之鐵芯材料之軟磁性材料。爲了圖這些電子機 器之效率之改善’或小型化起見,該電磁鋼乃被要求鐵損 低,而磁通密度高。 在於電動馬達之領域中也正進行該鐵芯材料之電磁鋼 板之磁性特性之改善,換言之進行低鐵損,高磁通密度化 之要求及改善,又,馬達本身也急速地從以往之非同步型 之A C感應馬達而置換爲更高效率之同步馬達,或高特性 化。 經濟部智慧財產局員工消費合作社印製 按同步馬達乃通常可分類爲:表面磁鐵型(S PM) 及埋入磁鐵型(I P Μ )之P C無電刷馬達,及利用轉子 與定子之磁性的凸極性所發生之電抗扭力之電抗馬達,其 中電抗馬達乃,其扭力之發生量乃依存於轉子及定子之形 狀’及轉子/定子間之間隙以及材料(胚材)之磁通密度 。所以做爲電抗馬達用之鐵芯材料時,與其他之馬達相比 較時更加被要求其高磁通密度,且在於沖切(沖裁)時之 本紙張尺度適用中國國家標準(CNS ) Α4規格(210Χ297公釐) -4- 555863 A7 B7 五、發明説明(2) 高精度之尺寸精度係屬重要事項。 (請先閲讀背面之注意事項再填寫本頁) 再者,隨著變頻機化之發展,爲了改善馬達效率或扭 力等起見,具有高速旋轉化之同時,極數有增加之趨向。 而這些都是須提高動作頻率之要素,因此對於馬達材料之 無方向性電磁鋼板亦不只是被要求以往所求之商用頻率( 5 0〜6 Ο Η z )時之磁性特性上之改善,在於4 〇 〇 Η ζ以上之高頻率域之磁性特性之改善也成爲必要。 現在爲止對於上述之無方向性電磁鋼板之磁通密度以 及鐵損之改善上,已做了種種之努力。 爲了減低無方向性電磁鋼板之鐵損,一般乃採取提高 其S i包含量之手法。例如最高級品級之無方向性電磁鋼 板乃,有時添加約3 . 5 m a s s %程度之S i 。惟隨著 S i含量之增加,雖然鐵損會減低,惟磁通密度會同時的 降低。 另一方面,在於低級品級之無方向性電磁鋼板時,由 於有抑制S i含量,因此可以獲得比較高的磁通密度,惟 具有鐵損高之問題。 經濟部智慧財產局員工消費合作杜印製 做爲此種低S i鋼之鐵損之改善方法,在於日本專利 公報特開昭6 2 — 2 6 7 4 2 1號揭示,在於使S i量爲 〇· 6mass%以下,A1量爲〇 . 15〜0 · 60 m a s s %之無方向性電磁鋼板中,限定了 c,S,N以 及〇等之雜物(不純物)之量,以求成爲阻礙結晶粒成長 之要因之介在物之減低以及無害化,以資促進粒成長達成 低鐵損化之技術。惟這種低S i鋼之粒子成長上會隨伴強 本紙張尺度適用中國國家標準(CNS ) A4規格(210X297公釐) -5- 555863 A7 B7 五、發明説明(3 ) 度之降低,因此在於沖切加工時會發生沖切面之不整或回 彈變大,有顯著的降低沖切性之降低之問題。 (請先閱讀背面之注意事項再填寫本頁} 關於調整低S i鋼之硬度而改善沖切性之方法有,添 加: 〇 · 〇 8〜0 _ 1 m a s s %程度之p之技術,例如 曰本專利公報,特開昭5 6 - 1 3 0 4 2 5號,即揭示添 加未滿0 . 2 m a s s %之P,以資改善沖切性之技術。 又關於對於低S i鋼積極的添加P之技術,於日本專利公 報揭示,將S i量抑制於0 . 1 m a s s :%以下,且以 〇 . 1〜1 · Oma s s%之範圍地含有A 1之A 1添加 鋼中,添加Ο · 1〜0 · 25mass%之P,藉由A1 與P之複合效果以資改善磁性特性之方法。 惟在於這些技術中,藉由添加P之沖切性之改善乃只 著眼於,由其硬度調整而抑制鋼板之不整爲目的,對於沖 切後之尺寸精度方面並沒有任何考量。 經濟部智慧財產局員工消費合作社印製 另一方面,在於埋入磁鐵型之D C馬達上,由高扭力 化,及小型化之觀點而被要求其沖切精度及高磁通密度化 ,再有,爲了能耐受馬達之高速旋轉或防止所埋入之磁鐵 之脫離,須要將電磁鋼板之強度維持於高値。如前面所述 ,從強度之觀點高級S i鋼乃有利,惟從磁通密度之觀點 乃以低S i化爲理想,以往很難做到強度及磁通密度之兩 立。 (發明之揭示) 本紙張尺度適用中國國家標準(CNS ) A4規格(210X297公釐) -6- 555863 A7 ____ B7 五、發明説明(4 ) (本發明欲解決之課題) (請先閲讀背面之注意事項再填寫本頁) 如上面所述,在於無方向性電磁鋼板之高磁通密度及 低鐵損特性乃,在於各種馬達,變壓器等之無方向性電磁 鋼板之全部之用途上被要求之共同之特性,惟其中做爲電 抗馬達用無方向性電磁鋼板材料而言,於其動作原理上該 特別高之磁通密度以及高的尺寸精度乃更顯其重要性。 惟至今仍然未尋出,具有高磁通密度,且低鐵損之優 異之磁性特性,並且兼備有優異之沖切性,特別是在於沖 切時之優異之尺寸精度之無方向性電磁鋼板。再者在於這 些特性上更加上於埋入磁鐵型之D C無電刷馬達等被要求 之強度,可以滿足上述之各要求之無方向性電磁鋼板亦仍 未尋出。 再者,在於上述之磁氣特性及沖切性之外,考量了兼 備可對處於近年來之馬達高速旋轉化及多極化之高頻率化 之點之無方向性電磁鋼板乃仍然在於尋求之中。 經濟部智慧財產局g(工消費合作社印製 本發明乃鑑於上述之現狀所開發,提案一種對於馬達 或變壓器等之鐵芯材料,特別是做爲如電抗馬達等被要求 具備特別高之磁通密度及高的尺寸精度之鐵芯材料而最合 宜之具有未曾有之優異之高磁通密度一低鐵損之磁性平衡 ,並且具有優異之沖切尺寸精度之無方向性電磁鋼板,以 及與沖切尺寸精度一齊兼備在於高磁通密度及轉子之高速 旋轉及防止埋入磁鐵之飛散之觀點而很重要之高強度特性 之電磁鋼板,以及其有剩之製造方法爲目的。 再者,爲了方便起見,此後,以S i與A 1之和爲約 本紙張尺度適用中國國家標準(CNS ) A4規格(210X297公釐) 555863 Α7 Β7 五、發明説明(5 ) 〇 · 〇3ma s s%以上,〇· 5ma s s%以下者稱爲 低Si鋼’ Si與A1之和之超過〇 · 5inass%以上 者稱謂中〜高S i鋼。 (解決課題之手段) 於是本發明人等爲了達成上述目的處心積慮硏究之結 果尋出:令S i或A 1量減低爲低S i鋼水平,使之成爲 本質上飽和磁通密度高之鋼,並且將平均結晶粒徑調整爲 規定之範圍,同時添加適正量之P,由而不但可獲得高磁 通密度,且低鐵損之優異之磁氣特性,而且沖切尺寸精度 能可以顯著的提高之知識及見解。 又同時獲得了,以S i與A 1控制於共計〇 · 0 5 m a s s %以上〜約2 . 5 m a s s %之範圍,加工添加 適宜量之P,由了達成沖切尺寸精度之提高之效果,加上 維持磁通密度之情況之下可以大幅度地提高強度,可以達 到以往未曾有之磁性-強度平衡之知識及見解也。 詳述之本發明之要旨構成如下: 經濟部智慧財產局員工消費合作社印製 1 . 一種具有優異之磁氣特性及沖切精度之無方向性 電磁鋼板,其特徵爲: 具有:以質量百分率換算時,由包含: C : 〇 〜〇 _ 0 1 〇 % ; S i與A 1的其中至少一種(s i及/或A 1 )合計 0 . 03%以上,0 . 5%以下; Μ η : 〇 . 5 % 以下; 本紙張尺度適用中國國家標準(CNS ) Α4規格(210Χ297公釐) -8 - 555863 A7 _ B7 五、發明説明(6 ) P : 0 .10%以上,0 . 26%以下; S : 0 . 0 1 5 % 以下; (請先閲讀背面之注意事項再填寫本頁) N : 0 _ 〇 1 〇 % 以下; 其餘爲F e以及不可避免的雜質(不純物)所構成的 組成份,且平均結晶粒徑爲3 0 μ m以上,8 0 μ m以 下。 2 ·在於上述1項之無方向性電磁鋼板,其中該鋼板 又含:Sb與Sn的其中至少一種(Sb及/或Sn), .其含量以質量百分率換算時,合計0 . 4 0 %以下。 3 ·如上述1或2之具有優異之磁氣特性及沖切精度 之無方向性電磁鋼板,其中該鋼板又含:N i ,其含量以 質量百分率換算時,係2.3%以下。 4 .在於上述1 ,2或3所述之具有優異之磁氣特性 及沖切精度之無方向性電磁鋼板,其中鋼板之板厚乃 〇· 3 5mm以下爲其特徵者。 5 · —種具有優異之磁氣特性及沖切精度之無方向性 電磁鋼板,其特徵爲: 經濟部智慧財產局員工消費合作社印製 具有:以質量百分率換算時,由包含: c:0 〜0.010%;555863 Α7 Β7 V. Description of the Invention (j) [Technical Field] (Please read the precautions on the back before filling out this page) The present invention relates to non-oriented electromagnetic steel sheets used as core materials for electrical equipment. Among them, the non-directionality of the iron core material of the DC brushless motor, which is embedded in a magnet-type DC motor, which is required to have high-level punching dimensional accuracy and local lift, is required. Electromagnetic steel plate and manufacturing method thereof. (Background Art) A non-oriented electromagnetic steel sheet is a soft magnetic material mainly used as a core material for electric machines such as motors and transformers. In order to improve efficiency or miniaturization of these electronic machines, the electromagnetic steel is required to have low iron loss and high magnetic flux density. In the field of electric motors, the magnetic characteristics of the electromagnetic steel sheet of the core material are also being improved. In other words, the requirements and improvements of low iron loss and high magnetic flux density are being improved. In addition, the motor itself has been rapidly out of sync with the past. Type AC induction motor is replaced with a more efficient synchronous motor, or with high characteristics. Printed by the Consumer Cooperatives of the Intellectual Property Bureau of the Ministry of Economic Affairs, the synchronous motors are usually classified into: surface-magnet type (S PM) and embedded magnet-type (IP Μ) brushless PC motors; Reactance motor with reactance torsion generated by polarity. The reactance motor is based on the shape of the rotor and stator, the gap between the rotor and stator, and the magnetic flux density of the material (green material). Therefore, when used as a core material for a reactance motor, it is required to have a higher magnetic flux density when compared with other motors, and the paper size when punching (blanking) applies the Chinese National Standard (CNS) Α4 specification (210 × 297 mm) -4- 555863 A7 B7 V. Description of the invention (2) High-precision dimensional accuracy is an important matter. (Please read the precautions on the back before filling in this page.) Furthermore, with the development of inverters, in order to improve the efficiency and torque of motors, the number of poles tends to increase at the same time as high-speed rotation. These are the factors that must increase the operating frequency. Therefore, the non-directional electromagnetic steel sheet for motor materials is not only required to improve the magnetic characteristics at the commercial frequency (50 ~ 6 0 Η z) required in the past. It is also necessary to improve the magnetic characteristics in the high frequency range above 40,000. Various efforts have been made so far to improve the magnetic flux density and iron loss of the aforementioned non-oriented electromagnetic steel sheet. In order to reduce the iron loss of non-oriented electrical steel sheets, a method of increasing the S i content is generally adopted. For example, the highest-grade non-oriented electromagnetic steel sheet is sometimes added with Si of about 3.5 m a s s%. However, as the Si content increases, although the iron loss will decrease, the magnetic flux density will decrease at the same time. On the other hand, when a non-oriented electrical steel sheet of a low grade is used, since the S i content is suppressed, a relatively high magnetic flux density can be obtained, but there is a problem of high iron loss. The consumption cooperation of employees of the Intellectual Property Bureau of the Ministry of Economic Affairs as a method to improve the iron loss of such low S i steel is disclosed in Japanese Patent Gazette No. 6 2-2 6 7 4 2 1, which is to make the amount of S i In non-oriented electrical steel sheets with an A1 content of 0.15 to 0. 60 mass%, the amount of impurities (impurities) such as c, S, N, and 〇 is limited so as to be an obstacle. The reason for the growth of crystal grains is the reduction of the intervening substances and the harmlessness, and the technology to promote the growth of grains and achieve low iron loss. However, the particle growth of this low Si steel will be accompanied by strong growth. The paper size applies the Chinese National Standard (CNS) A4 specification (210X297 mm) -5- 555863 A7 B7 5. The description of the invention (3) is reduced, so The problem is that the punching surface is uneven or the springback becomes large during punching processing, and there is a problem that the punching property is significantly reduced. (Please read the precautions on the back before filling in this page.) Regarding the method of adjusting the hardness of low Si steel to improve the punchability, there are: 〇 · 〇8 ~ 0 _ 1 mass% of p technology, such as In this patent publication, Japanese Patent Application Laid-Open No. 5 6-13 0 4 2 5 discloses a technique for adding P less than 0.2 mass% in order to improve the punchability. It also refers to the active addition of low Si steel. The technology of P is disclosed in the Japanese Patent Gazette. The amount of S i is suppressed to 0.1 mass:% or less, and A 1 is added to the steel containing A 1 in a range of 0.1 to 1 · Oma ss%, and 0 is added. · 1 ~ 0 · 25mass% of P, a method to improve the magnetic properties by the combined effect of A1 and P. However, in these technologies, the improvement of the punching property by adding P is only focused on the hardness For the purpose of adjusting and suppressing the irregularity of the steel plate, there is no consideration for the dimensional accuracy after punching. Printed by the Consumer Cooperatives of the Intellectual Property Bureau of the Ministry of Economic Affairs. , And the view of miniaturization is required for its cutting precision and high magnetic flux density In addition, in order to withstand the high-speed rotation of the motor or prevent the embedded magnet from detaching, it is necessary to maintain the strength of the electromagnetic steel plate at a high level. As mentioned above, from the viewpoint of strength, high-grade Si steel is advantageous. However, from the viewpoint of magnetic flux density, it is ideal to have a low Si, and it has been difficult to achieve a balance between strength and magnetic flux density in the past. (Disclosure of the invention) This paper size applies the Chinese National Standard (CNS) A4 specification (210X297) (%) -6- 555863 A7 ____ B7 V. Description of the invention (4) (Questions to be solved by the present invention) (Please read the precautions on the back before filling this page) As mentioned above, it is the height of non-oriented electromagnetic steel plate The magnetic flux density and low iron loss characteristics are common characteristics required for all uses of non-directional electromagnetic steel plates for various motors, transformers, etc., but among them are non-directional electromagnetic steel plate materials for reactive motors. The particularly high magnetic flux density and high dimensional accuracy are even more important in terms of its operation principle. However, it has not been found so far. It has excellent magnetic characteristics with high magnetic flux density and low iron loss. It also has excellent die-cutting properties, especially non-directional electromagnetic steel sheets with excellent dimensional accuracy at the time of die-cutting. In addition, these characteristics are even better than required strengths such as embedded DC brushless motors. The non-oriented electromagnetic steel sheet that can meet the above requirements has not yet been found. Furthermore, in addition to the above-mentioned magnetic characteristics and punching properties, consideration is given to both high-speed rotation and multi-polarization of motors in recent years. The high frequency of non-directional electromagnetic steel sheet is still in the pursuit. The Ministry of Economic Affairs, Intellectual Property Bureau, (printed by the Industrial and Consumer Cooperatives) The present invention was developed in view of the above situation, and proposes an iron for motors or transformers. The core material, especially as an iron core material that is required to have a particularly high magnetic flux density and high dimensional accuracy, such as a reactance motor, is the most suitable magnetic balance with unprecedented high magnetic flux density and low iron loss. And non-oriented electromagnetic steel sheet with excellent punching dimensional accuracy, and high precision magnetic flux density and high rotor The high-strength electromagnetic steel sheet, which is important from the viewpoints of fast rotation and prevention of scattering of the embedded magnet, and the remaining manufacturing method are aimed at. Furthermore, for the sake of convenience, hereafter, the sum of Si and A 1 is used as the paper standard to apply the Chinese National Standard (CNS) A4 specification (210X297 mm) 555863 Α7 B7 5. Description of the invention (5) 〇 · 〇 3ma ss% or more, 0.5ma ss% or less is referred to as low Si steel; the sum of Si and A1 exceeds 0.5inass% or more is referred to as medium to high Si steel. (Means to Solve the Problem) Therefore, the inventors have deliberately researched in order to achieve the above purpose, and found that the amount of S i or A 1 is reduced to a low S i steel level, and the steel is essentially a steel with a high saturation magnetic flux density. , And adjust the average crystal grain size to a specified range, while adding a proper amount of P, not only can obtain high magnetic flux density, and excellent magnetic characteristics of low iron loss, and punching dimensional accuracy can be significant Improved knowledge and insights. At the same time, it was obtained that S i and A 1 were controlled to a total of 0.05 mass% to about 2.5 mass%, and an appropriate amount of P was added to the process to achieve the effect of improving the dimensional accuracy of punching. In addition, under the condition of maintaining the magnetic flux density, the strength can be greatly increased, and the knowledge and insights of the magnetic-intensity balance that have never been achieved before can be achieved. The gist of the present invention is described in detail as follows: Printed by the Consumer Cooperative of the Intellectual Property Bureau of the Ministry of Economic Affairs 1. A non-directional electromagnetic steel sheet with excellent magnetic properties and punching accuracy, characterized by: In this case, C: 〇 ~ 〇_ 0 1 %; At least one of Si and A 1 (si and / or A 1) in total is 0.03% or more, 0.5% or less; M η: 〇 Less than 5%; This paper size applies the Chinese National Standard (CNS) A4 specification (210 × 297mm) -8-555863 A7 _ B7 V. Description of the invention (6) P: 0.10% or more, 0.26% or less; S: 0. 0 15% or less; (Please read the precautions on the back before filling in this page) N: 0 _ 〇1 〇% or less; the rest is composed of Fe and unavoidable impurities (impurities) And the average crystal grain size is 30 μm or more and 80 μm or less. 2 · The non-oriented electrical steel sheet according to the above item 1, wherein the steel sheet further contains at least one of Sb and Sn (Sb and / or Sn). When the content is converted by mass percentage, the total is 0.4% or less . 3. The non-oriented electromagnetic steel sheet having excellent magnetic characteristics and punching accuracy as described in 1 or 2 above, wherein the steel sheet further contains: Ni, and its content is 2.3% or less when converted by mass percentage. 4. The non-oriented electromagnetic steel sheet having excellent magnetic characteristics and punching accuracy as described in the above 1, 2, or 3, wherein the thickness of the steel sheet is 0.35 mm or less as its characteristic. 5 · —A non-directional electromagnetic steel sheet with excellent magnetic properties and punching accuracy, characterized by: Printed by the Consumer Cooperatives of the Intellectual Property Bureau of the Ministry of Economic Affairs: When converted by mass percentage, it includes: c: 0 ~ 0.010%;
Si與A1的其中至少一種(Si及/或A1),合 計0 . 5 %以上,2 . 5 %以下; Μ η : 〇 · 5 % 以下; Ρ:0. 10%以上,0.26%以下; S:〇.〇15%以下;及 本紙張尺度適用中國國家標準(CNS ) A4規格(210X297公釐) -9 - 555863 Α7 Β7 五、發明説明(7 ) N : 0 · 0 1 0 %以下;以及 因應需要而包含Ni :2.3%以下; 其餘爲F e以及不可避免的雜質所構成的組成份,且 至少符合;?$?4以及1^$〇.2 6的其中一種關係式 ,而At least one of Si and A1 (Si and / or A1), a total of 0.5% or more and 2.5% or less; M η: 0.5% or less; P: 0.1% or more and 0.26% or less; S : 〇15% or less; and this paper size applies Chinese National Standard (CNS) A4 specification (210X297mm) -9-555863 Α7 Β7 5. Description of the invention (7) N: 0 · 0 1 0% or less; and Contains Ni as required: 2.3% or less; the rest are composed of Fe and unavoidable impurities, and at least meet them; $? 4 and 1 ^ $ 〇.2 6 is one of the relations, and
