JP2017092162A - Method of manufacturing dust core - Google Patents
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本発明は、圧粉磁心の製造方法に関する。 The present invention relates to a method for manufacturing a dust core.
合金粉、例えば、軟磁性材料粉を圧縮することによって、圧粉磁心を製造する方法がある。例えば、特許文献１に開示される圧粉磁心の製造方法では、まず、バインダを軟磁性材料粉に混合させた混合粉を加圧成形することによって、高い強度を有する圧粉体を成形する。ここで、バインダは、例えば、ガラス（シリコーン樹脂）などを含む。さらに、圧粉体を熱処理することによって、圧粉磁心を製造する。この熱処理によって、圧粉体を構成する粒子にＡｌ酸化膜を形成させ、圧粉磁心の絶縁性を向上させる。 There is a method for producing a powder magnetic core by compressing alloy powder, for example, soft magnetic material powder. For example, in the method of manufacturing a powder magnetic core disclosed in Patent Document 1, first, a powder having high strength is formed by pressure-molding a mixed powder obtained by mixing a binder with a soft magnetic material powder. Here, the binder includes, for example, glass (silicone resin). Further, the powder magnetic core is manufactured by heat-treating the powder compact. By this heat treatment, an Al oxide film is formed on the particles constituting the powder compact, and the insulation of the powder magnetic core is improved.
ところで、特許文献１に開示されるようなバインダを用いた圧粉磁心の製造方法では、バインダを軟磁性材料粉に混合させるため、混合粉の流動性が減じ、加圧成形工程において、混合粉を金型に均一に充填させることができないことがあった。これによって、密度のバラツキが発生し、割れが圧粉磁心に生じることがあった。 By the way, in the manufacturing method of the powder magnetic core using the binder as disclosed in Patent Document 1, since the binder is mixed with the soft magnetic material powder, the fluidity of the mixed powder is reduced. May not be uniformly filled in the mold. As a result, density variation occurs, and cracks may occur in the dust core.
本発明は、強度の低下を抑制した圧粉磁心を製造する圧粉磁心の製造方法を提供する。 The present invention provides a method for manufacturing a dust core, which manufactures a dust core in which a decrease in strength is suppressed.
本発明に係る圧粉磁心の製造方法は、
複数の粒子を含む合金粉末を、加圧成形して圧粉磁心を製造する製造方法であって、
前記複数の粒子は、Ａｌと、主成分としてＦｅと、を含み、
前記合金粉末を熱処理温度８００℃〜１０００℃で加熱保持した後、
前記加熱保持した前記合金粉末を加圧成形する。
The method for producing a dust core according to the present invention includes:
An alloy powder containing a plurality of particles is a manufacturing method for producing a powder magnetic core by pressure molding,
The plurality of particles include Al and Fe as a main component,
After heating and holding the alloy powder at a heat treatment temperature of 800 ° C to 1000 ° C,
The alloy powder held by heating is pressure-molded.
また、前記合金粉末を熱処理温度８００℃〜１０００℃で加熱保持することによって、前記合金粉末の前記複数の粒子の表面に絶縁膜を形成してもよい。また、前記絶縁膜の厚みは、１０μｍ〜５００μｍの範囲内にある。また、前記加圧成形した前記合金粉末を焼鈍温度１０５０℃〜１２００℃で焼鈍してもよい。このような構成によれば、バインダを加えないために、合金粉末の流動性が減じないために合金粉末の圧縮性を維持することで、圧粉磁心の強度の低下を抑制することができる。 Further, an insulating film may be formed on the surface of the plurality of particles of the alloy powder by heating and holding the alloy powder at a heat treatment temperature of 800 ° C. to 1000 ° C. The insulating film has a thickness in the range of 10 μm to 500 μm. In addition, the pressure-molded alloy powder may be annealed at an annealing temperature of 1050 ° C to 1200 ° C. According to such a configuration, since the binder is not added and the fluidity of the alloy powder does not decrease, the compressibility of the alloy powder is maintained, so that a decrease in the strength of the dust core can be suppressed.
