JP2009084646A - Soft magnetic steel member, soft magnetic steel component, and method for producing the same - Google Patents
Soft magnetic steel member, soft magnetic steel component, and method for producing the same Download PDFInfo
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本発明は、軟磁性鋼部品を製造するための軟磁性鋼材、並びにそれから得られる軟磁性鋼部品(例えば自動車用センサ等の鉄心)、および軟磁性鋼部品の製造方法に関する。 The present invention relates to a soft magnetic steel material for producing a soft magnetic steel part, a soft magnetic steel part obtained from the soft magnetic steel part (for example, an iron core such as an automobile sensor), and a method for producing the soft magnetic steel part.
自動車電装部品等における磁気回路を構成する鋼部品には、省電力化と応答性向上のため、低い外部磁界で容易に磁化し、且つ保磁力が小さいといった特性が要求される。このため上記鋼部品を製造するための材料として、部品内部の磁束密度が外部磁界に応答し易い軟磁性鋼材が一般に使用されている。 Steel parts constituting a magnetic circuit in automobile electrical parts and the like are required to have characteristics such as easy magnetization with a low external magnetic field and low coercive force in order to save power and improve responsiveness. For this reason, as a material for manufacturing the steel part, a soft magnetic steel material in which the magnetic flux density inside the part easily responds to an external magnetic field is generally used.
上記電装部品のうち、直流特性が重要な部品には、例えばC量が0.01%以下の極低炭素鋼が用いられ、また交流特性が重要な部品には、電磁ステンレスなどの高い電気抵抗を有する材料が一般に用いられている。 Among the above-mentioned electrical components, for example, extremely low carbon steel having a C content of 0.01% or less is used for components in which DC characteristics are important, and high electrical resistance such as electromagnetic stainless steel is used for components in which AC characteristics are important. The material which has is generally used.
しかし近年、電装部品の制御を司るセンサ部品の高性能化が大きく伸展し、高周波−低磁界での磁気特性に対する要望が増加している。交流用磁気材料では、渦電流による磁気遮蔽効果を抑制するため、直流用磁気材料に比べて電気抵抗率を増加させる必要があり、100μΩcm程度の電気抵抗率を有する電磁ステンレス材料が用いられることが多い。しかし、電気抵抗率の増加、すなわち伝導電子の散乱確立の増加は、熱伝導率の低下をもたらすため、部品の小型・軽量化や部品特性の安定化を図る上で、大きな障害となりつつある。また、電気抵抗率の増加を目的に合金元素を増量添加することは、磁界を引加した際に生じる材料変形(磁歪)を助長するため、高精度の検出感度が求められるセンサ部品等に電磁ステンレス等を用いることには限界があった。 However, in recent years, the performance of sensor parts that control electric parts has been greatly improved, and the demand for magnetic characteristics in a high frequency-low magnetic field has increased. In the magnetic material for alternating current, in order to suppress the magnetic shielding effect due to the eddy current, it is necessary to increase the electrical resistivity as compared with the magnetic material for direct current, and an electromagnetic stainless steel material having an electrical resistivity of about 100 μΩcm may be used. Many. However, an increase in electrical resistivity, that is, an increase in the establishment of conduction electron scattering leads to a decrease in thermal conductivity, and is thus becoming a major obstacle to achieving a reduction in size and weight of components and stabilization of component characteristics. In addition, the addition of an increased amount of alloying elements for the purpose of increasing electrical resistivity promotes material deformation (magnetostriction) that occurs when a magnetic field is applied. There was a limit to using stainless steel or the like.
本発明はこの様な事情に鑑みてなされたものであって、その目的は、磁気焼鈍後に電磁ステンレスなみの優れた交流磁気特性および低磁歪を実現することのできる軟磁性鋼材、およびこの軟磁性鋼材を用いて得られる、交流磁気特性に優れかつ低磁歪である軟磁性鋼部品およびその製造方法を提供することにある。 The present invention has been made in view of such circumstances, and an object of the present invention is to provide a soft magnetic steel material capable of realizing excellent AC magnetic characteristics and low magnetostriction similar to those of electromagnetic stainless steel after magnetic annealing, and the soft magnetic material. An object of the present invention is to provide a soft magnetic steel part obtained by using a steel material and having excellent AC magnetic characteristics and low magnetostriction, and a method for producing the same.
本発明に係る軟磁性鋼材とは、
C:0.002〜0.050%(質量%の意味、以下同じ)、
Si:1.5〜2.8%、
Mn:0.2〜0.8%、
P:0.02%以下(0%を含まない)、
S:0.02〜0.10%、
Cu:0.1%以下(0%を含まない)、
Ni:1.0%以下(0%を含まない)、
Cr:1.0%以下(0%を含まない)、
Al:0.05〜1.0%、
N:0.0040%以下(0%を含まない)、
O:0.0100%以下(0%を含まない)、
5≦Mn/S≦50、
Si+Mn+Cr≦4.0を満たし、
残部:鉄および不可避不純物からなり、
金属組織に占めるフェライト相が95%以上であり、かつ
該フェライト中の炭化物およびMnSの最大粒径(長径と短径の平均値)が20μm以下であって、
常温(20℃)での電気抵抗率が40〜60μΩcmであり、かつ直流初期透磁率が4000以上であるところに特徴を有する。
With the soft magnetic steel material according to the present invention,
C: 0.002 to 0.050% (meaning mass%, the same shall apply hereinafter)
Si: 1.5 to 2.8%,
Mn: 0.2 to 0.8%
P: 0.02% or less (excluding 0%),
S: 0.02-0.10%,
Cu: 0.1% or less (excluding 0%),
Ni: 1.0% or less (excluding 0%),
Cr: 1.0% or less (excluding 0%),
Al: 0.05 to 1.0%,
N: 0.0040% or less (excluding 0%),
O: 0.0100% or less (excluding 0%),
5 ≦ Mn / S ≦ 50,
Satisfying Si + Mn + Cr ≦ 4.0,
The balance: iron and inevitable impurities
The ferrite phase occupying the metal structure is 95% or more, and the maximum particle size (average value of major axis and minor axis) of carbide and MnS in the ferrite is 20 μm or less,
It is characterized in that the electrical resistivity at normal temperature (20 ° C.) is 40 to 60 μΩcm, and the initial DC magnetic permeability is 4000 or more.
本発明の軟磁性鋼材は、更に他の元素として、B:0.0015〜0.005%を含んでいてもよい。 The soft magnetic steel material of the present invention may further contain B: 0.0015 to 0.005% as another element.
本発明は、上記軟磁性鋼材を用いて得られる軟磁性鋼部品も含むものであり、該鋼部品は、上記成分組成を満たし、金属組織に占めるフェライト相が95%以上であり、かつJIS G 0551で規定するフェライト結晶粒度番号が3以下であるところに特徴を有する。 The present invention also includes a soft magnetic steel part obtained by using the soft magnetic steel material. The steel part satisfies the above component composition, the ferrite phase occupying the metal structure is 95% or more, and JIS G It is characterized in that the ferrite grain size number specified by 0551 is 3 or less.