Pa = -0 . 2Si+〇 . 12Mn-〇 . 32A1 + 〇.〇5Ni2+〇.l〇Ni+〇.36 ”·(1)Pa = -0.2 Si + 〇. 12Mn-〇. 32A1 + 〇.〇5Ni2 + 〇.10Ni + 〇.36 "· (1)
Pf = — Ο · 34Si+〇 . 2〇Μπ~〇 . 54A1 + 〇.24Ni2+〇.28Ni+〇.76 ”·(2) 此處的各元素含量的單位是質量百分率。 6 .在於上述5之具有優異之強度、磁氣特性以及沖 切精度之無方向性電磁鋼板,其中該鋼板又含:S b與 S η的其中至少一種,其含量以質量百分率換算時,合計 〇 . 4 0 %以下爲其特徵者。 再者,在於上述之鋼種中做爲副次的含有元素而至少 又包含下列元素的其中一種,該元素以質量百分率換算時 ,係 C a : Ο · Ο 1 % 以下; Β:0·005%以下; C r : 0 . 1 % 以下; C u : Ο · 1 % 以下; Μ 〇 : Ο · 1 % 以下; 7 . —種具有優異之磁氣特性及沖切精度之無方向性 電磁鋼板之製造方法,其特徵爲: 本紙張尺度適用中國國家標準(CNS ) Α4規格(210Χ297公釐) 物 I ------------ (請先閲讀背面之注意事項再填寫本頁) 、11 經濟部智慈財產局8工消費合作社印製 -10- 555863 A7 ________B7 五、發明説明(8 ) 針對於上述之1至3之其中任一所述的組成份的薄板 用鋼片(鋼扁塊), (請先閱讀背面之注意事項再填寫本頁) 在於加熱温度fii於沃斯田鐵的單相領域內且鋼帶捲的 捲取溫度低於6 5 0。(:以下的條件之下進行熱軋處理,接 下來,貫施脫鏽皮處理之後,進行丨次或包括中間退火處 理在內的2次以上的冷軋處理,然後,在於超過7 〇 〇 t 以上的肥粒鐵的單相領域內,進行最終精製退火處理。 8 . —種具有優異之磁氣特性及沖切精度之無方向性 電磁鋼板之製造方法,其特徵爲: 針對於如上述1至4之其中任一所述的組成份的薄板 用鋼片(鋼扁塊), 在於加熱溫度位於沃斯田鐵的單相領域內且鋼帶捲的 捲取溫度低於6 5 0 °C以下的條件之下進行熱軋處理之後 如果是未添加N i或者是N i的含量低於1 . 〇質量 經濟部智慧財產局g(工消費合作社印製 百分率的情況,就在於9 0 0 t以上的肥粒鐵的單相領域 內,或者是在於A c 3點以上的沃斯田鐵的單相領域內進 行熱軋鋼板退火處理; 如果是N i的含量超過1 · 〇質量百分率,且低於 2 · 3質量百分率的情況,就在於A c 3點以上的沃斯田 鐵的單相領域內進行熱軋鋼板退火處理; 接下來,實施脫鏽皮處理之後,進行1次或包括中間 退火處理在內的2次以上的冷軋處理,然後,在於超過 7 0 0 °C以上的肥粒鐵的單相領域內,進行最終精製退火 本紙張尺度適用中.國國家標準(CNS ) A4規格(210X297公釐) -11 - 555863 A7 ___ B7 五、發明説明(9 ) 處理。 . (請先閲讀背面之注意事項再填寫本頁) 9 . 一種具有優異之強度,磁氣特性以及沖切精度之 無方向性電磁鋼板之製造方法,其特徵爲: 針對於如上述5〜6之其中任一項所述的組成份的薄 板用鋼片(鋼肩塊) 在於加熱溫度位於1 0 〇 〇〜1 2 0 〇 °C且鋼帶捲的 捲取溫度低於6 5 0 °C以下的條件之下進行熱軋處理之後 因應需要來實施熱軋鋼板退火處理; 接下來,實施脫鏽皮處理之後,進行1次或包括中間 退火處理在內的2次以上的冷軋處理,然後,進行最終精 製退火處理。 再者,在於上述9之電磁鋼板之製造方法中,在於熱 軋後施予熱軋板退火處理亦可以。 再者,在於上述7,8或9之任何一之電磁鋼板之製 法中,在施予最終精製退火處理之後施予賦予絕緣被膜之 處理亦可以。 經濟部智慧財產局員工消費合作社印製 (實施發明之最佳形態) 下面說明引至本發明之實驗結果。 又下面所示之成份組成之%表示均爲^ma s s%」 (質量百分率換算)。 〔實驗1〕 本紙張尺度適用中國國家標準(CNS ) A4規格(210X297公釐) -12- 555863 A7 _B7 五、發明説明(1〇) 首先爲了解明無方向性電磁鋼板之鋼成份與沖切尺寸 精度之關係,分別於實驗室的熔製.:C : 〇 . 〇 〇 1 6〜 (請先閲讀背面之注意事項再填寫本頁) 0.0028%,Μη:0·20 〜0.22%, Α1 : 0 · 0007 〜0· 0014%、 Ν:〇.〇〇12〜0.0022%以及Sb:〇.03 %地大致一定之成份爲基本組成,而P量爲0 . 0 2%之 一定値,S i量爲0 · 03〜1· 49%之範圍地使之變 化之鋼。以及S i量爲0·. 1 0〜〇 · 1 1%之一定,而 P含有量爲0 · 0 2〜0 · 2 9 %之範圍地使之變化之鋼 〇 經濟部智慈財產局Μ工消費合作杜印製 接著,將這些鋼材以1 1 0 0 °c加熱6 0 m i η之後 ,熱軋至板厚:2 m m,以 6 0 0 °C、實施相當於2 h j:之鋼帶捲捲取之均熱保持之後予以放冷。接著於 9 0 0 °C、6 0 S之熱軋板退火後,施予酰洗、冷軋到板 厚0 . 5mm,於700〜900 °C之各種溫度實施最終 精製退火處理,而將再結晶粒之粒徑變化爲各種,而後’ 對於此最終精製退火板噴塗平均膜厚:〇 . 6 μ m之半有 機絕緣被膜,製作了烤塗之樣品供沖切試驗。 又,平均結晶粒徑乃觀察平行於輥軋方向之板厚方向 斷面而採用以Jeffries法所求之圓相當徑。 沖切試驗乃使用直徑:2 1 m m 0之圓形沖模行之, 間隙即定爲板厚之8 %,測定與輥軋方向所成之角度爲 〇。 ,45。 ,90° , 135°之四方向之沖切出圓形 之直徑(內徑)而求出該4點之平均徑’同時測定4點中 本紙張尺度適用中國國家標準(CNS)A4規格(210x297公釐 1 " -13- 555863 A7 B7 五、發明説明(Ή) 之最大徑與最小徑之差,做爲沖切之方向異性之指標。 (請先閲讀背面之注意事項再填寫本頁) 由切出於輥軋方向之拉力試驗片(J I s 5號)所求 之降伏強度(Υ Ρ )之關係來整理所獲得之結果顯示於第 1圖及第2圖。 由第1圖,第2圖可知,全盤的來說,ΥΡ低之軟質 材料乃對於沖製模徑而言,沖切徑之差異大,隨著Υ Ρ之 上昇沖切徑愈靠近沖製模徑,而尺寸精度有改善之趨向, 這是由於如以往眾所周知,由強度之上昇而有抑制沖切時 之形狀不整之變形之效果。 惟在此實驗中値得注意之一點乃,該添加Ρ而實施強 度調整之試料乃與先前型之隨著S i量之變化而使強度變 化之電磁鋼板做比較時,在於同程度之強度水平中顯現優 異之尺寸精度,並且,在於比較的低之Y P域就能抑制與 沖製模之尺寸之差異(第1圖)。 經濟部智慧財產局員工消費合作社印製 再者,改變了 S i量之鋼乃隨著強度之上昇而沖切徑 係靠近於沖製模之尺寸,惟如第2圖所示,該以最大徑與 最小差之差所代表之方向異性仍然很大,而相對的由P量 增加而求其強度之上昇之鋼即連該沖切形狀之各方向異性 也有被改善。 將這些之關係與用最終精製退火板之平均結晶粒徑之 關係所整理而成者就是第3圖,第4圖。 由第3圖、第4圖而可以看出,使S i量變化之鋼乃 會在粒徑變大時沖切尺寸精度及沖切各方向異性也劣化, 而相對的增加Ρ 0 · 1 3 %以上之鋼時即結晶粒徑之大 本紙張尺度適用中國國家標準(CNS ) A4規格(210X297公釐) ' -14 - 555863 A7 B7 __ 五、發明説明(12) 者也是,沖切精度及沖切各方向異性均具有優異之水平。 (請先閲讀背面之注意事項再填寫本頁) 關於使P含有一定量而可以使沖切尺寸精度或沖切各 方向異性之有效果的改善之理由雖然其詳細理由仍須探究 ,惟可能使由於:(1 )由添加P而使強度上昇,可以緩 和沖切時之形狀不整之變形之效果之外。 (2 )藉適宜量的添加被認爲對於鋼而言屬於脆化元 素之P,由而會提早沖切(沖製)時之破斷限界之效果, 及 (3 )隨著P之添加而最終精製退火板之集中組織中 之{ 1 00丨<uvw>方位有增加之趨向,而這個乃有 緩和各方向異性之效果,等之複合的作用而成之結果。 接著說明,從磁氣特性之面所檢討之結果。 發明人等,針對於雖然會改善鐵損,惟會使飽和磁通 密度降低之S i或A 1之含量予以極力的限定,以資本質 上的提高了磁通密度之鋼爲胚材,而對於製造條件與磁氣 特性之關係詳細地做了檢討。 經濟部智慧財產局員工消費合作社印製 第5圖表示,關於各鋼材之板厚:〇·5mm之試片 調查了關於最終精製退火板之結晶粒徑與商用頻率域之鐵 損(W15/5 0 :頻率數5 0Hz,最大磁通密度 1 . 5 丁之値)之關係之結果。 由同圖可知,使之低S i就會使電阻減少,因此不利 於鐵損’惟鐵損乃由結晶粒徑而會有很大之變化,因此將 粒徑使之爲約3 0 μ m以上即可知會成爲安定的低鐵損。 再者使低A 1而致使電阻減少時亦查明同樣地使粒徑爲約 本紙張尺度適用中國國家標準(CNS ) M規格(21〇><297公釐) 15- 555863 A7 B7 五、發明説明(13) 3 Ο μ m以上就對於低鐵損化有效。 (請先閲讀背面之注意事項再填寫本頁) 惟到本案申請專利之前,本發明之低S i ,A 1組成 之屬於低級品級之無方向性電磁鋼板時,其最終精製退火 板之平均結晶粒徑乃被限制於1 5〜2 5 μ m程度爲通例 ’該理由乃如第3圖,第4圖之〇 . 1 1%S i〜0 . 7 % P鋼(圖中之記號)之例子所示,使它再粒徑成長時, 即由於強度之降低而會使沖切性顯著的劣化之緣故。 相對於它,提高了 P添加量之鋼時,即使平均結晶粒 徑提高到約3 Ο μ m以上仍然可以維持良好之沖切尺寸精 度。 接著於第6圖表示調查了各鋼種之平均結晶粒徑與磁 通密度之關係,於第7圖表示調查了鐵損與磁通密度之關 係之結果。 按Β5〇乃在於磁化力5 0 0 0 A/m之磁通密度。 添加了 S i之試料乃雖然會改善鐵損,惟磁通密度之 降低很大,相對的添加了 P之試料乃在於結晶粒成長而改 善了鐵損之後,仍然可維持很高之磁通密度。 經濟部智慈財產局員工消費合作社印製 按P乃脆化元素,如本發明一般,P添加量多時,主 要在於冷軋過程中有時會發生耳(earing )龜裂,或層 狀龜裂之現象。 本發明乃針對此現象處心積慮予以檢討調查,結果究 明了,當在於熱軋時之鋼扁塊之加熱時,溫度之成爲肥粒 鐵/沃斯田鐵共存領域時,在於肥粒鐵粒與沃斯田鐵粒間 發生P之分配,在於肥粒鐵粒中發生顯著之P之偏析,由 本紙張尺度適用中國國家標準(CNS ) A4規格(210X297公釐) ' -16- 555863 A7 __ B7 _ _ 五、發明説明(14) 而會促進鋼之脆化之事實。 (請先閲讀背面之注意事項再填寫本頁) 爲了防止此種脆化現象起見,須要在於本發明之鋼板 之製造時,使爲了熱軋用之鋼扁塊之加熱溫度定於沃斯田 鐵單相領域(或可能時定爲肥粒鐵單相)爲重要之條件。 又’ P乃屬於肥粒鐵形成元素,因此有縮小在於鋼扁 塊加熱溫附近之沃斯田鐵單相域之作用,雖在於低s i鋼 之成份範圍時,鋼扁塊(薄板用鋼片)之加熱溫度在於 1 0 0 0〜1 2 0 0 °C時,就可以使之成爲沃斯田鐵單相 者。 如上所述,究明了對於低S i鋼添加約〇 . 1 %以上 之P乃非常有效。於是對於含〇 . 5 %以上之S i之鋼板 也檢討了 P之積極之添加。 〔實驗2〕 將熔製C:〇.〇〇13〜0.0026、 Μη:〇·18 〜0.23%,A1 :0.0001 〜 0.0011%,N:〇.〇〇2 〇〜0.0029% 等 經濟部智慧財產局員工消費合作社印製 做成大致一定之成份,而將s i量爲〇 . 60〜2 . 42 ,以及P量0·04〜0·29%之間種種之鋼,在於 1 1 0 0 t加熱6 0分鐘後,熱軋到板厚2 m m,經酸洗 後冷軋到板厚0 · 5 m m。結果由鋼組成有別,有的在輥 軋後之鋼板內部與板面平行地發生層狀之龜裂,結果顯示 於第8圖。 以Ε Ρ Μ A對於層狀龜裂發生部份予以映像分析之結 本紙張尺度適用中國國家標準(CNS ) A4規格(210X297公釐) -17- 555863 A7 _B7___ 五、發明説明(15> (請先閲讀背面之注意事項再填寫本頁) 果,觀察到了在於龜裂發生部份有p之偏析或濃化之情形 ,於是詳細地硏討此p之偏析條件,究明在於熱軋之鋼扁 塊加熱時,成爲被形成於肥粒鐵與沃斯田鐵相之二個領域 地予以均熱保持之條件P分配於肥粒鐵相中而導致濃化之 事實。 換言之,查明了在於中〜高s i鋼板領域中,由於屬 於肥粒鐵形成元素之s i ,A 1量多,因此沃斯田鐵單相 域更爲縮小,該結果在於以往之加熱溫度時具有容易成爲 肥粒鐵/沃斯田鐵二相域之問題。 又,P超過0 . 2 6 %時,即任何組成條件都發生了 層狀龜裂。 於是藉硏究設備製作出具有各種Si ,Μη,A1 , Ρ量之鋼,調查了在於約1 Ο Ο 0〜1 2 Ο 0 °C之溫度域 而可以將P之偏析抑制於不發生輥軋不良之程度之條件。 再者上述之鋼扁塊加熱溫度乃從存在於鋼中之碳化物、氮 化物、硫化物之析出之安定化之觀點而合宜之。 經濟部智慧財產局員工消費合作社印製 首先,在於鋼扁塊加溫溫度爲可成爲沃斯田鐵單相域 或肥粒鐵單相域之條件下,由於不會發生相分配所致之偏 析,因此只要P添加量之被規定量少時就可以避免層狀龜 裂,由上述實驗可知P之添加量定爲約〇 . 2 6%以下之 必要。 於是首先調查中〜高S i鋼之成爲沃斯田鐵單相之條 件。 該結果查明,在於S i + A 1含有較0 . 5 %以上之 本紙張尺度適用中.國國家標準(CNS ) A4規格(210X297公釐) -18- 555863 A7 B7 五、發明説明(16) 鋼乃,其P添加量乃P $ P A ’,但是 PA,= — 0.2Si+0.12Mn- (請先閱讀背面之注意事項再填寫本頁) 0.32A1+0.36 ···("’ (Si ,Μη,A1 ,P之各含量以mass%表示 之)。 之範圍時即在於沃斯田鐵之單相域。所以滿足上述條件且 限定爲P $約0 . 2 6 %時就可以抑制由P所致之脆化現 象。 接著調查,中〜高S i鋼之成爲肥粒鐵單相之條件, 同樣將P添加量爲P 2 P F ’,但 PF5=-〇 . 34Si+〇 . 20Mn- 0.54A1+0.76 -(2)5 經濟部智慧財產局員工消費合作社印製 (Si ,Μη,A1 ,P之各含量以mass%表示) 之範圍時查明了在於肥粒鐵單相域,所以滿足此條件,且 限定P S約0 . 2 6 %之時亦可以抑制由P導致之脆化現 接著調查,在於沃斯田鐵單相域或肥粒鐵單相域之鋼 扁塊(薄板用鐵片)之加熱困難時之抑制P之偏析之條件 〇 於肥粒鐵/沃斯田鐵二相域發生P之濃度之分配時, 肥粒鐵相中之P濃度也成爲上述p F ’之情形,惟調查之 本紙張尺度適用中.國國家標準(CNS ) A4規格(210X297公釐) -19- 555863 A7 ___B7_ 五、發明説明(17) 結果究明此P F ’也使之爲約〇 · 2 6以下時就可以避免 由P所致之脆化者。 (請先閲讀背面之注意事項再填寫本頁) 整理上述二相領域之脆化避免條件,及在於肥粒鐵單 相域之脆化避免條件時,就可以綜括爲:P S約〇 . 2 6 %aPF’ $ 約 0.26%。 綜括上述關係,避免由P導致脆化之條件乃:P $約 0 · 26%,且 PSPA’或 PF,公約 〇 . 26%。 由上述之結果究明:P添加量爲約0 . 2 6 %以內, 且在於熱軋加熱時,在於沃斯田鐵單相或肥粒鐵單域地予 以加熱之條件時,得避免不發生冷軋後之層狀龜裂之問題 地可以製造。再者,在於成爲肥粒鐵/沃斯田鐵二相加熱 之條件之下,在於對於肥粒鐵相之P分配量之變低之S i ,A 1量之比較高之成份系中仍然可以製造之事實。 再關於,添加了約0 . 1 %以上之P之情形而在於熱 軋時之鋼扁塊加熱溫度域(1 0 0 0 t〜1 2 0 0 °c附近 )而成爲沃斯田鐵或肥粒鐵單相組織之種種之鋼組成予以 檢討。 經濟部智慧財產局員工消費合作社印製 該結果究明,添加了對於改善磁氣特性及確保強度上 合宜之元素之N i之結果,對於添加P之鋼之擴大在於熱 軋溫度附近之沃斯田鐵領域之目的上也很有效之事實。 〔實驗3〕 以 C:0 . 013 〜0· 026%、Μη··0· 18 〜0.28%、A1 :0.0007 〜0.0013%’ 本紙張尺度適用中國國家標準(CNS ) A4規格(210X297公釐1 " ' " -20- 555863 A7 B7_ 五、發明説明(18) N:0.0 014 〜0.0025% 及 Ρ:0·16 〜 (請先閲讀背面之注意事項再填寫本頁) 〇 · 1 8%地大致一定之成份爲基本組成,將S i量爲 〇 · 95〜2 . 44%,Ni量爲0〜2 . 20%地分別 變化之試料以實驗2同樣地輥軋至0 . 5 0 n m,調查所 獲得之冷軋鋼體之層狀龜裂之發生情形。其結果表示於第 9圖。 該無添加N i之情形上呈龜裂之1 . 1〜1 . 5 % S i鋼乃,在經添加N i而不會發生龜裂的可能輥軋。另 一方面在於不添加Ni或輥軋出之1 . 9 5%Si鋼或 2 · 4%S i鋼即在於增加N i而有時也發生龜裂,由而 可知N i之效果乃具有該適正領域之存在之事實。 .又查明:於加味了 N i之影響,而擴張上述之式時, 在於將S i + A 1含有較0 · 5%以上之鋼中,P添加量 爲約0 . 2 6 %以下,且 P S P A,但是 經濟部智慧財產局員工消費合作社印製 PA = — 〇 · 2Si+0 · 12Μη — 0 · 32A1 + 〇.〇5Ni2+〇.l〇Ni+〇.36 -(1) 之範圍時,在於1 0 0 0 °C〜1 2 0 0 °C之鋼扁塊加熱溫 度乃在於沃斯田鐵單相域, P F S 約 0 . 2 6 但 本紙張尺度適用中國國家標準(CNS ) A4規格(210X297公釐) 21 - 555863 A7 ΒΊ___ 五、發明説明( (請先閲讀背面之注意事項再填寫本頁) PF = -〇 . 34Si+0 . 2〇Mn-〇.54Al+〇.24Ni2 + 〇.28Ni+〇.76^P …(2) 之範圍時,即在於二相領域或肥粒鐵單相域之下可以使P 之濃化程度少,而任何一者均可避免由P導致之脆化之事 實。 又上述之二式中Si ,Mn,Al ’P’Ni之各含 量以ma s s%表示。又,PF及PA之技術的意義乃與 上述PF’及PA’相同。 〔實驗4〕 經濟部智慧財產局員工消費合作社印製 對於在實驗2及實驗3輥軋到0 . 5 0 m m之冷軋鋼 板實施最終精製退火之後塗佈平均膜厚0 . 6 μπι之半有 機絕緣被膜,實施了烤塗。對於這些試片實施依實驗1所 述之方法之沖切試驗,調查這些之直徑及各方向異性,其 結果顯示於第1 0圖及第1 1圖。由這些圖可知,在於 S i + Α 1含有〇 · 5%以上之鋼中,亦如使之含有卩^ 0 · 1 0 %之鋼均能顯著優異之沖切尺寸精度。 於是在於N i添加鋼中,使其添加量在〇 . 3 8〜 2 · 2 0 %之間地予以變化。 第1 2圖表示這些試料之磁通密度b5Q與抗張強度 T S之關係。本例中T S乃與實驗1同樣之抗張試驗求之 ,磁通密度亦採實驗1之方法測定之。 本紙張尺度適用中國國家標準(CNS ) A4規格(210X297公釐) -22- 555863 A7 B7 五、發明説明(20) 含有約0 . 1 %以上之P之鋼乃,與以往之中〜高 (請先閲讀背面之注意事項再填寫本頁) s i組成(即S i + A 1 > 〇 · 5 % )之電磁鋼板比較之 下顯現優異之B 5 〇 - T S平衡。特別是隨著P添加量之 增大,T S有增大惟未見磁通密度之降低,反而有提高之 趨勢。這一點乃,關於以往之電磁鋼板,之由於添加S i ,A 1之強磁性體以外之合金元素而實施之鋼板之強化時 會隨伴著磁通密度之降低之事實相比較乃屬於有特徵性。 這些特性乃做爲被要求馬達之高扭力化,小型化,高 速旋轉化等之D C無電刷馬達或電抗馬達等各種旋轉機( 馬達、發電機)之轉子胚材上很合宜之性質。 由上面之知見(知識及見解)而做爲兩立優異之磁通 密度及沖切精度之條件而規定了鋼中之S i ,A 1 ,P, N i量。進一步在低S i鋼時,最終精製退火板之平均結 晶粒徑規定爲下述之範圍。 低S i鋼時,S i ,A 1之一種或二種之合計:約 0 · 0 3 〜0 . 5 %。 經濟部智慧財產局g(工消費合作社印製 S i及A 1乃添加於鋼時具有脫氧效果,因此做爲脫 氧劑而單獨或倂用地供使用。爲了發揮其效果,S i 、 A 1分別以單獨或兩者之合計而須要約0 · 0 3 %以上, 又S i ,A 1乃有增加比電阻之鐵損之改善作用,惟另一 方面也會導致飽和磁通密度之降低,因此將其上限定爲 0.5%。 中〜高S i鋼時,S i ,A 1之一種或二種之合計·· 〇 · 5 %以上〜約2 · 5 %。 本紙張尺度適用中國國家標準(CNS ) A4規格(210X297公釐) -23- 555863 A7 B7 五、發明説明(21) 如果與優異之尺寸精度同時重視機械的強度或低鐵損 時’ s i + A 1之合計量可以含有0 . 5%以上。 (請先閲讀背面之注意事項再填寫本頁) 如前述,在於中〜高S i鋼時,仍然由添加P之效果 而可以獲得與以往之低P之中〜高S i鋼比較之下,具有 高之沖切精度及強度-磁通密度平衡之材料。惟,S i + A 1之合計量超過2 . 5%以上時,依本發明之方仍然會 使通常之冷軋發生困難,因此將其範圍規定爲〇 . 5 %以 上〜約2 . 5 %。 P :約0 · 1 0 %以上,約0 . 2 6 %以下, P乃於本發明中特別重要之元素,P乃如以往眾所周 知具有藉其高的固溶強化能來調整材料硬度之功能,特別 是低S i ,低A 1鋼板乃本來就比較的軟質,而在本發明 中爲了低鐵損化而須要將平均結晶粒徑定爲約3 Ο μ m以 上,所以會使鋼板更軟質化之虞。 P乃在此種本發明之鋼板之改善沖切性,換言之用於 抑制由於鋼板之強度不足所致之沖切形狀之不整或反彈之 增加上必要之元素。 經濟部智慧財產局Μ工消費合作社印製 在此種材料強度增加能,加上藉由提早沖切時之破斷 限界而抑制沖切時之總變形量之效果,以及增加最終精製 退火板之集合組織中之{ 1 0 0丨< u vw>方位以資改 善各方向異性之效果等之複合作用而可以改善沖切尺寸精 度也。 再者,亦具有雖然增加鋼板之強度之下仍然不會使磁 通密度降低之特性,而此效果仍在於中〜高S i鋼也會發 本紙張尺度適用中國國家標準(CNS ) Α4規格(210X297公釐) -24- 555863 A7 B7 五、發明説明(22) 揮。 爲了發揮此效果,P須要使之含有約0 . 1 0 %以上 (請先閲讀背面之注意事項再填寫本頁) 〇 另一方面P乃原來就對於鋼是脆化元素,如果添加的 過剩即會引起耳龜裂或層狀龜裂,會使製造性降低,關於 這一點乃在於製造方法上予以改進,或藉由添加N i而可 以做到以往製造困難之高P添加鋼之製造。惟超過 0 . 2 6%之含量時,採用本發明之製造方法時仍然很難 製造P添加鋼因此將P量限定於約0 . 1 0 %以上〜約 0 · 6 %之範圍。 N i :約2 . 3 %以下(亦可以選擇性而添加) N i乃不單具有改善鋼之集合組織而提高磁通密度之 效果,也倂備有:增加鋼之電阻,降低鐵損之效果,以及 藉由強化固溶以資提高鋼之強度以資抑制沖切加工時之形 狀不整等效果,因此得於積極地予以添加。 再者,N i乃屬於沃斯田鐵形成元素,所以具有擴大 合宜之鋼扁塊(薄板用鋼片)加熱溫度之1 0 0 Ot〜 經濟部智慧財產局員工消費合作社印製 1 2 0 0 °C附近之沃斯田鐵域(狀態圖中之r圈)之效果 。特別是S i + A 1量之多於0 · 5 %之組成之鋼而言, 在增大操業安定性上很有效。 應用此效果時,就可以大幅度的改善如本發明地積極 的添加屬於脆化元素之P時之輥軋之不安定性。換言之高 P鋼之安定的製造之要點乃爲抑制熱軋時之過剩之P,而 做爲其有力之手段乃設法避免鋼扁塊(薄片用鋼片)之加 本紙張尺度適用中國國家標準(CNS ) A4規格(210X297公釐) -25- 555863 A7 B7 五、發明説明(23^ (請先閲讀背面之注意事項再填寫本頁) 熱溫度之成爲肥粒鐵/沃斯田鐵二相域之情形。當S i含 有量與A 1含有量之合計超過〇 . 5 %,即在於鋼扁塊力口 熱溫度而容易分離爲二相。惟由N i之9"域之擴大效果, 而在此種S i ’ A 1組成之下,也可能使之在鋼扁塊加熱 時使之成爲沃斯田鐵單相。 惟,N i含有爲約2 · 3 %以上時,肥粒鐵(r )-> 沃斯田鐵(r )變態開始溫度降低,在於最終精製退火中 會引起沃斯田鐵變態,由而有導致磁通密度之降低之虞。 又在於變態溫度以下之低溫度之最終精製退火溫度下,在 於低S i鋼中很難確保約3 Ο μ m以上之平均粒徑,鐵損 也會劣化。所以N i即定爲含有約2 . 3 %以下也。 再者,添加N i時,添加約〇 . 5 0 %以上爲合宜。 於低S i鋼中,最終精製退火板之平均結晶粒徑:約 3 Ο μ m以上,約8 Ο μ m以下。 經濟部智慧財產局B(工消費合作社印製 在於本發明之低S i ,低A 1無方向性電磁鋼板中, 爲了獲得良好之鐵損特性起見,如第5圖所示,須要將最 終精製退火板之平均結晶粒徑爲約3 Ο μ m以上。惟使之 成爲超過約8 Ο μ m之粒徑時,無法更可以求其改善鐵損 之效果。又,屬於本發明之鋼均爲變態鋼,而其適合於再 結晶退火之肥粒鐵單相域乃大約在於7 0 0 t〜9 0 0 t 之範圍,與高S i組成之肥粒鐵單相鋼比較時即屬於低溫 ,因此使之溫度之粒成長乃在於連續短時間退火設備之生 產性之點而言屬於不利,因此將上限定爲約8 Ο μ m。 又,在於中〜高S i鋼中,乃由於具有藉合金之電阻 本紙張尺度適用中國國家標準(CNS ) A4規格(210 X 297公釐) -26- 555863 A7 ___B7 五、發明説明(24) (請先聞讀背面之注意事項再填寫本頁) 之提高之效果等,因此很容易獲得比較低的鐵損,因此粒 徑乃並不特別的做限定,以通常之範圍就可以。一般而言 ,20〜200 μπι程度者。 接著,發明人等隨著馬達之高速旋轉化及極數之增加 而近年來漸漸地被重視,惟爲了改善在於高頻域之磁氣特 性之手法做檢討,其結果究明:減低板厚爲有效,特別是 在於低S i鋼中,其效果很顯著,下面顯示引導至結果之 實驗。 〔實驗5〕 於第13圖表示調查,〇 . ll%Si— 〇 . 18% P 鋼,及 0 _ 95%Si—〇 . 02% 鋼,及 2 . 0% Si— 〇 · 5%A1鋼之在於4 0 0Hz時之鐵損之板厚 依存性之結果。 經濟部智慧財產局員工消費合作社印製 如同圖可知,任一試料亦由減少板厚而降低渦電流損 ’因而局頻率鐵損有被改善之趨向,並且亦可知由減少板 厚所導致之高頻率鐵損之改善效果乃低S i鋼者較爲大之 情形。 惟,至今爲止,無方向性電磁鋼板之板厚乃以 0 . 5 0 m m爲主流,其以上之板厚之減低乃只適用於比 電阻元素之S i及A 1之含有量高之高級品質之一部份, 在於S i或A 1之含有量少之無方向性電磁鋼板上未見有 所適用之製品例。 再者,第1 4圖表示對於這些胚材調查磁通密度之板 本紙張尺度適用中國國家標準(CNS ) A4規格(210X297公釐) -27- 555863 A7 B7 五、發明説明(25) 厚依存性之結果。 (請先閲讀背面之注意事項再填寫本頁) 如同圖所示,減低板厚時具有使磁通密度稍爲降低之 趨勢’惟該降低値微少,又在任一者之板厚上亦是低S i 鋼者顯著特別高之磁通密度。特別是對於電氣汽車(E V )或複合電氣汽車(HEV)之驅動用馬達之用途上被檢 討有高速旋轉型之電抗馬達,而在該用途上將重視高磁通 密度且在於高頻率下之低鐵損性,而對該問題而言如本發 明所示之低S i ,低A 1之本質上磁通密度高之鋼板乃藉 予以薄板化就可以對處也。 如第1 3圖所示,減低板厚之效果乃使之爲0 . 3 5 m m以下就開始顯著,使之約〇 . 3 0 m m以下就更爲顯 著。 又,板厚乃愈薄其減低渦電流損上很有效,因此不特 別地設下限,惟另一方面增加鐵芯之疊層之工數,而提高 成本,並具有疊層鐵芯之鉚固之困難之弊害,所以供一般 性之生產時,下限爲0 . 1 0 m m程度爲合宜。 經濟部智慧財產局員工消費合作社印製 下面說明在於本發明之鋼之Si ,A1 ,P以及Ni 以外之成份之限定之理由。 C : 〇 〜約 〇 · 〇 1 〇 % C乃由時效效果之作用,在製造鋼板之後,隨著時間 之經過而會使磁氣特性(鐵損)劣化之元素,其程度乃C 含量之超過約0 . 0 1 0 %時會呈顯著,因此c含量爲限 定於0 · 0 1 0 %以下,又關於此時效劣化特性即c量愈 本紙張尺度適用中國國家標準(CNS ) A4規格(210父297公羡1 -28- 555863 A7 B7 五、發明説明(26^ 少愈合宜,所以在本發明乃對於C量而言,也包含實質上 零(未滿分析限界位)之情形。 (請先閲讀背面之注意事項再填寫本頁) Μ η :約0 . 5 %以下 Μη乃以Mn S之方式來固定S,具有抑制起因於 F e s之熱軋中之脆化之效果。又隨著Μη含有量之增加 比電阻會增加而會改善鐵損,惟在另一方Μ η含有量之增 加會導致磁通密度之降低,因此將Μ η含有量之上限定爲 約 0 · 5 % 0 S :約〇.0 1 5 %以下 S乃不可避免之雜物(不純物),如上述地以F e s 地析出時,不但成爲熱軋脆性之原因,如微細地析出時, 就會使粒成長性劣化,因此從減低鐵損之觀點自應盡量減 低爲有利。又按S量超過約〇 · 〇 1 5 %時鐵損之劣化情 形乃顯著地變大,因此將其上限定爲約0 . 〇 1 5 %。惟 在另一方,S乃亦具有改善其沖接時之剪斷形狀之效果, 因此減低到如何之程度乃隨應於用途來決定。 經濟部智慧財產局員工消費合作社印製 N :約Ο . Ο 1 Ο %以下 Ν乃不能避免之混入雜物(不純物)。如成爲A 1 Ν 地微細地析出時,會阻礙粒成長而會使鐵損劣化,因此限 定爲約0 . 0 1 0 %以下。 上面說明了必須成份及抑制成份,惟本發明乃其他有 做爲磁氣特性改善成份而適宜地可以含有下述之元素。 本紙張尺度適用中國國家標準(CNS ) A4規格(210X297公釐) -29- 555863 A7 B7_ 五、發明説明(27)Pf = — 〇 · 34Si + 0.20Mπ ~ .54A1 + 〇.24Ni2 + 〇.28Ni + 〇.76 "(2) Here, the unit of the content of each element is mass percentage. 6. It is excellent in the above 5 The non-oriented electromagnetic steel sheet with high strength, magnetic characteristics, and punching accuracy, wherein the steel sheet further contains: at least one of S b and S η. When the content is converted by mass percentage, the total is 0.4% or less. In addition, the above-mentioned steel types are contained as secondary elements and at least one of the following elements. When the element is converted by mass percentage, it is C a: 〇 · 〇 1% or less; Β: 0 · 005% or less; C r: 0.1% or less; Cu: 〇 · 1% or less; Μ 〇: 〇 · 1% or less; 7.. Non-directionality with excellent magnetic characteristics and punching accuracy The manufacturing method of electromagnetic steel plate is characterized by: This paper size is applicable to Chinese National Standard (CNS) Α4 specification (210 × 297 mm) Material I ------------ (Please read the precautions on the back before (Fill in this page), 11 Printed by the 8th Consumer Cooperative of the Intellectual Property Bureau of the Ministry of Economic Affairs -10- 555863 A7 _ _______B7 V. Description of the invention (8) Regarding the steel sheet (steel flat block) for thin plates with the composition described in any one of 1 to 3 above, (please read the precautions on the back before filling this page). It is heating The temperature fii is in the single-phase area of Vosstian Iron, and the coiling temperature of the steel strip coil is lower than 6 50. (: The hot rolling treatment is performed under the following conditions, and then the descaling treatment is performed continuously.