本発明に係る圧粉磁心の製造方法によれば、強度の低下を抑制した圧粉磁心を製造することができる。 According to the method for manufacturing a dust core according to the present invention, it is possible to manufacture a dust core in which a decrease in strength is suppressed.
実施の形態１
図１を参照して実施の形態１に係る圧粉磁心の製造方法について説明する。図１は、実施の形態１に係る圧粉磁心の製造方法を示すフローチャートである。
Embodiment 1
A method for manufacturing a dust core according to Embodiment 1 will be described with reference to FIG. 1 is a flowchart showing a method for manufacturing a dust core according to Embodiment 1. FIG.
まず、軟磁性金属粒子からなる粉を窒素雰囲気中で熱処理を実施し、熱処理粉を製造する（絶縁膜形成ステップＳＴ１）。ここで、軟磁性金属粒子の表面に絶縁膜が形成される。絶縁膜は、例えば、ＡｌＮ膜又はＡｌＮ膜とＡｌ２Ｏ３膜との複合膜である。 First, the powder made of soft magnetic metal particles is heat-treated in a nitrogen atmosphere to produce heat-treated powder (insulating film forming step ST1). Here, an insulating film is formed on the surface of the soft magnetic metal particles. The insulating film is, for example, an AlN film or a composite film of an AlN film and an Al 2 O 3 film.
また、軟磁性金属粒子は、Ｆｅを主成分として含み、さらにＡｌを含む。軟磁性金属粒子は、さらに、圧粉磁心として必要な特性を満たすために、Ｓｉ、Ｃｒなどの他の元素を含んでもよい。軟磁性金属粒子の粒度分布は、例えば、下限１μｍから上限１ｍｍまでの範囲内にある。この下限は、１μｍ以下の値であってもよい。なお、軟磁性金属粒子からなる粉には、無機系バインダを加えない。無機系バインダは、例えば、ガラス、シリコーン樹脂である。 Further, the soft magnetic metal particles contain Fe as a main component and further contain Al. The soft magnetic metal particles may further contain other elements such as Si and Cr in order to satisfy characteristics required as a dust core. The particle size distribution of the soft magnetic metal particles is, for example, in a range from a lower limit of 1 μm to an upper limit of 1 mm. This lower limit may be a value of 1 μm or less. Note that an inorganic binder is not added to the powder made of soft magnetic metal particles. The inorganic binder is, for example, glass or silicone resin.
また、ＡｌＮ膜、又は、ＡｌＮ膜とＡｌ２Ｏ３膜との複合膜の厚みは、例えば、１０ｎｍ〜５００ｎｍの範囲内にある。ＡｌＮ膜、又は、ＡｌＮ膜とＡｌ２Ｏ３膜との複合膜は、ガラス又はガラスに相当する成分を有する絶縁膜と比較して、高い熱伝導性を有する。 Further, the thickness of the AlN film or the composite film of the AlN film and the Al 2 O 3 film is, for example, in the range of 10 nm to 500 nm. An AlN film or a composite film of an AlN film and an Al 2 O 3 film has higher thermal conductivity than glass or an insulating film having a component corresponding to glass.