また本発明は、上記軟磁性鋼部品を製造する方法も規定するものであって、該方法は、上記軟磁性鋼材を、形状加工した後、真空中または不活性ガス雰囲気下、850〜1000℃で3時間以上焼鈍処理することにより、JIS G 0551で規定するフェライト結晶粒度番号を3以下とするところに特徴を有する。 The present invention also defines a method for producing the soft magnetic steel part, which is formed at 850 to 1000 ° C. in a vacuum or under an inert gas atmosphere after the soft magnetic steel material is shaped. Is characterized in that the ferrite grain size number specified in JIS G 0551 is made 3 or less by annealing for 3 hours or more.
本発明によれば、磁気焼鈍を施すことにより、優れた交流磁気特性を示すと共に低磁歪を示す軟磁性鋼材が得られる。更に、該鋼材を用いて部品成形後に磁気焼鈍を施すことにより、電磁ステンレスと同等もしくはそれ以上の交流磁気特性を示すと共に、磁界を印加した際の磁歪による部品変形の少ない、自動車用センサ部品(鉄心材)等の様な自動車部品や電車、船舶用の電装部品を、高歩留まりかつ低コストで提供できる。 According to the present invention, by performing magnetic annealing, a soft magnetic steel material that exhibits excellent AC magnetic characteristics and low magnetostriction can be obtained. Further, by subjecting the steel material to magnetic annealing after molding, an automotive sensor component that exhibits AC magnetic characteristics equivalent to or higher than that of electromagnetic stainless steel and that is less deformed by magnetostriction when a magnetic field is applied ( It is possible to provide automobile parts such as iron cores) and electric parts for trains and ships with high yield and low cost.
本発明者は、上記磁歪を低減させるには、直流透磁率を4000以上と高くすることが大変有効であり、この様に直流透磁率を高めることによって、少ない磁界侵入領域で目的の磁束量を確保でき、交流磁界を引加した際の磁壁移動(磁束移動)に伴う磁歪を大幅に低減できることを見出した。更に、電気抵抗率を40μΩcm以上とすることが電磁ステンレス並みの優れた交流磁気特性を確保する為に不可欠であり、また、上記電気抵抗率を60μΩcm以下に制御すると共に上記直流透磁率を4000以上とすることで、低磁歪を実現できる、ことに着目して、これら磁気特性(更には冷間鍛造性等)に影響を及ぼす鋼材の成分組成、金属組織や析出物等について様々な角度から実験を行い検討してきた。 In order to reduce the magnetostriction, the present inventor is very effective in increasing the DC permeability to 4000 or more. By increasing the DC permeability in this way, the target magnetic flux amount can be reduced in a small magnetic field intrusion region. It was found that the magnetostriction accompanying the domain wall movement (magnetic flux movement) when an AC magnetic field is applied can be greatly reduced. Furthermore, it is indispensable to set the electric resistivity to 40 μΩcm or more in order to ensure the excellent AC magnetic characteristics similar to those of electromagnetic stainless steel, and the electric resistivity is controlled to 60 μΩcm or less and the DC permeability is 4000 or more. Focusing on the fact that low magnetostriction can be realized, the composition of steel materials that affect these magnetic properties (and cold forgeability, etc.), the metal structure and precipitates, etc. are tested from various angles. Have been considered.
そしてその結果、成分組成を制御し、粗大化させたフェライト組織中の固溶元素(特にC、N、Cr)およびMnS硫化物の分散を制御すればよいことを見出し、本発明に想到した。以下、本発明について詳述する。 As a result, the inventors have found that it is only necessary to control the component composition and control the dispersion of solid solution elements (particularly C, N, Cr) and MnS sulfide in the coarsened ferrite structure, and have arrived at the present invention. Hereinafter, the present invention will be described in detail.
〈フェライト中の炭化物およびMnSの最大粒径(長径と短径の平均値):20μm以下〉
軟磁性鋼材の磁気特性は、材料内部を移動する磁束を固定するエネルギー量に関係しており、フェライト結晶粒の大きさや、析出物の磁気的性質や分布形態で異なる。通常、フェライト組織中に析出物が多数存在する場合、磁気焼鈍時の結晶粒成長を妨げるため、磁壁移動の抵抗となる結晶粒界を十分に減少できず、また析出物自体も磁壁を縛束するため、外部磁界に対する応答性、即ち磁気特性が低下する結果となる。
<Maximum particle size of carbide and MnS in ferrite (average value of major axis and minor axis): 20 μm or less>
The magnetic characteristics of the soft magnetic steel material are related to the amount of energy for fixing the magnetic flux moving inside the material, and differ depending on the size of the ferrite crystal grains, the magnetic properties and the distribution form of the precipitates. Usually, when there are a large number of precipitates in the ferrite structure, it prevents the grain growth during magnetic annealing, so the grain boundary that becomes the resistance of domain wall movement cannot be reduced sufficiently, and the precipitate itself also binds the domain wall. As a result, the responsiveness to the external magnetic field, that is, the magnetic characteristics are deteriorated.
そこで本発明では、後述する実施例の方法で測定するフェライト中の炭化物(具体的にはFe3C、CrC)およびMnSの最大粒径(長径と短径の平均値)を20μm以下と規定した。好ましくは5μm以下である。 Therefore, in the present invention, the maximum particle size (average value of major axis and minor axis) of carbides (specifically, Fe 3 C, CrC) and MnS in ferrite measured by the method of the example described later is defined as 20 μm or less. . Preferably it is 5 micrometers or less.
〈5≦Mn/S≦50〉
上記フェライト中のMnSを微細化させるには、鋼中のMn量とS量の比:Mn/Sを50以下に抑えるのがよい。好ましくは20以下である。しかしMn/Sの値が低すぎると、FeSが結晶粒界に析出し、磁束密度の低下をもたらすため、Mn/Sは5以上となるようにする。好ましくは7以上、より好ましくは10以上である。
<5 ≦ Mn / S ≦ 50>
In order to make MnS in the ferrite finer, the ratio of Mn content to S content in steel: Mn / S should be suppressed to 50 or less. Preferably it is 20 or less. However, if the value of Mn / S is too low, FeS precipitates at the grain boundaries and causes a decrease in magnetic flux density, so Mn / S is set to 5 or more. Preferably it is 7 or more, More preferably, it is 10 or more.
〈Si+Mn+Cr≦4.0〉
Si、MnおよびCrの合計量が多いと、転炉出鋼温度が1750℃を超えて転炉耐火物の損傷が大きく、生産性の悪化を招くと共に、不純物が混入し易くなり、磁束密度に悪影響を及ぼす。よって本発明では、これらSi、MnおよびCrの合計量を4.0%以下とする。好ましくは合計で3.5%以下である。
<Si + Mn + Cr ≦ 4.0>
When the total amount of Si, Mn, and Cr is large, the converter steel temperature exceeds 1750 ° C. and the converter refractory is greatly damaged. Adversely affect. Therefore, in the present invention, the total amount of Si, Mn and Cr is 4.0% or less. Preferably, it is 3.5% or less in total.
〈C:0.002〜0.05%〉
Cは、鋼材の強度と延性のバランスを支配する元素であり、含有量が少ないほど強度は低下し、延性は向上する。またCは鋼中に固溶し、部品成型時にひずみ時効が生じるので極低Cが望ましく、磁気特性の面からも極低Cが好ましい。本発明では、電磁ステンレスなみ若しくはそれ以上の磁気特性を満足する観点から、C量の上限を0.05%と定めた。C量は、好ましくは0.03%以下である。
<C: 0.002 to 0.05%>
C is an element that governs the balance between the strength and ductility of the steel material. The smaller the content, the lower the strength and the ductility is improved. Further, C is dissolved in steel and strain aging occurs at the time of component molding, so that extremely low C is desirable, and extremely low C is also preferable from the viewpoint of magnetic properties. In the present invention, the upper limit of the amount of C is set to 0.05% from the viewpoint of satisfying magnetic characteristics similar to those of electromagnetic stainless steel or higher. The amount of C is preferably 0.03% or less.