丨 or two or more cold-rolling treatments including intermediate annealing treatments, and then perform final refining annealing treatment in a single-phase area of ferrous iron with more than 7000t or more. A method for manufacturing a non-oriented electromagnetic steel sheet with magnetic characteristics and punching accuracy, which is characterized in that the steel sheet (steel flat block) for a thin plate having a composition as described in any one of the above 1 to 4 is heated The temperature is within the single-phase area of Vosstian Iron and the coiling temperature of the steel strip coil is below 6 50 ° C. After hot rolling treatment, if Ni is not added or the Ni content is lower than 1.0 Intellectual Property Bureau of the Ministry of Quality and Economics In the case of the percentage printed by the company, the hot-rolled steel sheet is annealed in the single-phase area of ferrous iron above 900 t, or in the single-phase area of Vostian Iron above A c 3; In the case where the content of Ni is more than 1.0% by mass and less than 2.3% by mass, the hot-rolled steel sheet is annealed in the single-phase area of Vostian Iron, which is above A c 3; After descaling, cold rolling is performed once or twice or more, including intermediate annealing, and then the final refined annealing is performed in a single-phase region of ferrous iron having a temperature of more than 700 ° C. The size of this paper is applicable. China National Standard (CNS) A4 specification (210X297 mm) -11-555863 A7 ___ B7 V. Description of invention (9) Disposal. (Please read the precautions on the back before filling out this page) 9. A method for manufacturing non-oriented electromagnetic steel sheet with excellent strength, magnetic properties and punching accuracy, characterized by: 5 ~ 6 as above The steel sheet for steel sheet (steel shoulder block) according to any one of the above-mentioned components has a heating temperature of 100 to 120 ° C, and a coiling temperature of the steel strip coil is lower than 6 50 ° C. After the hot rolling treatment is performed under the following conditions, the hot-rolled steel sheet is annealed if necessary. Next, after the descaling treatment is performed, the cold rolling treatment is performed once or twice or more, including the intermediate annealing treatment. For the final refining annealing. Furthermore, in the method for manufacturing an electromagnetic steel sheet according to the above 9, the annealing process may be applied to the hot-rolled sheet after hot rolling. Furthermore, in the method for manufacturing an electromagnetic steel sheet according to any one of 7, 8, or 9, the treatment for imparting an insulating film after the final refining annealing treatment may be performed. Printed by the Consumer Cooperatives of the Intellectual Property Bureau of the Ministry of Economic Affairs (the best form of implementing the invention) The experimental results leading to the present invention will be described below. In addition, the% expressions of the component compositions shown below are all ^ ma s s% "(converted by mass percentage). [Experiment 1] This paper size applies Chinese National Standard (CNS) A4 specification (210X297 mm) -12- 555863 A7 _B7 V. Description of the invention (10) First, to understand the steel composition and punching size of non-oriented electromagnetic steel plate The relationship between accuracy is melted in the laboratory .: C: 〇. 〇〇1 6 ~ (Please read the notes on the back before filling in this page) 0.0028%, Μη: 0 · 20 ~ 0.22%, Α1: 0 0007 to 0. 0014%, Ν: 〇〇〇〇〇12 ~ 0.0022% and Sb: 0.03% are basically constant components as the basic composition, and the amount of P is a certain amount of 0.02%, S i amount It is a steel with a range of 0. 03 to 1. 49%. And the amount of S i is constant at 0 .. 1 0 to 0. 11%, and the content of P is changed within a range of 0. 0 2 to 0. 29%. Ministry of Economic Affairs, Intellectual Property Office M Industrial and consumer cooperation Du printing Next, after heating these steels at 1 100 ° C for 60 mi η, hot rolling to a sheet thickness of 2 mm, at 600 ° C, the steel strip equivalent to 2 hj: The coil is taken out and kept cool after being kept hot. Then, the hot-rolled sheet is annealed at 90 ° C and 60 S, then pickled and cold-rolled to a plate thickness of 0.5 mm, and finally refined and annealed at various temperatures of 700 to 900 ° C. The particle size of the crystal grains changes in various ways. Then, for this final refined annealed plate, the average film thickness is sprayed: a semi-organic insulating coating of 0.6 μm, and a baking-coated sample is prepared for a punching test. The average crystal grain size was determined by observing a cross-section in the thickness direction parallel to the rolling direction, and using a circle-equivalent diameter obtained by the Jeffries method. The punching test is performed using a round die with a diameter of 21 mm 0. The gap is set to 8% of the thickness of the plate, and the angle formed with the rolling direction is 0. , 45. The diameter of the circle (inner diameter) of the four directions of 90 °, 135 ° is punched out to find the average diameter of the 4 points. At the same time, the Chinese paper size of the 4 points is applicable to the Chinese National Standard (CNS) A4 specification (210x297). 1 mm " -13- 555863 A7 B7 V. The difference between the maximum diameter and the minimum diameter of the description of the invention (Ή) is used as an indicator of the anisotropy of punching. (Please read the precautions on the back before filling this page) The results obtained by sorting the relationship between the drop strength (降 Ρ) obtained from the tensile test piece (JI s 5) cut out in the rolling direction are shown in Fig. 1 and Fig. 2. From Fig. 1, It can be seen from the figure that for the whole, the soft material with a low ρ is for the punching die diameter, and the difference between the punching diameter is large. As the hp increases, the punching diameter is closer to the punching die diameter, and the dimensional accuracy is The improvement trend is because, as is well known in the past, the increase in strength has the effect of suppressing the deformation of the irregular shape at the time of punching. However, one point that must be paid attention to in this experiment is that the sample is added for the strength adjustment. It is the same as the previous type that changes the intensity with the change in the amount of S i When comparing electromagnetic steel plates, excellent dimensional accuracy appears in the same level of strength, and the low YP domain can suppress the difference from the size of the stamping die (Figure 1). Bureau of Intellectual Property, Ministry of Economic Affairs Furthermore, printed by the employee consumer cooperative, the steel with changed S i amount is close to the size of the punching die as the strength increases. However, as shown in Figure 2, the difference between the maximum diameter and the minimum The directional anisotropy represented by the difference is still very large, and the relative directional anisotropy of the punched shape is also improved in the steel whose relative strength is increased by the increase in the amount of P. The relationship between these and the use of the final refined annealed sheet The relationship between the average crystal grain size is shown in Figures 3 and 4. From Figures 3 and 4, it can be seen that the steel that changes the amount of Si will die when the particle size becomes larger. The dimensional accuracy and anisotropy of die cutting are also degraded, and the relative increase in P 0 · 13% or more is the large size of the crystal grain size. The paper size applies the Chinese National Standard (CNS) A4 (210X297 mm) '- 14-555863 A7 B7 __ V. Description of the invention (1 2) Also, the cutting accuracy and the anisotropy of the cutting direction are excellent. (Please read the precautions on the back before filling out this page.) About making P contain a certain amount, you can make the cutting size accuracy or the cutting The reason for the effective improvement of the directional anisotropy, although the detailed reason still needs to be explored, but it may be caused by: (1) the strength is increased by the addition of P, which can alleviate the effect of deforming the deformed shape at the time of punching. (2) ) By adding an appropriate amount, it is considered to be a brittle element of P for steel, so that the effect of breaking the boundary when punching (punching) early, and (3) final refinement with the addition of P The orientation of {1 00 丨 < uvw > in the concentrated structure of the annealed sheet tends to increase, and this is the result of the compound effect of alleviating the anisotropy of various directions. Next, the results reviewed from the aspect of magnetic characteristics will be described. The inventors have strongly limited the content of Si or A 1 that will reduce the saturation magnetic flux density, although it will improve the iron loss. The capital material is steel that has increased magnetic flux density as the base material. The relationship between manufacturing conditions and magnetic characteristics was reviewed in detail. Printed in Figure 5 by the Consumer Cooperative of the Intellectual Property Bureau of the Ministry of Economic Affairs, regarding the thickness of each steel plate: 0.5mm, a test piece was investigated about the crystal grain size of the final refined annealed plate and the iron loss in the commercial frequency domain (W15 / 5 0: The result of the relationship between the frequency of 50 Hz and the maximum magnetic flux density of 1.5 d. As can be seen from the same figure, lowering S i will reduce the resistance, which is not conducive to iron loss. However, the iron loss is greatly changed by the crystal grain size, so the particle size is set to about 30 μ m. From the above, it can be seen that it is a stable low iron loss. In addition, when the resistance was reduced by lowering A 1, it was found that the Chinese national standard (CNS) M specification (21〇 > < 297 mm) was applied to the same particle size as the paper size. 15- 555863 A7 B7 5 Explanation of the invention (13) 3 μm or more is effective for reducing iron loss. (Please read the notes on the back before filling this page.) However, before applying for a patent in this case, when the low S i and A 1 of the present invention is a low-grade non-oriented electromagnetic steel sheet, the average final refined annealed sheet The crystal grain size is limited to about 15 to 2 5 μm as a general rule. The reason is as shown in Fig. 3 and Fig. 4 of 0.1% S i ~ 0.7% P steel (marked in the figure). As shown in the example, when the particle size is increased, the punchability is significantly deteriorated due to the decrease in strength. In contrast, when steel with an increased amount of P is added, even if the average crystal grain diameter is increased to about 30 μm or more, a good punching size accuracy can be maintained. Next, the relationship between the average crystal grain size and the magnetic flux density of each steel type is shown in Fig. 6, and the results of the relationship between the iron loss and the magnetic flux density are shown in Fig. 7. According to B50, the magnetic flux density lies in a magnetizing force of 5 0 0 A / m. Although the sample added S i will improve the iron loss, the magnetic flux density will be greatly reduced. The sample added P is because the crystal grains grow and the iron loss is improved, and the high magnetic flux density can still be maintained. . Printed by the Consumer Cooperative of the Intellectual Property Bureau of the Ministry of Economic Affairs as a brittle element, as in the present invention, when P is added in a large amount, earing cracks or layered turtles sometimes occur during the cold rolling process. Cracking phenomenon. The present invention is a review and investigation in consideration of this phenomenon, and the results are clear. When it is the heating of the steel slabs during hot rolling, the temperature becomes the area of the coexistence of ferrous iron / vostian iron. The distribution of P between Sitian iron grains is due to the significant segregation of P in the fat iron grains. From this paper scale, the Chinese National Standard (CNS) A4 specification (210X297 mm) is applied. -16- 555863 A7 __ B7 _ _ V. Description of the invention (14) The fact that steel promotes brittleness. (Please read the precautions on the back before filling this page) In order to prevent such embrittlement, it is necessary to set the heating temperature of the steel slab for hot rolling to Vostian when manufacturing the steel plate of the present invention The iron single-phase domain (or, if possible, the fat single-phase iron single phase) is an important condition. Also, 'P is a ferrite-forming element, so it has the effect of reducing the single-phase domain of Vostian iron near the heating temperature of the steel flat block. Although it is in the composition range of low si steel, the steel flat block (steel sheet for thin plates) ) When the heating temperature is between 1 0 0 ~ 1 2 0 ° C, it can be made a Vostian iron single phase. As described above, it has been found that it is very effective to add about 0.1% or more of P to a low Si steel. Therefore, for steel plates containing more than 0.5% of Si, the positive addition of P was also reviewed. [Experiment 2] The Intellectual Property Bureau of the Ministry of Economic Affairs, such as fused C: 〇〇〇〇13 ~ 0.0026, Μη: 〇18 ~ 0.23%, A1: 0.0001 ~ 0.0011%, N: 〇〇〇〇〇〇〇〇0.0029% Printed by the employee consumer cooperatives with roughly constant composition, the amount of si is between 0.60 ~ 2.42, and the amount of steel between 0.04 ~ 0 · 29%, which is heated at 1 1 0 0 t 6 After 0 minutes, it was hot-rolled to a plate thickness of 2 mm and cold-rolled to a plate thickness of 0.5 mm after pickling. As a result, the steel composition differed, and in some cases, layered cracks occurred parallel to the surface of the steel sheet after rolling. The results are shown in Fig. 8. The paper size of the layered crack occurrence image analysis with ΕΡ Μ A applies the Chinese National Standard (CNS) A4 specification (210X297 mm) -17- 555863 A7 _B7___ V. Description of the invention (15 > (Please First read the notes on the back and then fill out this page.) As a result, it was observed that the segregation or thickening of p was found in the crack occurrence part, so the segregation conditions of this p were discussed in detail, and it was found that it was the hot-rolled steel flat block. During heating, the condition P, which is formed in two areas of the ferrous iron phase and the iron field iron phase, is soaked and maintained, and the fact that it is distributed in the ferrous iron phase leads to the enrichment. In other words, it was found to be in the middle ~ In the field of high si steel plate, since the amount of si, which is an element forming iron of fertile grains, is large, the single-phase domain of Vosstian iron is further reduced. The result is that it is easy to become ferrous iron / voss at conventional heating temperatures The problem of Tian iron two-phase domain. Also, when P exceeds 0.26%, lamellar cracking occurs under any composition condition. Therefore, the steel with various Si, Mn, A1, and P contents was produced by researching equipment. Investigated lies in about 1 Ο Ο 0 ~ 1 2 The temperature range of 0 ° C can suppress the segregation of P to the extent that no rolling defects occur. Furthermore, the aforementioned heating temperature of the steel slab is the precipitation of carbides, nitrides, and sulfides present in the steel. The stability of the viewpoint is appropriate. Printed by the Consumer Cooperatives of the Intellectual Property Bureau of the Ministry of Economic Affairs, first of all, the temperature of the steel flat block heating temperature can become a single phase domain of Vostian iron or single phase domain of ferrous iron, because Segregation due to phase distribution does not occur, so as long as the prescribed amount of P added is small, lamellar cracking can be avoided. From the above experiments, it is known that the added amount of P is necessary to be about 0.26% or less. First of all, investigate the conditions under which high Si steel becomes a single phase of Vosstian iron. The result confirms that Si + A 1 contains more than 0.5% of this paper standard is applicable. National National Standard (CNS) A4 specifications (210X297 mm) -18- 555863 A7 B7 V. Description of the invention (16) Steel is added with P as P $ PA ', but PA, = — 0.2Si + 0.12Mn- (Please read the back Please fill in this page for attention) 0.32A1 + 0.36 (" '(Si, Μη , A1, P are expressed in mass%). The range is in the single-phase domain of Vosstian Iron. Therefore, when the above conditions are met and limited to P $ about 0.26%, it can be suppressed by P Then investigate the conditions under which medium to high Si steel becomes a single phase of ferrous iron, and the amount of P added is also P 2 PF ', but PF5 = -0.34Si + 〇.20Mn- 0.54A1 + 0.76-(2) 5 The range printed by the Consumer Cooperatives of the Intellectual Property Bureau of the Ministry of Economic Affairs (each of the contents of Si, Mn, A1, and P is expressed as mass%) was found to be in the single-phase domain of ferrous iron, so this condition is satisfied When the limit of PS is about 0.26%, the embrittlement caused by P can also be suppressed. Now we will investigate the steel flat block (steel sheet for thin plate) in the single phase domain of ferrous iron or single phase domain of ferrous iron. Conditions for inhibiting the segregation of P when heating is difficult. When the concentration of P occurs in the two phases of ferrous iron / Wotian iron, the concentration of P in the ferrous iron phase also becomes the above-mentioned p F ', but The paper size of the survey is applicable. National National Standard (CNS) A4 specification (210X297 mm) -19- 555863 A7 ___B7_ V. Description of the invention (17 ) As a result, it was found that when P F ′ is reduced to about 0.26 or less, embrittlement caused by P can be avoided. (Please read the precautions on the back before filling this page) When finishing the embrittlement avoidance conditions of the above two-phase domain and the embrittlement avoidance conditions of the single phase domain of ferrous iron, it can be summarized as: PS about 0.2 6% aPF '$ is about 0.26%. Summarizing the above relationships, the conditions to avoid embrittlement caused by P are: P $ is about 0.26%, and PSPA 'or PF, the convention is 0.26%. From the above results, it is found that the amount of P added is within about 0.26%, and when hot rolling is heated, under conditions of single-phase heating of single-phase or ferrous iron by Vostian iron, it is necessary to avoid the occurrence of cold. It can be produced with the problem of lamellar cracks after rolling. In addition, under the condition that the ferrous iron / Wastian iron is heated in a two-phase condition, it is still possible to use a relatively high amount of A 1 for a component system in which the P distribution amount of the ferrous iron phase is reduced, and S i Manufacturing facts. Furthermore, when P is added by about 0.1% or more, the temperature range of the steel slab during hot rolling (approximately 1 0 0 0 t to 1 2 0 0 ° C) becomes a Vosstian iron or fertilizer. The various steel compositions of single-phase grain iron are reviewed. The results were printed by the Consumer Cooperative of the Intellectual Property Bureau of the Ministry of Economic Affairs. It was found that the result of the addition of Ni, which is an element suitable for improving magnetic properties and ensuring strength, and the expansion of P-added steel lies in Vostian near the hot rolling temperature. The fact that the purpose of the iron field is also very effective. 