また、熱処理は、複数の軟磁性金属粒子からなる粉を所定の熱処理温度に加熱し、所定の熱処理時間保持する。熱処理条件は、熱処理温度８００℃〜１０００℃、熱処理時間１８０分〜６００分である。熱処理温度が８００℃以上であるため、電気を十分に絶縁するような厚みを有する絶縁膜が形成される。熱処理温度が１０００℃以下であるため、加圧成形ステップＳＴ２（後述）で、熱処理粉が良好な流動性、言い換えると、良好な圧縮性を有するような適度な厚みを有する絶縁膜が形成される。絶縁膜の厚さは、例えば、１０ｎｍ〜５００ｎｍの範囲内にあり、２００ｎｍ〜３５０ｎｍの範囲内にあると好ましい。 In the heat treatment, a powder composed of a plurality of soft magnetic metal particles is heated to a predetermined heat treatment temperature and held for a predetermined heat treatment time. The heat treatment conditions are a heat treatment temperature of 800 ° C. to 1000 ° C. and a heat treatment time of 180 minutes to 600 minutes. Since the heat treatment temperature is 800 ° C. or higher, an insulating film having a thickness that sufficiently insulates electricity is formed. Since the heat treatment temperature is 1000 ° C. or lower, an insulating film having an appropriate thickness is formed in the pressure forming step ST2 (described later) so that the heat treated powder has good fluidity, in other words, good compressibility. . The thickness of the insulating film is, for example, in the range of 10 nm to 500 nm, and preferably in the range of 200 nm to 350 nm.
また、絶縁膜を有する軟磁性金属粒子からなる粉は、あまり固化しておらず、軟磁性金属粒子同士が、ごく一部固着している、又は、非常に小さな力で固着している。熱処理粉を分級時においてふるいをかけることで、これらの軟磁性金属粒子同士が分離され、熱処理粉は、流動性を有する粉状体となる。 In addition, the powder made of soft magnetic metal particles having an insulating film is not solidified so much that the soft magnetic metal particles are fixed to each other only partly or with a very small force. By sieving the heat-treated powder during classification, the soft magnetic metal particles are separated from each other, and the heat-treated powder becomes a powdery body having fluidity.
続いて、熱処理粉を圧粉成形し、圧粉体を形成する（加圧成形ステップＳＴ２）。ここでの成形条件の成形圧力は６００〜１８００ＭＰａである。熱処理粉を圧粉成形するために、圧粉磁心に相当するキャビティ形状を有する金型を用いる。このキャビティ形状は、例えば、円柱体や環状体である。上記したように、熱処理粉が良好な圧縮性を有するため、この金型のキャビティに均一に充填することができ、圧粉体は、各部位において均一な密度を有するとともに、高い強度を有する。 Subsequently, the heat-treated powder is compacted to form a compact (pressure molding step ST2). The molding pressure in the molding conditions here is 600 to 1800 MPa. In order to compact the heat-treated powder, a mold having a cavity shape corresponding to the dust core is used. The cavity shape is, for example, a cylindrical body or an annular body. As described above, since the heat treated powder has good compressibility, the cavity of this mold can be filled uniformly, and the green compact has a uniform density and high strength in each part.
最後に、圧粉体を窒素雰囲気中で焼鈍し、圧粉磁心を形成する（焼鈍ステップＳＴ３）。ここで焼鈍条件の焼鈍温度は、１０００℃〜１３００℃であり、焼鈍時間は、１５分から１８０分である。焼鈍温度が１０５０℃〜１２００℃であると好ましい。 Finally, the green compact is annealed in a nitrogen atmosphere to form a powder magnetic core (annealing step ST3). Here, the annealing temperature under the annealing conditions is 1000 ° C. to 1300 ° C., and the annealing time is 15 minutes to 180 minutes. The annealing temperature is preferably 1050 ° C to 1200 ° C.
以上より、圧粉磁心を製造することができる。圧粉磁心は、例えば、８０ＭＰａ以上の強度を有し、１０６Ωｍ以上の比抵抗を有する。 From the above, a dust core can be manufactured. The dust core has, for example, a strength of 80 MPa or more and a specific resistance of 10 6 Ωm or more.