一方、C量を低減しすぎると、部品の強度が低下し、且つ電気抵抗、ひいては交流磁束密度が低下する。そこでC量の下限を0.002%と定めた。C量は、好ましくは0.010%以上である。 On the other hand, if the amount of C is reduced too much, the strength of the parts decreases, and the electrical resistance, and consequently the alternating magnetic flux density, decreases. Therefore, the lower limit of the C amount is set to 0.002%. The amount of C is preferably 0.010% or more.
〈Si:1.5〜2.8%〉
Siは、溶製時に脱酸剤として用いられるものであり、また部品の交流磁束密度を向上させる作用を有する。このような作用を充分に発揮させるため、Si量の下限を1.5%と定めた。Si量は、好ましくは1.8%以上である。しかしSi量が過剰であると、磁気特性と鋼材の冷間鍛造性が劣化する。そこで本発明では、電磁ステンレス並みの磁気特性の確保と部品成型時の冷間鍛造性を確保する観点から、Si量の上限を2.8%と定めた。Si量は好ましくは2.5%以下である。
<Si: 1.5 to 2.8%>
Si is used as a deoxidizer at the time of melting, and has an effect of improving the AC magnetic flux density of parts. In order to sufficiently exhibit such an action, the lower limit of the Si amount was set to 1.5%. The amount of Si is preferably 1.8% or more. However, if the amount of Si is excessive, the magnetic properties and the cold forgeability of the steel material deteriorate. Therefore, in the present invention, the upper limit of the Si amount is set to 2.8% from the viewpoint of ensuring the magnetic characteristics similar to those of electromagnetic stainless steel and ensuring the cold forgeability at the time of molding the parts. The amount of Si is preferably 2.5% or less.
〈Mn:0.2〜0.8%〉
Mnは、溶製時に脱酸剤として用いられるものであり、また鋼中のSと結合し、Sによる脆化を抑制する作用も有する。またMnとSは、MnS析出物、または酸化物の周囲にMnSが存在する複合析出物(以下、これらを「MnS含有析出物」と省略することがある)を形成して、部品の電気抵抗を向上させる作用も有する。部品の電気抵抗が向上すると、渦電流および鉄損が抑制され、交流磁束密度の低下を防止することができる。これらの作用を充分に発揮させるために、Mn量の下限を0.2%と定めた。Mn量は、好ましくは0.3%以上、より好ましくは0.4%以上である。しかしMn量が過剰になると、磁気モーメントが低下し、電気抵抗向上による効果が減殺され、かえって交流磁束密度が低下する。そこでMn量の上限を0.8%と定めた。Mn量は、好ましくは0.7%以下、より好ましくは0.6%以下である。
<Mn: 0.2 to 0.8%>
Mn is used as a deoxidizer during melting, and also has an action of binding to S in steel and suppressing embrittlement due to S. Mn and S form MnS precipitates or composite precipitates in which MnS is present around the oxide (hereinafter, these may be abbreviated as “MnS-containing precipitates”), and the electrical resistance of the component It also has an effect of improving. When the electrical resistance of the component is improved, eddy current and iron loss are suppressed, and a decrease in AC magnetic flux density can be prevented. In order to fully exhibit these actions, the lower limit of the amount of Mn was set to 0.2%. The amount of Mn is preferably 0.3% or more, more preferably 0.4% or more. However, when the amount of Mn becomes excessive, the magnetic moment is lowered, the effect of improving the electric resistance is diminished, and the alternating magnetic flux density is lowered. Therefore, the upper limit of the amount of Mn is set to 0.8%. The amount of Mn is preferably 0.7% or less, more preferably 0.6% or less.
〈P:0.02%以下(0%を含まない)〉
Pは、粒界偏析して、冷間鍛造性および磁気特性の低下を招く。そこでP量は、できる限り低減されていることが好ましく、本発明ではP量を0.02%以下、好ましくは0.01%以下に抑える。
<P: 0.02% or less (excluding 0%)>
P segregates at the grain boundaries and causes a decrease in cold forgeability and magnetic properties. Therefore, the P amount is preferably reduced as much as possible. In the present invention, the P amount is 0.02% or less, preferably 0.01% or less.
〈S:0.02〜0.10%〉
Sは、MnとMnS含有析出物を形成し、電気抵抗を増加させて、部品の交流磁束密度を向上させる作用を有する。この作用を充分に発揮させるために、本発明ではS量の下限を0.02%と定めた。S量は、好ましくは0.025%以上、より好ましくは0.030%以上である。しかしS量が過剰になると、硫化物が結晶粒界に析出するため、鋼材の冷間鍛造性が劣化する。そこでS量の上限を、0.10%と定めた。S量は、好ましくは0.08%以下、より好ましくは0.06%以下である。
<S: 0.02-0.10%>
S forms an Mn and MnS-containing precipitate, increases electric resistance, and has an effect of improving the AC magnetic flux density of the component. In order to fully exhibit this action, in the present invention, the lower limit of the amount of S is set to 0.02%. The amount of S is preferably 0.025% or more, more preferably 0.030% or more. However, when the amount of S becomes excessive, sulfide precipitates at the grain boundaries, so that the cold forgeability of the steel material deteriorates. Therefore, the upper limit of the amount of S is set to 0.10%. The amount of S is preferably 0.08% or less, more preferably 0.06% or less.
〈Cu:0.1%以下(0%を含まない)〉
Cuは、電気抵抗を増加させる作用を有し、渦電流の発生を抑制して、交流磁束密度を向上させるのに有用な元素である。この作用を十分に発揮させるため、Cu量は、好ましくは0.01%以上、より好ましくは0.02%以上、さらに好ましくは0.03%以上とするのがよい。しかしCu量が過剰になると、磁気モーメントが低下して、かえって交流磁束密度が低下する。そこでCu量の上限を0.1%と定めた。Cu量は、好ましくは0.08%以下、より好ましくは0.06%以下である。
<Cu: 0.1% or less (excluding 0%)>
Cu has an effect of increasing electric resistance, is an element useful for suppressing the generation of eddy currents and improving the alternating magnetic flux density. In order to exhibit this effect sufficiently, the amount of Cu is preferably 0.01% or more, more preferably 0.02% or more, and further preferably 0.03% or more. However, when the amount of Cu becomes excessive, the magnetic moment decreases, and on the contrary, the alternating magnetic flux density decreases. Therefore, the upper limit of the Cu amount is set to 0.1%. The amount of Cu is preferably 0.08% or less, more preferably 0.06% or less.
