JPS62188756A - Grain-oriented foil of high saturation magnetic flux density and its production - Google Patents
Grain-oriented foil of high saturation magnetic flux density and its productionInfo
- Publication number
- JPS62188756A JPS62188756A JP61027991A JP2799186A JPS62188756A JP S62188756 A JPS62188756 A JP S62188756A JP 61027991 A JP61027991 A JP 61027991A JP 2799186 A JP2799186 A JP 2799186A JP S62188756 A JPS62188756 A JP S62188756A
- Authority
- JP
- Japan
- Prior art keywords
- magnetic flux
- flux density
- high saturation
- saturation magnetic
- rolling
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 230000004907 flux Effects 0.000 title claims abstract description 18
- 238000004519 manufacturing process Methods 0.000 title claims description 6
- 239000011888 foil Substances 0.000 title abstract 3
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 18
- 239000000956 alloy Substances 0.000 claims abstract description 18
- 238000005096 rolling process Methods 0.000 claims abstract description 18
- 229910052796 boron Inorganic materials 0.000 claims abstract description 10
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 10
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 9
- 239000000203 mixture Substances 0.000 claims abstract description 9
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 9
- 229910052715 tantalum Inorganic materials 0.000 claims abstract description 9
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 9
- 229910052785 arsenic Inorganic materials 0.000 claims abstract description 8
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 8
- 229910052718 tin Inorganic materials 0.000 claims abstract description 8
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 8
- 229910052725 zinc Inorganic materials 0.000 claims abstract description 8
- 229910052745 lead Inorganic materials 0.000 claims abstract description 7
- 229910052714 tellurium Inorganic materials 0.000 claims abstract description 7
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 7
- 229910052797 bismuth Inorganic materials 0.000 claims abstract description 6
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 6
- 239000000126 substance Substances 0.000 claims abstract description 6
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 6
- 229910052759 nickel Inorganic materials 0.000 claims abstract 5
- 229910052782 aluminium Inorganic materials 0.000 claims abstract 2
- 239000000463 material Substances 0.000 claims description 16
- 238000000137 annealing Methods 0.000 claims description 11
- 230000009467 reduction Effects 0.000 claims description 10
- 229910052717 sulfur Inorganic materials 0.000 claims description 9
- 229910052711 selenium Inorganic materials 0.000 claims description 8
- 238000005097 cold rolling Methods 0.000 claims description 7
- 229910052787 antimony Inorganic materials 0.000 claims description 5
- 239000013078 crystal Substances 0.000 claims description 3
- 230000035699 permeability Effects 0.000 abstract description 7
- 229910020598 Co Fe Inorganic materials 0.000 abstract description 6
- 229910002519 Co-Fe Inorganic materials 0.000 abstract description 6
- 229910001353 gamma loop Inorganic materials 0.000 abstract 1
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 14
- 238000000034 method Methods 0.000 description 9
- 239000002184 metal Substances 0.000 description 5
- 229910052751 metal Inorganic materials 0.000 description 5
- 238000005266 casting Methods 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 238000001953 recrystallisation Methods 0.000 description 4
- 238000002441 X-ray diffraction Methods 0.000 description 3
- 238000005098 hot rolling Methods 0.000 description 3
- 230000006872 improvement Effects 0.000 description 3
- 239000000047 product Substances 0.000 description 3
- 229910000831 Steel Inorganic materials 0.000 description 2
- 229910052799 carbon Inorganic materials 0.000 description 2
- 239000012467 final product Substances 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 239000010959 steel Substances 0.000 description 2
- 229910017061 Fe Co Inorganic materials 0.000 description 1
- 229910000640 Fe alloy Inorganic materials 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 239000003112 inhibitor Substances 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 239000000696 magnetic material Substances 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 230000008569 process Effects 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
Classifications
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
この発明は、エレクトロニクス機器のデバイスに用いら
れるトランス等をはじめとする磁性機器の素材としての
用途に供して好適な、一方向性で低鉄損を有する高飽和
磁束密度薄帯に関するものである。Detailed Description of the Invention (Field of Industrial Application) The present invention provides a unidirectional, low-iron iron material suitable for use as a material for magnetic equipment such as transformers used in devices of electronic equipment. The present invention relates to a high saturation magnetic flux density ribbon having loss.
（従来の技術）
近年、エレクトロニクスの発展に伴ってデバイスの軽薄
短小化が著しく進んでいる。従ってこのデバイスに組込
まれるトランスやチョーク類の小型化も併せて望まれて
いる。(Prior Art) In recent years, with the development of electronics, devices have become significantly smaller and lighter. Therefore, it is also desired to downsize the transformers and chokes incorporated into this device.
かかる要請に応じるためには、トランスやチョーク類の
動作磁束密度および動作周波数を高めることが肝要であ
る。In order to meet such demands, it is essential to increase the operating magnetic flux density and operating frequency of transformers and chokes.
