JPS6221041B2 - - Google Patents
Info
- Publication number
- JPS6221041B2 JPS6221041B2 JP10384282A JP10384282A JPS6221041B2 JP S6221041 B2 JPS6221041 B2 JP S6221041B2 JP 10384282 A JP10384282 A JP 10384282A JP 10384282 A JP10384282 A JP 10384282A JP S6221041 B2 JPS6221041 B2 JP S6221041B2
- Authority
- JP
- Japan
- Prior art keywords
- magnetic
- core
- firing
- powder
- iron
- 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.)
- Expired
Links
- 239000000843 powder Substances 0.000 claims description 17
- 238000010304 firing Methods 0.000 claims description 15
- 229910001004 magnetic alloy Inorganic materials 0.000 claims description 10
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 9
- 229910052782 aluminium Inorganic materials 0.000 claims description 9
- 229910052739 hydrogen Inorganic materials 0.000 claims description 9
- 239000001257 hydrogen Substances 0.000 claims description 9
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 claims description 8
- 238000000137 annealing Methods 0.000 claims description 8
- 229910052710 silicon Inorganic materials 0.000 claims description 8
- 239000000428 dust Substances 0.000 claims description 6
- 239000011230 binding agent Substances 0.000 claims description 5
- -1 iron-silicon-aluminum Chemical compound 0.000 claims description 5
- 238000004519 manufacturing process Methods 0.000 claims description 5
- 229910052742 iron Inorganic materials 0.000 claims description 4
- 238000000034 method Methods 0.000 claims description 2
- 238000010298 pulverizing process Methods 0.000 claims description 2
- 238000000465 moulding Methods 0.000 claims 1
- 230000035699 permeability Effects 0.000 description 15
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 8
- 239000011733 molybdenum Substances 0.000 description 8
- 229910000889 permalloy Inorganic materials 0.000 description 8
- 229910052750 molybdenum Inorganic materials 0.000 description 7
- 238000010438 heat treatment Methods 0.000 description 6
- 229910045601 alloy Inorganic materials 0.000 description 4
- 239000000956 alloy Substances 0.000 description 4
- 229910002796 Si–Al Inorganic materials 0.000 description 3
- 230000004907 flux Effects 0.000 description 3
- 239000002994 raw material Substances 0.000 description 3
- 229910000838 Al alloy Inorganic materials 0.000 description 2
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 238000005266 casting Methods 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 239000010703 silicon Substances 0.000 description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- 229910000640 Fe alloy Inorganic materials 0.000 description 1
- 229910017082 Fe-Si Inorganic materials 0.000 description 1
- 229910017133 Fe—Si Inorganic materials 0.000 description 1
- 229910001182 Mo alloy Inorganic materials 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 150000002431 hydrogen Chemical class 0.000 description 1
- 238000011068 loading method Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000005245 sintering Methods 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
- C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacture Of Metal Powder And Suspensions Thereof (AREA)
- Powder Metallurgy (AREA)
Description
本発明は、鉄（Fe）、珪素（Si）、アルミ