〈Ni:1.0%以下(0%を含まない)〉
Niも、Cuと同様に電気抵抗を増加させる作用を有する。この作用を十分に発揮させるため、Ni量は、好ましくは0.01%以上、より好ましくは0.02%以上、さらに好ましくは0.03%以上とするのがよい。しかしNi量が過剰になると、Cuと同様に磁気モーメントが低下する。そこでNi量の上限を1.0%と定めた。Ni量は、好ましくは0.5%以下、より好ましくは0.1%以下である。
<Ni: 1.0% or less (excluding 0%)>
Ni, as well as Cu, has an effect of increasing electrical resistance. In order to sufficiently exhibit this action, the Ni content is preferably 0.01% or more, more preferably 0.02% or more, and further preferably 0.03% or more. However, when the amount of Ni becomes excessive, the magnetic moment decreases as in the case of Cu. Therefore, the upper limit of Ni content is set to 1.0%. The amount of Ni is preferably 0.5% or less, more preferably 0.1% or less.
〈Cr:1.0%以下(0%を含まない)〉
鋼中で炭化物を生成し、電気抵抗を増加させる。電気抵抗の増加は磁壁移動領域を拡大するため、交流磁束密度の増加に有効である。この様な観点からはCrを0.1%以上含有させることが好ましい。しかし、Cr量が過剰になると磁歪量が増加するため、上限を1.0%とする。好ましくは0.9%以下である。
<Cr: 1.0% or less (excluding 0%)>
Generates carbides in steel and increases electrical resistance. Since the increase in electric resistance expands the domain wall motion region, it is effective in increasing the AC magnetic flux density. From such a viewpoint, it is preferable to contain 0.1% or more of Cr. However, if the amount of Cr becomes excessive, the amount of magnetostriction increases, so the upper limit is made 1.0%. Preferably it is 0.9% or less.
〈N:0.0040%以下(0%を含まない)〉
Nは、AlやB等と結合して窒化物を形成する。しかし窒化物を形成しないNは、固溶Nの状態で残存して結晶構造をひずませるため、磁気特性の低下を招く。固溶N量の低減には、鋼中全窒素量を低減することが効果的であるため、N量(鋼中の全窒素量)の上限を0.0040%と定めた。一方、N量の下限は、鋼材製造コストの点から0.0010%(工業的に一般的なN量の下限)程度である。
<N: 0.0040% or less (excluding 0%)>
N combines with Al, B, etc. to form a nitride. However, N which does not form nitrides remains in a solid solution N state and distorts the crystal structure, resulting in a decrease in magnetic properties. In order to reduce the amount of solute N, it is effective to reduce the total nitrogen amount in the steel, so the upper limit of the N amount (total nitrogen amount in the steel) was set to 0.0040%. On the other hand, the lower limit of the N amount is about 0.0010% (industrially general lower limit of the N amount) from the viewpoint of steel material manufacturing cost.
〈Al:0.05〜1.0%〉
Alは、磁気モーメントの低下を抑え、且つ電気抵抗を増加させる作用を有し、部品の交流磁束密度を向上させるために有効な元素である。これらの作用を充分に発揮させるためにAl量の下限を、0.05%と定めた。Al量は、好ましくは0.10%以上、より好ましくは0.3%以上である。しかしAl量が過剰になると、鋼材の冷間鍛造性が大きく低下する。そこでAl量の上限を1.0%に定めた。Al量は、好ましくは0.5%以下、より好ましくは0.3%以下である。
<Al: 0.05 to 1.0%>
Al has an effect of suppressing a decrease in magnetic moment and increasing electric resistance, and is an effective element for improving the AC magnetic flux density of the component. In order to fully exhibit these actions, the lower limit of the Al content was set to 0.05%. The amount of Al is preferably 0.10% or more, more preferably 0.3% or more. However, when the amount of Al becomes excessive, the cold forgeability of the steel material is greatly reduced. Therefore, the upper limit of Al content is set to 1.0%. The amount of Al is preferably 0.5% or less, more preferably 0.3% or less.
〈O:0.0100%以下(0%を含まない)〉
O(酸素)は常温では鋼に殆ど固溶せず、硬質の酸化物として存在し、磁気特性を大幅に低下させる。ゆえにO含有量は極力低減すべきであり、本発明では0.01%以下に抑える。O含有量は、0.005%以下に低減するのが好ましく、より好ましくは0.002%以下にするのがよい。
<O: 0.0100% or less (excluding 0%)>
O (oxygen) hardly dissolves in steel at room temperature, exists as a hard oxide, and greatly reduces the magnetic properties. Therefore, the O content should be reduced as much as possible, and is limited to 0.01% or less in the present invention. The O content is preferably reduced to 0.005% or less, and more preferably 0.002% or less.
本発明で規定する含有元素は上記の通りであって、残部は鉄および不可避不純物であり、該不可避不純物として、原料、資材、製造設備等の状況によって持ち込まれる元素の混入が許容され得る。更に、本発明の作用に悪影響を与えない範囲で下記元素を積極的に含有させることも可能である。 The contained elements specified in the present invention are as described above, and the balance is iron and unavoidable impurities, and as the unavoidable impurities, mixing of elements brought in depending on the situation of raw materials, materials, manufacturing facilities, etc. can be allowed. Furthermore, it is also possible to positively contain the following elements as long as the effects of the present invention are not adversely affected.
〈B:0.0015〜0.0050%〉
Bは、Fe原子との格子定数の差が大きく、電気抵抗率の増加に寄与する。また固溶NをBNの形で固定し、動的ひずみ時効を抑制する効果も有する。特に時効抑制効果を十分に発揮させるには、0.0015%以上のBを含有させることが好ましい。しかしBが過剰に存在すると磁気特性の低下を招くため、Bは0.0050%以下の範囲内で含有させるのがよい。
<B: 0.0015 to 0.0050%>
B has a large difference in lattice constant from Fe atoms and contributes to an increase in electrical resistivity. In addition, solid solution N is fixed in the form of BN and has an effect of suppressing dynamic strain aging. In particular, in order to sufficiently exhibit the effect of suppressing aging, it is preferable to contain 0.0015% or more of B. However, if B is excessively present, the magnetic properties are deteriorated, so B is preferably contained within a range of 0.0050% or less.
本発明の軟磁性鋼材を製造するにあたっては、本発明の軟磁性鋼材の冷間鍛造性を確保し、かつ磁気焼鈍後に優れた交流磁気特性および低磁歪を実現させるには、下記の条件で熱間圧延を行うことが大変有効である。 In producing the soft magnetic steel material of the present invention, in order to ensure the cold forgeability of the soft magnetic steel material of the present invention and to realize the excellent AC magnetic characteristics and low magnetostriction after magnetic annealing, the following conditions are used. It is very effective to perform hot rolling.
〈加熱温度〉
合金成分を母相に完全に固溶させるため、圧延前の加熱温度はできるだけ高温とすることが望ましい。しかし1200℃を超えると、フェライト結晶粒の粗大化が顕著となり、部品成型時の冷間鍛造性低下をもたらすので、その上限温度を1200℃とするのがよい。好ましくは1150℃以下である。一方、加熱温度が低すぎると異なる相が局所的に生成し圧延時の割れ発生を招く危険性がある。また、加熱温度が低いと圧延時のロール負荷が上昇し、生産性が低下する。よって加熱温度は、1000℃以上とすることが推奨される。
<Heating temperature>
In order to completely dissolve the alloy components in the matrix, it is desirable that the heating temperature before rolling be as high as possible. However, if it exceeds 1200 ° C., the ferrite crystal grains become prominent and the cold forgeability at the time of component molding is reduced, so the upper limit temperature should be 1200 ° C. Preferably it is 1150 degrees C or less. On the other hand, if the heating temperature is too low, different phases are locally generated and there is a risk of causing cracking during rolling. Moreover, when heating temperature is low, the roll load at the time of rolling will rise and productivity will fall. Therefore, it is recommended that the heating temperature be 1000 ° C. or higher.