デバイス用トランス等の素材としては、従来からＣｏ−
Ｆｅ系合金が知られている（例えば特開昭５７−１４５
９４５号公報）。Traditionally, Co-
Fe-based alloys are known (for example, JP-A-57-145
Publication No. 945).
（発明が解決しようとする問題点）
しかしながら従来のＣｏ−Ｆｅ系合金は、極めて脆く加
工性が悪かったために、薄板化が難しく、またたとえ薄
板化できたとしても著しい歩留りの低下を招いていた。(Problems to be solved by the invention) However, conventional Co-Fe alloys were extremely brittle and had poor workability, so it was difficult to make them into thin sheets, and even if they could be made into thin sheets, this caused a significant drop in yield. .
この発明は、上記の問題を有利に解決するもので、歩留
りの低下を招く不利なしに容易に薄板化が達成でき、し
かも軟磁気特性とくに透磁率および保磁力のより一層の
改善を可能ならしめた方向性高飽和磁束密度薄帯を、そ
の有利な製造方法と共に提案することを目的とする。The present invention advantageously solves the above-mentioned problems, and makes it possible to easily achieve thinner plates without the disadvantage of lowering yield, and further improves soft magnetic properties, particularly magnetic permeability and coercive force. The purpose of this invention is to propose a oriented high saturation magnetic flux density ribbon along with an advantageous manufacturing method thereof.
（問題点を解決するための手段）
Ｃｏ−Ｆｅ系合金を薄板化するに当って、圧延を利用す
る場合には、Ｃｏ−Ｆｅ系合金に特有の割れ易さを解決
する必要があるが、この点については、第３成分として
Ｔｉ、 Ｖ、 Ｃｒ、 Ｍｎ、 ｓｉ、 Ｚｒ、 Ｎｂ
、 Ｍｏ＋Ｓｎ、 Ｐｂ、 Ｚｎ、 Ｔａ、 Ｗ、 Ｎ
ｉ および八ｌのうちから選ばれる少なくとも一種を添
加すればじん性が向上し、もって加工性の改善を図り得
ることの知見を得た。(Means for solving the problem) When using rolling to thin a Co-Fe alloy, it is necessary to solve the susceptibility to cracking that is unique to the Co-Fe alloy. Regarding this point, as the third component, Ti, V, Cr, Mn, si, Zr, Nb
, Mo+Sn, Pb, Zn, Ta, W, N
It has been found that addition of at least one selected from i and 8l improves toughness and thereby improves workability.
また圧延によらず溶湯から直接薄帯を得る方法としてい
わゆる急冷薄帯化法が知られているが、この方法も有利
に適合することが判明した。In addition, a so-called rapid cooling ribbon forming method is known as a method for directly obtaining a ribbon from a molten metal without rolling, and it has been found that this method is also advantageously applicable.
さらに上記の如くして得られた薄帯に、さらに冷間圧延
を施すことによって効果的な一方向性化が導かれ、磁気
特性とくに透磁率の向上かもたらされることも併せて突
止めた。Furthermore, it has also been found that by subjecting the ribbon obtained as described above to further cold rolling, effective unidirectionality can be induced, leading to improvements in magnetic properties, particularly magnetic permeability.
この発明は、上記の知見に立脚するものである。This invention is based on the above knowledge.
すなわちこの発明は、下記の化学式（１）または（Ｉｆ
）で示される組成になり、結晶構造として（００１）軸
が圧延方向に揃った集合組織をそなえて成る方向性高飽
和磁束密度薄帯である。That is, this invention provides the following chemical formula (1) or (If
), and is a directional high saturation magnetic flux density ribbon having a crystal structure with a texture in which the (001) axis is aligned in the rolling direction.
記
（Ｆｅ＋−ａｃＯａ） ＋ ｏｏ−ｘＭｘ
−−（１）（Ｐｅ１−ａｃＯＪ ＋ ｏｏ−ｘ−ｙＭ
ｘ（ｌｙ ＝−−（ＩＩ ）ここでＭ ：
Ｔｉ、 Ｖ、 Ｃｒ、 Ｍｎ、 Ｓｉ、 Ｚｒ、 Ｎｂ
、 Ｍｏ、Ｓｎ、Ｐｂ、 Ｚｎ、 Ｔａ、 也りおよび
１１のうちから選んだ少なくとも一種
Ｑ ： Ｂ、 Ａｓ、 ＢｉおよびＴｅのうちから選
んだ少なくとも一種
ａ：Ｆｅに対するＣｏの原子比で０．２〜０．６
ｘ ： ０．０５〜１０．０ｗｔχ
ｙ ： ０．００１〜０．００１〜
０．６ｗｔ％またこの発明は、下記の化学式（ＩＩ［）
および（ＩＶ）で示される合金溶湯から、板材を作製し
、ついで４０〜９０％の圧下率で冷間圧延を施したのち
、直ちに７００〜１３００℃の温度範囲で焼鈍を施すこ
とから成る方向性高飽和磁束密度薄帯の製造方法である
。(Fe+-acOa) + oo-xMx
--(1) (Pe1-acOJ + oo-x-yM
x(ly =−−(II) where M:
Ti, V, Cr, Mn, Si, Zr, Nb
, Mo, Sn, Pb, Zn, Ta, and 11 Q: At least one selected from B, As, Bi, and Te a: Atomic ratio of Co to Fe is 0.2 ~0.6
A directional method consisting of producing a plate material from the molten alloy shown in This is a method for producing a high saturation magnetic flux density ribbon.
