JPH08127801A - Production of powder for producing magnetic sensor rotor and magnetic sensor rotor - Google Patents
Production of powder for producing magnetic sensor rotor and magnetic sensor rotorInfo
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- JPH08127801A JPH08127801A JP26880194A JP26880194A JPH08127801A JP H08127801 A JPH08127801 A JP H08127801A JP 26880194 A JP26880194 A JP 26880194A JP 26880194 A JP26880194 A JP 26880194A JP H08127801 A JPH08127801 A JP H08127801A
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- powder
- sensor rotor
- magnetic sensor
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Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、特に磁気センサーロー
ターの製造に適した焼結体用原料粉末および該粉末を用
いた磁気センサーローターの製造方法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a raw material powder for a sintered body, which is particularly suitable for manufacturing a magnetic sensor rotor, and a method for manufacturing a magnetic sensor rotor using the powder.
【０００２】[0002]
【従来の技術】磁気センサーローターの用いられる最も
一般的なものに図４に示すような自動車のＡＢＳ用セン
サー（１０１）がある。ＡＢＳ用センサの一例を図１〜
４に示す。このＡＢＳ用センサ１０１は、車輌の車軸部
たるハブ（回転軸）１０２にこれと一体に固定されるセ
ンサーローター１０３のほか、磁石１０４とコイル１０
５との組み合わせからなるセンサ本体１０６とから構成
され、センサ本体１０６の周りには磁石１０４の磁束１
０７が生じている。そして、ＡＢＳ用センサーローター
１０３には多数の穴１０８が等ピッチで形成されていて
実質的に歯車状の凹凸面となっており、車輪とともに回
転するＡＢＳ用センサーローター１０３の凹凸面が前記
磁束１０７を横切ることによりその磁束密度が変化して
コイル１０５に起電力が生じ、この電圧変化を車輪回転
数信号としてＡＢＳコントロールユニット１０９に取り
込むものである。2. Description of the Related Art The most commonly used magnetic sensor rotor is a sensor (101) for an automobile ABS as shown in FIG. An example of an ABS sensor is shown in FIGS.
4 shows. The ABS sensor 101 includes a sensor rotor 103 fixed integrally with a hub (rotating shaft) 102 which is an axle of a vehicle, a magnet 104 and a coil 10.
5 and a sensor main body 106 that is a combination of the magnetic flux 5 and the magnetic field 1 of the magnet 104 around the sensor main body 106.
07 has occurred. A large number of holes 108 are formed in the ABS sensor rotor 103 at equal pitches to form a substantially gear-shaped uneven surface, and the uneven surface of the ABS sensor rotor 103 rotating with the wheel is the magnetic flux 107. The magnetic flux density is changed by passing through the coil 105 to generate an electromotive force in the coil 105, and this voltage change is taken into the ABS control unit 109 as a wheel rotation speed signal.
【０００３】該コントロールユニット１０９は制動油圧
システムＳを介して、車輌状況に合った制動コントロー
ルを行う。ＡＢＳ用センサーローター１０３は図１，２
に示すように、薄肉のリング形状に形成され、外周に多
数のくし歯１１２が穴１０８によって仕切られ、等ピッ
チで配列した外側リング１１３と必要によって追加され
る、内側リング１１１とによって構成されている。該外
側リング１１３と内側リング１１１とは、くし歯１１２
側の周縁部１１４，１１０を折曲するカシメ加工によっ
て一体化されている。ＡＢＳ用センサーローターは車輌
の車軸部に取付けられるもので、外周に歯形を有する薄
肉のリング形状であるため、粉末冶金法に適しており、
多くがこの粉末冶金法で製造されている。The control unit 109 controls the braking through the braking hydraulic system S in accordance with the vehicle condition. ABS sensor rotor 103 is shown in Figs.
As shown in FIG. 3, the outer ring 113 is formed in a thin ring shape, and is surrounded by a large number of comb teeth 112 by holes 108, and is formed by an outer ring 113 arranged at an equal pitch and an inner ring 111, which is added if necessary. There is. The outer ring 113 and the inner ring 111 are comb teeth 112.
The peripheral portions 114 and 110 on the side are integrated by crimping. The ABS sensor rotor is attached to the axle of a vehicle and is suitable for powder metallurgy because it has a thin ring shape with teeth on the outer circumference.
Many are manufactured by this powder metallurgy method.