〈仕上げ圧延温度〉
仕上げ圧延温度が低すぎると、ミクロ組織が細粒となりやすく、その後の冷却過程や、部品製造時の焼鈍過程において、部分的な異常粒成長(GG)の発生を招く。GG発生部は、冷間鍛造時の肌荒れや磁気特性のばらつきの原因となるため、均一な整粒を確保することが好ましい。このような観点から、仕上げ圧延温度は、850℃以上(より好ましくは900℃以上)とすることが推奨される。
<Finishing rolling temperature>
If the finish rolling temperature is too low, the microstructure tends to become fine grains, and partial abnormal grain growth (GG) is caused in the subsequent cooling process and annealing process during component manufacturing. Since the GG generating part causes rough skin and variations in magnetic characteristics during cold forging, it is preferable to ensure uniform sizing. From such a viewpoint, it is recommended that the finish rolling temperature be 850 ° C. or higher (more preferably 900 ° C. or higher).
〈圧延後の巻取り温度〉
仕上げ圧延後の巻取り温度が低すぎると、仕上げ圧延温度と同様、ミクロ組織が細粒となりやすく、鋼材の冷間鍛造性および部品の磁気特性に支障をもたらすおそれがある。そこで800℃以上の温度で巻取りを完了することが推奨される。
<Winding temperature after rolling>
If the coiling temperature after finish rolling is too low, the microstructure is likely to become finer, similar to the finish rolling temperature, and there is a possibility that the cold forgeability of the steel material and the magnetic properties of the parts may be hindered. Therefore, it is recommended to complete the winding at a temperature of 800 ° C. or higher.
上記加熱温度、仕上圧延温度、および巻取り温度を上記範囲内とすることで、得られる圧延材またはその伸線材は、電磁ステンレスに比べて優れた透磁率特性を有し、少ない磁壁移動領域で高い磁束量を確保できるため、磁歪による部品変形が少なく、かつ電磁ステンレスと同等以上の交流磁気特性を安定して得ることができる。 By setting the heating temperature, finish rolling temperature, and coiling temperature within the above ranges, the obtained rolled material or the drawn wire material has excellent permeability characteristics compared with electromagnetic stainless steel, and has a small domain wall motion region. Since a high amount of magnetic flux can be secured, there is little deformation of the parts due to magnetostriction, and AC magnetic characteristics equivalent to or better than electromagnetic stainless steel can be stably obtained.
この様にして得られる本発明の軟磁性鋼材は、金属組織(ミクロ組織)がフェライト単相組織(金属組織に占めるフェライト相が95面積%以上)のものとなる。上記「フェライト単相組織」中には、フェライト組織以外に、上記MnS含有析出物や、製造工程で不可避的に形成され得るその他の析出物が含まれることを意図する。フェライト単相組織とするには、C量を極少レベルに抑えることが有効である。この様にフェライト単相組織にすることにより、磁気モーメントが増加して、交流磁束密度を向上させることができる。 The thus obtained soft magnetic steel material of the present invention has a metal structure (micro structure) having a ferrite single phase structure (the ferrite phase occupying 95% by area or more in the metal structure). The “ferrite single-phase structure” is intended to include, in addition to the ferrite structure, the MnS-containing precipitates and other precipitates that can be inevitably formed in the manufacturing process. In order to obtain a ferrite single phase structure, it is effective to suppress the C content to an extremely low level. By using a ferrite single-phase structure in this way, the magnetic moment can be increased and the alternating magnetic flux density can be improved.
尚、磁気焼鈍によりフェライト結晶粒を粗大化してより優れた磁気特性を得るには、この軟磁性鋼材の金属組織におけるJIS G 0551で規定するフェライト結晶粒度番号が4.0以下であることが好ましい。 Incidentally, in order to obtain larger magnetic properties by coarsening the ferrite crystal grains by magnetic annealing, it is preferable that the ferrite crystal grain size number defined by JIS G 0551 in the metal structure of this soft magnetic steel material is 4.0 or less. .
〈磁気焼鈍条件〉
本発明の軟磁性鋼部品を製造するためには、上記の成分組成の要件を満たす鋼材を、形状加工した後(好ましくは冷間鍛造により形状加工した後)、真空中または不活性ガス雰囲気下で焼鈍することにより、フェライト結晶粒を粗大化させることが有効である。
<Magnetic annealing conditions>
In order to produce the soft magnetic steel part of the present invention, a steel material that satisfies the above-mentioned component composition requirements is processed into a shape (preferably after being processed by cold forging), and then in a vacuum or under an inert gas atmosphere. It is effective to coarsen the ferrite crystal grains by annealing at.
該焼鈍温度が低すぎると、析出した窒化物が結晶粒の成長を阻害するため、実用的な熱処理時間で、フェライト結晶粒度番号が3以下という粗大な結晶粒を形成することが難しくなる。そこで焼鈍温度は850℃以上とすることが必要である。好ましい焼鈍温度の下限は900℃である。しかし焼鈍温度が高くなりすぎても、結晶粒を粗大化する効果は飽和する。よってコストなどの観点から、焼鈍温度を1000℃以下、好ましくは975℃以下に調整することが推奨される。 If the annealing temperature is too low, the deposited nitride inhibits the growth of crystal grains, so that it is difficult to form coarse crystal grains having a ferrite crystal grain size number of 3 or less in a practical heat treatment time. Therefore, the annealing temperature needs to be 850 ° C. or higher. The lower limit of the preferable annealing temperature is 900 ° C. However, even if the annealing temperature becomes too high, the effect of coarsening the crystal grains is saturated. Therefore, it is recommended that the annealing temperature be adjusted to 1000 ° C. or lower, preferably 975 ° C. or lower, from the viewpoint of cost and the like.
焼鈍時間が短すぎると、焼鈍温度を高めに設定しても、フェライト結晶粒を充分に粗大化させることができない。上記焼鈍温度での焼鈍時間は、3時間以上であることが必要である。好ましくは4時間以上である。しかし焼鈍時間が長すぎても、結晶粒を粗大化する効果は飽和する。よってコストなどの観点から、焼鈍時間を6時間以下、好ましくは5時間以下に調整することが推奨される。 If the annealing time is too short, the ferrite crystal grains cannot be sufficiently coarsened even if the annealing temperature is set high. The annealing time at the annealing temperature needs to be 3 hours or more. Preferably it is 4 hours or more. However, even if the annealing time is too long, the effect of coarsening the crystal grains is saturated. Therefore, from the viewpoint of cost and the like, it is recommended to adjust the annealing time to 6 hours or less, preferably 5 hours or less.
