JP2008045182A - Soft magnetic steel material, and soft magnetic component and method for producing the same - Google Patents
Soft magnetic steel material, and soft magnetic component and method for producing the same Download PDFInfo
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本発明は、軟磁性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部品（例えば自動車用センサ等の鉄心）、および軟磁性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 component, a soft magnetic component obtained therefrom (for example, an iron core such as an automobile sensor), and a method for producing the soft magnetic component.
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。例えば自動車用部品における油圧制御用ソレノイドといった直流磁気特性を重視する部品には、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. For example, an ultra-low carbon steel having a C content of 0.01% or less is used for a component that places importance on DC magnetic characteristics, such as a hydraulic control solenoid in an automotive component.
また近年における自動車制御のバイワイヤ化の伸展に伴い、電装部品の制御を司るセンサ部品の需要が拡大すると共に、消費電力を低減させるために、軟磁性部品の特性向上についての要望が高まっている。このため、例えば電子燃料噴射弁といった高周波数領域における磁気特性が重視される部品には、高電気抵抗を示す電磁ステンレス等の材料が使用されている。しかし部品製造コストを低減させるために、鋼材の形状加工として冷間鍛造が行われつつあるが、交流磁気特性に主眼を置いた電磁ステンレス等は、冷間鍛造性が良好とは言えないという問題がある。 In addition, with the recent expansion of by-wire control of automobiles, demand for sensor parts that control electric parts has increased, and in order to reduce power consumption, there has been an increasing demand for improved characteristics of soft magnetic parts. For this reason, materials such as electromagnetic stainless steel exhibiting high electrical resistance are used for components that place importance on magnetic characteristics in a high frequency region, such as electronic fuel injection valves. However, in order to reduce component manufacturing costs, cold forging is being carried out as shape processing of steel materials, but electromagnetic stainless steel etc. with an emphasis on AC magnetic properties cannot be said to have good cold forgeability. There is.
そこで、交流磁気特性および加工性に優れた軟磁性鋼材を得るために、様々な研究および提案がなされている。例えば特許文献１は、交流磁気特性に優れた従来のＦｅ−Ｓｉ合金に、Ｃｒを共存させて靱性を向上させることにより、加工性（殊に靱性）および交流磁気特性（殊に鉄損特性）に優れたＦｅ−Ｃｒ−Ｓｉ系合金が得られることを開示している（殊に請求項１および段落［００１０］参照）。
従来技術において、加工性および交流磁気特性に優れた軟磁性鋼材が、種々提案されているが、さらなる改良が絶えず求められている。そこで本発明の目的は、優れた交流磁気特性、殊に磁界振幅が８００Ａ／ｍ程度の中磁界領域でも高い交流磁束密度を示す軟磁性部品を製造することができ、且つ良好な冷間鍛造性を維持した軟磁性鋼材を提供することにある。 In the prior art, various soft magnetic steel materials excellent in workability and AC magnetic properties have been proposed, but further improvements are constantly being sought. Therefore, an object of the present invention is to produce a soft magnetic part exhibiting excellent AC magnetic characteristics, particularly high AC magnetic flux density even in a medium magnetic field region where the magnetic field amplitude is about 800 A / m, and good cold forgeability. It is to provide a soft magnetic steel material maintaining the above.
上記目的を達成し得た本発明の軟磁性鋼材とは、
Ｃ：０．００５〜０．０５％（質量％の意味、以下同じ）、
Ｓｉ：１．８〜３．０％、
Ｍｎ：０．２０〜０．８％、
Ｐ：０．０２％以下（０％を含まない）、
Ｓ：０．０２〜０．１％、
Ｃｕ：０．１％以下（０％を含まない）、
Ｎｉ：０．２％以下（０％を含まない）、
Ｃｒ：１〜３．５％、
Ａｌ：０．０５〜２．８％、
Ｎ：０．００４％以下（０％を含まない）、および
Ｏ：０．０２％以下（０％を含まない）
を含有し、残部がＦｅおよび不可避不純物からなり、
下記式（１）で計算されるＦ１値が６０以上であることを特徴とするものである。
Ｆ１＝９７．０［Ｃ］＋１０．９［Ｓｉ］＋４．２［Ｍｎ］＋２３．８［Ｐ］
＋１７２．０［Ｓ］＋１５．０［Ｃｕ］−０．０３［Ｎｉ］＋５．１［Ｃｒ］
＋８．６［Ａｌ］＋３４．０［Ｎ］＋８．３８ ・・・ （１）
〔式中、［ ］は、それぞれ軟磁性鋼材中の各元素の含有量（質量％）を表す。〕
With the soft magnetic steel material of the present invention that can achieve the above-mentioned object,
C: 0.005-0.05% (meaning mass%, the same shall apply hereinafter)
Si: 1.8-3.0%,
Mn: 0.20 to 0.8%,
P: 0.02% or less (excluding 0%),
S: 0.02-0.1%,
Cu: 0.1% or less (excluding 0%),
Ni: 0.2% or less (excluding 0%),
Cr: 1 to 3.5%,
Al: 0.05 to 2.8%,
N: 0.004% or less (not including 0%), and O: 0.02% or less (not including 0%)
And the balance consists of Fe and inevitable impurities,
The F1 value calculated by the following formula (1) is 60 or more.