次に、図２〜図７を参照して、実施の形態１に係る圧粉磁心の製造方法を用いて圧粉磁心を製造し、この製造した圧粉磁心を評価した結果について説明する。図２は、製造条件及び計測結果を示す表である。図３は、熱処理温度に対する鉄損を示すグラフである。図４は、実施例及び比較例の熱処理温度に対する圧環強度を示すグラフである。図５は、実施例の熱処理粉の断面組織を示す写真である。図６は、熱伝導率を示すグラフである。図７は、比較例の熱処理粉の断面組織を示す写真である。 Next, with reference to FIG. 2 to FIG. 7, a result of manufacturing a dust core using the method for manufacturing a dust core according to Embodiment 1 and evaluating the manufactured dust core will be described. FIG. 2 is a table showing manufacturing conditions and measurement results. FIG. 3 is a graph showing the iron loss with respect to the heat treatment temperature. FIG. 4 is a graph showing the crushing strength with respect to the heat treatment temperature of Examples and Comparative Examples. FIG. 5 is a photograph showing a cross-sectional structure of the heat-treated powder of the example. FIG. 6 is a graph showing the thermal conductivity. FIG. 7 is a photograph showing a cross-sectional structure of the heat-treated powder of the comparative example.
実施例１〜４は、図２に示す各製造条件で製造した。具体的には、加圧成形ステップＳＴ２では、金型温度８０℃〜１３０℃、成形圧力８００〜１４００ＭＰａとした。内径３０ｍｍ、外径３９ｍｍのリング形状をキャビティ形状として有する金型と、直径１７ｍｍの円柱形状をキャビティ形状として有する金型とを、用いた。焼鈍ステップＳＴ３では、焼鈍時間３０分〜６０分とした。 Examples 1-4 were manufactured on each manufacturing condition shown in FIG. Specifically, in the pressure molding step ST2, the mold temperature was set to 80 ° C to 130 ° C and the molding pressure was set to 800 to 1400 MPa. A mold having a ring shape having an inner diameter of 30 mm and an outer diameter of 39 mm as a cavity shape and a mold having a cylindrical shape having a diameter of 17 mm as a cavity shape were used. In the annealing step ST3, the annealing time was 30 minutes to 60 minutes.
実施例１〜４の圧粉磁心は、図２に示す各評価項目について評価された。 The dust cores of Examples 1 to 4 were evaluated for each evaluation item shown in FIG.
具体的には、まず、実施例１〜４の圧粉磁心の重量を計測し、密度を測定した。続いて、実施例１〜４の圧粉磁心について磁気測定を行った。測定項目は鉄損と比透磁率とである。鉄損の測定条件は、０．１Ｔ、２０ｋＨｚとした。続いて、実施例１〜４の圧粉磁心について圧環強度試験を行った。より具体的には、オートグラフを用いて、最大荷重を測定し、圧環強度を算出した。ＪＩＳＺ２５０７に準ずる方法を用いて測定した。続いて、実施例１〜４の圧粉磁心について熱伝導率を測定した。ここでは、フラッシュ法を用いた。
また、実施例１〜４の圧粉磁心の断面組織を観察し、圧縮性を確認した。絶縁膜厚さは、粉末のオージェ分析を行い、depthから求めた。
Specifically, first, the weight of the dust cores of Examples 1 to 4 was measured, and the density was measured. Subsequently, magnetic measurements were performed on the dust cores of Examples 1 to 4. The measurement items are iron loss and relative permeability. The measurement conditions for the iron loss were 0.1 T and 20 kHz. Then, the crushing strength test was done about the powder magnetic core of Examples 1-4. More specifically, the maximum load was measured using an autograph, and the crushing strength was calculated. It measured using the method according to JISZ2507. Subsequently, the thermal conductivity of the dust cores of Examples 1 to 4 was measured. Here, the flash method was used.
Moreover, the cross-sectional structure | tissue of the powder magnetic core of Examples 1-4 was observed, and compressibility was confirmed. The insulation film thickness was obtained from depth by performing Auger analysis of the powder.
上記した評価の結果を図２に示した。焼鈍温度が１０５０℃である場合の熱処理温度に対する圧環強度を図３に示した。焼鈍温度が１０５０℃である場合の熱処理温度に対する鉄損を図４に示した。比較例１１、実施例３及び比較例１０の圧粉磁心の熱伝導率を図６に示した。 The results of the above evaluation are shown in FIG. FIG. 3 shows the crushing strength with respect to the heat treatment temperature when the annealing temperature is 1050 ° C. The iron loss with respect to the heat treatment temperature when the annealing temperature is 1050 ° C. is shown in FIG. The thermal conductivities of the dust cores of Comparative Example 11, Example 3 and Comparative Example 10 are shown in FIG.