本発明は、この様にして得られる軟磁性鋼部品も含む。軟磁性鋼部品の交流磁気特性は、部品(鋼材)内部を移動する磁束を固定するエネルギー量に関係しており、フェライト結晶粒の大きさの影響を受ける。そのためフェライト結晶粒を上述の通り粗大化させて、粒界面積を低減させれば、保磁力を小さく、且つ交流磁束密度を高めることができ、ソレノイド、リレーまたは電磁弁の鉄心材といった電装部品の構成部品に好適な磁気特性を確保することができる。 The present invention also includes soft magnetic steel parts obtained in this manner. The AC magnetic characteristics of soft magnetic steel parts are related to the amount of energy for fixing the magnetic flux moving inside the part (steel material), and are affected by the size of ferrite crystal grains. Therefore, if the ferrite crystal grains are coarsened as described above and the grain boundary area is reduced, the coercive force can be reduced and the alternating magnetic flux density can be increased. Magnetic characteristics suitable for the components can be ensured.
そこで本発明の軟磁性鋼部品は、優れた交流磁気特性を達成するため、フェライト単相組織(金属組織に占めるフェライト相が95%以上)であって、粗大なフェライト結晶粒を有することを特徴とする。具体的には本発明の軟磁性鋼部品は、JIS G 0551で規定するフェライト結晶粒度番号が3以下、好ましくは2.5以下、より好ましくは2.0以下であることを特徴とする。 Therefore, the soft magnetic steel part of the present invention has a ferrite single-phase structure (the ferrite phase occupying 95% or more of the metal structure) and has coarse ferrite crystal grains in order to achieve excellent AC magnetic characteristics. And Specifically, the soft magnetic steel part of the present invention is characterized in that the ferrite grain size number defined by JIS G 0551 is 3 or less, preferably 2.5 or less, more preferably 2.0 or less.
以下、実施例を挙げて本発明をより具体的に説明するが、本発明はもとより下記実施例によって制限を受けるものではなく、前・後記の趣旨に適合し得る範囲で適当に変更を加えて実施することも可能であり、それらはいずれも本発明の技術的範囲に含まれる。 EXAMPLES Hereinafter, the present invention will be described more specifically with reference to examples. However, the present invention is not limited by the following examples, but may be appropriately modified within a range that can meet the purpose described above and below. It is also possible to implement, and they are all included in the technical scope of the present invention.
表1に示す化学成分組成の供試材を真空溶製にて各150kg試作した。そして溶製材を155mm×155mm角に鍛造加工し、ダミービレット材に溶接した後、表2に示す条件で熱間圧延を行ってφ20mmの軟磁性鋼材No.1〜25を得た。鋼材No.1〜25のフェライト結晶粒度番号を、下記の方法で測定した。 150 kg of test materials having chemical composition shown in Table 1 were manufactured by vacuum melting. The melted material was forged into a 155 mm × 155 mm square, welded to a dummy billet material, and then hot-rolled under the conditions shown in Table 2 to obtain a soft magnetic steel No. 1-25 were obtained. Steel No. The ferrite grain size number of 1 to 25 was measured by the following method.
〈フェライト結晶粒度番号の測定〉
鋼材(線材)の横断面(圧延方向に垂直な断面)が露出する状態で支持基材内に埋め込み、研磨後、5%のピクリン酸アルコール液に15〜30秒間浸漬して腐食させ、その後、光学顕微鏡でD/4(Dは直径)部位の組織を100倍で10視野撮影し、JIS G 0551(2005)で規定するフェライト結晶粒度番号を調べ、その平均値をフェライト結晶粒度番号と定めた。その結果を表2に併記する。尚、鋼材No.1〜25のいずれの金属組織も、フェライトが面積率で95%以上であることを確認した。
<Measurement of ferrite grain size number>
The steel (wire) cross section (cross section perpendicular to the rolling direction) is exposed and embedded in the support substrate, and after polishing, is immersed in a 5% picric acid alcohol solution for 15 to 30 seconds to corrode. The structure of the D / 4 (D is the diameter) part was photographed with an optical microscope at 10 magnifications in 10 fields, the ferrite crystal grain size number defined in JIS G 0551 (2005) was examined, and the average value was determined as the ferrite crystal grain size number. . The results are also shown in Table 2. Steel No. In any of the metal structures 1 to 25, it was confirmed that ferrite was 95% or more in area ratio.
また、フェライト中の炭化物およびMnSの最大粒径は次の様にして測定した。即ち、鋼材(線材)の縦断面(圧延方向に平行であって鋼材の軸心を通る断面)が露出する状態で支持基材内に埋め込み、研磨後、5%のピクリン酸アルコール液に15〜30秒間浸漬して腐食させたものと、該腐食を行わないものを用意した。そして、光学顕微鏡で上記縦断面におけるD/4部位を400倍で10視野撮影し、10視野において最大サイズの炭化物またはMnSの長径と短径を測定し、最大粒径(長径と短径の平均値)を求めた。その結果、No.1〜5、7〜10では、炭化物またはMnSの最大粒径(長径と短径の平均値)がいずれも20μm以下であった。 Further, the maximum particle sizes of carbides and MnS in ferrite were measured as follows. That is, the steel material (wire material) is embedded in a supporting substrate in a state in which a longitudinal section (cross section parallel to the rolling direction and passing through the axis of the steel material) is exposed, and after polishing, 15% in a 5% picric acid alcohol solution is obtained. What was immersed for 30 seconds and corroded and what did not perform this corrosion were prepared. Then, 10 fields of the D / 4 portion in the longitudinal section were photographed at 400 × with an optical microscope, and the major axis and minor axis of the maximum size carbide or MnS were measured in ten fields, and the maximum grain size (average of major axis and minor axis) was measured. Value). As a result, no. In 1 to 5 and 7 to 10, the maximum particle size (average value of major axis and minor axis) of carbide or MnS was 20 μm or less.
次に、上記鋼材No.1〜25に対し、下記表3に示す条件で焼鈍して、鋼部品No.1〜25を製造した。鋼部品のフェライト結晶粒度番号および組織を、鋼材のフェライト結晶粒度番号の測定した方法と同様にして測定した。得られたフェライト結晶粒度番号の結果を表3に示す。なお部材No.1〜25の金属組織は、全て、フェライトが面積率で95%以上であることを確認した。また部材の電気抵抗率および磁気特性(直流磁束密度および交流磁束密度)を、下記の方法で測定した。 Next, the steel material No. 1 to 25 were annealed under the conditions shown in Table 3 below, and steel part No. 1-25 were produced. The ferrite grain size number and structure of the steel part were measured in the same manner as the method for measuring the ferrite grain size number of the steel material. The obtained ferrite grain size number results are shown in Table 3. In addition, member No. It was confirmed that all the metal structures of 1 to 25 had ferrite with an area ratio of 95% or more. Further, the electrical resistivity and magnetic properties (DC magnetic flux density and AC magnetic flux density) of the member were measured by the following methods.