F1 = 97.0 [C] +10.9 [Si] +4.2 [Mn] +23.8 [P]
+172.0 [S] +15.0 [Cu] -0.03 [Ni] +5.1 [Cr]
+8.6 [Al] +34.0 [N] +8.38 (1)
[In formula, [] represents content (mass%) of each element in a soft-magnetic steel material, respectively. ]
本発明の軟磁性鋼材には、前記の基本成分の他、必要に応じてさらに、（ア）Ｂ：０．００５％以下（０％を含まない）、（イ）Ｔｉ：０．３５％以下（０％を含まない）、（ウ）Ｖ：１．５％以下（０％を含まない）および／または（エ）Ｂｉ：０．３％以下（０％を含まない）を含有させることも有効であり、含有させる成分の種類に応じて、鋼材の特性がさらに改善される。但し、本発明の軟磁性鋼材が、Ｂ、Ｔｉ、Ｖおよび／またはＢｉを含有する場合、下記式（６）で計算されるＦ値が６０以上であることが必要である。
Ｆ＝９７．０［Ｃ］＋１０．９［Ｓｉ］＋４．２［Ｍｎ］＋２３．８［Ｐ］
＋１７２．０［Ｓ］＋１５．０［Ｃｕ］−０．０３［Ｎｉ］＋５．１［Ｃｒ］
＋８．６［Ａｌ］＋３４［Ｎ］−１２０［Ｂ］−０．２［Ｔｉ］
＋４．５［Ｖ］＋２．９［Ｂｉ］＋８．３８ ・・・ （６）
〔式中、［ ］は、それぞれ軟磁性鋼材中の各元素の含有量（質量％）を表す。〕
In addition to the basic components described above, the soft magnetic steel material of the present invention may further include (a) B: 0.005% or less (not including 0%), and (b) Ti: 0.35% or less. (0) not included, (c) V: 1.5% or less (not including 0%) and / or (d) Bi: 0.3% or less (not including 0%) It is effective, and the properties of the steel material are further improved according to the type of component to be contained. However, when the soft magnetic steel material of the present invention contains B, Ti, V and / or Bi, the F value calculated by the following formula (6) needs to be 60 or more.
F = 97.0 [C] +10.9 [Si] +4.2 [Mn] +23.8 [P]
+172.0 [S] +15.0 [Cu] -0.03 [Ni] +5.1 [Cr]
+8.6 [Al] +34 [N] -120 [B] -0.2 [Ti]
+4.5 [V] +2.9 [Bi] +8.38 (6)
[In formula, [] represents content (mass%) of each element in a soft-magnetic steel material, respectively. ]
なお本発明の軟磁性鋼材が、Ｂ、Ｔｉ、ＶおよびＢｉの一部または全部を含有しない場合には、上記式（６）中の［Ｂ］、［Ｔｉ］、［Ｖ］および［Ｂｉ］の一部または全部には、「０」の数値を代入してＦ値を計算する。そのため上記式（１）および特許請求の範囲に記載する上記式（２）〜（５）で計算されるＦ１〜Ｆ５値と、上記式（６）で計算されるＦ値とは一致する。そこで以下では、上記式（６）で計算されるＦ値を用いて、本発明を説明する。 When the soft magnetic steel material of the present invention does not contain part or all of B, Ti, V and Bi, [B], [Ti], [V] and [Bi] in the above formula (6). The F value is calculated by substituting a numerical value of “0” for a part or all of. Therefore, the F1 to F5 values calculated by the above formula (1) and the above formulas (2) to (5) described in the claims coincide with the F value calculated by the above formula (6). Therefore, in the following, the present invention will be described using the F value calculated by the above formula (6).