（Al）を主成分とする鉄―珪素―アルミ磁性合金
を原料とした圧粉磁心の製造方法に関するもので
ある。
Fe―Si―Al磁性合金は既に公知であり、重量
でSi4〜13％、Al4〜７％、残鉄の組成のものが透
磁率が最も大きくなることが知られている。
従来、Fe―Si―Al磁性合金で圧粉磁心を構成
し、インダクタンス素子として装荷線輪や高周波
磁心に用いられている。このような圧粉磁心は、
合金イレゴツトを粉砕して得た合金粉末に絶縁皮
膜を施した後、バインダーを加えてプレス成形
し、これを焼成することによつて製造されてお
り、こうして得られた圧粉磁心は、ヒステリシス
損および渦電流損が小さく、飽和磁束密度が大き
く、温度特性が良好である等の特長を有してい
た。
しかしながら、高性能な磁気特性を有するフエ
ライトの出現によつて、装荷線輪、LCフイルタ
用チヨークコイルはフエライトに置き換えられ、
また電源用チヨークコイル等には透磁率が高く、
電力損失の低いMo―Ni―Feを主成分とするモリ
ブデンパーマロイ圧粉磁心が用いられ、現在で
は、Fe―Si―Al系磁性合金の圧粉磁心はほとん
ど用いられなくなつている。
この理由は、Fe―Si―Al系磁性合金は透磁率
が80（10kHz）、電力損失が250kW／m3
（25kHz、1000G）であり、モリブデンパーマロ
イ圧粉磁心の透磁率125（10kHz）、電力損失
150kW／m3（25kHz、1000G）に比して磁気特性
が悪いことによる。
一方で、モリブデンパーマロイの原料であるモ
リブデンやパーマロイの価格が高いので、合金自
身が高価となる欠点があるが、Fe―Si―Alは逆
に廉価である。
従つて、本発明は廉価なFe―Si―Al系磁性合
金からなり、磁気特性を改善した圧粉磁心を製造
する方法を提供することを目的とする。
本発明は、重量でSi4〜13％、Al4〜７％、残鉄
を主成分とする鉄―珪素―アルミ磁性合金インゴ
ツトを700〜1100℃で熱処理（焼鈍）後、粉砕
し、得られた粉末にバインダを加えてプレス成形
し、この成形体を水素雰囲気中で600〜800℃にて
焼成することを特徴とする鉄―珪素―アルミ系磁
性合金圧粉磁心の製造方法である。
Fe―Si―Al合金では溶解鋳造時にAlやSiが偏
析を起し易い。このためインゴツトの焼鈍は、バ
ルクへのSi、Alの拡散を考慮し、高い温度ほど望
ましい。しかし、余り高いとSi、Alが表面から酸
化物として出てしまうので、組成が変化してしま
う。またSiが少なくAlに富んだ異相が結晶粒内お
よび粒界に析出し磁気特性を劣化させる。焼鈍温
度が1200℃を越えると、この特性劣化がはなはだ
しい。従つて、焼鈍温度は700〜1100℃が望まし
い。
また焼成は、プレス成形時のひずみを除去する
ために600〜800℃で行なうことが望ましいが、大
気焼成の場合、この温度では、粒子が酸化し、透
磁率の低下とともに電力損失の増大を招く。しか
し、水素中にて焼成すれば、粒子が酸化せず効果
的に透磁率・電力損失を改善できる。
以下本発明を図面を参照して詳細に説明する。
第１図および第２図は（熱処理温度（即ち焼鈍
温度））と透磁率（10kHz）および電力損失
（1000G）との関係を示し、それぞれ曲線ａは焼
成を水素中700℃で行なつたもの、曲線ｂは焼成
を大気中700℃で行なつたものを示す。第１図お
よび第２図から、焼鈍温度は700〜1100℃の範囲
が良いことがわかる。また焼成は大気中より水素
中の方が良いことがわかる。
第３図から第５図は、インゴツトの熱処理を
1000℃で行ない、コア焼成の雰囲気を水素中（曲
線ａ）としたものおよび大気中（曲線ｂ）とした
ものについての、コア焼成温度に対する透磁率
（10kHz）、透磁率（1000kHz）および電力損失
（25kHz、1000G）の変化を、それぞれ、示して
いる。
第３図〜第５図から、コア焼成の雰囲気は大気
中より水素中の方が良いこと、焼成温度は600〜
800℃の範囲が良いことがわかる。
Si9.2重量％、Al5.7重量％、残FeのFe―Si―
Al合金インゴツトを、本発明に従つて、1000℃
で３時間熱処理し、これを粉砕（スタンプミル）
後、150〜250メツシユに篩分けし、680℃で１時
間粉末酸化して絶縁皮膜を形成し、これに無機質
絶縁結着剤のバインダーを添加混合後、32メツシ
ユ以下に整粒し、これを20t／cm2でプレスして、
水素中にて700℃、１時間の焼成を行なつて圧粉
磁心試料を得た。この本発明による圧粉磁心試料
の磁気特性と電力損失を測定した。その結果を第
１表および第２表で示す。
第１表、第２表には、比較例として、本発明の
製造方法に従がわず、熱処理温度を1250℃、コア
焼成温度を700℃で１時間とし、他の条件は、上
記の本発明試料と同一として製造した試料につい
ての特性および、従来のモリブデンパーマロイの
特性を示した。
なお、第２表は各直流重量時の場合の透磁率を
示す。
The present invention relates to a method for manufacturing a powder magnetic core using an iron-silicon-aluminum magnetic alloy as a raw material, the main components of which are iron (Fe), silicon (Si), and aluminum (Al). Fe--Si--Al magnetic alloys are already known, and it is known that those with a composition of 4 to 13% Si, 4 to 7% Al, and balance iron have the highest magnetic permeability. Conventionally, powder magnetic cores are made of Fe--Si--Al magnetic alloys and used as inductance elements in loaded coils and high-frequency magnetic cores. Such a powder magnetic core is
It is manufactured by applying an insulating film to the alloy powder obtained by crushing the alloy irregularity, adding a binder, press-forming it, and firing it.The powder magnetic core obtained in this way has a low hysteresis loss. It also had features such as low eddy current loss, high saturation magnetic flux density, and good temperature characteristics. However, with the advent of ferrite, which has high-performance magnetic properties, loading coils and chiyoke coils for LC filters have been replaced with ferrite.