記
（Ｆｅｌ−ｉｃＯａ） ＋００−ｘ−ｙＭｘＱ ’ ｙ
’−’・ （Ｉ［［）（Ｆｆ３＋−ａｃＯ，）
１００−ｘ−ｙ−ＪｘＱ ’ ｙＣｚ ”’直■）ここ
でＭ ：Ｔｉ、 Ｖ、 Ｃｒ、 Ｍｎ、 Ｓｉ、 Ｚｒ
、 Ｎｂ、 Ｍｏ。Note (Fel-icOa) +00-x-yMxQ' y
'-'・ (I[[)(Ff3+-acO,)
100-x-y-JxQ' yCz '''Direct■) Here, M: Ti, V, Cr, Mn, Si, Zr
, Nb, Mo.
Ｓｎ＋Ｐｔｌ＋ Ｚｎ、 Ｔａ＋ Ｗ＋ ＮｉおよびＡ
Ｎのうらから選んだ少なくとも一種
Ｑ ’ ： Ｓ＋ Ｓｂ、 Ｂ＋ Ｓｅ、 Ａｓ、 Ｂ
ｉおよびＴｅのうちから選んだ少なくとも一種
ａ：Ｆｅに対するＣｏの原子比で０．２〜０．６ｘ：
０．０５〜１０．０ｗｔＸ
ｙ ： ０．００１〜０．００１〜
０．６ｗｔ％２ ： ０．００５〜０．０５ｗｔ％以
下この発明を具体的に説明する。Sn+Ptl+ Zn, Ta+ W+ Ni and A
At least one Q' selected from the back of N: S+ Sb, B+ Se, As, B
At least one selected from i and Te a: atomic ratio of Co to Fe 0.2 to 0.6x:
0.05-10.0wt
まずこの発明において成分組成を上記の範囲に限定した
理由について説明する。First, the reason why the component composition is limited to the above range in this invention will be explained.
Ｆｅに対するＣｏの原子比： ０．２〜０．にの発明で
は、飽和磁束密度Ｂｓが高いＣｏ−Ｆｅ系合金の中でも
Ｂｓ≧２．２テスラ（Ｔ）以上の高飽和磁束密度のもの
を対象とするが、Ｆｅに対するＣｏの原子比が０．２に
満たなかったり０．６を超えた場合には、２．２Ｔ以上
の高飽和磁束密度が得られないので上記の範囲に限定し
た。Atomic ratio of Co to Fe: 0.2-0. The invention targets Co--Fe based alloys with a high saturation magnetic flux density Bs≧2.2 Tesla (T) or higher among Co-Fe alloys with a high saturation magnetic flux density Bs, but the atomic ratio of Co to Fe is 0. If it is less than 2 or exceeds 0.6, a high saturation magnetic flux density of 2.2T or more cannot be obtained, so it is limited to the above range.
Ｍ ： ０．０５〜１０．０ｗｔＸ （以下単ニ％テ示
す）記号Ｍで示されるＴｉ＋ Ｖ＋ Ｃｒ、 Ｓ＋＋
Ｚｒ、Ｎｂ＋ Ｍｎ。M: 0.05 to 10.0wtX (hereinafter referred to as single %) Ti+ V+ Cr, S++ shown by the symbol M
Zr, Nb+Mn.
Ｓｎ、 ｐｂ、 Ｚｎ、 Ｔａ＋ Ｉ’ｌ＋ Ｍｏ、
ＮｉおよびＡＮはいずれも、γループを形成または開放
する元素であって、じん性ひいては加工性を改善する点
において同効である。しかしながら含有量が０．０５％
に満たないとその添加効果に乏しく、一方１０．０％を
超えると飽和磁束密度の劣化を招くので、単独添加また
は複合添加いずれの場合であっても０．０５〜１０．０
％の範囲で含有させるものとした。Sn, pb, Zn, Ta+ I'l+ Mo,
Both Ni and AN are elements that form or open γ loops, and are equally effective in improving toughness and thus processability. However, the content is 0.05%
If it is less than 10.0%, the effect of the addition will be poor, while if it exceeds 10.0%, the saturation magnetic flux density will deteriorate.
%.