なお、比較例５〜１０は、図２に示す各製造条件で製造し、比較例５〜１０の圧粉磁心は、実施例１〜４と同様の方法を用いて、評価された。 In addition, Comparative Examples 5-10 were manufactured on each manufacturing condition shown in FIG. 2, and the dust cores of Comparative Examples 5-10 were evaluated using the same method as in Examples 1-4.
比較例１０の圧粉磁心の製造方法において、絶縁膜形成ステップＳＴ１に相当するステップでは、ガラスを添加し、絶縁膜として窒化膜を形成した。 In the method of manufacturing the dust core of Comparative Example 10, in a step corresponding to the insulating film forming step ST1, glass was added and a nitride film was formed as an insulating film.
なお、比較例１１は、絶縁膜形成ステップＳＴ１に相当するステップでは、絶縁膜として酸化膜のみを形成したところを除き、比較例１０と同じ製造条件で製造した。比較例１１の熱伝導率を計測した。 Comparative Example 11 was manufactured under the same manufacturing conditions as Comparative Example 10 except that only the oxide film was formed as the insulating film in the step corresponding to the insulating film forming step ST1. The thermal conductivity of Comparative Example 11 was measured.
圧粉磁心の磁気特性では、鉄損６００ｋＷ／ｍ３以下、圧環強度７０ＭＰａ越えを良好であるとして評価した。なお、絶縁膜形成ステップＳＴ１に相当するステップにおいてガラスを添加した、比較例１０の圧環強度は、７０ＭＰａである。 In the magnetic characteristics of the dust core, the iron loss of 600 kW / m 3 or less and the crushing strength exceeding 70 MPa were evaluated as good. In addition, the crushing strength of the comparative example 10 which added glass in the step corresponding to the insulating film forming step ST1 is 70 MPa.
図２に示すように、実施例１〜４の圧粉磁心では、鉄損、圧環強度が良好な値であった。一方、比較例５では、圧環強度が良好な値であるものの、鉄損が高く良好な値ではなかった。比較例６〜１０では、鉄損が良好な値であるものの、圧環強度が足りず、良好な値ではなかった。 As shown in FIG. 2, in the dust cores of Examples 1 to 4, the iron loss and the crushing strength were good values. On the other hand, in Comparative Example 5, although the crushing strength was a good value, the iron loss was high and not a good value. In Comparative Examples 6 to 10, although the iron loss was a good value, the crushing strength was insufficient and it was not a good value.
図３に示すように、熱処理温度が、８００〜１１００℃の範囲内において、鉄損はいずれも６００ｋＷ／ｍ３を下回り、良好な値を示した。一方で、熱処理温度が７００℃であるとき、鉄損は６００ｋＷ／ｍ３を上回った。 As shown in FIG. 3, when the heat treatment temperature was in the range of 800 to 1100 ° C., the iron loss was less than 600 kW / m 3 and showed a good value. On the other hand, when the heat treatment temperature was 700 ° C., the iron loss exceeded 600 kW / m 3 .
図４に示すように、熱処理温度が７００〜１０００℃の範囲内において、圧環強度はいずれも７０ＭＰａを超えており、良好な値を示した。一方で、熱処理温度が１１００℃であるとき、圧環強度は７０ＭＰａを下回った。 As shown in FIG. 4, the crushing strength exceeded 70 MPa in the heat treatment temperature range of 700 to 1000 ° C., indicating a good value. On the other hand, when the heat treatment temperature was 1100 ° C., the crushing strength was less than 70 MPa.