〔Experiment 3〕 C: 0. 013 ~ 0. 026%, Mη ·· 0 · 18 ~ 0.28%, A1: 0.0007 ~ 0.0013% 'This paper size applies the Chinese National Standard (CNS) A4 specification (210X297 mm1) " '" -20- 555863 A7 B7_ V. Description of the invention (18) N: 0.0 014 ~ 0.0025% and P: 0 · 16 ~ (Please read the precautions on the back before filling this page) 〇 · 1 8% The substantially constant composition of the ground is the basic composition. Samples whose S i content is 0.95 to 2.44% and Ni content is 0 to 2.20% were respectively rolled in Experiment 2 to 0.50 nm. , Investigation of the occurrence of layered cracks in the cold-rolled steel body obtained. The results are shown in Figure 9. The cracked 1.1% ~ 1.5% Si steel is the case without Ni. It is possible to roll when Ni is added without cracking. On the other hand, 1.95% Si steel or 2. 4% Si steel without Ni addition or rolled out has the effect of increasing Ni. There are also cracks from time to time, which shows that the effect of Ni is the fact that the correct field exists. It was also found that when the effect of Ni was added, and the above formula was expanded, it was S i + A 1 Contains less than 0.5% In the above steel, the amount of P added is about 0.26% or less, and PSPA, but printed by the Consumer Cooperatives of the Intellectual Property Bureau of the Ministry of Economic Affairs. PA = — 〇 2Si + 0 · 12Μη — 0 · 32A1 + 〇.〇5Ni2 + For the range of 〇.10Ni + 〇.36-(1), the heating temperature of steel slabs at 1000 ° C ~ 12 0 ° C lies in the single-phase domain of Vosstian iron, and the PFS is about 0. 2 6 But this paper size applies Chinese National Standard (CNS) A4 specification (210X297 mm) 21-555863 A7 ΒΊ ___ 5. Description of the invention ((Please read the precautions on the back before filling this page) PF = -〇. 34Si + 0.20Mn-〇.54Al + 〇.24Ni2 + + 〇28Ni + 〇.76 ^ P… (2), that is, the degree of concentration of P can be concentrated under the two-phase domain or single phase domain of ferrous iron Less, and any one can avoid the embrittlement caused by P. Also in the above two formulas, the respective contents of Si, Mn, Al'P'Ni are expressed as ma ss%. Also, the technical of PF and PA The meaning is the same as the above-mentioned PF 'and PA'. [Experiment 4] Printed by the Consumer Cooperative of the Intellectual Property Bureau of the Ministry of Economic Affairs for rolling to 0.5 mm in Experiment 2 and Experiment 3. After the steel sheet to final finish annealing average film thickness of the coating 0. 6 μπι semi-organic insulating coating of, embodiments of the baking finish. The test pieces were subjected to a punching test according to the method described in Experiment 1. The diameter and anisotropy of these samples were investigated. The results are shown in Figs. 10 and 11. From these figures, it can be seen that the steel with Si + Α 1 containing 5% or more and the steel containing 卩 ^ 0 · 10% can significantly improve the punching dimensional accuracy. Therefore, in the Ni-added steel, the amount of addition was changed between 0.38 and 2.20%. Figure 12 shows the relationship between the magnetic flux density b5Q and the tensile strength T S of these samples. In this example, T S is obtained by the same tensile test as Experiment 1, and the magnetic flux density is also measured by Experiment 1. This paper size applies the Chinese National Standard (CNS) A4 specification (210X297 mm) -22- 555863 A7 B7 V. Description of the invention (20) The steel containing P above 0.1% is higher than before. Please read the notes on the back before filling in this page) The comparison of electromagnetic steel plates with si composition (ie, Si + A 1 > 0.5%) shows excellent B 5 〇-TS balance. In particular, as the amount of P added increases, T S increases but no decrease in magnetic flux density is seen, but it tends to increase. This is a feature compared to the fact that conventional steel sheets are strengthened by adding alloying elements other than ferrites such as S i and A 1 when the steel sheet is strengthened with a decrease in magnetic flux density. Sex. These characteristics are very suitable for the rotor base material of various rotating machines (motors, generators) such as DC brushless motors and reactors that require high torque, miniaturization, and high-speed rotation of motors. From the above knowledge (knowledge and insights), as the conditions for the excellent magnetic flux density and punching accuracy of the two, the amount of Si, A1, P, Ni in the steel is specified. Furthermore, in the case of a low S i steel, the average crystal grain size of the final refined and annealed sheet is defined in the following range. For low Si steels, the total of one or two of Si and A 1 is about 0. 0 3 to 0.5%. The Intellectual Property Bureau of the Ministry of Economic Affairs (Si and A 1 printed by the Industrial and Consumer Cooperatives have a deoxidizing effect when added to steel. Therefore, they are used alone or as a deoxidizer for deoxidizing. Separately or the total of the two is required to be about 0.30% or more, and Si and A1 can improve the iron loss of the specific resistance, but on the other hand, it can also cause the saturation magnetic flux density to decrease, so The upper limit is 0.5%. For medium to high Si steels, the total of one or two of Si and A1 is 5% or more to approximately 2.5%. This paper size applies to Chinese national standards ( CNS) A4 specification (210X297 mm) -23- 555863 A7 B7 V. Description of the invention (21) If the mechanical strength or low iron loss is valued at the same time as excellent dimensional accuracy, the total amount of si + A 1 may contain 0. 5% or more (Please read the precautions on the back before filling out this page) As mentioned above, in the case of medium to high Si steel, the effect of adding P can still be obtained from the low P medium to high Si steel. By comparison, materials with high punching accuracy and strength-magnetic flux density balance. However, S When the total amount of i + A 1 exceeds 2.5% or more, the method according to the present invention still makes ordinary cold rolling difficult, so the range is specified to be 0.5% to 2.5%. P: Above about 0.10% and below about 0.26%, P is a particularly important element in the present invention, and P is a function of adjusting the hardness of the material by its high solid solution strengthening energy, as is well known in the past, especially Low S i and low A 1 steel sheets are relatively soft in nature. In the present invention, in order to reduce iron loss, the average crystal grain size must be set to about 30 μm or more. Therefore, the steel sheet may be softened. P is an element necessary for improving the punchability of the steel sheet of the present invention, in other words, to suppress the irregularity or increase in rebound of the punched shape due to insufficient strength of the steel sheet. Consumption of the Industrial Property, Intellectual Property Bureau, Ministry of Economic Affairs Cooperative printed on the increase in strength of this material, plus the effect of suppressing the total deformation during punching by breaking the boundary early, and increasing the {1 0 0丨 < u vw > Orientation to improve directional anisotropy The combined effect of the effects can improve the dimensional accuracy of punching. Furthermore, it has the characteristic that the magnetic flux density does not decrease even though the strength of the steel plate is increased, and this effect is still in the medium to high Si steel. The paper size will be issued in accordance with the Chinese National Standard (CNS) A4 specification (210X297 mm) -24- 555863 A7 B7 V. Description of the invention (22). In order to exert this effect, P needs to contain about 0.10% The above (please read the precautions on the back before filling in this page). On the other hand, P is originally an embrittlement element for steel. If the excess is added, it may cause ear cracks or layer cracks, which will reduce the manufacturability. In this regard, it is because the manufacturing method is improved, or by adding Ni, it is possible to make high-P added steel, which has been difficult to manufacture in the past. However, when the content exceeds 0.26%, it is still difficult to manufacture the P-added steel when the manufacturing method of the present invention is used. Therefore, the amount of P is limited to a range of about 0.10% to about 0.6%. Ni: about 2.3% or less (can be added optionally) Ni not only has the effect of improving the aggregate structure of steel and the magnetic flux density, but also has the effect of increasing the resistance of steel and reducing the iron loss , And the effect of strengthening the solid solution to increase the strength of the steel to suppress the shape irregularity during punching, so it must be actively added. Furthermore, Ni is a forming element of Vostian iron, so it has a heating temperature of 1 0 Ot, which is suitable for expanding the flat steel block (steel sheet for thin plates) ~ Printed by the Consumer Cooperative of the Intellectual Property Bureau of the Ministry of Economic Affairs 1 2 0 0 The effect of Vostian iron domain (circle r in the state diagram) near ° C. In particular, steels with a composition of Si + A 1 in an amount of more than 0.5% are effective in increasing operational stability. When this effect is applied, the rolling instability when P, which is an embrittlement element, is actively added as in the present invention can be greatly improved. In other words, the main point of the stable manufacturing of high-P steel is to suppress the excess P during hot rolling, and as a powerful method, it is to try to avoid the addition of steel flat blocks (steel sheets for thin sheets). The paper size applies Chinese national standards ( CNS) A4 specification (210X297 mm) -25- 555863 A7 B7 V. Description of the invention (23 ^ (Please read the precautions on the back before filling this page) The thermal temperature becomes the ferritic iron / vostian iron two-phase domain When the total content of Si content and A1 content exceeds 0.5%, it is due to the hot temperature of the steel slab and it is easy to separate into two phases. However, due to the expansion effect of the 9 " domain of Ni, and Under such a S i 'A 1 composition, it is also possible to make it a single phase of Vosstian iron when the steel flat block is heated. However, when Ni content is about 2.3% or more, the ferrous iron ( r)-> The reduction of the temperature of the Vostian iron (r) at the beginning of metamorphosis is due to the fact that the Vostian iron is deformed during the final refining annealing, which may cause a decrease in the magnetic flux density. It is also a low temperature below the metamorphic temperature. At the final refining annealing temperature, it is difficult to ensure a flatness above about 3 μm in low Si steel. The particle size and iron loss also deteriorate. So Ni is set to contain about 2.3% or less. In addition, when Ni is added, it is appropriate to add about 0.50% or more. In low Si steel, The average crystal grain size of the final refined and annealed plate: above about 30 μm, below about 80 μm. The Bureau of Intellectual Property, Ministry of Economic Affairs, B (printed by the Industrial and Consumer Cooperatives in the present invention has low S i and low A 1 has no directivity In order to obtain good iron loss characteristics in the electromagnetic steel sheet, as shown in FIG. 5, the average crystal grain size of the final refined and annealed sheet must be about 30 μ m or more. However, it should be more than about 80 μm. When the particle size is smaller, the effect of improving iron loss cannot be obtained. In addition, the steels belonging to the present invention are all metamorphic steels, and the single-phase domain of ferrous iron suitable for recrystallization annealing is about 7 0 t ~ The range of 9 0 0 t is low temperature when compared with the ferrite single-phase steel with a high Si composition. Therefore, the temperature of the grain growth is disadvantageous because of the productivity of the continuous short-time annealing equipment. The upper limit is limited to about 80 μm. In addition, in medium to high Si steel, it is because The resistance of the paper is in accordance with the Chinese National Standard (CNS) A4 specification (210 X 297 mm) -26- 555863 A7 ___B7 V. Description of the invention (24) (Please read the precautions on the back before filling this page) It is easy to obtain a relatively low iron loss due to the improvement effect, etc. Therefore, the particle size is not particularly limited, and a normal range is sufficient. Generally, it is about 20 to 200 μm. Then, the inventors and others followed In recent years, due to the high-speed rotation of the motor and the increase in the number of poles, it has been gradually valued. However, in order to review the methods to improve the magnetic characteristics in the high-frequency region, the results show that reducing the thickness of the board is effective, especially in low S. The effect is remarkable in i steel, and the experiments leading to the results are shown below. [Experiment 5] The survey shown in Fig. 13 shows 0.1% Si—0.01% P steel, 0—95% Si—0.02% steel, and 2.0% Si—0.5% A1 steel. The result lies in the thickness dependence of the iron loss at 400 Hz. Printed by the Consumer Cooperative of the Intellectual Property Bureau of the Ministry of Economic Affairs as shown in the figure, any sample also reduces the eddy current loss by reducing the thickness of the plate. Therefore, the local frequency iron loss has a tendency to be improved, and it is also known that the high thickness caused by reducing the thickness of the plate The improvement effect of frequency iron loss is the case where the low Si steel is larger. However, up to now, the thickness of non-oriented electromagnetic steel sheets has mainly been 0.5 mm, and the reduction of the thickness above is only applicable to high-quality products with higher content than Si and A 1 of the resistance element. Part of it is that there are no examples of applicable products on non-oriented electrical steel sheets with small contents of Si or A1. In addition, Figure 14 shows that the paper size of these blanks for surveying the magnetic flux density is subject to the Chinese National Standard (CNS) A4 specification (210X297 mm) -27- 555863 A7 B7 V. Description of the invention (25) Thick dependence Sexual results. (Please read the precautions on the back before filling this page) As shown in the figure, when reducing the thickness of the board, there is a tendency to decrease the magnetic flux density slightly. However, it should be reduced slightly, and it is also low in any of the board thicknesses. Si steels have significantly higher magnetic flux densities. In particular, high-speed rotary reactance motors have been reviewed for the use of electric motors (EVs) or hybrid electric vehicles (HEVs) as driving motors. In this application, high magnetic flux density and low frequencies at high frequencies will be valued. Iron loss property, but for this problem, as shown in the present invention, low S i, low A 1 and essentially high steel flux density steel sheet can be reduced by thinning. As shown in FIG. 13, the effect of reducing the thickness of the plate is significant when it is 0.35 m or less, and it is more significant when it is 0.30 m or less. In addition, the thinner the plate, the more effective it is in reducing eddy current losses. Therefore, no lower limit is specifically set, but on the other hand, the number of laminations of the iron core is increased to increase the cost, and the lamination of the laminated iron core is also performed. The disadvantages are difficult, so for general production, the lower limit is about 0.10 mm is appropriate. Printed by the Consumer Cooperatives of the Intellectual Property Bureau of the Ministry of Economic Affairs The reasons for limiting the components other than Si, A1, P, and Ni in the steel of the present invention will be described below. C: 〇 ~ 〜〇. 