【０００４】このＡＢＳ用センサーローターは高い耐食
性が要求され、又、磁気センサーへ高出力信号を発せさ
せるため、高軟磁気特性が要求される。そのため下記の
２つの方法で製造されている。 （１）純鉄焼結体にＮｉメッキあるいはダクロ処理等の
表面処理を施す。 （２）磁性ステンレス粉末を焼結する。 ところで、前述のようにＡＢＳ用センサーローターは車
軸部に取付けられるため、小石等のはね返り衝突によ
り、上記（１）により得られたものは表面処理部分が剥
離し、その部分を起点に腐食が進行する恐れがある。そ
のため、最近では耐食性において信頼性のある上記
（２）の磁性ステンレス焼結体の方が一般的になりつつ
ある。磁性ステンレスとしては従来、ＳＵＳ４３０（１
７％Ｃｒ−Ｆｅ）もしくはＳＵＳ４３４（１７％Ｃｒ−
１％Ｍｏ−Ｆｅ）が用いられ、これらの粉末を原料とし
て用いた焼結体が生産されている。This ABS sensor rotor is required to have high corrosion resistance, and also to have high soft magnetic characteristics in order to generate a high output signal to the magnetic sensor. Therefore, it is manufactured by the following two methods. (1) The pure iron sintered body is subjected to surface treatment such as Ni plating or dacro treatment. (2) Sinter magnetic stainless powder. By the way, since the ABS sensor rotor is mounted on the axle as described above, the rebound collision of pebbles, etc. causes the surface-treated part of the product obtained in (1) above to peel off, and corrosion starts from that part. There is a risk of Therefore, recently, the magnetic stainless steel sintered body of (2), which is reliable in corrosion resistance, is becoming more popular. Conventionally, as magnetic stainless steel, SUS430 (1
7% Cr-Fe) or SUS434 (17% Cr-
1% Mo-Fe) is used, and a sintered body using these powders as a raw material is produced.
【０００５】[0005]
【発明が解決しようとする課題】上述のＳＵＳ４３０も
しくはＳＵＳ４３４では、北米、北欧等の寒冷地帯にお
いて道路に凍結防止剤を撒布したいわゆる塩道環境では
耐食性が不十分である。その耐食性を向上させるために
は、Ｃｒ、Ｍｏの増量が必要であるが、これは軟磁気特
性を劣化させる。焼結体の軟磁気特性を改善するために
は原料に黒鉛を添加し、真空もしくは減圧雰囲気で焼結
することにより、原料粉末の有する酸素量を減じること
が効果的である。しかし黒鉛の添加、混合によると黒鉛
の偏析が生じ、焼結体の寸法精度に問題が生じる。磁気
センサーローターとして要求される耐食性と軟磁気特性
の性能を発揮するためには所定の焼結密度が必要であ
る。焼結時の寸法収縮をなるべく小さくし、寸法精度に
優れた、所定焼結密度を有する焼結体を得るためには、
所定の成形体密度が必要となる。圧粉密度が低い粉末で
はこの所定の成形体密度を得るために、より高い成形圧
力が必要となる。成形圧力の増加は金型寿命を短くす
る。さらにより高出力のプレス成形装置が必要となり、
工業的に極めて不経済である。そこで、本発明では耐食
性、軟磁気特性に優れ、しかも金型寿命、設備投資に影
響を与えない圧粉密度の大きい粉末を提供し、優れた磁
気センサーローターを得ることを目的とするものであ
る。In the above-mentioned SUS430 or SUS434, the corrosion resistance is insufficient in a so-called salt road environment where the road is sprayed with an antifreezing agent in cold regions such as North America and Northern Europe. In order to improve its corrosion resistance, it is necessary to increase the amounts of Cr and Mo, but this deteriorates the soft magnetic characteristics. In order to improve the soft magnetic properties of the sintered body, it is effective to add graphite to the raw material and sinter it in a vacuum or reduced pressure atmosphere to reduce the amount of oxygen contained in the raw material powder. However, when graphite is added or mixed, segregation of graphite occurs, which causes a problem in dimensional accuracy of the sintered body. A predetermined sintered density is required in order to exhibit the corrosion resistance and soft magnetic properties required for a magnetic sensor rotor. In order to reduce the dimensional shrinkage during sintering as much as possible, and to obtain a sintered body that has excellent dimensional accuracy and a predetermined sintering density,
A certain compact density is required. With a powder having a low green compact density, a higher compaction pressure is required to obtain this predetermined compact density. Increasing the molding pressure shortens the mold life. Furthermore, a press molding machine with higher output is required,
It is industrially extremely uneconomical. Therefore, it is an object of the present invention to provide a powder having a large green compact density, which is excellent in corrosion resistance and soft magnetic properties, and has no influence on mold life and facility investment, and to obtain an excellent magnetic sensor rotor. .
