JPS58100659A - Wound iron core - Google Patents
Wound iron coreInfo
- Publication number
- JPS58100659A JPS58100659A JP56196894A JP19689481A JPS58100659A JP S58100659 A JPS58100659 A JP S58100659A JP 56196894 A JP56196894 A JP 56196894A JP 19689481 A JP19689481 A JP 19689481A JP S58100659 A JPS58100659 A JP S58100659A
- Authority
- JP
- Japan
- Prior art keywords
- wound core
- wound
- magnetic field
- amorphous
- core
- 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.)
- Granted
Links
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical group [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 title abstract description 5
- 229910000808 amorphous metal alloy Inorganic materials 0.000 claims abstract description 9
- 238000001816 cooling Methods 0.000 claims abstract description 8
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 7
- 239000000956 alloy Substances 0.000 claims abstract description 7
- 239000000203 mixture Substances 0.000 claims abstract description 6
- 229910052779 Neodymium Inorganic materials 0.000 claims abstract description 4
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 4
- 229910052735 hafnium Inorganic materials 0.000 claims abstract description 4
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 4
- 230000035699 permeability Effects 0.000 claims abstract description 4
- 229910052707 ruthenium Inorganic materials 0.000 claims abstract description 4
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 4
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 4
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 4
- 229910052777 Praseodymium Inorganic materials 0.000 claims abstract description 3
- 229910052788 barium Inorganic materials 0.000 claims abstract description 3
- 229910052790 beryllium Inorganic materials 0.000 claims abstract description 3
- 229910052749 magnesium Inorganic materials 0.000 claims abstract description 3
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 3
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 3
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 3
- 229910052715 tantalum Inorganic materials 0.000 claims abstract description 3
- 229910052727 yttrium Inorganic materials 0.000 claims abstract description 3
- 229910052725 zinc Inorganic materials 0.000 claims abstract description 3
- 229910052693 Europium Inorganic materials 0.000 claims abstract 2
- 229910052688 Gadolinium Inorganic materials 0.000 claims abstract 2
- 229910052772 Samarium Inorganic materials 0.000 claims abstract 2
- 229910052791 calcium Inorganic materials 0.000 claims abstract 2
- 238000004804 winding Methods 0.000 claims description 4
- 229910052771 Terbium Inorganic materials 0.000 abstract description 3
- 229910052763 palladium Inorganic materials 0.000 abstract description 3
- 229910052802 copper Inorganic materials 0.000 abstract description 2
- 229910052719 titanium Inorganic materials 0.000 abstract description 2
- 229910052684 Cerium Inorganic materials 0.000 abstract 1
- 229910052692 Dysprosium Inorganic materials 0.000 abstract 1
- 229910008423 Si—B Inorganic materials 0.000 abstract 1
- 229910052712 strontium Inorganic materials 0.000 abstract 1
- 239000011162 core material Substances 0.000 description 27
- 230000005284 excitation Effects 0.000 description 14
- 229910000889 permalloy Inorganic materials 0.000 description 6
- 230000000694 effects Effects 0.000 description 5
- 229910000815 supermalloy Inorganic materials 0.000 description 5
- 239000000463 material Substances 0.000 description 4
- 230000004907 flux Effects 0.000 description 3
- 230000035945 sensitivity Effects 0.000 description 3
- 239000000654 additive Substances 0.000 description 2
- 230000000996 additive effect Effects 0.000 description 2
- 238000000137 annealing Methods 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 239000000470 constituent Substances 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 230000001771 impaired effect Effects 0.000 description 2
- 229910000976 Electrical steel Inorganic materials 0.000 description 1
- 239000003513 alkali Substances 0.000 description 1
- 238000005280 amorphization Methods 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 230000007613 environmental effect Effects 0.000 description 1
- 238000005755 formation reaction Methods 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 230000003993 interaction Effects 0.000 description 1
- 230000005389 magnetism Effects 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 229910052752 metalloid Inorganic materials 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 230000008569 process Effects 0.000 description 1
Landscapes
- Heat Treatment Of Articles (AREA)
- Iron Core Of Rotating Electric Machines (AREA)
Abstract
Description
【発明の詳細な説明】
本発明は、高透磁率合金薄板を巻回してなる励磁電流特
性の良好な巻鉄心に関するものである。DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a wound core with good excitation current characteristics, which is formed by winding a high magnetic permeability alloy thin plate.