〇1 〇% C is caused by the aging effect. After the steel plate is manufactured, the element that degrades the magnetic characteristics (iron loss) with the passage of time. The degree is more than the content of C. At about 0.10%, it will be significant, so the content of c is limited to less than 0 · 0 1 0%. Regarding the deterioration characteristics of ageing, that is, the amount of c is greater, the Chinese standard (CNS) A4 specification (210 Father 297 public envy 1 -28- 555863 A7 B7 V. Description of the invention (26 ^ less healing is appropriate, so in the present invention, for the amount of C, it also includes the case of substantially zero (under the analysis limit). (Please Read the precautions on the back before filling in this page) Μ η: About 0.5% or less Mn is used to fix S in the form of Mn S, which has the effect of suppressing embrittlement during hot rolling caused by Fes. The increase in the Mn content will increase the specific resistance and improve iron loss, but the increase in the Mn content in the other side will lead to a decrease in the magnetic flux density. Therefore, the upper limit of the Mn content is limited to about 0.5 · 5% 0 S : About 0.05% or less S is an inevitable impurity (impurity), and F e is as described above. In the case of s-situ precipitation, it is not only the cause of hot rolling brittleness. If it is finely precipitated, the grain growth is deteriorated. Therefore, it is advantageous to reduce it as much as possible from the viewpoint of reducing iron loss. In addition, the amount of S exceeds approximately 〇 · 〇 At 15%, the deterioration of iron loss becomes significantly larger, so the upper limit is limited to about 0.015%. However, on the other hand, S also has the effect of improving the shape of the shear when it is punched. Therefore, the degree of reduction depends on the use. Printed by the Consumer Cooperatives of the Intellectual Property Bureau of the Ministry of Economic Affairs N: about 〇. 〇 1 〇% NR is unavoidably mixed with impurities (impurities). If it becomes A 1 When Ν is finely precipitated, it will hinder the growth of grains and degrade the iron loss, so it is limited to about 0. 10% or less. The above has explained the essential components and inhibitory components, but the present invention has other magnetic properties. It can improve the composition and may contain the following elements as appropriate. This paper size applies the Chinese National Standard (CNS) A4 specification (210X297 mm) -29- 555863 A7 B7_ V. Description of the invention (27)
Sb及/或Sn:合計而約〇·40%以下 (請先閲讀背面之注意事項再填寫本頁) S b ’ S η乃偏在於粒界,在於鋼之再結晶時藉抑制 來自結晶粒界之{ 1 1 1丨方位之再結晶核之生成以資改 善磁通密度及鐵損之效果,爲了獲得此效果起見,於單獨 使用或并用任一情形均以合計含有〇 . 〇 1 %以上爲宜。 雖說如此過剩的含有它時由於其效果乃已達飽和,反而含 有量之超過0·40%時即脆化而在於冷軋時發生龜裂, 因此不管單獨使用或倂而使用時均以含有合計約〇 . 4 0 %以下爲合宜。 下面說明其他之副次的含有元素。 本發明乃,做爲脫氧劑,或做爲不純物而存在之S爲 與Μ η —齊有效的捕捉之元素而在於約〇 · 〇 1 %以下之 範圍地含有C a亦可以。 再者,做爲緩和去應變之退火時之氧化、氮化添加B :約0 · 0 0 5 %以下,C r約0 · 1 %以下亦可以。 經濟部智慈財產局員工消費合作社印製 再者,其他有,不損及磁氣特性之元素而添加習知之 C u、Μ 〇等元素時雖不會損及本發明之效果,惟以添加 之成本之面而言,各各之元素之含有量乃以〇 · 1 %以下 爲合宜。 關於其他成份,即例如T i 、N b、V等之碳氮化物 形成元素乃可容許少量之存在,惟盡量少時反而在維持鐵 損上較合宜。 再者在於中高S i鋼時,乃如前述,使之在於鋼扁塊 本紙張尺度適用中國國家標準(CNS ) A4規格(210X297公釐) -30- 555863 A7 B7___ 五、發明説明(28) (請先閱讀背面之注意事項再填寫本頁) 加熱溫度時,得據於沃斯田鐵相或肥粒鐵相其中之一單相 地予以成份設計,或在於沃斯田鐵/肥粒鐵之二相狀態時 ,可以抑制P之容易濃化之肥粒鐵相之P之分配濃化量地 做成份設計,以資實施抑制P之過剩之局部偏析,由而安 定的可以製造高P添加量也。 具體的說,爲了抑制存在於鋼中之碳化物、氮化物、 硫化物等之析出安定化而合宜之鋼扁塊加熱溫度(約 1 0 0 0 t〜1 2 0 0 °C )時之P之過剩之局部偏析起見 令 以下述之式所表示之指數PA: PA = -〇 . 2Si+〇 . 12Mn-0 . 32A1 + 0.05Ni2+0.10Ni+0.36 …(1 ) 與P含量之關係爲滿足P S P A或 以下述之式所表示之指數P F : 經濟部智慧財產局g(工消費合作社印製 = - 〇 _ 34Si+〇 . 20Mn - Ο . 54A1 + 〇.24Ni2+〇.28Ni+〇.76 …(2 ) 乃以P F S約〇 . 2 6就可以(S i ,Μ η,A 1 ,Sb and / or Sn: about 40% or less in total (please read the precautions on the back before filling in this page) S b 'S η is mainly at the grain boundary, which is derived from the grain boundary by suppressing the recrystallization of steel 〇1 % 的 The recrystallization nucleus of the {1 1 1 丨 orientation is generated to improve the effect of magnetic flux density and iron loss. In order to obtain this effect, it is contained in a total of 0.01% or more in either case alone or in combination. Better. Although it contains such an excessive amount, its effect is saturated, but when the content exceeds 0 · 40%, it becomes brittle and cracks occur during cold rolling. Therefore, whether it is used alone or tincture, the total content is included. Below about 0.4% is suitable. Next, other secondary contained elements will be described. In the present invention, S which exists as a deoxidizing agent or as an impurity is an element that is effective in capturing with M η and may contain Ca in a range of about 0. 0.001% or less. In addition, it is possible to add B: oxidizing and nitriding during annealing to relieve strain; about 0: 0.5% or less, and Cr: about 0.1% or less. Printed by the Consumer Cooperative of the Intellectual Property Bureau of the Ministry of Economic Affairs. Other elements that do not impair the magnetic characteristics and add conventional elements such as Cu and M0 will not impair the effect of the present invention. In terms of cost, the content of each element is preferably 0.1% or less. Regarding other components, ie, carbonitride-forming elements such as T i, N b, V, etc., a small amount is allowed, but it is more suitable to maintain iron loss when it is as small as possible. Furthermore, when it comes to medium and high Si steel, as mentioned above, the paper size of the steel flat block is applicable to the Chinese National Standard (CNS) A4 specification (210X297 mm) -30- 555863 A7 B7___ V. Description of the invention (28) ( Please read the precautions on the back before filling this page.) The heating temperature may be based on the single phase design of one of the Wastfield iron phase or the ferrite phase, or the In the two-phase state, the component concentration design of P that can easily reduce the concentration of P, which is easy to be enriched, and the iron phase, can be used to implement the local segregation that suppresses the excess of P, so that a stable high P addition can be produced. and also. Specifically, in order to suppress the precipitation and stability of carbides, nitrides, sulfides, and the like present in the steel, the heating temperature (approximately 1 0 0 0 t ~ 1 2 0 0 ° C) of the steel block is suitable. For excessive local segregation, let the index PA expressed by the following formula: PA = -0.2.2Si + 0.12Mn-0. 32A1 + 0.05Ni2 + 0.10Ni + 0.36. (1) The relationship between P content is satisfied PSPA or the index PF expressed by the following formula: Intellectual Property Bureau of the Ministry of Economic Affairs g (printed by the Industrial and Consumer Cooperatives =-〇_ 34Si + 〇. 20Mn-〇. 54A1 + 〇.24Ni2 + 〇.28Ni + 〇.76… (2) With PFS about 0.26 (S i, M η, A 1,
Ni ’ Ρ之單位爲ma s s%)。 本紙張尺度適用中國國家標準(CNS ) A4規格(210X297公釐) -31 - 555863 A7 B7 五、發明説明(29) 本例中P A係在於各種之s i ,Μ η,A 1 ,N i組 成中,以賓驗求出約1 Ο Ο 0 °C〜1 2 Ο 〇 t溫度域之沃 (請先閲讀背面之注意事項再填寫本頁) 斯田鐵單相之上限之P含有量者,而P F乃以貧驗求出之 成爲肥粒鐵之下限之P含有量也。 下面說明本發明之製造條件。 藉轉爐精鍊法或電氣爐熔融法等而熔製調整於上述合 宜成份組成之纟谷鋼之後,以連續鑄造法或造塊一分塊_軋 法而做成鋼扁塊(薄板用之鋼片)。 接著,將此鋼扁塊加熱後提供於熱軋。本案中,爲了 存在於鋼中之碳化物、氮化物、硫化物等之析出安定化, 鋼扁塊加熱溫度乃以約1 0 0 0 °C〜1 2 0 0 °C爲合宜。 又如前述,鋼扁塊加熱時之相狀態乃對於抑制p之過剩之 局部偏析上非常重要。 由於P係肥粒鐵形成元素,所以具有縮小鋼扁塊加熱 度附近之沃斯田鐵單相域之作用,惟低S i鋼時,在本發 明之成份範圍時,只要鋼扁塊加熱溫度爲約1 〇 〇 〇 °c〜 1 2 0 0 °C時就可以成爲沃斯田鐵單相。 經濟部智慧財產局Μ工消費合作社印製 又中〜高S i鋼時,亦只要能滿足上述pspa之成 份系時,即在於鋼扁塊加熱溫度在約1 〇 〇 〇〜1 2 0 0 °C之範圍中,可以使之成爲沃斯田鐵單相也。 再者,中〜高S i鋼時,能滿足P F S約〇 · 2 6之 成份系時,雖然成爲肥粒鐵/沃斯田鐵共存域之下,該對 於肥粒鐵相之P之偏析之程度乃可以維持於能避免脆化之 水平。 本紙張尺度適用中國國家標準(CNS ) Α4規格(210X297公釐) -32- 555863 A7 B7 五、發明説明(3〇) 又在於肥粒鐵.單相域而被加熱時,只要P含量在於約 〇 · 2 6 %以內就可以不發生層狀龜裂等的可以製造。 (請先閱讀背面之注意事項再填寫本頁) 熱軋後之鋼帶捲(C 〇 i 1)之捲取溫度乃在本發明 係爲了確保高P鋼之製造性上很重要之點。詳述之,鋼帶 捲之捲取溫度高時,在於鋼帶捲之冷卻中,會生成鐵磷化 物(F e 3 P )、而使熱軋板之彎曲性或輥軋性降低,捲 取溫度乃以約6 5 0 °C以下,最好以約6 0 0 °C以下,又 更好以約5 5 0 t以下地盡可能以低溫地實施捲取爲宜。 又’以浸漬於水槽來加速捲取後之鋼帶捲,或對於鋼帶捲 放水等等使鋼帶捲加速冷卻之方法也有效。 接著,熱軋鋼帶捲乃藉酸洗等之手法施予脫鏽皮處理 之後供冷軋處理,惟爲了更提高磁氣特性起見也可以實施 熱軋板退火。 經濟部智慧財產局8工消費合作社印製 關於S i含量與A 1含量之合計爲0 . 5%以下之低 S i鋼中,熱軋板退火溫度乃避免肥粒鐵/沃斯田鐵共存 域(二相領域)爲宜。這是由於在於二相領域實施退火時 ,結晶粒成長不易進行,由而很難期望磁通密度等之磁氣 特性之提高。 下面以N i量別說明在於低S i鋼之合宜之熱軋板退 火溫度。 無添加N i鋼,或N i量1 · 0 %以下等比較少之 N i含量時,對於無方向性電磁鋼板得以通常實施熱軋板 退火一般,在於約9 0 0 °C以上之肥粒鐵單相域可以實施 退火。或將退火溫度稍高溫地,以A c 3點之沃斯田鐵單 本紙張尺度適用中國國家標準(CNS ) A4規格(210X297公釐) -33- 555863 A7 B7 五、發明説明(31) (請先閱讀背面之注意事項再填寫本頁) 相域(最合宜爲1 0 5 0〜1 1 0 〇 °C程度)亦可。總之 避免在於兩者之中間領域之二相領域實施退火(特別是 9501附近)爲重要。 另一方面Ni量1.0以上〜2.3%之比較多之 N i含量時,由於退火中之沃斯田鐵生成溫度會降低,因 此在於9 0 0 °C程度之退火溫度也成爲二相領域,致使磁 通密度降低。雖說如此,在於9 0 0 °C以下之肥粒鐵單相 域之退火乃由於粒成長性不足,所以無法獲得充分之磁通 密度,因而在此成份系之熱軋板退火條件乃限定爲, A c 3點以上之沃斯田鐵單相域(最好1 〇 5 0 °C〜 1 1 0 0 °C 程度)。 再者,中〜高S i鋼時,如上述於細粒之狀態也容易 獲得低鐵損,因此在於退火中之粒成長乃並沒有以低s i 鋼之重要,所以熱軋板退火溫度並不特別地限定,惟通常 以700 1〜1 1 〇〇 °C之範圍爲合宜。 經濟部智慧財產局員工消費合作社印製 接著,所獲得之鋼帶捲乃,經脫鏽皮處理後實施一次 冷軋或溫軋,或夾著中間退火之二次之冷軋(或溫軋), 加工成爲規定之板厚之製品。 而後實施最終精製退火。而低S i鋼時,此最終精製 退火乃在於7 0 0 °C以上之肥粒鐵單相域來實施。其理由 乃’如果最終精製退火溫度未滿7 0 0 °C時,很難以安定 的使平均結晶粒徑成長到3 0 μ m以上。另一方面超過肥 粒鐵單相域地使沃斯田鐵粒成長時,將致使集合組織之劣 化招致磁通密度及鐵損之劣化。 本紙張尺度適用中國國家標準(CNS ) A4規格(210X297公釐) ' ' -34- 555863 A7 _B7_ 五、發明説明(32) (請先閲讀背面之注意事項再填寫本頁) 又’中〜局S i鋼乃’如即述’於退火時之粒成長乃 沒有如低S i鋼那麼地重要,所以最修精製退火之溫度不 做特別之限定,惟通常以7 0 0 °C〜1 1 0 0 °C之範圍內 爲合宜° 熱軋板及冷軋板之肥粒鐵單相溫度或沃斯田鐵單相域 溫度乃,以光學顯微鏡等觀察預先將同組成之鋼板在於種 種之溫度域而施予加熱水冷所獲得之組織而可以決定。其 他之方法乃利用 Thermo-CaUTM等之熱力學計算軟體所 求出之計算狀態圖而預先予以推定。 最終精製退火之後,與一般之無方向性電磁鋼板同樣 ,可實施絕緣被膜之賦予,賦予方法不特別限定,在於處 理液之塗佈後,實施烤塗處理之方法乃很合宜。 又所得之鋼帶捲乃,被裁斷加工成必要之寬、尺寸之 後,在於使用廠商沖切(沖裁)成馬達定子,轉子之形狀 ,疊層,予以製品化,有時即在於經沖切後施予去應變退 火(通常7 5 °C X 1〜2 h )予以製品化也。 經濟部智慧財產局g(工消費合作社印製 (實施例) 〔實施例1〕 以實驗室的熔製,由表1所成之成份組成之熔鋼,鑄 製後,以熱軋製成板厚:3 0 m m之鋼片。接著於 1 1 0 0°C加熱6 〇m i η之後熱軋爲板厚2mm,於 6 0 0 °C均熱保持2 h之相當於鋼帶捲之後,予以放冷。 而後,以9 5 °C行6 0 S之熱軋板退火後’經酸洗’實施 本紙張尺度適用中國國家標準(CNS ) A4規格(210><297公釐) -35- 555863 A7 B7 五、發明説明(33) 冷軋至0 · 5 0 m m厚(1次冷軋)。於7 〇 〇 °c〜 (請先閲讀背面之注意事項再填寫本頁) 9 0 〇 °C之種種之溫度施予最終精製退火,將再結晶粒徑 變化爲種種。 又在於冷軋時,P含量之超過本發明之範圍之鋼J乃 ’在於冷軋中發生多數之平行於板面之層狀之龜裂,因此 停止斯後之處中,亦不做評鑑。 又’No _ 56〜59乃在熱軋後,不實施熱軋板退 火,而在於夾著8 0 0°C之中間退火之二次冷軋法來完成 冷軋者。 接著對於所獲得之最終精製退火板塗佈平均膜厚: 0 . 6 μ m之半有機絕緣被膜,製成試樣,供各種試驗。 沖切試驗:使用直徑:2 1 m m 0之圓形沖切模,間 隙係定爲板厚之8 %,測定與輥軋方向形成之角度分別爲 0° ,45° ,90° , 135°之四方向之沖切圓形之 直徑(內徑),而求該四點之平均徑,又採取四點中最大 徑與最小徑之差,做爲沖切各方向異性之指標。 經濟部智慈財產局員工消費合作社印製 磁氣特性,乃以與輥軋方法所形成之角度爲0 ° ,及 9 0 °地使用剪裁爲1 8 0 m m X 3 0 m m之細帶狀試驗 片,以愛普斯坦法(Epstein Process )測定之。 降伏應力(Y P )即以與輥軋方法平行地切出之 J I S 5號試驗片以速度1 〇mm/mi η之條件實施 抗張試驗,採用上降優點。 所獲得之結果顯不於表2、及表3。 本紙張尺度適用中國國家標準(CNS )八4規格(210X297公釐) -36- 555863 A7 i、發明説明(34) 表1 鋼 記 號 成份組成(mass%) C Si A1 Mn S P N Sb Sn A 0.0027 0.03 0.0008 0.21 0.0040 0.02 0.0015 0.030 <0.001 B 0.0026 0.10 0.0008 0.22 0.0035 0.02 0.0020 0.032 <0.001 C 0.0019 0.53 0.0012 0.22 0.0023 0.02 0.0018 0.030 <0.001 D 0.0019 0.95 0.0007 0.20 0.0033 0.02 0.0012 0.030 <0.001 E 0.0022 1.48 0.0014 0.21 0.0041 0.02 0.0022 0.033 <0.001 F 0.0016 0.11 0.0015 0.20 0.0074 0.07 0.0019 0.030 <0.001 G 0.0017 0.11 0.0008 0.21 0.0036 0.13 0.0022 0.031 <0.001 Η 0.0023 0.11 0.0011 0.22 0.0022 0.18 0.0014 0.030 <0.001 I 0.0028 0.11 0.0006 0.22 0.0075 0.25 0.0018 0.031 <0.001 J 0.0016 0.11 0.0014 0.21 0.0060 0.29 0.0016 0.032 <0.001 ----------^衣-- (請先閱讀背面之注意事項再填寫本頁)The unit of Ni ′ P is ma s s%). This paper size applies the Chinese National Standard (CNS) A4 specification (210X297 mm) -31-555863 A7 B7 V. Description of the invention (29) In this example, PA is in the composition of various si, M η, A 1, N i Based on the guest test, the temperature range of about 1 〇 〇 0 ° C ~ 1 2 〇 〇t (please read the precautions on the back before filling in this page). PF is also the P content which becomes the lower limit of the iron content of the fat obtained from the lean test. The manufacturing conditions of the present invention will be described below. After melting and adjusting the Kariya steel with the above-mentioned suitable composition by the converter refining method or the electric furnace melting method, it is made into a steel flat block (steel sheet for thin plates) by continuous casting method or a block_rolling method. ). Next, this steel slab is heated and provided for hot rolling. In this case, in order to stabilize the precipitation of carbides, nitrides, sulfides, and the like existing in the steel, the heating temperature of the steel slab is preferably about 100 ° C to 120 ° C. As mentioned before, the phase state of the steel slab during heating is very important to suppress the local segregation of excess p. Due to the P-type fertilizer grain iron forming element, it has the effect of reducing the single-phase domain of Vosstian iron near the heating degree of the steel slab. However, in the case of low S i steel, in the composition range of the present invention, only the steel slab heating temperature is required. When it is about 1000 ° c ~ 12 0 ° C, it can become a single phase of Vosstian iron. When the medium-high Si steel is printed by the Intellectual Property Cooperative of the Intellectual Property Bureau of the Ministry of Economic Affairs, as long as it can meet the composition system of the above-mentioned pspa, it means that the heating temperature of the steel flat block is about 1000-1200. In the range of C, it can be made into a single phase of Vosstian iron. In addition, when medium to high Si steels can satisfy the composition system of PFS of about 0.26, although it is under the coexisting domain of ferrous iron / Vostian iron, the segregation of P in the ferrous iron phase The degree can be maintained at a level that avoids embrittlement. This paper size applies the Chinese National Standard (CNS) A4 specification (210X297 mm) -32- 555863 A7 B7 V. Description of the invention (30) It is also in the ferrous iron. When the single-phase domain is heated, as long as the P content is about Within 0.26%, it can be manufactured without causing layered cracks. (Please read the notes on the back before filling this page.) The coiling temperature of the hot rolled steel strip coil (C0i 1) is very important in the present invention to ensure the manufacturability of high-P steel. In detail, when the coiling temperature of the steel strip coil is high, iron phosphide (F e 3 P) is generated during the cooling of the steel strip coil, and the bendability or rollability of the hot-rolled sheet is reduced. The temperature is preferably about 6 5 0 ° C or less, preferably about 6 0 0 ° C or less, and more preferably about 5 5 0 t or less as low temperature as possible. It is also effective to speed up the coiling by immersing in a water tank, or to accelerate the cooling of the coils by discharging water or the like. Next, the hot-rolled steel strip coil is subjected to descaling treatment by means of pickling or the like, and then subjected to cold-rolling treatment, but hot-rolled sheet annealing may