【０００６】[0006]
【課題を解決するための手段】本発明は、重量パーセン
トで、Ｃ：０．１０超〜０．２５％、Ｓｉ：０．５０〜
１．５０％、Ｍｎ：０．１０〜０．６０％、Ｃｒ：１
８．０〜２０．０％、Ｍｏ：２．０〜４．０％、残部Ｆ
ｅおよび不可避不純物からなる合金を粉末化後焼鈍して
なることを特徴とする磁気センサーローター製造用粉末
並びに該粉末を所望形状に成形し、真空もしくは減圧雰
囲気で焼結することにより、焼結体の酸素量を粉末での
酸素量より低減せしめ、炭素量も０．０３％以下とする
ことを特徴とする磁気センサーローターの製造方法であ
る。合金の粉末化には各種の方法が考えられるが水アト
マイズ法が最適である。本発明は耐食性を向上させるた
めに、ＳＵＳ４３０もしくはＳＵＳ４３４におけるＣｒ
とＭｏの量を増加して、Ｃｒ：１８．０〜２０．０％、
Ｍｏ：２．０〜４．０％とした。このことによって劣化
する軟磁気特性を改善するために合金粉末自体に０．１
０超〜０．２５％の炭素を合金化し、後の焼結段階で、
この炭素をもって粉末中に存在する酸素量を低減し、同
時に炭素自体の量も低減せしめる。又、炭素を合金化し
たため粉末が硬化し、圧粉性が劣化するのを防ぐため、
本発明では粉末を焼鈍処理する。焼鈍処理は例えば真空
雰囲気下８５０℃で加熱後、２０℃／ｈの冷却速度で冷
却する。According to the present invention, in weight percent, C: more than 0.10 to 0.25%, Si: 0.50.
1.50%, Mn: 0.10 to 0.60%, Cr: 1
8.0-20.0%, Mo: 2.0-4.0%, balance F
A powder for manufacturing a magnetic sensor rotor, characterized by being formed by powdering an alloy consisting of e and unavoidable impurities, and a sintered body obtained by shaping the powder into a desired shape and sintering in a vacuum or reduced pressure atmosphere. Is less than the oxygen content of the powder, and the carbon content is 0.03% or less. Various methods can be considered for powdering the alloy, but the water atomizing method is most suitable. In order to improve corrosion resistance, the present invention uses Cr in SUS430 or SUS434.
And Mo to increase the amount of Cr: 18.0 to 20.0%,
Mo: 2.0 to 4.0%. In order to improve the soft magnetic properties which are deteriorated by this, the alloy powder itself has 0.1
More than 0 to 0.25% of carbon is alloyed, and in a later sintering step,
This carbon reduces the amount of oxygen present in the powder and at the same time reduces the amount of carbon itself. In addition, since carbon is alloyed to harden the powder and prevent the powder compaction from deteriorating,
In the present invention, the powder is annealed. In the annealing treatment, for example, after heating at 850 ° C. in a vacuum atmosphere, it is cooled at a cooling rate of 20 ° C./h.
【０００７】本発明における粉末の組成の限定理由は下
記のとおりである。 Ｃ：本発明における水アトマイズ粉末は通常０．２０％
以上の酸素を含有する。この酸素を真空もしくは減圧下
で焼結し、ＣＯ反応で酸素量を減ずるためには最低０．
１０％を超えるＣが必要である。しかし、粉末のＣの量
が０．２５％を超えた場合は、逆に０．０３％を超える
量のＣが焼結体中に残留する恐れがある。焼結体中のＣ
量が０．０３％以下でないと、結晶粒界にε炭化物が析
出し、耐食性と軟磁気特性を劣化させる。 Ｓｉ：水アトマイズ法における溶湯の湯流性を確保し、
かつ、粉末の酸素量をできるだけ低くするために、０．
５０％以上の量が必要である。一方、１．５０％を超え
ると粉末が硬化し、高い圧粉性が得られない。The reasons for limiting the composition of the powder in the present invention are as follows. C: The water atomized powder in the present invention is usually 0.20%
It contains the above oxygen. In order to sinter this oxygen under vacuum or reduced pressure and reduce the amount of oxygen by CO reaction, at least 0.
Greater than 10% C is required. However, when the amount of C in the powder exceeds 0.25%, on the contrary, the amount of C in excess of 0.03% may remain in the sintered body. C in the sintered body
If the amount is not 0.03% or less, ε-carbide precipitates at the grain boundaries, deteriorating corrosion resistance and soft magnetic properties. Si: Securing the flowability of the molten metal in the water atomizing method,
And, in order to make the amount of oxygen of the powder as low as possible,
An amount of 50% or more is required. On the other hand, if it exceeds 1.50%, the powder is hardened and high compacting property cannot be obtained.