磁気移相器、磁気増幅器、直流電流検出器、磁気変調器
などには、例えば、異方性so%Niパーマロイ、スー
パーマロイ、方向性ケイ素鋼などから成る巻鉄心が使用
されている。これら従来の巻鉄心は、励磁電流特性に優
れ、また飽和までの急峻性が大きいことで知られている
が、近年より小さい電流による励磁、飽和電圧の増加、
飽和に至る急峻なI−V特性が求められている。For magnetic phase shifters, magnetic amplifiers, DC current detectors, magnetic modulators, etc., wound cores made of, for example, anisotropic SO%Ni permalloy, supermalloy, grain-oriented silicon steel, etc. are used. These conventional wound cores are known for their excellent excitation current characteristics and their steepness until saturation.
A steep IV characteristic that reaches saturation is required.
また、従来の鉄心のうち、特に5oNiパーマロイ、ス
ーパーマロイ等のパーマロイ系鉄心ハ、構成材料の歪感
受性が大きいために、運搬、輸送、巻線などの作業の際
に、機械的歪による磁気特性の劣化が著しく、巻鉄心と
しての所要機能、電気的平衡を損なうなど大きな欠点を
有している。加うるに、これら従来の巻鉄心構成材料を
製造するKは、溶解、造塊、熱間圧延、酸洗、冷間圧延
などの複雑で周到な工程を必要とするため、巻鉄心の価
格を高価なものとしていた。In addition, among conventional iron cores, especially permalloy iron cores such as 5oNi permalloy and supermalloy, the magnetic properties due to mechanical strain during transportation, transportation, winding, etc. are high due to the high strain sensitivity of the constituent materials. It has major drawbacks, such as significant deterioration of the core, impairing the required functions as a wound core and electrical balance. In addition, K to manufacture these conventional wound core constituent materials requires complicated and detailed processes such as melting, ingot formation, hot rolling, pickling, and cold rolling, which makes the wound core less expensive. It was considered expensive.
本発明は、上記従来技術の欠点を解消し、励磁電流特性
、歪感受性、耐衝撃性に優れ、より安価な巻鉄心を提供
するこ七を目的とする。The object of the present invention is to eliminate the drawbacks of the above-mentioned prior art and to provide a wound core that is excellent in excitation current characteristics, strain sensitivity, and impact resistance, and is less expensive.
上記目的を達成するために本発明は、巻鉄心を構成する
高透磁率合金薄板としてFe−Co−8t−B系の非晶
質合金薄板を用いたことを特徴とするものである。In order to achieve the above object, the present invention is characterized in that an Fe-Co-8t-B based amorphous alloy thin plate is used as a high magnetic permeability alloy thin plate constituting the wound core.
本願発明者らは、式F @ 4 CO@ T (S i
g B h(式中TはBe、Mg、 0m%8rSB
a%Ti、Zr、 Hf、 V、 Nb。The inventors have developed the formula F @ 4 CO @ T (S i
g B h (in the formula, T is Be, Mg, 0m%8rSB
a%Ti, Zr, Hf, V, Nb.
Ta% Cr、Me、W、Mn% Ru、NiS Pd
、Cu、Zn、Y。Ta% Cr, Me, W, Mn% Ru, NiS Pd
, Cu, Zn, Y.
Co、Pr、 Nd、 amlEts、G(1%Tb、
D7 のうちの1種または2種以上であシ、d+・
+f+g+h=100)で示される非晶質合金、特に上
記式において、72≦d+・≦85、(L70≦−/d
十、≦α99、O≦f≦5.7 (g (16,7(h
(10,15≦g十h≦25なる条件を満足する非晶質
合金を磁場中で焼なまし、冷却したものを用いて巻鉄心
を構成すると優れた励磁電流特性が得られることを見出
し、本発明を完成したものである。Co, Pr, Nd, amlEts, G (1%Tb,
D7 One or more of the following, d+・
+f+g+h=100), especially in the above formula, 72≦d+・≦85, (L70≦−/d
10, ≦α99, O≦f≦5.7 (g (16,7(h
(We discovered that excellent excitation current characteristics can be obtained by constructing a wound core using an amorphous alloy that satisfies the following conditions: 10,15≦g1h≦25, annealed in a magnetic field and cooled. This completes the present invention.
本発明において、非晶質形成元素であるSlとBの総和
が15原子−(以下単に−と記す)未満では非晶質化そ
のものが困離とな?)、2s%をこえると磁束密度の低
下をきたすので、15〜25−とする。非晶質形成元素
として他の半金属元素、たとえばC,P、 G@、Bi
、ムlが知られているが、熱的安定性および靭性の点で
81とBとの組合せが優れている。C%P、 G・、B
i、 AIを含んでいても特に本発明の効果を大きく損
なうことはないが、5−以下であることが望ましい。In the present invention, if the total of Sl and B, which are amorphous forming elements, is less than 15 atoms (hereinafter simply referred to as -), it is difficult to form the amorphous state itself. ), if it exceeds 2s%, the magnetic flux density will decrease, so it is set to 15 to 25-. Other metalloid elements as amorphous forming elements, such as C, P, G@, Bi
, ml are known, but the combination of 81 and B is superior in terms of thermal stability and toughness. C%P, G.,B
Although the effects of the present invention are not significantly impaired even if AI is contained, it is desirable that the content be 5- or less.