したがって、熱処理温度が８００〜１０００℃の範囲内（図３及ぶ図４では、熱処理領域Ｚ１）にあると好ましい。これは、鉄損及び圧環強度が良好な値を示す傾向にあるためである。 Therefore, the heat treatment temperature is preferably in the range of 800 to 1000 ° C. (the heat treatment region Z1 in FIGS. 3 and 4). This is because the iron loss and the crushing strength tend to show good values.
図５に示すように、実施例３の圧粉磁心の断面組織では、各粒子が確認された。一方、図７に示すように、比較例８の圧粉磁心の断面組織でも、同様に、各粒子が確認された。実施例３の圧粉磁心の粒子間距離は、比較例８の圧粉磁心の粒子間距離と比較して、小さい。そのため、実施例３の熱処理粉は、比較例８の熱処理粉と比較して、良好な圧縮性を有する。実施例４と比較例９も同様である。図２に示すように、圧粉磁心に含まれる粒子表面に形成される絶縁膜の厚さは、２００ｎｍ〜３５０ｎｍの範囲内にあった。 As shown in FIG. 5, each particle was confirmed in the cross-sectional structure of the dust core of Example 3. On the other hand, as shown in FIG. 7, each particle was confirmed in the cross-sectional structure of the dust core of Comparative Example 8 as well. The interparticle distance of the dust core of Example 3 is smaller than the interparticle distance of the dust core of Comparative Example 8. Therefore, the heat-treated powder of Example 3 has better compressibility than the heat-treated powder of Comparative Example 8. The same applies to Example 4 and Comparative Example 9. As shown in FIG. 2, the thickness of the insulating film formed on the particle surface included in the dust core was in the range of 200 nm to 350 nm.
図６に示すように、実施例３が、比較例１１及び比較例１０と比較して高い熱伝導率を有する。この一因として、熱伝導率の良いＡｌＮ皮膜が形成されていること、また、比較例１１及び比較例１０の圧粉磁心の製造方法において、絶縁膜形成ステップＳＴ１に相当するステップでは、ガラスを添加した一方で、実施例３の圧粉磁心の製造方法において、絶縁膜形成ステップＳＴ１では、ガラスを添加していないことが挙げられる。
より具体的には、実施例３の圧粉磁心の製造方法において、絶縁膜形成ステップＳＴ１では、ガラスを添加していないことによって、ガラス又はガラスに相当する成分を有しない絶縁膜が軟磁性金属粉の粒子の表面に形成される。ガラス又はガラスに相当する成分を有しない絶縁膜が、ガラス又はガラスに相当する成分を有する絶縁膜と比較して、高い熱伝導率を有するからである。
As shown in FIG. 6, Example 3 has a higher thermal conductivity than Comparative Example 11 and Comparative Example 10. One reason for this is that an AlN film having good thermal conductivity is formed, and in the method of manufacturing the dust cores of Comparative Example 11 and Comparative Example 10, glass is used in a step corresponding to the insulating film forming step ST1. On the other hand, in the manufacturing method of the dust core of Example 3, it can be mentioned that glass is not added in the insulating film forming step ST1.
More specifically, in the manufacturing method of the dust core of Example 3, in the insulating film forming step ST1, glass is not added, so that the insulating film not having glass or a component corresponding to glass is a soft magnetic metal. Formed on the surface of the powder particles. This is because glass or an insulating film having no component corresponding to glass has higher thermal conductivity than glass or an insulating film having a component corresponding to glass.
以上、実施の形態１の圧粉磁心の製造方法は、バインダを用いることなく、熱処理条件を変えることによって、合金粉末を構成する粒子の表面に、絶縁膜を形成する。合金粉末の流動性を減じさせないので、合金粉末を金型へ均一に装填し、合金粉末の圧縮性を良好に維持し、加圧成形を良好に行うことができる。したがって、圧粉磁心の強度低下を抑制させるとともに、圧粉磁心の電気的な絶縁性を確保することができる。 As mentioned above, the manufacturing method of the powder magnetic core of Embodiment 1 forms an insulating film on the surface of the particle | grains which comprise alloy powder by changing heat processing conditions, without using a binder. Since the fluidity of the alloy powder is not reduced, the alloy powder can be uniformly loaded into the mold, the compressibility of the alloy powder can be maintained well, and the pressure molding can be performed well. Accordingly, it is possible to suppress a decrease in strength of the dust core and to ensure electrical insulation of the dust core.