【０００８】Ｍｎ：水アトマイズ法における溶湯を脱酸
し、湯流性を改善するため０．１０％以上の量が必要で
ある。０．６０％を超えると粉末の酸素量が多くなって
好ましくない。 Ｃｒ：耐食性を改善するためには１８．０％以上のＣｒ
量が必要であるが、２０．０％を超えると、軟磁気特性
が劣化するとともに粉末が硬くなり、良好な圧粉性が得
られなくなる。 Ｍｏ：耐食性改善のためには２．０％以上が必要である
が、４．０％を超えるとその効果は飽和するので不経済
である。さらにＭｏは圧粉性、軟磁気特性を低減する。 本発明における焼結条件は、真空中もしくはＡｒ、Ｎ2
の不活性雰囲気下の１０ｔｏｒｒ程度の減圧下で、１１
００〜１２５０℃、１〜３時間焼結する。この焼結によ
りＣＯ反応で酸素量が軟磁気特性を改善する程度例えば
０．１５％以下に低減する。Mn: An amount of 0.10% or more is required to deoxidize the molten metal in the water atomizing method and improve the flowability. If it exceeds 0.60%, the amount of oxygen in the powder increases, which is not preferable. Cr: 18.0% or more of Cr for improving the corrosion resistance
Although the amount is required, if it exceeds 20.0%, the soft magnetic properties are deteriorated and the powder becomes hard, so that good compacting property cannot be obtained. Mo: 2.0% or more is necessary for improving the corrosion resistance, but if it exceeds 4.0%, the effect is saturated and it is uneconomical. Furthermore, Mo reduces powder compaction and soft magnetic properties. The sintering conditions in the present invention are vacuum, Ar, N 2
Under a reduced pressure of about 10 torr in an inert atmosphere of
Sinter at 00 to 1250 ° C. for 1 to 3 hours. By this sintering, the amount of oxygen is reduced to the extent of improving the soft magnetic characteristics by CO reaction, for example, to 0.15% or less.
【０００９】[0009]
【実施例】表１に示す本発明鋼粉６種と比較鋼粉９種の
合金材料の溶湯により水アトマイズ法によってそれぞれ
の粉末を作製した。比較鋼粉１の粉末を除き、その他の
粉末を真空雰囲気下、８５０℃で加熱後、２０℃／ｈの
冷却速度で冷却して焼鈍処理した。[Examples] Powders of 6 kinds of the present invention powders and 9 kinds of comparative steel powders shown in Table 1 were prepared by a water atomizing method using molten alloy materials. Except for the powder of Comparative Steel Powder 1, other powders were heated at 850 ° C. in a vacuum atmosphere, then cooled at a cooling rate of 20 ° C./h and annealed.
【００１０】[0010]
【表１】 [Table 1]
【００１１】次に各粉末に潤滑剤としてステアリン酸亜
鉛を１％添加して混合し、６Ｔ／ｃｍ2の圧力にて１
１．３ｍｍ径×１０ｍｍ高さの円筒形形状に金型成形
し、その圧粉密度を測定した。又、上記各粉末を６．３
５ｇ／ｃｍ3の成形体密度が得られるような成形圧力
で、磁気測定と腐食試験のためにそれぞれ下記形状に成
形した。 磁気測定および寸法測定用リング：３６ｍｍ外径×２４
ｍｍ内径×３ｍｍ厚 腐食試験片：３０ｍｍ径×５ｍｍ厚 なお、Ｃ値以外は本発明の限定範囲内であるが、Ｃ値が
下限値未満である比較鋼粉６に各々黒鉛粉末０．０９
％、０．１８％を添加混合したものを比較鋼１０、１１
として同様の成形をした。Next, 1% of zinc stearate as a lubricant was added to each powder and mixed, and the mixture was mixed at a pressure of 6 T / cm 2 to 1
Molding was performed into a cylindrical shape having a diameter of 1.3 mm and a height of 10 mm, and the green compact density was measured. In addition, the above powders were added to 6.3.
For the magnetic measurement and the corrosion test, molding was performed in the following shapes under a molding pressure such that a molded body density of 5 g / cm 3 was obtained. Ring for magnetic and dimensional measurement: 36 mm outer diameter x 24
mm inner diameter × 3 mm thickness Corrosion test piece: 30 mm diameter × 5 mm thickness Note that, except for the C value, it is within the limited range of the present invention, but the C value is less than the lower limit value.
% And 0.18% were added and mixed in Comparative Steels 10 and 11
The same molding was performed.