Bの含有量は7q4未満では非晶質化が困−であシ、1
〇−以上では耐環境特性、たとえば耐湿性、耐アルカリ
性が大巾に低下して好ましくない。If the B content is less than 7q4, it is difficult to make it amorphous;
If it is 0- or higher, the environmental resistance properties, such as moisture resistance and alkali resistance, will be greatly reduced, which is not preferable.
81の含有量は7チ未満では熱的安定性が損われ16哄
以上ではHeが(110・以上となシ好ましくない。If the content of 81 is less than 7%, the thermal stability will be impaired, and if the content is more than 16%, the He content will be less than 110%, which is not preferable.
F・とCoの総和は72−から85−であシ、85哄を
こえると非晶質化が困拳となり、72%未満では磁束密
度の低下がToJ)好ましくない。The sum of F and Co is between 72 and 85. If it exceeds 85%, amorphization becomes difficult, and if it is less than 72%, the magnetic flux density decreases (ToJ), which is not preferable.
F・はCoとの相互作用によシ磁場中焼なまし及び冷却
による鱒導磁気異方性を発生せしめB−H―纏の角型性
を、改善し、従って励磁電流特性における飽和までの急
峻度を生じる効果を有す。F generates magnetic anisotropy through annealing and cooling in a magnetic field through interaction with Co, improves the squareness of the B-H-clad, and therefore improves the excitation current characteristics up to saturation. It has the effect of creating steepness.
まえ、F@とCoの比率をa70≦C9//Fe+CO
≦α!9に限定し九遍由は、これ以外の組成では、磁歪
定数λlを実質的に小さくできない為である。First, the ratio of F@ and Co is a70≦C9//Fe+CO
≦α! The reason why it is limited to 9 is that the magnetostriction constant λl cannot be made substantially smaller with a composition other than this.
なお、磁歪定数は、非晶質材料の軟磁気特性を支配すゐ
重要な定数であシ、これを実質的に零にする事は優れ九
励磁電流特性を得るために極めて重畳である。Incidentally, the magnetostriction constant is an important constant that governs the soft magnetic properties of an amorphous material, and making it substantially zero is extremely superimposed in order to obtain excellent excitation current characteristics.
を九、添加元素としてでて示す各元素を総量でst4以
下含むことが可能である。TI、Zr、 Hf。9. It is possible to contain the total amount of each element shown as an additive element in a total amount of st4 or less. TI, Zr, Hf.
V、 Nb、 Ta、Mo、 W、 Nl、Pdの一詳
拡添加により非晶質形成能を向上させ、Cr、 Pdは
耐食性、耐湿性を向上させる。Y%CI、Pr、 Nd
%8mSgu。The addition of V, Nb, Ta, Mo, W, Nl, and Pd improves the amorphous formation ability, and Cr and Pd improve corrosion resistance and moisture resistance. Y%CI, Pr, Nd
%8mSgu.
Gd%Tb%D7の一群は硬さを向上せしめるとともに
結晶化温度を上げ熱的安定性を増大させる。B・、Mg
、Ca、8r、 Ba、 Ruは非晶質形成能を向上さ
せ、特に他の添加元素と複合されて用いるとその傾向が
強まる。MnはHeを低くする効果がある。これらの添
加元素Tの総量はs%以下であることが好ましくない。The group Gd%Tb%D7 improves hardness and increases crystallization temperature and thermal stability. B., Mg
, Ca, 8r, Ba, and Ru improve the ability to form an amorphous state, and this tendency is particularly enhanced when used in combination with other additive elements. Mn has the effect of lowering He. It is not preferable that the total amount of these additional elements T be less than s%.
以上の組成範囲の非晶質鉄心材料をトロイダル鉄心とじ
100・以上の直流ないし交流磁場中で、250℃から
450℃の間の適切な温度で焼なまし、毎時500℃以
下の冷却速度で磁場中冷却することKより、胞で(LO
20・以下、B、。で8000Q。An amorphous core material having the above composition range is formed into a toroidal core and annealed in a direct current or alternating current magnetic field of 100 °C or more at an appropriate temperature between 250 °C and 450 °C, and at a cooling rate of 500 °C or less per hour in the magnetic field. Cool in the cell (LO).