In addition, magnetic permeability is high for power source coils, etc.
Molybdenum permalloy dust cores whose main components are Mo--Ni--Fe, which has low power loss, are now used, and powder magnetic cores made of Fe--Si--Al magnetic alloys are almost no longer used. The reason for this is that Fe-Si-Al magnetic alloy has a magnetic permeability of 80 (10kHz) and a power loss of 250kW/ m3.
(25kHz, 1000G), permeability of molybdenum permalloy powder magnetic core is 125 (10kHz), power loss
This is due to poor magnetic properties compared to 150kW/m 3 (25kHz, 1000G). On the other hand, since molybdenum and permalloy, the raw materials for molybdenum permalloy, are expensive, the alloy itself has the disadvantage of being expensive, but Fe-Si-Al, on the other hand, is inexpensive. Therefore, an object of the present invention is to provide a method for producing a dust core made of an inexpensive Fe--Si--Al based magnetic alloy and with improved magnetic properties. The present invention is a powder obtained by heat-treating (annealing) an iron-silicon-aluminum magnetic alloy ingot whose main components are 4 to 13% Si, 4 to 7% Al, and residual iron by weight at 700 to 1100°C, and then pulverizing the ingot. This is a method for producing an iron-silicon-aluminum magnetic alloy dust core, which is characterized by adding a binder to the material, press-forming the product, and firing the molded product at 600 to 800°C in a hydrogen atmosphere. In Fe-Si-Al alloys, Al and Si tend to segregate during melting and casting. For this reason, when annealing the ingot, a higher temperature is preferable in consideration of the diffusion of Si and Al into the bulk. However, if it is too high, Si and Al will come out as oxides from the surface, resulting in a change in composition. In addition, a heterogeneous phase rich in Al and low in Si precipitates within the crystal grains and at the grain boundaries, deteriorating the magnetic properties. When the annealing temperature exceeds 1200°C, this property deterioration becomes significant. Therefore, the annealing temperature is preferably 700 to 1100°C. Additionally, it is desirable to perform firing at a temperature of 600 to 800°C to remove strain during press forming, but in the case of atmospheric firing, at this temperature the particles will oxidize, leading to a decrease in magnetic permeability and an increase in power loss. . However, by firing in hydrogen, the particles are not oxidized and magnetic permeability and power loss can be effectively improved. The present invention will be described in detail below with reference to the drawings. Figures 1 and 2 show the relationship between (heat treatment temperature (i.e. annealing temperature)), magnetic permeability (10kHz) and power loss (1000G), where curve a is for sintering in hydrogen at 700°C. , curve b shows that the firing was carried out in the air at 700°C. From FIG. 1 and FIG. 2, it can be seen that the annealing temperature is preferably in the range of 700 to 1100°C. It is also clear that firing in hydrogen is better than in the air. Figures 3 to 5 show the heat treatment of ingots.
Magnetic permeability (10kHz), magnetic permeability (1000kHz), and power loss versus core firing temperature for core firing conducted at 1000℃ and in hydrogen (curve a) and in air (curve b). (25kHz, 1000G) are shown respectively. From Figures 3 to 5, it is clear that the core firing atmosphere is better in hydrogen than in the air, and the firing temperature is 600~600℃.
It can be seen that the range of 800℃ is good. Si9.2% by weight, Al5.7% by weight, remaining Fe—Si—
According to the present invention, an Al alloy ingot was heated to 1000°C.
Heat treated for 3 hours and crushed (stamp mill)
After that, the powder is sieved into 150 to 250 meshes and oxidized at 680℃ for 1 hour to form an insulating film.After adding and mixing an inorganic insulating binder, the powder is sized to 32 meshes or less. Press at 20t/ cm2 ,
A powder magnetic core sample was obtained by firing in hydrogen at 700°C for 1 hour. The magnetic properties and power loss of this powder magnetic core sample according to the present invention were measured. The results are shown in Tables 1 and 2. Tables 1 and 2 show comparative examples in which the manufacturing method of the present invention was not followed, the heat treatment temperature was 1250°C, the core firing temperature was 700°C for 1 hour, and the other conditions were the same as in the above book. The characteristics of a sample manufactured identical to the invention sample and the characteristics of conventional molybdenum permalloy are shown. Note that Table 2 shows the magnetic permeability at each DC weight.