【００１２】これらを真空中もしくはＡｒあるいはＮ2
ガス雰囲気の１０ｔｏｒｒの減圧下で１２００℃×１時
間焼結し、各々を磁気測定、寸法測定並びに腐食試験に
供した。磁気測定は直流磁化特性自動記録装置によりヒ
ステリシス曲線を描き、最大透磁率（μｍ）を算出し
た。寸法はリングの外径をマイクロメーターで測定し
た。腐食試験はＪＩＳ Ｚ ２３７１に基づく塩水噴霧
試験方法により暴露時間２００時間後の試験片の観察を
行なった。結果を表２に示す。なお、表２中塩水噴霧試
験結果は、Ａ：発錆なし、Ｂ：発錆率２５％以下、Ｃ：
発錆率２５〜５０％、Ｄ：発錆率５０％以上の４段階評
価とした。又、寸法精度は、所定寸法±１．５％以内の
良品率で、Ａ：９７％以上、：８５〜９７％、Ｃ：８５
％未満の３段階評価とした。These are placed in a vacuum or Ar or N 2
Sintering was performed at 1200 ° C. for 1 hour under a reduced pressure of 10 torr in a gas atmosphere, and each was subjected to magnetic measurement, dimension measurement, and corrosion test. For magnetic measurement, a hysteresis curve was drawn by a DC magnetization characteristic automatic recording device, and the maximum magnetic permeability (μm) was calculated. The size was measured by measuring the outer diameter of the ring with a micrometer. The corrosion test was carried out by observing the test piece after an exposure time of 200 hours by the salt spray test method based on JIS Z2371. Table 2 shows the results. The results of the salt spray test in Table 2 are: A: no rust, B: rust rate of 25% or less, C:
The rusting rate was 25 to 50%, and the rusting rate was 50% or more. In addition, the dimensional accuracy is a non-defective rate within a predetermined dimension of ± 1.5%, A: 97% or more ,: 85 to 97%, C: 85
The evaluation was made in 3 grades of less than%.
【００１３】[0013]
【表２】 [Table 2]
【００１４】表１に示すとおり、本発明鋼粉ではＣが合
金化されているにも拘らず、粉末に焼鈍処理が施されて
いるため、いずれも圧粉密度６．１２ｇ／ｃｍ3以上が
確保されている。比較鋼粉１の組成は本発明の限定成分
の範囲内であるが、粉末に焼鈍処理が施されていないた
め、粉末が硬く、圧粉密度は５．４３ｇ／ｃｍ3と本発
明鋼粉に比べて低い。比較鋼２，３，４は各々Ｃｒ，Ｍ
ｏ，Ｓｉが本発明限定成分範囲を超えているため、焼鈍
処理を施しているにも拘わらず圧粉密度は５．９３ｇ／
ｃｍ3以下で本発明鋼粉に比べて低い。本発明鋼粉はい
ずれも圧粉密度が６．１２ｇ／ｃｍ3以上と高いため、
表２に示すとおり、本発明鋼は成形圧力７Ｔ／ｃｍ2以
下の低圧力で所定成形密度の６．３５ｇ／ｃｍ3前後が
得られており、後の１２００℃焼結で所定焼結密度７．
０／ｃｍ3以上に到達している。As shown in Table 1, in the steel powder of the present invention, although C is alloyed, since the powder is annealed, the powder density is not less than 6.12 g / cm 3 in all cases. Has been secured. The composition of the comparative steel powder 1 is within the range of the limiting components of the present invention, but since the powder is not annealed, the powder is hard and the green compact density is 5.43 g / cm 3 Lower than Comparative steels 2, 3 and 4 are Cr and M, respectively
Since o and Si are out of the range of the limited components of the present invention, the green compact density is 5.93 g / in spite of the annealing treatment.
It is less than cm 3 and lower than the steel powder of the present invention. Since all of the steel powders of the present invention have a high green compact density of 6.12 g / cm 3 or more,
As shown in Table 2, the steel of the present invention has a predetermined forming density of about 6.35 g / cm 3 at a low forming pressure of 7 T / cm 2 or less. ．
It has reached 0 / cm 3 or more.