20. Below, B. So 8000Q.
/ih * 75 慢以上の低保磁力、高磁束密度、
高角1・
臘比巻鉄心が容易に得られる。磁界の波形は従来直流が
一般的に採用されているが、半波整流及び交流(商用周
波数)でも効果はほとんど減じない。/ih * 75 Low coercive force, high magnetic flux density,
A high-angle 1/1-inch winding core can be easily obtained. Conventionally, direct current is generally used as the waveform of the magnetic field, but half-wave rectification and alternating current (commercial frequency) also have little effect.
熱処理温度は組成の変化によシ最適温度がずれるが45
0℃をこえると脆化が著しくなυ、また、250℃未満
では焼なましによる応力緩和が不可能であシ、効果がほ
とんどない。磁場中冷却速度が毎時300℃をこえると
冷却むらが発生し易く75嗟以上の 職、。が得られな
い。The optimum temperature for heat treatment may deviate due to changes in composition45
When the temperature exceeds 0°C, embrittlement becomes significant, and when the temperature is lower than 250°C, stress relaxation by annealing is impossible and has little effect. If the cooling rate in a magnetic field exceeds 300°C per hour, uneven cooling is likely to occur, and this is the case when the cooling rate exceeds 300°C per hour. is not obtained.
以下、実施例に基き詳細に説明する。Hereinafter, it will be explained in detail based on examples.
111t1表ハ、従来のスーパーマロイと5ONiパー
マロイに対する本発明の巻鉄心を構成する非晶質合金鉄
心の直流磁性の例を示す。いずれの組成においても最適
の熱処理温度を採った場合である。111t1 Table C shows examples of DC magnetism of the amorphous alloy core constituting the wound core of the present invention with respect to conventional supermalloy and 5ONi permalloy. This is the case when the optimum heat treatment temperature is adopted for any composition.
第 1 表
第1表から明らかなように1本発明の巻鉄心を構成する
非晶質合金鉄心はスーパーマロイと同等以下の低い保磁
力を示しており 、%は5ONiパーマロイと同郷レベ
ルのものがあυ総合的に従来材の長所を兼備した優れた
性能をもっており、嵐好な励磁電流特性を示すことが明
らかである。 ′第1図は、第1表中の合金A!
(3)、ム+6(4)よ構成る巻鉄心のsOHmにおけ
る励磁電流特性をスーパーマロイ(1)、5ONiパー
マロイ(2)との対比で示したものである(()内は図
中の符号を示す)。Table 1 As is clear from Table 1, the amorphous alloy core constituting the wound core of the present invention exhibits a low coercive force that is equal to or lower than that of supermalloy, and the percentage is on the same level as that of 5ONi permalloy. It is clear that it has overall excellent performance, combining the advantages of conventional materials, and exhibits excellent excitation current characteristics. 'Figure 1 shows alloy A in Table 1!
(3), the excitation current characteristics in sOHm of the wound core configured as M + 6 (4) are shown in comparison with supermalloy (1) and 5ONi permalloy (2) (the numbers in parentheses are the numbers in the figure). ).
巻鉄心の鉄心寸法は内径25971φ、外径55xmφ
、高さSws、励磁巻数は1次、2次側とも15ターン
である。第1図から明らかなように本発明の巻鉄心は低
い励磁起磁力(励磁電流)が出力電圧の高いレベルまで
維持され、ま九この間の直線性が嵐好であシ、優れた励
磁特性を有している。The core dimensions of the wound core are inner diameter 25971φ, outer diameter 55xmφ
, the height Sws, and the number of excitation turns are 15 turns on both the primary and secondary sides. As is clear from Fig. 1, the wound core of the present invention maintains a low excitation magnetomotive force (excitation current) up to a high level of output voltage, has excellent linearity during this period, and has excellent excitation characteristics. have.
上記実施例から明らかな如く、本発明の巻鉄心の励磁特
性は極めて優れてシシ、磁気増巾器、磁気移相器、直流
電流検出器、磁気変調器などの制御用巻鉄心として優れ
たものである。また、鉄心素材の非晶質合金が本来的に
持っている強度と靭性から本発明の巻鉄心は応力感受性
が低く、耐衝撃性に優れ喪信頼性の高いものである。As is clear from the above examples, the wound core of the present invention has extremely excellent excitation characteristics and is excellent as a control wound core for shields, magnetic amplifiers, magnetic phase shifters, DC current detectors, magnetic modulators, etc. It is. Further, due to the strength and toughness inherent in the amorphous alloy of the core material, the wound core of the present invention has low stress sensitivity, excellent impact resistance, and high reliability.