〈鋼部品の電気抵抗率および磁気特性の測定〉
各試料の鋼部品の電気抵抗率は、直流四端子法により測定した。また各試料の磁気特性は、上記線材を用いて次のように実施した。まず透磁率特性は、渦電流による遮蔽効果の影響を除す為、直流磁気測定で評価した。前記鋼材を外径32mm×内径28mm×高さ4mmのリング状に形状加工した後、表3に示す条件で焼鈍して、磁気特性測定用の試料を作製した。これに磁界印加用の1次コイルと磁束検出用の2次コイルを巻線し、自動磁化測定装置(岩通製BHアナライザ:SY−8232)を用いてB−H曲線を測定することによって直流初期透磁率を求めた。
<Measurement of electrical resistivity and magnetic properties of steel parts>
The electrical resistivity of the steel part of each sample was measured by a DC four-terminal method. Moreover, the magnetic characteristics of each sample were implemented as follows using the said wire. First, the magnetic permeability characteristics were evaluated by DC magnetic measurement in order to eliminate the influence of the shielding effect by eddy current. The steel material was shaped into a ring shape with an outer diameter of 32 mm, an inner diameter of 28 mm, and a height of 4 mm, and then annealed under the conditions shown in Table 3 to prepare a sample for measuring magnetic properties. A primary coil for applying a magnetic field and a secondary coil for detecting a magnetic flux are wound around this, and a direct current is measured by measuring a BH curve using an automatic magnetization measuring device (BH analyzer: SY-8232 manufactured by Iwatatsu). The initial permeability was determined.
また、交流磁気特性(磁束密度)は次のようにして測定した。即ち、図1に示す通り、外径10mm×内径5mm×厚さ0.5mmのリング状試料を作製し、表3に示す条件で焼鈍後、これに磁界印加用の1次コイルと磁束検出用の2次コイルを巻線し、その後、自動磁化測定装置(岩通製BHアナライザ:SY−8232)を用いてB−H曲線を測定することによって磁束密度を求めた。そして磁界振幅:800A/m、周波数:10kHzでの交流磁束密度が、450mT以上のものを交流磁気特性に優れると評価し、450mT未満のものを交流磁気特性に劣ると評価した。測定例として、磁界周波数と磁束密度の関係を試料別に示したグラフを図2に示す。 The AC magnetic characteristics (magnetic flux density) were measured as follows. That is, as shown in FIG. 1, a ring-shaped sample having an outer diameter of 10 mm, an inner diameter of 5 mm, and a thickness of 0.5 mm is prepared, annealed under the conditions shown in Table 3, and then a primary coil for applying a magnetic field and a magnetic flux for detection. The magnetic flux density was calculated | required by measuring a BH curve using the automatic magnetization measuring apparatus (Iwatori BH analyzer: SY-8232) after that. A magnetic flux with an AC magnetic flux density of 450 mT or higher at a magnetic field amplitude of 800 A / m and a frequency of 10 kHz was evaluated as being excellent in AC magnetic properties, and a magnetic flux density of less than 450 mT was evaluated as being inferior in AC magnetic properties. As a measurement example, a graph showing the relationship between magnetic field frequency and magnetic flux density for each sample is shown in FIG.
また、磁歪の測定は、前記鋼材から5mm×5mm×5mmの試料を作製し、該試料に磁界を引加し、磁歪変形量を電気回路のコンデンサ容量の変化として検出することで求めた。そして磁歪が1.2×10−5以下のものを低磁歪であると評価し、1.2×10−5超のものを磁歪が大きいと評価した。測定例として、磁界の強さと磁歪の関係を試料別に示したグラフを図3に示す。尚、図3中、「E−5」「E+4」は、それぞれ「×10−5」、「×104」を示す。 The magnetostriction was measured by preparing a 5 mm × 5 mm × 5 mm sample from the steel material, applying a magnetic field to the sample, and detecting the amount of magnetostriction deformation as a change in the capacitor capacity of the electric circuit. Those having a magnetostriction of 1.2 × 10 −5 or less were evaluated as low magnetostriction, and those having a magnetostriction exceeding 1.2 × 10 −5 were evaluated as having large magnetostriction. As a measurement example, a graph showing the relationship between magnetic field strength and magnetostriction for each sample is shown in FIG. In FIG. 3, “E-5” and “E + 4” indicate “× 10 −5 ” and “× 10 4 ”, respectively.
これらの結果を表3に併記する。尚、表3中、「E−06」「E−05」は、それぞれ「×10−6」、「×10−5」を示す。 These results are also shown in Table 3. In Table 3, “E-06” and “E-05” indicate “× 10 −6 ” and “× 10 −5 ”, respectively.
表1〜3に示すように、本発明の成分組成の要件を満たす鋼材を用い、規定の条件で製造したNo.1〜5、7〜10の鋼部品は、いずれも電磁ステンレス並みの交流磁気特性を有し、かつ低磁歪であることが分かる。これに対し、本発明の要件を満たさない鋼材を用いているか規定の条件で製造しなかった鋼部品No.6、11〜25は、磁気特性が劣っている。 As shown in Tables 1 to 3, a steel material that satisfies the requirements of the component composition of the present invention was used and No. manufactured under specified conditions. It can be seen that the steel parts 1 to 5 and 7 to 10 all have AC magnetic properties similar to those of electromagnetic stainless steel and have low magnetostriction. On the other hand, a steel part No. that uses a steel material that does not satisfy the requirements of the present invention or has not been manufactured under specified conditions. 6, 11-25 are inferior in magnetic properties.
詳細には、No.6は、化学成分は本発明の範囲内であるが、磁気焼鈍条件が不適であり、十分な透磁率が確保できなかった為、磁束特性に劣っている。 Specifically, no. No. 6, the chemical component is within the scope of the present invention, but the magnetic annealing conditions are inappropriate, and sufficient magnetic permeability cannot be ensured, so that the magnetic flux characteristics are inferior.
No.10は、Si+Mn+Cr量が本発明の規定範囲から外れるため、交流磁束密度の低下を招いた。 No. No. 10 caused a decrease in AC magnetic flux density because the amount of Si + Mn + Cr deviated from the specified range of the present invention.
No.11はC量の影響を示している。C添加量が過多になると、磁気モーメントの低下により目標の磁束密度を満足できないことに加え、磁歪が増加することが分かる。 No. 11 shows the influence of the C amount. It can be seen that when the amount of addition of C is excessive, the magnetostriction increases in addition to not being able to satisfy the target magnetic flux density due to a decrease in the magnetic moment.
No.12は、電気抵抗率の増加に必要なSi量、S量およびAl量が不足した例である。このNo.12では、電気抵抗率が低く磁気遮蔽効果が大きい為、交流での磁気特性が大幅に低下している。 No. No. 12 is an example in which the amount of Si, the amount of S and the amount of Al necessary for increasing the electrical resistivity are insufficient. This No. In No. 12, since the electrical resistivity is low and the magnetic shielding effect is large, the magnetic characteristics at alternating current are greatly deteriorated.
No.13はSi量が過多な例である。電気抵抗率を大きく増加させ磁気遮蔽効果を抑制できるため、交流磁束密度は良好な値を示すが、磁歪が増加する結果となった。 No. 13 is an example in which the amount of Si is excessive. Since the electrical resistivity can be greatly increased and the magnetic shielding effect can be suppressed, the AC magnetic flux density shows a good value, but the magnetostriction increases.
No.14およびNo.15は、Mn量の影響を調べた例である。No.14の通りMnが不足すると、鋼中のSがFeSとして析出し、延性を害して、試験片の内部に微小な割れが認められた。また割れ発生に伴い、交流磁束密度が大幅に低下する結果となった。またNo.15の通りMn量が過剰であると、電気抵抗は増加するが、磁気モーメント自体を低下させるため、磁気特性が著しく低下している。 No. 14 and no. 15 is an example in which the influence of the amount of Mn was examined. No. When Mn was insufficient as shown in FIG. 14, S in the steel was precipitated as FeS, and the ductility was impaired, and minute cracks were observed inside the test piece. In addition, with the occurrence of cracks, the AC magnetic flux density decreased significantly. No. As shown in FIG. 15, when the amount of Mn is excessive, the electric resistance increases, but the magnetic moment itself is lowered, so that the magnetic properties are remarkably deteriorated.