【００１５】本発明による焼結体中にはＣは０．０３％
以下、Ｏは０．１５％以下と原料粉末中の量に比べて十
分低減されている。そのため、本発明鋼すべてにおい
て、最大透磁率μｍは２７００以上で、耐食性も塩水噴
霧試験２００時間暴露後、発錆が全く見られなかった。
さらにＣは粉末粒子内に均一に合金化されているため寸
法精度においても良好な結果が得られている。比較鋼１
は焼鈍されていない、圧粉密度の低い粉末を原料として
いるため、成形圧力を１０Ｔ／ｃｍ2まで上昇させても
所定の成形密度６．３５ｇ／ｃｍ3を大きく下廻る成形
密度５．９０ｇ／ｃｍ3しか得られなかった。従って焼
結密度も低くなり、軟磁気特性、耐食性共に劣化してい
る。成形圧力が１０Ｔ／ｃｍ2を超えると金型が損傷す
る恐れがあるため、試験は１０Ｔ／ｃｍ2に抑えた。C is 0.03% in the sintered body according to the present invention.
Hereinafter, O is 0.15% or less, which is sufficiently reduced as compared with the amount in the raw material powder. Therefore, in all the steels of the present invention, the maximum magnetic permeability μm was 2700 or more, and corrosion resistance was not observed at all after 200 hours of salt spray test.
Furthermore, since C is uniformly alloyed in the powder particles, good results are obtained in dimensional accuracy. Comparative steel 1
Is a raw material which is not annealed and has a low compaction density, so even if the compaction pressure is increased to 10 T / cm 2 , the compaction density is 5.90 g / cm 3 which is far below the prescribed compaction density of 6.35 g / cm 3. Only cm 3 was obtained. Therefore, the sintered density becomes low, and the soft magnetic characteristics and the corrosion resistance are deteriorated. If the molding pressure exceeds 10 T / cm 2 , the mold may be damaged, so the test was limited to 10 T / cm 2 .
【００１６】比較鋼２，３，４は前述の如く圧粉密度の
低い粉末を原料としているため、所定の成形密度６．３
５ｇ／ｃｍ3程度を得るために８．８Ｔ／ｃｍ2以上の成
形圧力を必要としている。成形圧力が８Ｔ／ｃｍ2を超
えると、金型の寿命が短くなるばかりでなく、プレス設
備も大型化し、設備費が高くなり工業的には適切な条件
とは言えない。さらに比較鋼２，３は各々Ｃｒ，Ｍｏが
限定成分上限を超えているため最大透磁率μｍが１６７
０、１６２０と本発明鋼に比べ極めて低い。比較鋼４は
Ｃｒが下限値以下であるため耐食性の点で劣っている。
比較鋼５は本発明限定成分範囲のＭｏが下限値未満、Ｍ
ｎが上限値を超える粉末を原料としているため、成形圧
力６．２Ｔ／ｃｍ2と低い圧力で所定成形密度の６．３
５ｇ／ｃｍ3前後が得られるものの、Ｍｎ量が多いため
焼結体のＯが０．４７％と高く、最大透磁率μｍは１３
１０と低い。又、Ｍｏ量が低いため塩水噴霧試験でも発
錆が認められる。Since the comparative steels 2, 3 and 4 are made of powder having a low green compact density as described above, they have a predetermined compacting density of 6.3.
A molding pressure of 8.8 T / cm 2 or more is required to obtain about 5 g / cm 3 . If the molding pressure exceeds 8 T / cm 2 , not only the life of the mold is shortened, but also the press equipment becomes large and the equipment cost becomes high, which is not an industrially appropriate condition. Further, in Comparative Steels 2 and 3, the maximum magnetic permeability μm is 167 because Cr and Mo exceed the upper limit of the limiting component, respectively.
0, 1620, which is extremely low as compared with the steels of the present invention. Comparative Steel 4 is inferior in corrosion resistance since Cr is below the lower limit.
In Comparative Steel 5, Mo in the component range of the present invention is less than the lower limit value, M
Since the powder whose n exceeds the upper limit is used as the raw material, the molding pressure of 6.2 T / cm 2 is as low as 6.3 and the predetermined molding density is 6.3.
Although about 5 g / cm 3 was obtained, the O content of the sintered body was as high as 0.47% and the maximum magnetic permeability μm was 13 because the Mn content was large.
As low as 10. Further, since the amount of Mo is low, rust is recognized even in the salt spray test.
【００１７】比較鋼６は本発明限定成分範囲からＣが下
限値を下廻ったもので、そのため焼結中において粉末の
Ｏを還元するためのＣが不足し、焼結後のＯ量が０．３
２％と高い。そのため最大透磁率μｍが１６７０と本発
明鋼より低い値となっている。比較鋼７はＣ値が本発明
限定成分範囲の上限を超えたもので焼結中のＣＯ反応で
Ｏは０．０５％まで低減するが、Ｃが０．０７％残留し
てしまう。その結果、最大透磁率、耐食性ともに劣化す
る。In Comparative Steel 6, C was below the lower limit value in the range of the restricted components of the present invention, so that C for reducing O in the powder during sintering was insufficient, and the amount of O after sintering was 0. Three
It is as high as 2%. Therefore, the maximum magnetic permeability μm is 1670, which is lower than that of the steel of the present invention. Comparative Steel 7 has a C value exceeding the upper limit of the component range of the present invention, and O is reduced to 0.05% by the CO reaction during sintering, but 0.07% of C remains. As a result, the maximum magnetic permeability and the corrosion resistance are deteriorated.