第1図は50H$における本発明の巻鉄心と従来の巻鉄
心の励磁電流特性を示した図である。FIG. 1 is a diagram showing the excitation current characteristics of the wound core of the present invention and the conventional wound core at 50 H$.
Claims (1)
いて、前記合金薄板としてF・−Co −S l−B系
非晶質合金薄板を用いたことを特徴とする巻鉄心。 2、特許請求の範囲第1項記載のものにおいて、上記非
晶質合金が組成式F・、CoeTf81.B、(式中、
TFi、Be、Mg、 Ca、 8r、 Ba、 TI
、Zr、 Hf。 V、Nb、Ta、Cr、Mo、W、Mn、Ru、Ni、
Pd。 Cu%Zn、Y、Co、Pr、Nd、Sm、Eu、Gd
、Tb。 Dyのうちの1種または2種以上、d+・十f+g +
h= 100.72≦d十〇≦85、α70≦”/(a
+・)≦199.0≦f≦3.7くg〈16.7くhく
10.15≦g十h≦25)で示されることを特徴とす
る巻鉄心。 五 特許請求の範囲第1項を九は第2項記載のもOにお
いて、上記非晶質合金が10エルステッド以上の直流ま
たは交流磁場中にて250℃から450℃の間で焼なま
しを行ない、毎時300℃以下の冷却速度にて磁場中冷
却を施すことにより得たものであることを特徴とする巻
鉄心。[Claims] t A wound core formed by winding a high magnetic permeability alloy thin plate, characterized in that an F.-Co-S l-B based amorphous alloy thin plate is used as the alloy thin plate. Wound core. 2. In the item described in claim 1, the amorphous alloy has a composition formula F., CoeTf81. B, (in the formula,
TFi, Be, Mg, Ca, 8r, Ba, TI
, Zr, Hf. V, Nb, Ta, Cr, Mo, W, Mn, Ru, Ni,
Pd. Cu%Zn, Y, Co, Pr, Nd, Sm, Eu, Gd
,Tb. One or more types of Dy, d+・10f+g+
h= 100.72≦d10≦85, α70≦”/(a
+・)≦199.0≦f≦3.7×g (16.7×h×10.15≦g10h≦25). (5) Claims 1 and 9 are also set forth in paragraph 2, in which the amorphous alloy is annealed at a temperature between 250°C and 450°C in a direct current or alternating current magnetic field of 10 Oe or more. , a wound core obtained by cooling in a magnetic field at a cooling rate of 300°C or less per hour.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP56196894A JPS58100659A (en) | 1981-12-09 | 1981-12-09 | Wound iron core |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP56196894A JPS58100659A (en) | 1981-12-09 | 1981-12-09 | Wound iron core |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS58100659A true JPS58100659A (en) | 1983-06-15 |
JPH0323619B2 JPH0323619B2 (en) | 1991-03-29 |
Family
ID=16365412
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP56196894A Granted JPS58100659A (en) | 1981-12-09 | 1981-12-09 | Wound iron core |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS58100659A (en) |
Cited By (3)
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CN106208432A (en) * | 2016-07-30 | 2016-12-07 | 杨帆 | A kind of driving motor |
CN108597795A (en) * | 2018-04-13 | 2018-09-28 | 河南宝泉电力设备制造有限公司 | Amorphous dry-type transformer |
CN111575610A (en) * | 2020-06-29 | 2020-08-25 | 华麟津磁(天津)科技有限公司 | SmFeB amorphous soft magnetic alloy material and preparation method thereof |
-
1981
- 1981-12-09 JP JP56196894A patent/JPS58100659A/en active Granted
Cited By (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN106208432A (en) * | 2016-07-30 | 2016-12-07 | 杨帆 | A kind of driving motor |
CN108418320A (en) * | 2016-07-30 | 2018-08-17 | 杨帆 | A kind of driving motor |
CN108418320B (en) * | 2016-07-30 | 2019-12-31 | 佛山市顺德区恒德电机制品有限公司 | Driving motor |
CN108597795A (en) * | 2018-04-13 | 2018-09-28 | 河南宝泉电力设备制造有限公司 | Amorphous dry-type transformer |
CN108597795B (en) * | 2018-04-13 | 2020-11-06 | 河南宝泉电力设备制造有限公司 | Amorphous dry-type transformer |
CN111575610A (en) * | 2020-06-29 | 2020-08-25 | 华麟津磁(天津)科技有限公司 | SmFeB amorphous soft magnetic alloy material and preparation method thereof |
Also Published As
Publication number | Publication date |
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JPH0323619B2 (en) | 1991-03-29 |
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