Ｑ ’ ： ０．００１〜０．６％
記号Ｑ′で示されるＳ、 Ｓｂ、 Ｂ＋ Ｓｅ、 Ａｓ
＋ ＢｉおよびＴｅはいずれも、鋼中に微細に分散する
ことによって、焼鈍時における一次再結晶粒の正常成長
を効果的に抑制するいわゆるインヒビターとして有用な
元素であり、特定方位の２次再結晶粒の優先成長の促進
に有効に寄与する点において同効である。Q': 0.001~0.6% S, Sb, B+ Se, As indicated by symbol Q'
+ Both Bi and Te are elements that are useful as so-called inhibitors that effectively suppress the normal growth of primary recrystallized grains during annealing by finely dispersing them in steel, and they also inhibit secondary recrystallization in specific orientations. They are equally effective in contributing effectively to the promotion of preferential growth of grains.
しかしながら添加量がｏ、ｏｏｉ％に満たないとその添
加効果に乏しく、一方０．６％を超えると析出物が粗大
化して粒成長抑制力が劣化する等の不利があるので、単
独添加または複合添加いずれの場合においても０．００
１〜０．６％の範囲で添加することにした。However, if the amount added is less than o or ooi%, the effect of the addition will be poor, while if it exceeds 0.6%, there will be disadvantages such as coarsening of precipitates and deterioration of grain growth suppressing power. 0.00 in either case of addition
It was decided to add it in a range of 1 to 0.6%.
なおＱ′中、Ｓ、Ｓｅおよびｓｂは焼鈍処理中に合金中
から揮散するので、合金中にはＢ、 Ａｓ＋ Ｂ＋およ
びＴｅすなわち記号Ｑで示される元素群のうちから選ば
れる少なくとも一種が残存することになる。Note that in Q', S, Se, and sb are volatilized from the alloy during the annealing process, so at least one selected from the group of elements represented by B, As+, B+, and Te, that is, the symbol Q, remains in the alloy. It turns out.
Ｃ： ０．００５〜０．０５％
Ｃは、圧延時に鋼中の転位を集積させて再結晶時の粒径
を微細化すると共に、組織の一方向性化を図る上で有利
な元素であるが、含有量が０．００５％に満たないと転
位のタンプリング効果が不十分となって組織の一方向性
化の達成が難しく、一方０．０５％を超えると脆くなっ
て加工性の劣化を招くので、添加量は０．００５〜０．
０５％の範囲に限定した。C: 0.005-0.05% C is an element that is advantageous in accumulating dislocations in the steel during rolling to refine the grain size during recrystallization and to make the structure unidirectional. However, if the content is less than 0.005%, the tampling effect of dislocations will be insufficient and it will be difficult to achieve a unidirectional structure, while if it exceeds 0.05%, it will become brittle and deteriorate workability. The amount added is 0.005 to 0.
It was limited to a range of 0.05%.
なおこのＣも上掲したＳやＳｅ、 Ｓｂ同様、焼鈍中に
揮散するので最終製品中に残存することはない。Note that like S, Se, and Sb listed above, this C also volatilizes during annealing, so it does not remain in the final product.
次にこの発明に従う製造方法について説明する。Next, a manufacturing method according to the present invention will be explained.
まず上記した如き好適成分組成に調製した溶湯から、板
材を作製するわけであるが、かかる板材の作製に当って
は、従来の造塊−分塊圧延一熱間圧延法および溶湯から
直接に製仮にする単ロール法や双ロール法などの急冷薄
帯化法いずれもが使用できる。First, a plate material is produced from a molten metal prepared to have a suitable composition as described above. In producing such a plate material, the conventional ingot-blurring-rolling-hot rolling method and direct production from the molten metal are used. Any quenching method such as a single roll method or a twin roll method can be used.
上記の如くして得られた板材に４０〜９０％の圧下率で
冷間圧延を施す。ここに冷延圧下率を４０〜９０％の範
囲に限定したのは、４０％未満では十分満足のいく一方
向性化ひいては磁気特性の改善が望み得す、一方９０％
を超えるとかえって尖鋭化した方位の分散化を招きやは
り良好な磁気特性の向上は期待できないからである。The plate material obtained as described above is cold rolled at a rolling reduction of 40 to 90%. The reason why the cold rolling reduction ratio is limited to the range of 40 to 90% is that if it is less than 40%, it is possible to achieve satisfactory unidirectionality and eventually improve the magnetic properties, while if it is less than 40%,
This is because if it exceeds this value, it will instead lead to the dispersion of sharpened orientations, and good improvement in magnetic properties cannot be expected.
次にかかる冷延板に焼鈍処理を施して、圧延により尖鋭
化した特定方位粒の優先的な２次再結晶を促すが、この
とき処理温度が７００℃に満たないと再結晶に長時間を
要し生産性の点で好ましくなく、一方１３００℃を超え
ると成分系によっては表面が溶融する場合もあるので、
焼鈍温度は７００〜１３００″Ｃの範囲に限定した。Next, the cold-rolled sheet is subjected to an annealing treatment to promote preferential secondary recrystallization of grains with specific orientations sharpened by rolling. However, if the treatment temperature is lower than 700°C, recrystallization takes a long time. On the other hand, if the temperature exceeds 1300°C, the surface may melt depending on the component system.