be performed in order to further improve magnetic characteristics. For low Si steels with a total Si content and A 1 content of 0.5% or less printed by the 8th Industrial Cooperative Cooperative of the Intellectual Property Bureau of the Ministry of Economic Affairs, the annealing temperature of the hot-rolled sheet is to avoid the coexistence of ferrous iron and Vostian iron Domain (two-phase domain) is preferred. This is because when annealing is performed in the two-phase domain, crystal grain growth is difficult to progress, and it is difficult to expect improvement in magnetic characteristics such as magnetic flux density. In the following, the appropriate hot-rolled sheet annealing temperature for low Si steels will be described in terms of the amount of Ni. When no Ni steel is added, or when the Ni content is relatively small, such as Ni content less than 1.0%, hot-rolled sheet annealing is usually performed on non-oriented electrical steel sheets. Generally, it is about 90 ° C or more. The iron single-phase domain may be annealed. Or, the annealing temperature is slightly higher, and the standard of Chinese paper (CNS) A4 (210X297 mm) is applicable to the standard of Vostian iron single paper at A c 3 -33- 555863 A7 B7 V. Description of the invention (31) ( Please read the notes on the back before filling in this page) Phase domain (most suitable is about 1050 ~ 110 ° C). In short, it is important to avoid annealing in the two-phase domain (especially around 9501) in the middle of the two. On the other hand, when the Ni content is more than 1.0 to 2.3%, the production temperature of Vosted iron during annealing will decrease, so the annealing temperature at about 900 ° C will also become a two-phase field, resulting in The magnetic flux density decreases. Even so, the annealing of the ferrous grain iron single-phase domain below 900 ° C is not able to obtain sufficient magnetic flux density due to insufficient grain growth, so the hot-rolled sheet annealing conditions in this composition are limited to, A c Vostian iron single-phase domain above 3 o'clock (preferably in the range of 105 ° C to 110 ° C). In addition, for medium to high Si steels, low iron loss is also easily obtained in the state of fine grains as described above. Therefore, the grain growth during annealing is not as important as that of low si steels, so the annealing temperature of hot-rolled steel is not It is specifically limited, but it is usually suitable to be in the range of 700 1 to 1100 ° C. Printed by the Consumer Cooperative of the Intellectual Property Bureau of the Ministry of Economic Affairs. Then, the obtained steel strip coil is subjected to descaling and then subjected to cold rolling or warm rolling, or secondary cold rolling (or warm rolling) with intermediate annealing in between. , Processed into products of the specified thickness. Thereafter, final refining annealing is performed. In the case of low S i steel, this final refining annealing is performed in a single phase domain of ferrous iron above 700 ° C. The reason is that if the final refining annealing temperature is less than 700 ° C, it is difficult to stably increase the average crystal grain size to 30 µm or more. On the other hand, when growing Vostian iron grains beyond the single phase domain of ferrous grain iron, the deterioration of the aggregate structure leads to deterioration of magnetic flux density and iron loss. This paper size applies to China National Standard (CNS) A4 specification (210X297 mm) '' -34- 555863 A7 _B7_ V. Description of the invention (32) (Please read the precautions on the back before filling this page) The grain growth of Si steel is not as important as that of low Si steel during annealing, so the temperature for the most refined annealing is not specifically limited, but it is usually 7 0 0 ° C ~ 1 1 The range of 0 0 ° C is suitable ° Single-phase temperature of ferrous grain iron or hot-steel single-phase domain of hot-rolled and cold-rolled steel is observed by optical microscope, etc. The domain can be determined by applying heat to the water-cooled tissue. The other method is to estimate it in advance using a calculation state diagram obtained by thermodynamic calculation software such as Thermo-CaUTM. After the final refining and annealing, the insulating film can be applied in the same way as a general non-oriented electrical steel sheet. The method of applying the insulating film is not particularly limited. The method of baking coating after the application of the treatment liquid is very suitable. The resulting steel strip coil is cut and processed to the necessary width and size, and then it is punched (punched) into the shape of the motor stator and rotor by the manufacturer, and the product is laminated. Sometimes it is punched. After applying strain relief annealing (usually 7 5 ° CX 1 ~ 2 h), the product is also manufactured. Bureau of Intellectual Property, Ministry of Economic Affairs (printed by the Industrial and Consumer Cooperatives (Example) [Example 1] Melt steel composed of the ingredients shown in Table 1 by laboratory melting, after casting, and hot rolling into plates Thickness: 30 mm steel sheet. After heating at 600 ° C at 110 ° C, it is hot rolled to a sheet thickness of 2 mm. After being uniformly heated at 600 ° C for 2 h, it is equivalent to a steel strip coil. After cooling, the hot-rolled sheet was annealed at 9 5 ° C for 60 S and was 'picked' to implement this paper. The Chinese standard (CNS) A4 specification (210 > < 297 mm) was applied -35- 555863 A7 B7 V. Description of the invention (33) Cold rolled to 0 · 50 mm thickness (1 cold rolling). At 7 〇 °° C ~ (Please read the precautions on the back before filling this page) 9 0 〇 ° The temperature of various kinds of C is subjected to the final refining annealing, and the recrystallized grain size is changed into various kinds. Also, in cold rolling, the steel J whose P content exceeds the range of the present invention is that most of the cold rolling occurs parallel to the plate surface. The layered cracks, therefore, will not be judged after stopping the post. Also 'No _ 56 ~ 59 is after hot rolling without hot rolled sheet annealing, but in The cold rolling is completed by a secondary cold rolling method with intermediate annealing at 800 ° C. Then, the obtained final refined annealed plate is coated with a semi-organic insulating coating with an average film thickness of 0.6 μm to make Samples for various tests. Punching test: Use a round punching die with a diameter of 21 mm 0, the gap is set to 8% of the thickness of the plate, and the angles formed with the rolling direction are 0 ° and 45 °, respectively. The diameter (inner diameter) of the punched circle in four directions of 90 ° and 135 °. To find the average diameter of the four points, the difference between the largest and smallest diameters of the four points is taken as the anisotropy of the punching in all directions. The magnetic characteristics printed by the Consumer Cooperative of the Intellectual Property Bureau of the Ministry of Economic Affairs are printed at an angle of 0 ° with the rolling method, and are trimmed to a fineness of 180 mm X 30 mm at 90 °. The strip-shaped test piece was measured by the Epstein Process. The yield stress (YP) is a JIS No. 5 test piece cut out parallel to the rolling method, and the resistance is implemented at a speed of 10 mm / mi η. Zhang test, using the advantages of up and down. The results obtained are not shown in Table 2, and Table 3. The paper ruler Applicable to China National Standards (CNS) 8-4 specifications (210X297 mm) -36- 555863 A7 i. Description of invention (34) Table 1 Composition of steel symbols (mass%) C Si A1 Mn SPN Sb Sn A 0.0027 0.03 0.0008 0.21 0.0040 0.02 0.0015 0.030 < 0.001 B 0.0026 0.10 0.0008 0.22 0.0035 0.02 0.0020 0.032 < 0.001 C 0.0019 0.53 0.0012 0.22 0.0023 0.02 0.0018 0.030 < 0.001 D 0.0019 0.95 0.0007 0.20 0.0033 0.02 0.0012 0.030 < 0.001 E 0.0022 1.48 0.0014 0.21 0.0041 0.02 0.0022 0.033 < 0.001 F 0.0016 0.11 0.0015 0.20 0.0074 0.07 0.0019 0.030 < 0.001 G 0.0017 0.11 0.0008 0.21 0.0036 0.13 0.0022 0.031 < 0.001 Η 0.0023 0.11 0.0011 0.22 0.0022 0.18 0.0014 0.030 < 0.001 I 0.0028 0.11 0.0006 0.22 0.0075 0.25 0.0018 0.031 < 0.001 J 0.0016 0.11 0.0014 0.21 0.0060 0.29 0.0016 0.032 < 0.001 ---------- ^ clothing-(Please read the precautions on the back before filling this page)
、1T 經濟部智慧財產局員工消費合作社印製 本紙張尺度適用中國國家標準(CNS ) Α4規格(210Χ297公釐) -37- 555863 A7 B7 經濟部智慧財產局員工消費合作社印製 五、發明説明(35) 表2, 1T Printed by the Intellectual Property Bureau of the Ministry of Economy ’s Consumer Cooperatives. This paper is printed according to the Chinese National Standard (CNS) A4 specification (210 × 297 mm) -37- 555863 A7 B7 Printed by the Employee ’s Cooperatives of the Intellectual Property Bureau of the Ministry of Economy 35) Table 2
No. 鋼 記 號 粒徑 (μιη) Β50 (Τ) Wl5/50 (W/kg) YP (MPa) 沖切徑 (mm) 沖切徑 Max-min (μιη) 備考 1 A 11.3 1.818 9.79 311 20.979 17 比較例 2 // 20.5 1.811 6.85 243 20.963 21 // 3 // 28.2 1.807 5.90 214 20.959 28 // 4 // 31.9 1.804 5.45 204 20.957 29 // 5 // 42.8 1.797 5.09 182 20.952 25 // 6 // 61.3 1.785 4.62 160 20.950 34 // 7 B 10.8 1.808 10.23 322 20.981 16 比較例 8 // 20.3 1.806 6.85 249 20.968 14 // 9 // 26.8 1.801 5.99 223 20.961 18 // 10 // 31.5 1.796 5.52 210 20.959 19 // 11 // 46.2 1.786 4.94 183 20.954 23 // 12 // 78.2 1.775 4.50 152 20.945 26 // 13 C 9.3 1.786 10.95 375 20.985 9 比較例 14 // 16.0 1.782 7.57 305 20.980 14 // 15 // 33.6 1.771 5.22 236 20.970 13 11 16 // 59.4 1.764 4.43 198 20.964 17 // 17 // 78.9 1.757 4.25 183 20.957 31 // 18 D 12.2 1.772 8.57 368 20.990 15 比較例 19 // 23.5 1.767 5.88 297 20.977 12 // 20 // 27.2 1.764 5.54 284 20.976 14 // 21 // 42.8 1.758 4.56 249 20.968 12 // 22 // 55.5 1.754 4.25 233 20.964 15 // 23 // 64.9 1.746 4.20 224 20.962 16 11 24 E 18.2 1.755 6.48 361 20.990 16 比較例 25 // 26.8 1.752 5.20 324 20.986 15 // 26 // 31.7 1.749 4.68 310 20.983 13 // 27 // 45.6 1.741 4.18 284 20.980 14 // 28 // 66.8 1.726 3.90 261 20.976 17 // (請先閱讀背面之注意事項再填寫本頁) 本紙張尺度適用中國國家標準(CNS ) A4規格(210X297公釐) -38- 555863 A7No. Steel mark particle size (μιη) Β50 (Τ) Wl5 / 50 (W / kg) YP (MPa) Punching diameter (mm) Punching diameter Max-min (μιη) Remarks 1 A 11.3 1.818 9.79 311 20.979 17 Compare Example 2 // 20.5 1.811 6.85 243 20.963 21 // 3 // 28.2 1.807 5.90 214 20.959 28 // 4 // 31.9 1.804 5.45 204 20.957 29 // 5 // 42.8 1.797 5.09 182 20.952 25 // 6 // 61.3 1.785 4.62 160 20.950 34 // 7 B 10.8 1.808 10.23 322 20.981 16 Comparative Example 8 // 20.3 1.806 6.85 249 20.968 14 // 9 // 26.8 1.801 5.99 223 20.961 18 // 10 // 31.5 1.796 5.52 210 20.959 19 // 11 // 46.2 1.786 4.94 183 20.954 23 // 12 // 78.2 1.775 4.50 152 20.945 26 // 13 C 9.3 1.786 10.95 375 20.985 9 Comparative Example 14 // 16.0 1.782 7.57 305 20.980 14 // 15 // 33.6 1.771 5.22 236 20.970 13 11 16 // 59.4 1.764 4.43 198 20.964 17 // 17 // 78.9 1.757 4.25 183 20.957 31 // 18 D 12.2 1.772 8.57 368 20.990 15 Comparative example 19 // 23.5 1.767 5.88 297 20.977 12 // 20 // 27.2 1.764 5.54 284 20.976 14 // 21 // 42.8 1.758 4.56 249 20.968 12 // 22 // 55.5 1.754 4.25 233 20.9 64 15 // 23 // 64.9 1.746 4.20 224 20.962 16 11 24 E 18.2 1.755 6.48 361 20.990 16 Comparative example 25 // 26.8 1.752 5.20 324 20.986 15 // 26 // 31.7 1.749 4.68 310 20.983 13 // 27 // 45.6 1.741 4.18 284 20.980 14 // 28 // 66.8 1.726 3.90 261 20.976 17 // (Please read the notes on the back before filling out this page) This paper size applies to the Chinese National Standard (CNS) A4 specification (210X297 mm) -38 -555863 A7
7 B 五、發明説明(36) 表3 經濟部智慈財產局員工消費合作社印製7 B V. Description of Invention (36) Table 3 Printed by the Consumer Cooperative of the Intellectual Property Office of the Ministry of Economic Affairs
No. 鋼記號 粒徑 (μιη) Β50 (Τ) Wl5/50 (W/kg) YP (MPa) 沖切徑 (mm) 沖切徑 Max-min (μιη) 備考 29 F 8.6 1.813 11.80 377 20.989 7 比較例 30 11 26.5 1.811 5.99 246 20.975 11 // 31 // 33.4 1.809 5.45 227 20.973 10 // 32 // 52.0 1.802 4.77 196 20.966 14 // 33 // 59.7 1.797 4.75 188 20.960 16 // 34 G 11.3 1.817 9.69 363 20.995 6 比較例 35 // 16.2 1.815 7.70 320 20.993 5 // 36 // 26.5 1.814 5.95 271 20.989 6 // 37 // 33.6 1.812 5.40 252 20.988 4 發明例 38 // 43.8 1.808 4.95 233 20.986 5 // 39 // 75.2 1.804 4.45 201 20.984 7 // 40 Η 11.3 1.822 9.66 384 20.995 3 比較例 41 // 14.8 1.819 8.10 351 20.996 4 11 42 // 23.0 1.819 6.34 305 20.995 5 // 43 11 25.6 1.819 6.02 295 20.994 6 // 44 11 35.6 1.816 5.26 269 20.993 4 發明例 45 11 40.2 1.814 5.05 260 20.933 4 11 46 // 56.8 1.813 4.62 237 20.992 3 // 47 // 77.6 1.811 4.41 220 20.991 6 // 48 I 10.8 1.826 9.93 420 20.994 3 比較例 49 // 13.5 1.824 8.55 391 20.995 4 // 50 // 26.8 1.821 5.77 321 20.996 5 II 51 // 32.5 1.820 5.15 305 20.9994 4 發明例 52 // 40.8 1.818 4.94 288 20.993 5 // 53 // 56.4 1.817 4.59 267 20.994 4 // 54 11 60.5 1.816 4.53 263 20.992 4 55 J 由於發生冷軋龜裂不做評鑑 比較例 56 Β 19.8 1.784 7.98 260 20.965 16 比較例 57 // 39.4 1.761 5.22 199 20.953 21 // 58 Η 18.2 1.795 7.81 335 20.993 6 比較例 59 // 35.6 1.861 5.26 269 20.993 4 發明例 本紙張尺度適用中國國家標準(CNS ) A4規格(210X297公釐) (請先閲讀背面之注意事項再填寫本頁) -39- 555863 A7 B7 五、發明説明(37) (請先閱讀背面之注意事項再填寫本頁) 在於P含量之未滿本發明之適宜範圍,或由s i量及 結晶粒徑之變化而強度發生變化之鋼A〜F ( N 〇 . 1〜 33,56,57)乃,隨著γρ之增加而沖切徑有靠近 於沖切模徑之趨向。惟最大徑與最小徑之差而顯示之沖切 尺寸之各方向異性乃以1 0〜2 Ο μ m程度地比較大,再 者,S i量增加時,有磁通密度降低之問題。 而相對地,依照本發明,採低S i ,A 1之組成而將 P含有0.1%以上之鋼G〜Η乃,YP爲350MPa 以下之比較低之値之情形下也呈顯良好之沖切徑,並且沖 切尺寸之各方向異性也小,由從磁性特性之面而言,雖然 這些之鋼種之平均結晶粒徑控制於3 Ο μ m以上,惟( Νο·37,38,39,44,45,46,47, 51 ,52,53,54,59)均呈顯安定之低鐵損且 獲得高磁通密度也。 〔實施例2〕 經濟部智慧財產局Μ工消費合作社印製 以實驗室的熔製以表4所示之成份組成之熔鋼’與實 施例1同樣製成板厚2 m m之熱軋板後’以1 1 0 0 °C 3 0 S之熱軋板退火之後,施予酸洗’冷軋到〇 . 5 0 m m厚,接著在於7 0 0 t以上,且在於肥粒鐵單相域之 種種之溫度施予最終精製退火’將再結晶粒徑變心爲種種 尺寸。 接著,塗佈與實施例1同樣之半有機絕緣被膜’製造 出試片供各種試驗。 本纸張尺度適用中國國家標準(CNS ) A4規格(210X297公楚:Ί -40- 555863 A7 B7 五、發明説明(38) 試驗結果表示於表5。 本例中,鋼K〜Μ乃減低S i ,施予藉A 1之脫氧者 ’而鋼N . ◦之組及鋼Q . R之組乃得於評鑑添加N i之 影響地予以熔製者。 滿足了本發明之鋼組成,且將平均結晶粒徑定爲3 〇 μ m以上地予以適宜化之鋼乃,均具有優異之沖切尺寸精 度,並且不但其沖切各方向異性小,磁氣特性也優異,特 別是比較鋼N與鋼◦,及鋼Q與鋼R時,添加了 N i之鋼 〇及鋼R乃看出磁通密度之顯著之提高。 表4 (請先閲讀背面之注意事項再填寫本頁) 經濟部智慧財產局員工消費合作社印製 鋼 記 號 成份組成(mass%) C Si A1 Μη S Ni P N Sb Sn K 0.0011 0.01 0.32 0.25 0.0032 一 0.05 0.0020 <0.001 0.044 L 0.0009 0.01 0.33 0.24 0.0039 0.16 0.0021 <0.001 0.046 Μ 0.0019 0.02 0.31 0.22 0.0018 一 0.24 0.0024 <0.001 <0.001 Ν 0.0033 0.21 0.23 0.15 0.0028 0.16 0.0012 0.060 <0.001 〇 0.0024 0.21 0.24 0.18 0.0016 1.23 0.16 0.0018 0.055 <0.001 Ρ 0.0088 0.35 0.0011 0.35 0.0046 0.05 0.0031 <0.001 <0.001 Q 0.0082 0.34 0.0007 0.33 0.0040 一 0.19 0.0019 <0.001 <0.001 R 0.0080 0.35 0.0011 0.33 0.0051 0.95 0.19 0.0018 <0.001 <0.001 本紙張尺度適用中國國家標準(CNS ) A4規格(210X297公釐) -41 - 555863 A7 B7 五、發明説明(39) 表5 經濟部智慧財產局員工消費合作社印製No. Steel particle size (μιη) Β50 (Τ) Wl5 / 50 (W / kg) YP (MPa) Punching diameter (mm) Punching diameter Max-min (μιη) Remarks 29 F 8.6 1.813 11.80 377 20.989 7 Compare Example 30 11 26.5 1.811 5.99 246 20.975 11 // 31 // 33.4 1.809 5.45 227 20.973 10 // 32 // 52.0 1.802 4.77 196 20.966 14 // 33 // 59.7 1.797 4.75 188 20.960 16 // 34 G 11.3 1.817 9.69 363 20.995 6 Comparative Example 35 // 16.2 1.815 7.70 320 20.993 5 // 36 // 26.5 1.814 5.95 271 20.989 6 // 37 // 33.6 1.812 5.40 252 20.988 4 Invention Example 38 // 43.8 1.808 4.95 233 20.986 5 // 39 / / 75.2 1.804 4.45 201 20.984 7 // 40 Η 11.3 1.822 9.66 384 20.995 3 Comparative Example 41 // 14.8 1.819 8.10 351 20.996 4 11 42 // 23.0 1.819 6.34 305 20.995 5 // 43 11 25.6 1.819 6.02 295 20.994 6 // 44 11 35.6 1.816 5.26 269 20.993 4 Invention Example 45 11 40.2 1.814 5.05 260 20.933 4 11 46 // 56.8 1.813 4.62 237 20.992 3 // 47 // 77.6 1.811 4.41 220 20.991 6 // 48 I 10.8 1.826 9.93 420 20.994 3 Compare Example 49 // 13.5 1.824 8.55 391 20.995 4 // 50 // 26.8 1.821 5.77 321 20.996 5 II 51 // 32.5 1.820 5.15 305 20.9994 4 Invention Example 52 // 40.8 1.818 4.94 288 20.993 5 // 53 // 56.4 1.817 4.59 267 20.994 4 // 54 11 60.5 1.816 4.53 263 20.992 4 55 J Cracked without evaluation Comparative Example 56 Β 19.8 1.784 7.98 260 20.965 16 Comparative Example 57 // 39.4 1.761 5.22 199 20.953 21 // 58 Η 18.2 1.795 7.81 335 20.993 6 Comparative Example 59 // 35.6 1.861 5.26 269 20.993 4 Invention Example This paper size applies to China National Standard (CNS) A4 (210X297 mm) (Please read the precautions on the back before filling out this page) -39- 555863 A7 B7 V. Description of the invention (37) (Please read the precautions on the back first Please fill in this page again) The steels A ~ F (N 〇. 1 ~ 33, 56, 57) which are within the appropriate range of the present invention for P content, or whose strength changes due to changes in the amount of si and the grain size With the increase of γρ, the punching diameter tends to be closer to the punching die diameter. However, the directional anisotropy of the punched size displayed by the difference between the maximum diameter and the minimum diameter is relatively large at about 10 to 20 μm. Furthermore, as the amount of Si increases, there is a problem that the magnetic flux density decreases. In contrast, according to the present invention, when the composition of S i and A 1 is low and P contains more than 0.1% of steel G ~ ΗNa, YP is lower than 350MPa, which is a relatively low die, it also shows a good punching. Diameter, and the dimensional anisotropy of the punching size is also small. From the aspect of magnetic properties, although the average crystal grain size of these steels is controlled to be more than 30 μm, but (Νο · 37,38,39,44 , 45, 46, 47, 51, 52, 53, 54, 59) all show stable low iron loss and obtain high magnetic flux density. [Example 2] Printed by the laboratory of the Ministry of Economic Affairs and the Intellectual Property Bureau of the Ministry of Economic Affairs and Consumer Cooperatives, the molten steel composed of the components shown in Table 4 was melted in the same manner as in Example 1, and a hot-rolled sheet having a thickness of 2 mm was produced. 