【００１８】比較鋼８はＳＵＳ４３０、比較鋼９はＳＵ
Ｓ４３４相当組成の粉末を原料としたものであるが、い
ずれも本発明鋼に比べＣｒ，Ｍｏの成分が低いため、塩
水噴霧試験において発錆する。又、本発明鋼に比べ粉末
でのＣ量が少ないため焼結体の酸素が高くなり最大透磁
率μｍも低い値となっている。比較鋼１０，１１はＣ値
が本発明限定成分範囲の下限未満であるが、その他の成
分は限定成分範囲内である比較鋼粉６を原料とし、それ
に黒鉛粉末を各々０．１１％、０．１８％添加混合し、
成形、焼結したものである。本発明鋼同様、焼結体のＯ
は０．１５％以下に低減し、最大透磁率、塩水噴霧試験
で良好な結果が得られているが、黒鉛添加によるＣ偏析
が原因して寸法精度において致命的欠陥をきたしてい
る。Comparative steel 8 is SUS430, comparative steel 9 is SU
Although a powder having a composition equivalent to S434 is used as a raw material, both have low Cr and Mo components as compared with the steels of the present invention, and thus rust in a salt spray test. Further, since the amount of C in the powder is smaller than that of the steel of the present invention, the oxygen content of the sintered body is high and the maximum magnetic permeability μm is also low. Comparative steels 10 and 11 have C values less than the lower limit of the limiting component range of the present invention, but other components are made from comparative steel powder 6 which is within the limiting component range, and graphite powder is added to each of 0.11% and 0%. Add 18% and mix,
It is molded and sintered. Like the steel of the present invention,
Was reduced to 0.15% or less, and good results were obtained in the maximum magnetic permeability and salt spray tests, but there was a fatal defect in dimensional accuracy due to C segregation due to addition of graphite.
【００１９】[0019]
【発明の効果】本発明によれば圧粉密度の高い粉末が得
られ、したがって、低い成形圧力で所定の成形密度が得
られ、又、Ｃが粉末粒子内に均一に合金化されているた
め焼結体の寸法精度も優れている。さらに、耐食性並び
に軟磁性特性において優れた製品が得られる。EFFECTS OF THE INVENTION According to the present invention, a powder having a high green compact density can be obtained. Therefore, a desired compacting density can be obtained with a low compacting pressure, and C is uniformly alloyed in the powder particles. The dimensional accuracy of the sintered body is also excellent. Further, a product excellent in corrosion resistance and soft magnetic properties can be obtained.
【図１】ＡＢＳセンサーローターの斜視図である。FIG. 1 is a perspective view of an ABS sensor rotor.
【図２】図１の断面図である。FIG. 2 is a cross-sectional view of FIG.
【図３】ＡＢＳセンサーローターを用いた制動コントロ
ールの説明図である。FIG. 3 is an explanatory diagram of braking control using an ABS sensor rotor.
【図４】自動車におけるＡＢＳセンサーローターの取付
説明図である。FIG. 4 is an explanatory view of mounting an ABS sensor rotor in an automobile.
１０１ ＡＢＳ用センサ １０２ ハブ １０３ センサーロータ １０４ 磁石 １０５ コイル １０６ センサ本体 １０７ 磁束 １０８ 穴 １０９ ＡＢＳコントロールユニット １１０ 周縁部（くし歯の） １１１ 内側リング １１２ くし歯 １１３ 外側リング １１４ 周縁部（くし歯の） 101 ABS Sensor 102 Hub 103 Sensor Rotor 104 Magnet 105 Coil 106 Sensor Main Body 107 Magnetic Flux 108 Hole 109 ABS Control Unit 110 Peripheral Edge (Comb) 111 Inner Ring 112 Comb 113 Outer Ring 114 Peripheral (Comb)
───────────────────────────────────────────────────── フロントページの続き (72)発明者 曽田 裕二 東京都江東区東雲１−９−31 三菱製鋼株 式会社技術開発センター内 (72)発明者 岸 雄治 神奈川県横浜市神奈川区宝町二番地 日産 自動車株式会社内 (72)発明者 高山 康 神奈川県横浜市神奈川区宝町二番地 日産 自動車株式会社内 ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Yuji Soda 1-9-31 Shinonome, Koto-ku, Tokyo Mitsubishi Steel Mfg. Co., Ltd.Technical Development Center (72) Inventor Yuji Kishi No. 2 Takaracho, Kanagawa-ku, Yokohama, Kanagawa Prefecture Nissan Automobile Co., Ltd. (72) Inventor Yasushi Takayama 2 Takaracho, Kanagawa-ku, Yokohama-shi, Kanagawa Nissan Motor Co., Ltd.