The annealing temperature was limited to a range of 700-1300''C.
なお上記の冷間圧延に先立ち又は圧延中に、７００〜１
３００”Ｃの温度範囲で焼鈍を施すこともでき、かかる
焼鈍処理によって磁気特性のより一層の向上がもたらさ
れる。In addition, prior to or during the above cold rolling, 700 to 1
Annealing can also be performed in the temperature range of 300''C, and such annealing treatment provides further improvement in magnetic properties.
（作 用）
この発明に従い、板材作製後、高圧下率の下で冷間圧延
を施すことによって効果的な一方向性化が達成でき、磁
気特性とくに透磁率の向上を図り得る。(Function) According to the present invention, effective unidirectionality can be achieved by performing cold rolling under a high rolling reduction rate after producing a plate material, and it is possible to improve magnetic properties, particularly magnetic permeability.
この点、従来のＦｅ−Ｃｏ系合金は脆いこともあってほ
とんど冷延加工を受けることがなく、またかりに冷間圧
延を施す場合であっても、かような冷間圧延は板厚を若
干減少させるために施されるもので、合金組織の方向性
化のために行われるものではなかった。In this regard, conventional Fe-Co alloys are brittle and are rarely subjected to cold rolling, and even when they are cold rolled, such cold rolling requires a slight reduction in sheet thickness. It was performed to reduce the grain size, and was not performed to orient the alloy structure.
（実施例）
大流■上
下表１に示される合金成分を鋳造後、加熱、熱延を施し
て２．Ｏｔｍ厚の熱延板としたのち、９００℃で焼鈍し
てから圧下率７０％の冷延を施しさらに９５０℃で焼鈍
を加えた。その後この板材に対して６８％の圧下率で冷
間圧延を施して最終板厚としたのち、１１８０℃で最終
焼鈍を施した。(Example) After casting the alloy components shown in Tables 1 and 2, heating and hot rolling were performed. After forming a hot-rolled sheet with a thickness of Otm, it was annealed at 900°C, cold-rolled at a rolling reduction of 70%, and further annealed at 950°C. Thereafter, this plate material was cold rolled at a reduction rate of 68% to obtain the final thickness, and then final annealed at 1180°C.
このようにして得られた製品薄帯の磁気特性について調
べた結果を同表に示す。なお最終製品組成では下表中の
Ｓｅ、 Ｓは含まれない。The results of an investigation of the magnetic properties of the product ribbon thus obtained are shown in the same table. Note that Se and S in the table below are not included in the final product composition.
また適合例においては、Ｃ００Ｌ）軸が圧延方向に従来
例より揃っていることがＸ線回折により確かめられた。Furthermore, in the conforming example, it was confirmed by X-ray diffraction that the C00L) axis was more aligned in the rolling direction than in the conventional example.
天屓ｌ岨λ
Ｃｏ： ４９χ、ｖ：２χを含み、残部Ｆｅの組成にな
る溶湯に、Ｃ： ０．０３χ、 Ｍｎ： ０．０６％お
よびＳ： ０．０３％を添加配合した合金溶湯を、鋳造
ついで熱間圧延を施して２．０龍厚の熱延板としたのち
、９００℃で焼鈍してから圧下率：５０％の冷間圧延を
施し、さらに９５０″Ｃで焼鈍を施した。An alloy molten metal was prepared by adding C: 0.03χ, Mn: 0.06% and S: 0.03% to a molten metal containing Co: 49χ, v: 2χ, and the balance Fe. After casting and hot rolling to obtain a hot rolled sheet with a thickness of 2.0 mm, it was annealed at 900°C, cold rolled at a rolling reduction of 50%, and further annealed at 950°C. .
その後この板材に対し、６５％の圧下率で冷間圧延を施
して最終板厚としたのち、８５０℃で脱炭焼鈍ついで１
１５０℃で最終焼鈍を施した。After that, this plate material was cold rolled at a reduction rate of 65% to obtain the final thickness, and then decarburized and annealed at 850°C.
Final annealing was performed at 150°C.
かくして得られた製品薄帯の磁気特性について調べた結
果を、従来の単なる鋳造法により得られたＣＯ４，Ｖｚ
Ｆｅ材丸棒材料棒試料と比較して下表２に示す。The results of investigating the magnetic properties of the thus obtained product ribbon were compared to CO4, Vz obtained by a conventional simple casting method.
A comparison with the Fe material round bar material bar sample is shown in Table 2 below.
同表より明らかなように、この発明に従い得ら ゛れ
たＣｏ−Ｆｅ系合金は、従来材に較べて、飽和磁束密度
はほぼ等しいものの、最大透磁率、保磁力および残留磁
束密度は格段に改善されている。As is clear from the table, the Co-Fe alloy obtained according to the present invention has approximately the same saturation magnetic flux density as the conventional material, but the maximum magnetic permeability, coercive force, and residual magnetic flux density are significantly higher. It has been improved.