No.16は、P量過多の例である。この場合、Mnが不足するNo.14の場合と同様に、試験片中に微小クラックが認められ、磁気特性が低下する結果となった。 No. 16 is an example of excessive P amount. In this case, no. As in the case of 14, fine cracks were observed in the test piece, resulting in a decrease in magnetic properties.
No.17は、Cu量が過剰な例である。Cuの増量は、鋼材の磁気モーメントを低下させるため、磁気特性が低下する結果となっている。 No. 17 is an example in which the amount of Cu is excessive. Increasing the amount of Cu decreases the magnetic moment of the steel material, resulting in a decrease in magnetic properties.
No.18は、Niを多量に含有させた場合の影響を示している。Niは電気抵抗率を増加させる作用を有することから、交流磁束密度は良好な値を示すが、Feと同様に大きな磁気モーメントを有する元素であるため、磁歪が大きくなる結果となった。 No. 18 shows the influence when Ni is contained in a large amount. Since Ni has an effect of increasing the electrical resistivity, the AC magnetic flux density shows a good value, but since it is an element having a large magnetic moment like Fe, magnetostriction is increased.
No.19、No.20は、それぞれCr、Alが本発明範囲から外れるものである。いずれも、電気抵抗率の増加により磁気遮蔽効果が抑制されるため、交流磁束密度は向上するが、磁歪特性に対しては望ましくない結果となった。 No. 19, no. In No. 20, Cr and Al are out of the scope of the present invention. In either case, the magnetic shielding effect is suppressed by increasing the electrical resistivity, so that the alternating magnetic flux density is improved, but the magnetostrictive characteristics are undesirable.
No.21は、B量の影響を示したものである。Bを推奨される範囲内で含有させると、磁気特性および冷間鍛造性に有害な固溶NをBNとして固定し無害化する作用を有するが、多量に添加すると、磁気モーメントを低下させる為、磁気特性が低下する。 No. 21 shows the influence of the B amount. If B is contained within the recommended range, it has the effect of fixing and detoxifying solute N, which is harmful to magnetic properties and cold forgeability, as BN, but adding a large amount reduces the magnetic moment. Magnetic properties are degraded.
No.22は、Al量が不足しかつN量が過剰な例である。上記No.21で記載したように、固溶Nが磁気特性に悪影響を及ぼすことから、磁気特性の低下を招いている。 No. No. 22 is an example in which the Al amount is insufficient and the N amount is excessive. No. above. As described in 21, since the solid solution N adversely affects the magnetic characteristics, the magnetic characteristics are deteriorated.
No.23は電磁ステンレスに相当する鋼材である。電気抵抗を増加させるために、Crを多量に添加しているため、磁歪が大きくなっていることが分かる。 No. 23 is a steel material corresponding to electromagnetic stainless steel. It can be seen that magnetostriction is increased because a large amount of Cr is added to increase the electrical resistance.
No.24は、S量が過剰であり、またNo.25は、Mn/Sが規定の範囲を外れているため、磁気特性が低下している。 No. No. 24 has an excessive amount of S. In No. 25, since Mn / S is out of the specified range, the magnetic properties are deteriorated.
尚、上記No.7の金属組織の顕微鏡観察写真(光学顕微鏡で倍率100倍)を図4に、またNo.11の金属組織の顕微鏡観察写真(光学顕微鏡で倍率100倍)を図5に示す。これらNo.7とNo.11の写真を対比すると、No.11では、黒点状の析出物(主に炭化物であり、MnSも若干含む)が多数析出しており、これが磁気特性低下の原因となっていることがわかる。 In addition, said No. 7 is a microscopic observation photograph of the metal structure (magnification 100 times with an optical microscope) in FIG. FIG. 5 shows a microscopic observation photograph (11 magnification with an optical microscope) of 11 metal structures. These No. 7 and no. When comparing the 11 photos, no. In No. 11, a large number of black-spotted precipitates (mainly carbides, including a little MnS) are precipitated, which is a cause of a decrease in magnetic properties.
Claims (4)
Si:1.5〜2.8%、
Mn:0.2〜0.8%、
P:0.02%以下(0%を含まない)、
S:0.02〜0.10%、
Cu:0.1%以下(0%を含まない)、
Ni:1.0%以下(0%を含まない)、
Cr:1.0%以下(0%を含まない)、
Al:0.05〜1.0%、
N:0.0040%以下(0%を含まない)、
O:0.0100%以下(0%を含まない)、
5≦Mn/S≦50、
Si+Mn+Cr≦4.0を満たし、
残部:鉄および不可避不純物からなり、
金属組織に占めるフェライト相が95面積%以上であり、かつ
該フェライト中の炭化物およびMnSの最大粒径(長径と短径の平均値)が20μm以下であって、常温(20℃)での電気抵抗率が40〜60μΩcmであり、かつ直流初期透磁率が4000以上であることを特徴とする軟磁性鋼材。 C: 0.002 to 0.050% (meaning mass%, the same shall apply hereinafter),
Si: 1.5 to 2.8%,
Mn: 0.2 to 0.8%
P: 0.02% or less (excluding 0%),
S: 0.02-0.10%,
Cu: 0.1% or less (excluding 0%),
Ni: 1.0% or less (excluding 0%),
Cr: 1.0% or less (excluding 0%),
Al: 0.05 to 1.0%,
N: 0.0040% or less (excluding 0%),
O: 0.0100% or less (excluding 0%),
5 ≦ Mn / S ≦ 50,
Satisfying Si + Mn + Cr ≦ 4.0,
The balance: iron and inevitable impurities
The ferrite phase in the metal structure is 95% by area or more, and the maximum particle size (average value of the major axis and the minor axis) of carbide and MnS in the ferrite is 20 μm or less, and electricity at normal temperature (20 ° C.) A soft magnetic steel material having a resistivity of 40 to 60 μΩcm and a direct current permeability of 4000 or more.
請求項1または2に記載の成分組成を満たし、金属組織に占めるフェライト相が95%以上であり、かつJIS G 0551で規定するフェライト結晶粒度番号が3以下であることを特徴とする軟磁性鋼部品。 A soft magnetic steel part obtained by using the soft magnetic steel material according to claim 1 or 2,
A soft magnetic steel satisfying the component composition according to claim 1 or 2, wherein the ferrite phase occupying the metal structure is 95% or more, and the ferrite crystal grain size number defined in JIS G 0551 is 3 or less parts.
請求項1または2に記載の軟磁性鋼材を、形状加工した後、真空中または不活性ガス雰囲気下、850〜1000℃で3時間以上焼鈍処理することにより、JIS G 0551で規定するフェライト結晶粒度番号を3以下とすることを特徴とする軟磁性鋼部品の製造方法。 A method for producing a soft magnetic steel part according to claim 3,
After processing the shape of the soft magnetic steel material according to claim 1 or 2, the ferrite crystal grain size specified by JIS G 0551 is annealed in vacuum or in an inert gas atmosphere at 850 to 1000 ° C for 3 hours or more. A method for producing a soft magnetic steel part, wherein the number is 3 or less.
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