Claims (3)
０．２５％、Ｓｉ：０．５０〜１．５０％、Ｍｎ：０．
１０〜０．６０％、Ｃｒ：１８．０〜２０．０％、Ｍ
ｏ：２．０〜４．０％、残部Ｆｅおよび不可避不純物か
らなる合金を粉末化後焼鈍してなることを特徴とする磁
気センサーローター製造用粉末。1. By weight percent, C: greater than 0.10.
0.25%, Si: 0.50 to 1.50%, Mn: 0.
10 to 0.60%, Cr: 18.0 to 20.0%, M
o: A powder for manufacturing a magnetic sensor rotor, characterized by being annealed after powdering an alloy consisting of 2.0 to 4.0% and the balance Fe and unavoidable impurities.
項１記載の磁気センサーローター製造用粉末。2. The powder for producing a magnetic sensor rotor according to claim 1, wherein the powdering is performed by a water atomizing method.
し、真空もしくは減圧雰囲気で焼結することにより、焼
結体の酸素量を粉末での酸素量より低減せしめ炭素量も
０．０３％以下とすることを特徴とする磁気センサーロ
ーターの製造方法。3. The powder according to claim 1 is molded into a desired shape and sintered in a vacuum or reduced pressure atmosphere to reduce the oxygen content of the sintered body to a value lower than the oxygen content of the powder, and also the carbon content is 0.03. % Or less, a method for manufacturing a magnetic sensor rotor.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP26880194A JP3412719B2 (en) | 1994-11-01 | 1994-11-01 | Powder for manufacturing magnetic sensor rotor and method for manufacturing magnetic sensor rotor |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP26880194A JP3412719B2 (en) | 1994-11-01 | 1994-11-01 | Powder for manufacturing magnetic sensor rotor and method for manufacturing magnetic sensor rotor |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH08127801A true JPH08127801A (en) | 1996-05-21 |
| JP3412719B2 JP3412719B2 (en) | 2003-06-03 |
Family
ID=17463461
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP26880194A Expired - Fee Related JP3412719B2 (en) | 1994-11-01 | 1994-11-01 | Powder for manufacturing magnetic sensor rotor and method for manufacturing magnetic sensor rotor |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3412719B2 (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106659104A (en) * | 2016-12-28 | 2017-05-10 | 南京南大波平电子信息有限公司 | Moisture-proof and antioxidant low-frequency electromagnetic wave absorbing materials |
| CN106636950A (en) * | 2016-12-28 | 2017-05-10 | 南京南大波平电子信息有限公司 | Moisture-resistant and oxidation-resistant electromagnetic wave absorbent |
| JP2018535312A (en) * | 2015-09-25 | 2018-11-29 | ローベルト ボツシユ ゲゼルシヤフト ミツト ベシユレンクテル ハフツングＲｏｂｅｒｔ Ｂｏｓｃｈ Ｇｍｂｈ | Parts made of sintered material and manufacturing method thereof |
| JP2020161695A (en) * | 2019-03-27 | 2020-10-01 | Tdk株式会社 | Soft magnetic metal powder |
-
1994
- 1994-11-01 JP JP26880194A patent/JP3412719B2/en not_active Expired - Fee Related
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2018535312A (en) * | 2015-09-25 | 2018-11-29 | ローベルト ボツシユ ゲゼルシヤフト ミツト ベシユレンクテル ハフツングＲｏｂｅｒｔ Ｂｏｓｃｈ Ｇｍｂｈ | Parts made of sintered material and manufacturing method thereof |
| CN106659104A (en) * | 2016-12-28 | 2017-05-10 | 南京南大波平电子信息有限公司 | Moisture-proof and antioxidant low-frequency electromagnetic wave absorbing materials |
| CN106636950A (en) * | 2016-12-28 | 2017-05-10 | 南京南大波平电子信息有限公司 | Moisture-resistant and oxidation-resistant electromagnetic wave absorbent |
| JP2020161695A (en) * | 2019-03-27 | 2020-10-01 | Tdk株式会社 | Soft magnetic metal powder |
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| Publication number | Publication date |
|---|---|
| JP3412719B2 (en) | 2003-06-03 |
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