またＸ線回折により、この発明に従うＣｏ−Ｆｅ系合金
薄帯はＣｏｏｌ）軸が圧延方向に高度に揃っていること
が確かめられた。Furthermore, it was confirmed by X-ray diffraction that the Co--Fe alloy ribbon according to the present invention had its Cool axis highly aligned in the rolling direction.
失施炭ユ
Ｃｏ ： ３５％、Ｃｒ：１．０％、Ｍｏ：１．０％を
含み、かつＣ： ０．０３５％、 Ｍｎ ： ０．０６
５％、 Ｓｅ ： ０．０２５％およびＢ ： ０．０
０３％を含有し、残部実質的にＦｅになる組成の合金溶
湯を、高速で回転する双ロールのロールキス部に連続し
て供給し、急冷凝固させて、０．５龍厚の急冷薄帯を作
製した。ついでこの板材に対して圧下率８０％の冷間圧
延を施したのぢ、８５０℃の脱炭焼鈍ついで１１５０℃
における最終焼鈍を施した。Contains unused Co: 35%, Cr: 1.0%, Mo: 1.0%, and C: 0.035%, Mn: 0.06
5%, Se: 0.025% and B: 0.0
A molten alloy having a composition of 0.3% and the remainder being substantially Fe is continuously supplied to the roll kiss section of twin rolls rotating at high speed, and is rapidly solidified to form a quenched ribbon with a thickness of 0.5 mm. Created. This plate material was then cold rolled at a reduction rate of 80%, decarburized at 850°C, and then decarburized at 1150°C.
Final annealing was performed at .
かくして得られた製品薄帯の磁気特性について調べた結
果を、従来の単なる鋳造法により得られたＣ０１ｓＣｒ
＋、。Ｍｏ＋、。Ｆｅ九丸棒料の場合と比較してＴ１３
に示す。The results of investigating the magnetic properties of the thus obtained product ribbon were compared to C01sCr obtained by a conventional simple casting method.
+,. Mo+,. T13 compared to the case of Fe nine-round bar charge
Shown below.
同表に示したとおり、この発明に従い得られたものは、
従来材に較べて残留磁束密度、保磁力および最大透磁率
が路間に改善されている。As shown in the table, what was obtained according to this invention was:
Compared to conventional materials, residual magnetic flux density, coercive force, and maximum magnetic permeability are improved between the tracks.
また適合例においては、（００１）軸が圧延方向に高度
に揃っていることがＸ線回折により確められた。In addition, in the conforming example, it was confirmed by X-ray diffraction that the (001) axis was highly aligned in the rolling direction.
（発明の効果）
かくしてこの発明によれば、じん性に冨み、しかも軟磁
気特性とくに透磁率および保磁力に優れた高飽和磁束密
度薄帯を容易に得ることができ、従って磁性材料ひいて
はエレクトロニクス機器の小型化、軽量化等に大きく貢
献する。(Effects of the Invention) Thus, according to the present invention, it is possible to easily obtain a high saturation magnetic flux density ribbon that is rich in toughness and has excellent soft magnetic properties, especially magnetic permeability and coercive force, and is therefore useful for magnetic materials and electronics. This greatly contributes to making equipment smaller and lighter.
Claims (1)
０＿−＿ｘＭ＿ｘここでＭ：Ｔｉ、Ｖ、Ｃｒ、Ｍｎ、Ｓ
ｉ、Ｚｒ、Ｎｂ、Ｍｏ、Ｓｎ、Ｐｂ、Ｚｎ、Ｔａ、Ｗ、
Ｎｉおよび Ａｌのうちから選んだ少なくとも 一種 ａ：Ｆｅに対するＣｏの原子比で０．２〜０．６ｘ：０
．０５〜１０．０ｗｔ％ で示される組成になり、結晶構造として 〔００１〕軸が圧延方向に揃った集合組織を有すること
を特徴とする方向性高飽和磁束密度薄帯。 ２、化学式：（Ｆｅ＿１＿−＿ａＣｏ＿ａ）＿１＿０＿
０＿−＿ｘ＿−＿ｙＭ＿ｘＱ＿ｙここでＭ：Ｔｉ、Ｖ、
Ｃｒ、Ｍｎ、Ｓｉ、Ｚｒ、Ｎｂ、Ｍｏ、Ｓｎ、Ｐｂ、Ｚ
ｎ、Ｔａ、Ｗ、Ｎｉおよび Ａｌのうちから選んだ少なくとも 一種 Ｑ：Ｂ、Ａｓ、ＢｉおよびＴｅのうちから選んだ少なく
とも一種 ａ：Ｆｅに対するＣｏの原子比で０．２〜０．６ｘ：０
．０５〜１０．０ｗｔ％ ｙ：０．００１〜０．６ｗｔ％ で示される組成になり、結晶構造として 〔００１〕軸が圧延方向に揃った集合組織を有すること
を特徴とする方向性高飽和磁束密度薄帯。 ３、化学式：（Ｆｅ＿１＿−＿ａＣｏ＿ａ）＿１＿０＿
０＿−＿ｘ＿−＿ｙＭ＿ｘＱ’＿ｙここでＭ：Ｔｉ、Ｖ
、Ｃｒ、Ｍｎ、Ｓｉ、Ｚｒ、Ｎｂ、Ｍｏ、Ｓｎ、Ｐｂ、
Ｚｎ、Ｔａ、Ｗ、Ｎｉおよび Ａｌのうちから選んだ少なくとも 一種 Ｑ’：Ｓ、Ｓｂ、Ｂ、Ｓｅ、Ａｓ、ＢｉおよびＴｅのう
ちから選んだ少なくとも 一種 ａ：Ｆｅに対するＣｏの原子比で０．２〜 ０．６ ｘ：０．０５〜１０．０ｗｔ％ ｙ：０．００１〜０．６ｗｔ％ で示される組成になる合金溶湯から、板材を作製し、つ
いで４０〜９０％の圧下率で冷間圧延を施したのち、直
ちに７００〜１３００℃の温度範囲で焼鈍を施すことを
特徴とする方向性高飽和磁束密度薄帯の製造方法。 ４、化学式： （Ｆｅ＿１＿−＿ａＣｏ＿ａ）＿１＿０＿０＿−＿ｘ＿
−＿ｙ＿−＿ｚＭ＿ｘＱ’＿ｙＣ＿ｚここでＭ：Ｔｉ、
Ｖ、Ｃｒ、Ｍｎ、Ｓｉ、Ｚｒ、Ｎｂ、Ｍｏ、Ｓｎ、Ｐｂ
、Ｚｎ、Ｔａ、Ｗ、ＮｉおよびＡｌのうちから選んだ少
なくとも 一種 Ｑ’：Ｓ、Ｓｂ、Ｂ、Ｓｅ、Ａｓ、ＢｉおよびＴｅのう
ちから選んだ少なくと も一種 ａ：Ｆｅに対するＣｏの原子比で０．２〜 ０．６ ｘ：０．０５〜１０．０ｗｔ％ ｙ：０．００１〜０．６ｗｔ％ ｚ：０．００５〜０．０５ｗｔ％ で示される組成になる合金溶湯から、板材を作製し、つ
いで４０〜９０％の圧下率で冷間圧延を施したのち、直
ちに７００〜１３００℃の温度範囲で焼鈍を施すことを
特徴とする方向性高飽和磁束密度薄帯の製造方法。[Claims] 1. Chemical formula: (Fe_1_-_aCo_a)_1_0_