なお、本発明は上記実施の形態に限られたものではなく、趣旨を逸脱しない範囲で適宜変更することが可能である。例えば、実施の形態１に係る圧粉磁心の製造方法では、軟磁性金属粒子からなる粉を用いて圧粉磁心を製造したが、合金粉を用いて圧粉磁心を製造してもよい。合金粉は、磁性を有する粒子からなる粉であればよい。 Note that the present invention is not limited to the above-described embodiment, and can be changed as appropriate without departing from the spirit of the present invention. For example, in the method for manufacturing a powder magnetic core according to Embodiment 1, the powder magnetic core is manufactured using powder made of soft magnetic metal particles, but the powder magnetic core may be manufactured using alloy powder. The alloy powder may be a powder made of magnetic particles.
ＳＴ１ 絶縁膜形成ステップ ＳＴ２ 加圧成形ステップ
ＳＴ３ 焼鈍ステップ
ST1 Insulating film forming step ST2 Pressure forming step ST3 Annealing step
Claims (4)
前記複数の粒子は、Ａｌと、主成分としてＦｅと、を含み、
前記合金粉末を熱処理温度８００℃〜１０００℃で加熱保持した後、
前記加熱保持した前記合金粉末を加圧成形する、
圧粉磁心の製造方法。 An alloy powder containing a plurality of particles is a manufacturing method for producing a powder magnetic core by pressure molding,
The plurality of particles include Al and Fe as a main component,
After heating and holding the alloy powder at a heat treatment temperature of 800 ° C to 1000 ° C,
Pressure-molding the heated and held alloy powder,
Manufacturing method of a dust core.
請求項１に記載される圧粉磁心の製造方法。 Forming an insulating film on the surfaces of the plurality of particles of the alloy powder by heating and holding the alloy powder at a heat treatment temperature of 800C to 1000C;
The manufacturing method of the powder magnetic core described in Claim 1.
請求項２に記載される圧粉磁心の製造方法。 The insulating film has a thickness in the range of 10 nm to 500 nm.
A method for manufacturing a dust core according to claim 2.
請求項１〜３のいずれか１項に記載される圧粉磁心の製造方法。 Annealing the pressure-formed alloy powder at an annealing temperature of 1050 ° C. to 1200 ° C.,
The manufacturing method of the powder magnetic core described in any one of Claims 1-3.
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| JP2005220438A (en) * | 2004-01-06 | 2005-08-18 | Hitachi Metals Ltd | Fe-Cr-Al BASED MAGNETIC POWDER, Fe-Cr-Al BASED MAGNETIC POWDER COMPACT, AND ITS PRODUCTION METHOD |
| JP2009010180A (en) * | 2007-06-28 | 2009-01-15 | Kobe Steel Ltd | Soft magnetic powder, soft magnetic formed object, and method of manufacturing them |
| JP2015088529A (en) * | 2013-10-28 | 2015-05-07 | 株式会社豊田中央研究所 | Powder-compact magnetic core, powder for magnetic core, and manufacturing method thereof |
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| JPH03278407A (en) * | 1989-06-09 | 1991-12-10 | Matsushita Electric Ind Co Ltd | Composite magnetic material |
| JP2005220438A (en) * | 2004-01-06 | 2005-08-18 | Hitachi Metals Ltd | Fe-Cr-Al BASED MAGNETIC POWDER, Fe-Cr-Al BASED MAGNETIC POWDER COMPACT, AND ITS PRODUCTION METHOD |
| JP2009010180A (en) * | 2007-06-28 | 2009-01-15 | Kobe Steel Ltd | Soft magnetic powder, soft magnetic formed object, and method of manufacturing them |
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