【表】【table】
【表】
第１表および第２表から明らかなように、本発
明によるコアは、本発明によらないものおよびモ
リブデンパーマロイに比して、透磁率において、
それぞれ、約２倍、約1.2倍である。磁束密度、
電力損失、直流重量においては、モリブデンパー
マロイより同等以上、本発明によらないFe―Si
―Al合金コアに代えて大巾に改善されている。
以上述べた如く本発明によれば、珪素４〜13
％、アルミニウム４〜７％残部鉄とした合金にお
いて、溶解鋳造後、熱処理（焼鈍）として、700
〜1100℃に加熱保持後室温に至るようにし、その
後、機械的粉砕により粉末化しこれを、原料とし
バインダー混合、プレス、水素中にて、600〜
800tで焼成したので磁気特性を良好な圧粉磁心を
提供し得しかも、天然埋蔵量の豊富な元素Si、
Al、Feを、主成分としているため、同様な磁気
特性を有するこの種圧粉磁心を極めて低廉に提供
し得る効果を有する。また、従来のモリブデンパ
ーマロイ圧粉磁心の磁気特性に比して、透磁率、
磁束密度が大きく電力損失直流重畳同程度の圧粉
磁心を極めて低廉に供給し得る。
従つて、本発明によつて得られる圧粉磁心は、
高周波電源用インダクタ、LCフイルタを始め各
種のインダクタに適用して好適であることは勿論
である。[Table] As is clear from Tables 1 and 2, the core according to the invention has a lower magnetic permeability than the core according to the invention and molybdenum permalloy.
They are about 2 times and about 1.2 times, respectively. magnetic flux density,
In terms of power loss and DC weight, it is equivalent to or better than molybdenum permalloy, and Fe-Si which is not based on the present invention
- Substantially improved by replacing the Al alloy core. As described above, according to the present invention, silicon 4 to 13
% aluminum, 4 to 7% iron alloy, after melting and casting, as heat treatment (annealing), 700
After heating and holding at ~1100℃, it was allowed to reach room temperature, and then mechanically pulverized to powder, which was used as a raw material, mixed with a binder, pressed, and heated in hydrogen for 600~
Because it was fired at 800 tons, it was able to provide a dust core with good magnetic properties.
Since it contains Al and Fe as the main components, it has the effect of being able to provide this type of powder magnetic core with similar magnetic properties at an extremely low cost. In addition, compared to the magnetic properties of conventional molybdenum permalloy powder magnetic cores, magnetic permeability,
A dust core with a large magnetic flux density and a power loss equivalent to DC superposition can be supplied at an extremely low cost. Therefore, the powder magnetic core obtained by the present invention is
Of course, it is suitable for application to various inductors including high frequency power supply inductors and LC filters.
第１図および第２図は、熱処理温度による透磁
率および電力損失の変化をそれぞれ示す図、第３
図、第４図および第５図は、コア焼成温度によ
る、透磁率（10kHz）、透磁率（1000kHz）およ
び電力損失の変化をそれぞれ示す図である。
Figures 1 and 2 are diagrams showing changes in magnetic permeability and power loss depending on heat treatment temperature, respectively.
4 and 5 are diagrams showing changes in magnetic permeability (10 kHz), magnetic permeability (1000 kHz), and power loss, respectively, depending on the core firing temperature.
Claims (1)
とする鉄―珪素―アルミ系磁性合金インゴツトを
700〜1100℃で焼鈍後、粉砕し、得られた粉末に
バインダを加えてプレス成形し、該成形体を水素
雰囲気中で600〜800℃にて焼成することを特徴と
する鉄―珪素―アルミ系磁性合金圧粉磁心の製造
方法。1 An iron-silicon-aluminum magnetic alloy ingot whose main components are 4 to 13% Si, 4 to 7% Al, and residual iron by weight.
Iron-silicon-aluminum, which is characterized by annealing at 700-1100°C, pulverizing, adding a binder to the resulting powder, press-molding, and firing the compact at 600-800°C in a hydrogen atmosphere. A method for manufacturing a magnetic alloy dust core.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10384282A JPS58221204A (en) | 1982-06-18 | 1982-06-18 | Production of iron-silicon-aluminum magnetic alloy compact core |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10384282A JPS58221204A (en) | 1982-06-18 | 1982-06-18 | Production of iron-silicon-aluminum magnetic alloy compact core |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS58221204A JPS58221204A (en) | 1983-12-22 |
| JPS6221041B2 true JPS6221041B2 (en) | 1987-05-11 |
Family
ID=14364679
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP10384282A Granted JPS58221204A (en) | 1982-06-18 | 1982-06-18 | Production of iron-silicon-aluminum magnetic alloy compact core |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS58221204A (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS62222002A (en) * | 1986-03-20 | 1987-09-30 | Hitachi Metals Ltd | Production of dust core of fe-si-al alloy |
| JP7418194B2 (en) * | 2019-12-06 | 2024-01-19 | 株式会社タムラ製作所 | Manufacturing method of powder magnetic core |
-
1982
- 1982-06-18 JP JP10384282A patent/JPS58221204A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPS58221204A (en) | 1983-12-22 |
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