0_-_xM_x where M: Ti, V, Cr, Mn, S
i, Zr, Nb, Mo, Sn, Pb, Zn, Ta, W,
At least one selected from Ni and Al a: atomic ratio of Co to Fe 0.2 to 0.6x:0
．． A oriented high saturation magnetic flux density ribbon having a composition of 05 to 10.0 wt% and having a crystal structure with a [001] axis aligned in the rolling direction. 2. Chemical formula: (Fe_1_-_aCo_a)_1_0_
0_-_x_-_yM_xQ_y where M: Ti, V,
Cr, Mn, Si, Zr, Nb, Mo, Sn, Pb, Z
At least one selected from n, Ta, W, Ni and Al Q: At least one selected from B, As, Bi and Te a: Atomic ratio of Co to Fe 0.2 to 0.6 x: 0
．． A directional high saturation magnetic flux having a composition of 05 to 10.0 wt% y: 0.001 to 0.6 wt%, and having a texture in which the [001] axis is aligned in the rolling direction as a crystal structure. Density ribbon. 3. Chemical formula: (Fe_1_-_aCo_a)_1_0_
0_-_x_-_yM_xQ'_y where M: Ti, V
, Cr, Mn, Si, Zr, Nb, Mo, Sn, Pb,
At least one selected from Zn, Ta, W, Ni, and Al Q': At least one selected from S, Sb, B, Se, As, Bi, and Te a: The atomic ratio of Co to Fe is 0. A plate material is produced from a molten alloy having a composition shown by 1. A method for producing a oriented high saturation magnetic flux density ribbon, which comprises performing inter-rolling and then immediately annealing in a temperature range of 700 to 1300°C. 4. Chemical formula: (Fe_1_-_aCo_a)_1_0_0_-_x_
-_y_-_zM_xQ'_yC_z where M: Ti,
V, Cr, Mn, Si, Zr, Nb, Mo, Sn, Pb
, Zn, Ta, W, Ni and Al Q': at least one selected from S, Sb, B, Se, As, Bi and Te a: atomic ratio of Co to Fe is 0 .2 to 0.6 x: 0.05 to 10.0 wt% y: 0.001 to 0.6 wt% z: 0.005 to 0.05 wt% A plate material is produced from a molten alloy having the composition shown. , followed by cold rolling at a reduction rate of 40 to 90%, followed by immediately annealing at a temperature range of 700 to 1300°C.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61027991A JPS62188756A (en) | 1986-02-13 | 1986-02-13 | Grain-oriented foil of high saturation magnetic flux density and its production |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61027991A JPS62188756A (en) | 1986-02-13 | 1986-02-13 | Grain-oriented foil of high saturation magnetic flux density and its production |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS62188756A true JPS62188756A (en) | 1987-08-18 |
Family
ID=12236290
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP61027991A Pending JPS62188756A (en) | 1986-02-13 | 1986-02-13 | Grain-oriented foil of high saturation magnetic flux density and its production |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS62188756A (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH02298219A (en) * | 1989-05-13 | 1990-12-10 | Nippon Steel Corp | Production of thin grain-oriented silicon steel sheet having high magnetic flux density and excellent in iron loss |
| US9028625B2 (en) | 2004-10-21 | 2015-05-12 | Nippon Steel Materials Co., Ltd. | High Al-content steel sheet excellent in workability and method of production of same |
| WO2018091694A1 (en) * | 2016-11-18 | 2018-05-24 | Vacuumschmelze Gmbh & Co. Kg | Method for producing a strip from a cofe alloy, and semi-finished product containing said strip |
| CN110551885A (en) * | 2018-06-04 | 2019-12-10 | 武汉尚瑞科技有限公司 | Novel high-magnetic-induction oriented silicon steel normalized cooling production method and product |
-
1986