'After annealing at 1 1 0 0 ° C 3 0 S hot-rolled sheet, pickling is applied' Cold rolling to a thickness of 0.50 mm, followed by more than 7 0 t, and in the single phase domain of ferrous iron The final refining annealing applied at various temperatures will change the recrystallized grain size to various sizes. Next, the same semi-organic insulating film as in Example 1 was applied to produce test pieces for various tests. This paper size applies the Chinese National Standard (CNS) A4 specification (210X297 Gongchu: Ί -40-555863 A7 B7 V. Description of the invention (38) The test results are shown in Table 5. In this example, steel K ~ M is a reduction of S i, the deoxidizer who lends A 1 and the steel N. ◦ group and the steel Q. R group are those who can be melted under the influence of adding Ni. The steel composition of the present invention is satisfied, and Suitable steels with an average crystal grain size of 30 μm or more have excellent punching dimensional accuracy, and not only have small anisotropy in punching, but also have excellent magnetic properties, especially compared with steel N. With steel ◦ and steel Q and steel R, the addition of Ni 〇 and steel R shows a significant increase in magnetic flux density. Table 4 (Please read the precautions on the back before filling this page) Ministry of Economy Composition of the printed steel mark composition (mass%) of the Intellectual Property Bureau employee consumer cooperative C Si A1 Μη S Ni PN Sb Sn K 0.0011 0.01 0.32 0.25 0.0032-0.05 0.0020 < 0.001 0.044 L 0.0009 0.01 0.33 0.24 0.0039 0.16 0.0021 < 0.001 0.046 Μ 0.0019 0.02 0.31 0.22 0.0018-0.24 0.0024 < 0.001 & l t; 0.001 Ν 0.0033 0.21 0.23 0.15 0.0028 0.16 0.0012 0.060 < 0.001 〇0.0024 0.21 0.24 0.18 0.0016 1.23 0.16 0.0018 0.055 < 0.001 P 0.0088 0.35 0.0011 0.35 0.0046 0.05 0.0031 < 0.001 < 0.001 Q 0.0082 0.34 0.0007 0.33 0.0040 -0.19 0.0019 < 0.001 < 0.001 R 0.0080 0.35 0.0011 0.33 0.0051 0.95 0.19 0.0018 < 0.001 < 0.001 This paper size is applicable to China National Standard (CNS) A4 (210X297 mm) -41-555863 A7 B7 V. Description of the invention ( 39) Table 5 Printed by the Consumer Cooperatives of the Intellectual Property Bureau of the Ministry of Economic Affairs
No. 鋼 記 號 粒徑 (μιη) B50 (T) Wl5/50 (W/kg) YP (MPa) 沖切徑 (mm) 沖切徑 Max-min (μιη) 備考 1 K 36.1 1.777 4.95 211 20.959 18 比較例 2 // 61.3 1.769 4.27 177 20.950 26 比較例 3 L 26.5 1.789 5.57 283 20.982 8 比較例 4 // 34.2 1.785 4.98 262 20.985 7 發明例 5 // 47.0 1.785 4.47 240 20.982 9 發明例 6 Μ 12.5 1.777 8.63 396 20.995 6 比較例 7 // 35.2 1.774 4.88 294 20.991 8 發明例 8 11 70.2 1.768 4.06 250 20.992 9 發明例 9 Ν 28.7 1.786 5.38 289 20.990 8 比較例 10 // 36.2 1.785 4.89 270 20.989 9 發明例 11 η 58.1 1.779 4.26 239 20.989 9 發明例 12 〇 6.8 1.807 12.96 484 20.995 2 比較例 13 // 22.7 1.803 5.28 329 20.992 2 比較例 14 // 32.1 1.803 4.37 299 20.992 3 發明例 15 // 48.2 1.797 3.70 270 20.995 7 發明例 16 P 43.0 1.768 4.88 218 20.966 16 比較例 17 // 60.4 1.766 4.50 197 20.959 18 比較例 18 // 72.0 1.769 4.38 187 20.961 21 比較例 19 Q 18.4 1.766 6.99 348 20.987 7 比較例 20 // 44.8 1.766 4.76 273 20.977 8 發明例 21 // 75.1 1.775 4.29 243 20.984 8 發明例 22 R 22.6 1.778 5.07 359 20.990 4 比較例 23 // 39.7 1.784 3.75 313 20.992 5 發明例 24 // 56.8 1.781 3.30 290 20.991 5 發明例 本紙張尺度適用中國國家標準(CNS ) A4規格(210X297公釐) (請先閲讀背面之注意事項再填寫本頁) -42- 555863 A7 B7_ 五、發明説明(40) 〔實施例3〕 實驗室的熔製由表1之鋼F,表4之鋼N及鋼0所示 之組成之熔鋼,與實施例1同樣地製成板厚:2 m m之熱 軋板之後,以1 1 0 0 °C 3 0 S之熱軋板退火之後’施 予酸洗,藉冷軋加工爲0·50〜0.20mm之各種厚 度。 接著在於7 0 0 °C以上,且於肥粒鐵單相域之各種溫 度施予最終精製退火,將再結晶粒徑控制爲3 5〜4 5 μ m之間。 接著製作塗佈與實施例1同樣之半有機絕緣被膜之試 片。供各種試驗。在這些試片也調查了在於4 0 0 Η z之 高頻率鐵損。 所得之結果也倂記於表6 表6 (請先閲讀背面之注意事項再填寫本頁) 經濟部智慧財產局員工消費合作社印製No. Steel particle size (μιη) B50 (T) Wl5 / 50 (W / kg) YP (MPa) Punching diameter (mm) Punching diameter Max-min (μιη) Remarks 1 K 36.1 1.777 4.95 211 20.959 18 Compare Example 2 // 61.3 1.769 4.27 177 20.950 26 Comparative Example 3 L 26.5 1.789 5.57 283 20.982 8 Comparative Example 4 // 34.2 1.785 4.98 262 20.985 7 Invention Example 5 // 47.0 1.785 4.47 240 20.982 9 Invention Example 6 Μ 12.5 1.777 8.63 396 20.995 6 Comparative Example 7 // 35.2 1.774 4.88 294 20.991 8 Invention Example 8 11 70.2 1.768 4.06 250 20.992 9 Invention Example 9 Ν 28.7 1.786 5.38 289 20.990 8 Comparative Example 10 // 36.2 1.785 4.89 270 20.989 9 Invention Example 11 η 58.1 1.779 4.26 239 20.989 9 Invention Example 12 06.8 1.807 12.96 484 20.995 2 Comparative Example 13 // 22.7 1.803 5.28 329 20.992 2 Comparative Example 14 // 32.1 1.803 4.37 299 20.992 3 Invention Example 15 // 48.2 1.797 3.70 270 20.995 7 Invention Example 16 P 43.0 1.768 4.88 218 20.966 16 Comparative Example 17 // 60.4 1.766 4.50 197 20.959 18 Comparative Example 18 // 72.0 1.769 4.38 187 20.961 21 Comparative Example 19 Q 18.4 1.766 6.99 348 20.987 7 Comparative Example 20 // 44.8 1.766 4.7 6 273 20.977 8 Invention Example 21 // 75.1 1.775 4.29 243 20.984 8 Invention Example 22 R 22.6 1.778 5.07 359 20.990 4 Comparative Example 23 // 39.7 1.784 3.75 313 20.992 5 Invention Example 24 // 56.8 1.781 3.30 290 20.991 5 Invention Example This Paper size applies Chinese National Standard (CNS) A4 specification (210X297 mm) (Please read the precautions on the back before filling out this page) -42- 555863 A7 B7_ V. Description of Invention (40) [Example 3] The molten steel consisting of the steel F in Table 1, steel N in Table 4 and steel 0 was melted, and the plate thickness was made in the same manner as in Example 1. After the hot-rolled plate was 2 mm, the thickness was 1 1 0 0 °. After hot-rolled sheet of C 3 0 S is annealed, it is subjected to pickling and cold-rolled to a thickness of 0.50 to 0.20 mm. Then, the final refining annealing is performed at a temperature of more than 700 ° C and various temperatures in the single phase domain of the ferrous iron, and the recrystallization particle size is controlled to be between 3 5 and 4 5 μm. Next, a test piece coated with a semi-organic insulating film similar to that of Example 1 was prepared. For various tests. In these test strips, high-frequency iron loss at 400 Η z was also investigated. The results obtained are also recorded in Table 6 Table 6 (Please read the notes on the back before filling out this page) Printed by the Consumer Cooperatives of the Intellectual Property Bureau of the Ministry of Economic Affairs
No· 鋼 記 號 板厚 (μιη) 粒徑 (μιη) Β50 (Τ) Wl5/50 (W/kg) Wl 5/400 (W/kg) YP (MPa) 沖切徑 (mm) 沖切徑 Max-min (μιη) 備考 1 F 0.50 38.2 1.807 4.84 171 217 20.968 14 比較例 2 // 0.35 37.1 1.804 3.78 98 219 20.983 12 // 3 // 0.20 42.8 1.803 3.41 58 209 20.989 11 // 4 N 0.50 42.0 1.785 4.84 141 259 20.988 8 發明例 5 // 0.35 37.9 1.783 3.39 71 267 20.993 7 // 6 // 0.20 41.3 1.783 3.08 42 261 20.995 5 // 7 〇 0.50 37.4 1.802 3.86 89 288 20.992 4 發明例 8 // 0.35 43.5 1.797 3.05 48 277 20.995 3 // 9 // 0.20 35.2 1.798 2.78 29 292 20.995 4 // 本紙張尺度適用中國國家標準(CNS ) Α4規格(210Χ297公釐) -43- 555863 A7 B7 五、發明説明(41) (請先閱讀背面之注意事項再填寫本頁) 隨著使板厚變厚,特別是在於高頻率下之鐵損之改善 效果很顯著。 又,沖切尺寸精度也隨著板厚之減小而有改善之趨勢 ,惟於能滿足本發明之成份範圍之鋼N,鋼〇乃與比較鋼 F而優異,又在於本發明之鋼中之任何板厚均呈顯優異之 沖切尺寸之各方向異性。 〔實施例4〕 實驗室的熔製以表示於表7所成之成份組成之熔鋼鑄 成鋼塊之後,實施1 1 5 0 °C X 1小時之均熱,而後以熱 軋製成板厚3 0 m m之扁片塊。將獲得之扁片塊加熱爲表 8所示之溫度(S R T )保持1小時之後,熱軋至2 · 0 mm,實施5 8 Otx 1小時之相當於鋼帶捲之處理,予 以放冷。而後除了一部份之鋼,其他以表8所示之條件實 施熱軋板退火,然後經酸洗之後冷軋至0 . 5 0 m m。 經濟部智慧財產局員工消費合作社印製 在於冷軋時,藉由冷軋中之板之狀況及觀察冷軋後之 斷面組織來評鑑冷軋時之加工性。 高P (SO·10%)且不能滿足本發明之成份範圍 之鋼(W、Z、a、c、d、K、及I)、及成份範圍雖 能滿足本發明之成份範圍,惟鋼扁塊(薄板用鐵片)加熱 溫度(S R T )或熱軋捲取溫度(C T )之離開本發明之 範圍者(No . 25,26)乃在觀察出平行於板面之層 狀之龜裂,在於一部份之試片(No . 5,19,25) 本紙張尺度適用中國國家標準(CNS ) A4規格(210乂297公^1 一 ~ -44- 555863 Μ Β7五、發明説明(42) 及在於輥軋中分離成爲層狀,在下序之輥軋上發生困難, 在這些結果之狀態下,工業上安定的製造乃屬困難。對於 這些試片即不做以後之處理及評鑑。 接著對於冷軋板實施7 0 〇 °C以上之種種之溫度之最 終精製退火,施予如實施例1同樣之半有機絕緣被膜之塗 膜,供各種試驗。在此以與輥軋方向平行地載出J I S 5號試驗片,以牽引速度1 〇 m m / s牽拉而以所獲得之 抗張強度(T S )來評鑑該強度,將所獲得之結果倂記於 表8 〇 (請先閱讀背面之注意事項再填寫本頁) 經濟部智慧財產局B(工消費合作社印製 本紙張尺度適用中國國家標準(CNS ) A4規格(210X297公釐) -45- 555863 A7 B7No. Steel Mark Plate Thickness (μιη) Particle Size (μιη) Β50 (Τ) Wl5 / 50 (W / kg) Wl 5/400 (W / kg) YP (MPa) Punching Diameter (mm) Punching Diameter Max- min (μιη) Remarks 1 F 0.50 38.2 1.807 4.84 171 217 20.968 14 Comparative Example 2 // 0.35 37.1 1.804 3.78 98 219 20.983 12 // 3 // 0.20 42.8 1.803 3.41 58 209 20.989 11 // 4 N 0.50 42.0 1.785 4.84 141 259 20.988 8 Invention Example 5 // 0.35 37.9 1.783 3.39 71 267 20.993 7 // 6 // 0.20 41.3 1.783 3.08 42 261 20.995 5 // 7 〇0.50 37.4 1.802 3.86 89 288 20.992 4 Invention Example 8 // 0.35 43.5 1.797 3.05 48 277 20.995 3 // 9 // 0.20 35.2 1.798 2.78 29 292 20.995 4 // This paper size applies to China National Standard (CNS) A4 specification (210 × 297 mm) -43- 555863 A7 B7 V. Description of the invention (41) ( (Please read the notes on the back before filling in this page.) As the thickness of the plate becomes thicker, especially the improvement of iron loss at high frequencies is significant. In addition, the die cutting dimensional accuracy also tends to improve as the thickness of the plate decreases. However, the steel N, which can satisfy the composition range of the present invention, is superior to the comparative steel F, and also lies in the steel of the present invention. Any thickness of the plate exhibits anisotropy of excellent punching dimensions. [Example 4] After melting in a laboratory, a molten steel having the composition shown in Table 7 was cast into a steel block, and then soaked at 1 150 ° CX for 1 hour, and then hot-rolled to a plate thickness. Flat piece of 30 mm. The obtained slab pieces were heated to the temperature (S R T) shown in Table 8 for 1 hour, then hot-rolled to 2.0 mm, and subjected to a treatment equivalent to a steel strip coil of 5 8 Otx for 1 hour, and allowed to cool. Then, except for a part of the steel, the hot-rolled sheet was annealed under the conditions shown in Table 8, and then cold-rolled to 0.50 mm after pickling. Printed by the Consumer Cooperative of the Intellectual Property Bureau of the Ministry of Economic Affairs During cold rolling, the processability during cold rolling is evaluated by examining the condition of the plate during cold rolling and observing the cross-section structure after cold rolling. Steel (W, Z, a, c, d, K, and I) that has a high P (SO · 10%) and can not satisfy the composition range of the present invention, and the composition range can satisfy the composition range of the present invention, but the steel is flat When the heating temperature (SRT) or hot-rolling coiling temperature (CT) of the block (iron sheet for thin plate) leaves the scope of the present invention (No. 25, 26), the layered cracks parallel to the plate surface are observed. A part of the test piece (No. 5, 19, 25) This paper size is applicable to the Chinese National Standard (CNS) A4 specification (210 乂 297 public ^ 1 1 ~ -44- 555863 Μ B7 V. Description of the invention (42) And it is separated into layers during rolling, and difficulties occur in the subsequent rolling. Under these conditions, industrially stable manufacturing is difficult. For these test pieces, subsequent processing and evaluation are not performed. The cold-rolled sheet is subjected to final refining annealing at a temperature of more than 700 ° C, and a coating film of a semi-organic insulating film similar to that in Example 1 is applied for various tests. Here, the film is loaded in parallel with the rolling direction. JIS No. 5 test piece was pulled out and pulled at a pulling speed of 10 mm / s to obtain the obtained tensile strength (T S) to evaluate the intensity, and write down the results obtained in Table 8 (please read the precautions on the back before filling out this page) Bureau of Intellectual Property, Ministry of Economic Affairs Standard (CNS) A4 specification (210X297 mm) -45- 555863 A7 B7
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/D -- (請先閱讀背面之注意事項再填寫本頁)/ D-(Please read the notes on the back before filling this page)
、1T 555863 A7 B7 五、發明説明(#4) 經濟部智慧財產局員工消費合作社印製 中 用 適 尺 張 紙 本、 1T 555863 A7 B7 V. Description of the invention (# 4) Printed by the Consumer Cooperative of the Intellectual Property Bureau of the Ministry of Economic Affairs
00條 Pf < 6726 g ϋ g g o g i g g g g g g g g g g g g £ 0.591 : 1593 ] 1600 ] 1592 ] 0.585 ] 0.451 : 0.461 : 3.465 ] D.452 ] 0.283 0.274 0.300 0.242 0.252 -0.076 -0.092 -0.056 -0.055 -0.059 0.489 0.894 1.296 1.978 0.461 1.461 1.461 Pa^P o o o n 〇 g g g Ο Ο g g g g g g g § g g g g § 3.261 i 3.262 ( 3.266 ( 1261 ( 1257 ] 0.178 0.185 1187 ] 1179 ] 0.080 0.074 10.090 0.056 0.061 -0.132 -0.142 -0.120 -0.120 -0.122 0.146 0.261 0.351 0.525 0.185 0.185 0.185 m m Κπ 向. O O 〇 〇 幽 Ο Ο 〇 , _ 〇 〇 〇 〇 〇 〇 M « 4< ifiS) 4< 〇 〇 〇 〇 獅 Wr 4< 總 3¾ _ 3¾ 難 1¾ 15 _ _ 沖切徑 max-min :μη〇 VO VO ir\ Csl ir^ ITi r-H I I 寸 CO r-H »r^ CO CO 1 1 CO 寸 寸 1 1 ε ^0.969 \ Z0.988 : 20.991 ( 20.993 ; 20.9681 20.9921: 20.9741 1 1 120.9931 20.992 120.990 20.995 20.996 20.994 1 1 20.996 20.995 20.996 〇 On On 窆 l 1 -- 〇〇 οα oo CO 410 : ON ο cn 寸 400 : 1 1 1470 1 494 444 as 等 as 〇 CO 1 1 wo 寸 CO 00 寸 l/n 〇> VD r—H 寸 1 1 ΥΡ :MPa) < O' CN /*-0 o VO /^vl VD OO ΚΓ) IT) rsi ON rsi t—t ON csl 1 1 ο cn CO 00 CO 〇〇 CO CO C<I 00 CO 0 0 ON ^~~1 1 1 CO CO OJ CO CO 00 CO cs r-H CO 1 1 Β50 :Τ) < L.775 : L774: 1.776: r- 1.762 : 1.764 CO cn 1 1 |1.735 1.733 1.703 1.708 1.709 1.704 1 1 1.742 L748 r—H I/O 1.75 之 1 1 熱軋板. 退火溫< tiC ) o g o g 〇 o ο 〇 § ο 冢 900 900 o o ο ο ο ο 〇 2 1100 ! 11000 11000 11000 11000 1000 11100 1100 1100 1100 壊 550 1700 另 I f^\ o CNl 宕 1/-^ o ο <r^ O 1/^ o un ir^ un ο ΐΓί 〇 1/Ί m 0 ID ur> 1580 ' 0 〇〇 IT) 〇 〇〇 IT·) 〇 〇〇 0 00 IT) 0 wn ιτ·> 1/Ί un ο wo 0 0 r-H ISRT i (C。< )__ 〇 ID o o o o IT) 〇 〇 o 〇 〇 y-D Ο ο ID 〇 wr> 〇 ir> 11150 11150 1150 丨 1150 11150 11150 1150 11150 11150 11100 1250 I__ m. aJ r A^s 塑 m 藤 m 驪 m [3 m m m > 鎰 m 鎰 鎰 匿 备 λλ χ 趣 薇 m 鎰 J_J ±Λ W AJ ^1Λ N u AJ J-Λ MI <i^ 鐵 J_J ΑΛ csi J_J JA 匿 JJ ΑΛ Γ) 运 u λα W: 鐵 〇 J-Λ 疆 -a m (Ο 癖 HP fnr、 m f 1 ^ *=n Μ: i m m • i-Η m 覉 s 變 m s: m c m 器 m 〇 m m i m m 器 U 口 CA2 L ^ cs CO 寸 ΙΟ V£> oo ON ο r-H CNl cn 寸 iD v£) 〇〇 〇V CNl r<i CO csi ID CNl VO CO I -- (請先閲讀背面之注意事項再填寫本頁) 訂 555863 A7 B7____ 五、發明説明(45) 做爲本發明之範圍之成份,特別是添加了 P 0.1 %以上之鋼(No . 2〜4,7,13,14,16〜 (請先閲讀背面之注意事項再填寫本頁) 1 8及2 1〜2 4)乃均呈顯優異之沖切尺寸精度。詳述 之·· P添加量未滿0 . 1%之鋼(No . 1 ,6,10及 1 5 )中沖切徑乃隨著S i + A 1量之增加而具有改善之 趨勢,惟沖切徑之各方向異性很大。另一方面,本發明鋼 乃顯然沖切徑以及沖切徑之各方向異性均優異者。加上這 些發明鋼乃雖然具有與P含有量未滿0 . 1 %之比較鋼同 等以上之磁通密度仍然高強度,且具有優異之強度-磁通 密度平衡。 〔實施例5〕 經濟部智慧財產局員工消費合作社印製 以實驗室的熔製表4之鋼Μ,鋼N及鋼◦所示之組成 之熔鋼,鑄製之後,以熱軋而製成板厚:30mm之扁鋼 片。接著以表9所示之各溫度(SRT)加熱6 0分鐘後 ,熱軋到板厚:2 m m,而以表9所示之各溫度(C T ) 而實施相當於鋼帶捲捲取之均熱保持1小時之後,予以放 冷。而後除了一部份之鋼之外,以表9所示之各溫度而實 施6 0秒之熱軋板退火。 對於所獲得之熱軋鋼板,在於室溫(2 3 °C )而實施 彎曲試驗彎曲試驗乃從熱軋板上以輥軋方向成爲長軸方向 地採取1 0 Ommx 3 0mm之試驗片,依據J I S C 2 5 5 0實施彎曲半徑1 5mm之反複彎曲試驗,於表 示在於熱軋板表面發生龜裂之(彎曲)次數。 1紙張尺度適用中國國家標準(CNS ) A4規格(210X297公釐) -48- 555863 A7 B7 五、發明説明(46) 再者,以下述之方法調查鋼扁塊加熱時之熱軋板退火 時之組織(相)。鋼扁片、熱軋板均分別在於規定溫度( 記載於表9 )保持於規定時間(鋼扁片加熱:1小時、退 火:6 0秒)之後,施予水淬火而凍結加熱時之組織,藉 由光學顯微鏡之組織觀察而同定了相。其結果亦倂記於表 9 ° 將上述熱軋板乃經酸洗之後,實施0 . 5 0 m m厚爲 止之冷軋(1次冷軋),評鑑了有無發生由脆化所致之冷 軋不良(層狀龜裂)之情形。對於沒有發生層狀龜裂之冷 軋板即,以表9所示之種種之溫度實施最終精製退火,接 著塗佈與實施例1同樣之半有機絕緣被膜,製作成試片供 各種試驗。結果表示於表9。 * I ----------衣-- (請先閲讀背面之注意事項再填寫本頁)00 Pf < 6726 g ϋ ggogigggggggggggggg £ 0.591: 1593] 1600] 1592] 0.585] 0.451: 0.461: 3.465] D.452] 0.283 0.274 0.300 0.242 0.252 -0.076 -0.092 -0.056 -0.055 -0.059 0.489 0.894 1.296 1.978 0.461 1.461 1.461 Pa ^ P ooon 〇ggg 〇 〇 ggggggg § gggg § 3.261 i 3.262 (3.266 (1261 (1257) 0.178 0.185 1187] 1179] 0.080 0.074 10.090 0.056 0.061 -0.132 -0.142 -0.120 -0.120 -0.122 -0.122 0.146 0.261 0.351 0.525 0.185 0.185 0.185 mm π direction. OO 〇〇 幽 〇 〇 〇 _ 〇〇〇〇〇〇〇M «4 < ifiS) 4 < 〇〇〇〇 Lion Wr 4 < total 3¾ _ 3¾ difficult 1¾ 15 _ _ punching diameter max -min: μη〇VO VO ir \ Csl ir ^ ITi rH II inch CO rH »r ^ CO CO 1 1 CO inch 1 1 ε ^ 0.969 \ Z0.988: 20.991 (20.993; 20.9681 20.9921: 20.9741 1 1 120.9931 20.992 120.990 20.995 20.996 20.994 1 1 20.996 20.995 20.996 〇 On On 1-〇〇οα oo CO 410: ON ο cn inch 400: 1 1 1470 1 494 444 as et as 〇CO 1 1 wo inch CO 00 inch l / n 〇 > VD r—H inch 1 1 ΥΡ: MPa) < O 'CN / *-0 o VO / ^ vl VD OO ΚΓ) IT) rsi ON rsi t—t ON csl 1 1 ο cn CO 00 CO 〇〇CO CO C < I 00 CO 0 0 ON ^ ~~ 1 1 1 CO CO OJ CO CO 00 CO cs rH CO 1 1 B50: T) < L.775: L774: 1.776: r- 1.762: 1.764 CO cn 1 1 | 1.735 1.733 1.703 1.708 1.709 1.704 1 1 1.742 L748 r—HI / O 1.75 of 1 1 Hot rolled sheet. Annealing temperature < tiC) ogog 〇o ο 〇§ ο Tsuk 900 900 oo ο ο ο ο 〇2 1100! 11000 11000 11000 11000 1000 11100 1100 1100 1100 壊 550 1700 Also I f ^ \ o CNl DOWN 1-^^ o ο < r ^ O 1 / ^ o un ir ^ un ο ΐΓί 〇1 / Ί m 0 ID ur > 1580 '0 〇〇IT) 〇〇〇IT ·) 〇〇〇00 00 IT) 0 wn τ · > 1 / Ί un ο wo 0 0 rH ISRT i (C. <) __ 〇ID oooo IT) 〇〇o 〇〇yD Ο ο ID 〇wr > 〇ir > 11150 11150 1150 丨 1150 11150 11150 1150 11150 11150 11100 1250 I__ m. aJ r A ^ s plastic m vine m 骊 m (3 mmm > 镒 m 镒 镒 密 备 λλ χ χ 薇 m 镒 J_J ± Λ W AJ ^ 1Λ N u AJ J-Λ MI < i ^ Iron J_J ΑΛ csi J_J JA 匿 JJ ΑΛ Γ) Win λα W : Iron 〇J-Λ Jiang-am (〇 HP HP fnr, mf 1 ^ * = n Μ: imm • i-Η m 覉 s change ms: mcm device m 〇mmimm device U port CA2 L ^ cs CO inch ΙΟ V £ > oo ON ο rH CNl cn inch iD v £) 〇〇〇V CNl r < i CO csi ID CNl VO CO I-(Please read the notes on the back before filling this page) Order 555863 A7 B7____ V. Description of the invention (45) As a component of the scope of the present invention, in particular steel (No. 2 ~ 4, 7, 13, 14, 16 ~ added with P 0.1% or more) (Please read the precautions on the back before filling in this (Pages) 1 8 and 2 1 to 2 4) Both show excellent punching dimensional accuracy. Details ... The punching diameter in steels (No. 1, 6, 10 and 15) where the P addition amount is less than 0.1% has a tendency to improve as the amount of Si + A 1 increases, but Punching diameter is very different in different directions. On the other hand, it is apparent that the steel of the present invention is excellent in the directional anisotropy of the punching diameter and the punching diameter. In addition, these invention steels have high strength and high magnetic flux density even though they have a P content less than 0.1% compared to steel, and they have excellent strength-magnetic flux density balance. [Example 5] The Consumer Cooperative of the Intellectual Property Bureau of the Ministry of Economic Affairs printed a laboratory melting steel of Table M, Steel N and Steel as shown in Table 4, and after casting, it was made by hot rolling. Plate thickness: 30mm flat steel sheet. After heating at the respective temperatures (SRT) shown in Table 9 for 60 minutes, it was hot-rolled to a sheet thickness of 2 mm, and at the temperatures (CT) shown in Table 9, the equivalent of coiling of steel strip was performed. After the heat was maintained for 1 hour, it was allowed to cool. Then, except for a part of the steel, a hot-rolled sheet annealing was performed at a temperature shown in Table 9 for 60 seconds. The obtained hot-rolled steel sheet was subjected to a bending test at room temperature (2 3 ° C). The bending test was performed by taking a test piece of 100 mm x 30 mm from the hot-rolled plate with the rolling direction becoming the long axis direction in accordance with JISC. A repeated bending test with a bending radius of 15 mm was carried out at 2 5 50, and the number of times (bending) that cracks occurred on the surface of the hot-rolled sheet was shown. 1 Paper size applies Chinese National Standard (CNS) A4 specification (210X297 mm) -48- 555863 A7 B7 V. Description of invention (46) Furthermore, the following method is used to investigate the hot rolled steel sheet annealing during the heating of steel slabs. Organization (phase). Both the steel slab and the hot-rolled sheet are maintained at a predetermined temperature (described in Table 9) for a predetermined time (steel slab heating: 1 hour, annealing: 60 seconds), and then the structure at the time of freezing and heating is given by water quenching Phase alignment was achieved by microscopic observation of the tissue. The results are also recorded in Table 9 ° After the above hot-rolled sheet was pickled, cold rolling was performed to a thickness of 0.50 mm (1 cold rolling), and the presence or absence of cooling caused by embrittlement was evaluated. Poor rolling (layer cracking). For the cold-rolled sheet having no layered cracks, that is, the final refining annealing was performed at various temperatures shown in Table 9, and then a semi-organic insulating film similar to that in Example 1 was applied, and test pieces were prepared for various tests. The results are shown in Table 9. * I ---------- Clothing-(Please read the precautions on the back before filling this page)
、1T 經濟部智慧財產局員工消費合作社印製 本紙張尺度適用中國國家標準(CNS ) Α4規格(210Χ297公釐) -49- 555863 A7 B7 經濟部智慧財產局員工消費合作社印製 五、發明説明 ^ 1 1 in 〇〇 〇〇 CS1 1 〇〇 〇〇 OQ CSI 荠 VO 荠 CO 〇 ON CNl 〇〇 C<1 oo On CNl On OO CvJ 〇 ^ S3 r-H CO CO CO VD cn oo CO CO r—H S Ο r-H 1 1 MD PQ C ig CN1 <〇 CN1 s VO CO oo VO VO r- r^· t—H CO CO CO CO 1 τ—Η r-H 1 Γ-; Η ι < ir^ r-H tr^ r—H t—H !>; t—H 1 CSI 赛 CNl 〇6 cn 1 Η CM U^) oo cn un r—H cs wo § r—H ^£5 cn UO 〇6 cn 〇q CO oo MD cn 最終精製 退火溫度 (C。) 1 ο οο ο οο 1 〇〇 〇 uo oo oo o oo o 8 oo 〇 〇〇 o oo 〇 oo 雜 Κπ It i5 〇 〇 i5 竖 〇 〇 〇 〇 〇 〇 〇 〇 熱軋板 扳彎次 數 寸 οο CN1 ι〇 CO CNl CNl CNl CO CO oo CSI nn 血 血 ^T- nn nn rm ^- V. ΠΉ 4^- ^ ^ Μ 酹 gt + 酹 酹 g| + □m| nttir 1 1 1 1 卜 m- ^ \j 癒蹓S 壊 壊 壊 壊 8 ON 8 as s ON Ο \ < 〇 σ\ 8 Η τ—Η ο ο Η 8 On 〇 OO u U l/Ί l〇 un 〇> VsD to 8 to S ο S >y^ 异芻 卜 ΠΕΠ ΠΉ 4^τ ΠΉ 血 nm ΙΙΠ 皆 nzr ΠΕΠ ΠΉ tm 4^r· ΠΉ 職盤 + g| U + 酹 酹 gffif 酹 酹 SBf □ml 翳癒繼 卜 卜 _ U C0 Η τ—Η Ο S y—i σ> τ-Ή r-H r—H H r-H r-H r-H Ο τ—Η ν Η Ο ι < V " < 〇 r " Ή τ—Η 〇 H r-H m 孽 孽 s 鎰 鎰 鎰 鎰 鎰 鎰 鎰 _ J-Λ 粼 粼 ±Λ JJ m 粼 粼 粼 JJ ^LA 匿 匿 ML 匿 匿 匿 癖 匿 匿 匿 ML <M 疆 m 粼 m 微 粼 粼 微 m 粼 粼 粼 粼 粼 翳2 S S S 2 2 2 〇 〇 〇 〇 Η CN1 cn 寸 iD VO 卜 〇〇 On 〇 1 i r-H CN r—H CO \ 4 ------------ (請先閱讀背面之注意事項再填寫本頁) 本紙張尺度適用中國國家標準(CNS ) A4規格(210X297公釐)_ f 〇 — 、-口 555863 A7 B7 五、發明説明(48^ (請先閲讀背面之注意事項再填寫本頁) 在於本發明之鋼組成(低S i鋼)中,滿足本發明之 製造條件時,(N 〇 · 2,3,6,8,1 0,及 1 1 ) 乃雖然屬於P之高添加不發生問題地製造出鋼板,其各特 性也良好。 另一方面,本發明之鋼扁塊(薄板用鐵片)之成爲二 相領域(N 〇 . 1及4 )時,可知容易發生由其脆化所致 之冷軋不良。由而很難做到製品化。又在鋼帶捲之捲取溫 度高於6 5 0 t:時(N 〇 · 5 )時,熱軋板之加工性降低 而獲得之電磁鋼板之鐵損也不佳。又在於熱軋板退火溫度 之成爲二相域時(No · 7及No · 12),以及將Ni 添加多於1 . 0 m a s s %之鋼乃,在於α單相域地實施 熱軋板退火時(Ν ο · 1 3 )乃所獲得之電磁鋼板之磁通 密度降低。 再者,最終精製退火溫度之脫離本發明之製造條件, 而不足於將再結晶粒徑形成爲3 0 μ m以上時(Ν 〇 . 9 )時磁性特性亦呈劣化。 經濟部智慧財產局員工消費合作社印製 產業上之利用可能性 總而言之,依本發明時,可以安定的獲得具有高磁通 密度,且低鐵損之優異之磁氣特性,並且具有高的沖切尺 寸精度之無方向性電磁鋼板,以及具有高強度之無方向性 電磁鋼板。 並且本發明之無方向性電磁鋼板乃最適合於,各種馬 達之鐵芯胚材,其中最適合於特別被要求需要兼備有高的 本紙張尺度適用中國國家標準(CNS ) A4規格(210X297公釐) -51 - 555863 A7 B7 五、發明説明(49) (請先閲讀背面之注意事項再填寫本頁) 尺寸精度以及高磁通密度之電抗馬達,以及需要有胚材強 度之埋入磁鐵型之D C無電刷馬達等之鐵芯胚材而最適合 之材料也。 圖式之簡單說明 第1圖表示S i含量及P含量之對於降伏強度與沖切 直徑之關係之影響之曲線圖。 第2圖表示s i含量及P含量之對於降伏強度與沖切 方向異性之關係之影響之曲線圖。 第3圖表示S i含量及P含量之對於平均結晶粒徑與 沖切直徑之關係之影響之曲線圖。 第4圖表示S i含量及P含量之對於平均結晶粒徑與 沖切方異性之關係之影響之曲線圖。 第5圖表示S i含量及P含量之對於平均結晶粒徑與 鐵損之關係之影響之曲線圖。 第6圖表示S i含量及P含量之對於平均結晶粒徑與 磁通密度之關係之影響之曲線圖。 經濟部智慧財產局8工消費合作社印製 第7圖表示S i含量及P含量之對於鐵損與磁通密度 之關係之影響之曲線圖。 第8圖表示S i含量及P含量之對於發生層狀龜裂之 影響之曲線圖。 第9圖表示S i含量與N i含量之對於發生層狀龜裂 之影響之曲線圖。 第1 0圖表示s i含量與添加N i對於P含量及沖切 本紙張尺度適用中國國家標準(CNS ) A4規格(210X297公釐) -52- 555863 A7 B7 五、發明説明(5〇) 切 沖 及 量 含 P 於 對 •1 N 加。 添圖 與線 。 量曲 圖含之 線i 響 曲 S 影 之示之 響表係 影圖關 之 1 之 係一-^性 關第異 之向 徑方 影 之 度 密 通 磁 與 度 強 張 抗 於 對 量 含 P 示 表 圖 2 ο 1 圖 第線 曲 之 圖 圖 線線 曲 之之 係係 之之 損度 鐵密 0 S 高磁 與與 厚厚 板板 示示 表表 圖 圖 3 4 IX IX 第第 (請先閱讀背面之注意事項再填寫本頁) 經濟部智慈財/$局員工消費合作社印製 本紙張尺度適用中國國家標準(CNS ) Α4規格(210Χ297公釐) -53-、 1T Printed by the Intellectual Property Bureau of the Ministry of Economic Affairs, Consumer Cooperatives This paper is printed in accordance with the Chinese National Standard (CNS) A4 specification (210 × 297 mm) -49- 555863 A7 B7 Printed by the Employees ’Cooperative of the Intellectual Property Bureau of the Ministry of Economic Affairs 1 1 in 〇〇〇〇〇〇CS1 1 〇〇〇〇OQ CSI 荠 VO CO 〇ON CN1 〇〇C < 1 oo On CNl On OO CvJ 〇 ^ S3 rH CO CO CO VD cn oo CO CO r-HS 〇 rH 1 1 MD PQ C ig CN1 < 〇CN1 s VO CO oo VO VO r- r ^ · t—H CO CO CO CO 1 τ—Η rH 1 Γ-; Η ι < ir ^ rH tr ^ r-H t-H! > t-H 1 CSI match CNl 〇6 cn 1 Η CM U ^) oo cn un r-H cs wo § r-H ^ £ 5 cn UO 〇6 cn 〇q CO oo MD cn final Refining annealing temperature (C.) 1 ο οο ο οο 1 〇〇〇〇oo oo oo o oo o 8 oo 〇〇〇oo oo 〇oo Miscellaneous κπ It i5 〇〇i5 vertical hot rolled plate Turning times οο CN1 ι〇CO CNl CNl CNl CO CO o o CSI nn Blood ^ T- nn nn rm ^-V. ΠΉ 4 ^-^ ^ Μ 酹 gt + 酹 酹 g | + □ m | nttir 1 1 1 1 m m- ^ \ j 蹓 蹓 S 壊 壊 壊ON8 ON 8 as s ON 〇 \ < 〇σ \ 8 Η τ—Η ο ο Η 8 On 〇OO u U l / Ί l〇un 〇 > VsD to 8 to S ο S > y ^ ΠΠΠΠ ΠΉ 4 ^ τ ΠΉ Blood nm ΙΙΠ nzr ΠΕΠ ΠΉ tm 4 ^ r · ΠΉ Position + g | U + 酹 酹 gffif 酹 酹 SBf □ ml 翳 越 继 卜卜 _ U C0 Η τ—Η Ο S y --I σ > τ-Ή rH r—HH rH rH rH Ο τ—Η ν Η Ο ι < V " < 〇r " Ή τ—Η 〇H rH m镒 _ J-Λ Sparkling ± Λ JJ m Sparkling Sparkling JJ ^ LA Hidden ML Hidden Hidden Hidden ML < M Jiang Medun m Slightly sparked Slightly m Sparked Singing 翳 2 SSS 2 2 2 〇〇〇〇〇 CN1 cn inch iD VO 〇〇On 〇1 i rH CN r—H CO \ 4 ------------ (Please Read the notes on the back and then fill out this page) This paper size is applicable to the Chinese National Standard (CNS) A4 specification (210X297 mm) _ f 〇—,-555863 A7 B7 V. Description of the invention (48 ^ (Please read the Note: Please fill in this page again.) In the steel composition (low Si steel) of the present invention, when the manufacturing conditions of the present invention are satisfied, (N 0.2, 3, 6, 8, 10, and 1 1) is A steel plate that is high in P is produced without problems, and its properties are also good. On the other hand, when the steel slab (iron sheet for sheet metal) of the present invention is in the two-phase domain (No. 1 and 4), it is found that cold rolling defects due to embrittlement are liable to occur. This makes it difficult to make products. When the coiling temperature of the steel strip coil is higher than 650 t: (N 0 · 5), the workability of the hot-rolled sheet is reduced and the iron loss of the electromagnetic steel sheet obtained is not good. Also, when the annealing temperature of the hot-rolled sheet becomes a two-phase domain (No. 7 and No. 12), and when the amount of Ni is more than 1.0 mass%, the hot-rolled sheet annealing is performed in the α single-phase domain. (N ο · 1 3) is a decrease in the magnetic flux density of the obtained electromagnetic steel sheet. In addition, the final refining annealing temperature deviates from the manufacturing conditions of the present invention, and the magnetic properties are also deteriorated when the recrystallization particle size is not more than 30 μm (N 0.9). Utilization possibilities in the printing industry for employees ’cooperatives in the Intellectual Property Bureau of the Ministry of Economic Affairs In short, according to the present invention, excellent magnetic characteristics with high magnetic flux density and low iron loss can be obtained stably, and high punching Non-oriented electromagnetic steel sheet with dimensional accuracy, and non-oriented electromagnetic steel sheet with high strength. In addition, the non-directional electromagnetic steel sheet of the present invention is most suitable for iron core blanks of various motors. Among them, it is most suitable for particularly required to have a high paper size. Applicable to China National Standard (CNS) A4 specification (210X297 mm). ) -51-555863 A7 B7 V. Description of the invention (49) (Please read the precautions on the back before filling this page) Dimensional accuracy and high magnetic flux density of the reactance motor, and the embedded magnet type that requires the strength of the blank material DC brushless motors are the most suitable materials. Brief Description of the Drawings Fig. 1 is a graph showing the effect of the Si content and the P content on the relationship between the drop strength and the punching diameter. Fig. 2 is a graph showing the influence of the si content and the P content on the relationship between the drop strength and the anisotropy of the punching direction. Fig. 3 is a graph showing the effect of the Si content and the P content on the relationship between the average crystal grain size and the punching diameter. Fig. 4 is a graph showing the effect of the Si content and the P content on the relationship between the average crystal grain size and the punching anisotropy. Fig. 5 is a graph showing the effect of the Si content and the P content on the relationship between the average crystal grain size and the iron loss. Fig. 6 is a graph showing the effect of the Si content and the P content on the relationship between the average crystal grain size and the magnetic flux density. Printed by the Intellectual Property Bureau of the Ministry of Economic Affairs, 8 Industrial Consumer Cooperatives. Figure 7 is a graph showing the effect of Si content and P content on the relationship between iron loss and magnetic flux density. Fig. 8 is a graph showing the effect of the Si content and the P content on the occurrence of lamellar cracking. Fig. 9 is a graph showing the effect of the Si content and the Ni content on the occurrence of lamellar cracking. Fig. 10 shows the content of si and the addition of Ni. For the content of P and the size of the paper, the Chinese national standard (CNS) A4 (210X297 mm) is applicable. -52- 555863 A7 B7 5. Description of the invention (50) And the quantity contains P in addition to • 1 N. Add pictures and lines. The line of the imitated curve i, the rhyme S, the display of the shadow, is the one of the first one of the shadow map. Chart 2 ο 1 Figure No. 2 Figure No. 1 Figure No. 2 Figure No. 4 Figure No. 2 Figure No. 2 Figure No. 4 Figure No. 2 Figure No. 4 (Please read the notes on the back and fill in this page) The paper size printed by the Ministry of Economic Affairs, Chi Tzu Choi / $ Bureau Consumer Cooperatives applies the Chinese National Standard (CNS) Α4 specification (210 × 297 mm) -53-
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US (2) | US20040149355A1 (en) |
EP (1) | EP1411138A4 (en) |
JP (1) | JP4329538B2 (en) |
KR (1) | KR100956530B1 (en) |
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2002
- 2002-06-27 JP JP2003508741A patent/JP4329538B2/en not_active Expired - Fee Related
- 2002-06-27 US US10/481,919 patent/US20040149355A1/en not_active Abandoned
- 2002-06-27 KR KR1020037002839A patent/KR100956530B1/en active IP Right Grant
- 2002-06-27 EP EP02738812A patent/EP1411138A4/en not_active Withdrawn
- 2002-06-27 WO PCT/JP2002/006458 patent/WO2003002777A1/en active Application Filing
- 2002-06-27 CN CNB028128907A patent/CN1318627C/en not_active Expired - Fee Related
- 2002-06-27 TW TW091114213A patent/TW555863B/en not_active IP Right Cessation
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2007
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Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
TWI672384B (en) * | 2017-03-30 | 2019-09-21 | 日商杰富意鋼鐵股份有限公司 | Method for manufacturing non-oriented electrical steel sheet, method for manufacturing motor core, and motor core |
US11136645B2 (en) | 2017-03-30 | 2021-10-05 | Jfe Steel Corporation | Method for producing non-oriented electrical steel sheet, method for producing motor core, and motor core |
Also Published As
Publication number | Publication date |
---|---|
EP1411138A1 (en) | 2004-04-21 |
KR20040014960A (en) | 2004-02-18 |
CN1520464A (en) | 2004-08-11 |
JP4329538B2 (en) | 2009-09-09 |
CN1318627C (en) | 2007-05-30 |
US20040149355A1 (en) | 2004-08-05 |
JPWO2003002777A1 (en) | 2004-10-21 |
KR100956530B1 (en) | 2010-05-07 |
EP1411138A4 (en) | 2005-01-12 |
WO2003002777A1 (en) | 2003-01-09 |
US20080060728A1 (en) | 2008-03-13 |
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