- 1986-02-13 JP JP61027991A patent/JPS62188756A/en active Pending
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH02298219A (en) * | 1989-05-13 | 1990-12-10 | Nippon Steel Corp | Production of thin grain-oriented silicon steel sheet having high magnetic flux density and excellent in iron loss |
| US9028625B2 (en) | 2004-10-21 | 2015-05-12 | Nippon Steel Materials Co., Ltd. | High Al-content steel sheet excellent in workability and method of production of same |
| US9616411B2 (en) | 2004-10-21 | 2017-04-11 | Nippon Steel & Sumkin Materials Co., Ltd. | High Al-content steel sheet excellent in workability and method of production of same |
| WO2018091694A1 (en) * | 2016-11-18 | 2018-05-24 | Vacuumschmelze Gmbh & Co. Kg | Method for producing a strip from a cofe alloy, and semi-finished product containing said strip |
| CN110551885A (en) * | 2018-06-04 | 2019-12-10 | 武汉尚瑞科技有限公司 | Novel high-magnetic-induction oriented silicon steel normalized cooling production method and product |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP2012046806A (en) | Method for manufacturing non-oriented electromagnetic steel sheet | |
| US20220042135A1 (en) | Oriented electrical steel sheet and manufacturing method thereof | |
| JPH10259424A (en) | Production of silicon-chromium grain-oriented silicon steel | |
| JPS625972B2 (en) | ||
| EP0374948B1 (en) | Very thin electrical steel strip having low core loss and high magnetic flux density and a process for producing the same | |
| KR920004678B1 (en) | METHOD FOR MANUFACTURING Ni-Fe ALLOY SHEET HAVING EXCELLENT DC MAGNETIC PROPERTY AND EXCELLENT AC MAGNETIC PROPERTY | |
| JP2639227B2 (en) | Manufacturing method of non-oriented electrical steel sheet | |
| JPS6212296B2 (en) | ||
| JPS62188756A (en) | Grain-oriented foil of high saturation magnetic flux density and its production | |
| JP2787776B2 (en) | Manufacturing method of grain-oriented electrical steel sheet with excellent magnetic properties | |
| JPS5924177B2 (en) | Square hysteresis magnetic alloy | |
| JPH076046B2 (en) | Method for producing Ni-Fe alloy plate having excellent magnetic properties | |
| JP2898793B2 (en) | Method for producing non-oriented electrical steel sheet having high magnetic flux density and low iron loss | |
| JPS58150119A (en) | Alloy having high magnetic permeability for magnetic recording and reproducing head and its production, and magnetic recording and reproducing head | |
| JP3498978B2 (en) | Manufacturing method of grain-oriented electrical steel sheet with extremely low iron loss | |
| JPH07110974B2 (en) | Method for producing directional silicon iron alloy ribbon | |
| JPS6218619B2 (en) | ||
| US3761253A (en) | Steel for electrical applications and novel article | |
| JPS5814499B2 (en) | Kakugata Hysteresis Jisei Gokin Oyobi Sonoseizouhouhou | |
| JPS6155583B2 (en) | ||
| JPH07197126A (en) | Production of grain oriented silicon steel sheet having high magnetic flux density | |
| JPS6134160A (en) | Wear resistant and high magnetic permeability alloy for magnetic record regenerating head, its manufacture and magnetic record regenerating head | |
| JPH05186829A (en) | Production of grain-oriented silicon steel sheet having crystal orientation integrated in goss orientation | |
| JPS6130405B2 (en) | ||
| JPH05186831A (en) | Production of grain-oriented silicon steel sheet having crystal orientation integrated in goss orientation |