本発明は、（Ｉ）前記成分組成の要件を満たし、且つ鋼組織がフェライト単相組織であり、ＪＩＳ Ｇ ０５５２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部品、および（ＩＩ）前記軟磁性鋼材を、形状加工した後、真空中または不活性ガス雰囲気下、８５０〜１０００℃の温度で２時間以上焼鈍処理することを特徴とする軟磁性部品の製造方法も提供する。ここで本発明の製造方法における「焼鈍」とは、組織を再結晶させることで形状加工により生じた鋼中の内部応力を除去して、交流磁束密度などの磁気特性を向上させることを目的とするものであり、詳しくは「磁気焼鈍」と呼ばれるものである。 The present invention provides (I) a soft magnetic component characterized by satisfying the above-mentioned component composition, the steel structure is a ferrite single phase structure, and the ferrite crystal grain size number defined by JIS G 0552 is 3 or less, And (II) providing a method of manufacturing a soft magnetic component, characterized by annealing the soft magnetic steel material at a temperature of 850 to 1000 ° C. for 2 hours or more in a vacuum or under an inert gas atmosphere after the shape processing. To do. Here, “annealing” in the production method of the present invention is intended to remove internal stress in steel caused by shape processing by recrystallizing the structure and improve magnetic properties such as AC magnetic flux density. More specifically, it is called “magnetic annealing”.
本発明の軟磁性鋼材を、形状加工し、焼鈍して得られる軟磁性部品は、磁界振幅が８００Ａ／ｍ程度の中磁界領域でも高い交流磁束密度を達成することができる。このように本発明の軟磁性鋼材は、交流磁束密度に優れた部品を製造できることに加えて、冷間鍛造性が良好に維持されており、形状加工に冷間鍛造を採用でき、軟磁性部品の製造コストを低減することができる。 The soft magnetic component obtained by shape-processing and annealing the soft magnetic steel material of the present invention can achieve a high AC magnetic flux density even in a medium magnetic field region with a magnetic field amplitude of about 800 A / m. As described above, the soft magnetic steel material of the present invention is capable of producing a part excellent in AC magnetic flux density, and has good cold forgeability, and can employ cold forging for shape processing. The manufacturing cost can be reduced.
本発明者らが鋭意検討した結果、軟磁性鋼材中の各成分の含有量を適正範囲に維持し、且つ上記式（６）で示されるＦ値が６０以上となるように化学成分組成を適正化することにより、良好な冷間鍛造性を維持しつつ、交流磁束密度に優れた軟磁性部品を製造できる軟磁性鋼材が得られることを見出した。そこで、まず本発明の軟磁性鋼材中に含まれる各成分（元素）について説明する。 As a result of intensive studies by the present inventors, the chemical component composition is appropriately adjusted so that the content of each component in the soft magnetic steel material is maintained in an appropriate range and the F value represented by the above formula (6) is 60 or more. As a result, it was found that a soft magnetic steel material capable of producing a soft magnetic part excellent in alternating magnetic flux density while maintaining good cold forgeability can be obtained. Therefore, first, each component (element) contained in the soft magnetic steel material of the present invention will be described.
〈Ｃ：０．００５〜０．０５％〉
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、ひずみ時効が生じるので、冷間鍛造性の観点から、極低Ｃが望ましい。また軟磁性部品の磁気特性を向上させるためにも、極低Ｃとすることが好ましい。よって本発明では、Ｃ量の上限を０．０５％と定めた。Ｃ量は、好ましくは０．０４％以下、より好ましくは０．０２％以下である。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０．００５％と定めた。Ｃ量は、好ましくは０．０１０％以上である。
<C: 0.005 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, since C dissolves in steel and strain aging occurs, extremely low C is desirable from the viewpoint of cold forgeability. Further, in order to improve the magnetic characteristics of the soft magnetic component, it is preferable to set it to extremely low C. Therefore, in the present invention, the upper limit of the C amount is set to 0.05%. The amount of C is preferably 0.04% or less, more preferably 0.02% or less. 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 0.005%. The amount of C is preferably 0.010% or more.
〈Ｓｉ：１．８〜３．０％〉
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にＳｉ量の下限を１．８％と定めた。Ｓｉ量は、好ましくは２．０％以上である。しかしＳｉ量が過剰であると、鋼材の冷間鍛造性が劣化する。そこでＳｉ量の上限を、３．０％と定めた。Ｓｉ量は、好ましくは２．８％以下、より好ましくは２．６％以下である。
<Si: 1.8-3.0%>
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 1.8%. The amount of Si is preferably 2.0% or more. However, if the amount of Si is excessive, the cold forgeability of the steel material deteriorates. Therefore, the upper limit of Si content is set to 3.0%. The amount of Si is preferably 2.8% or less, more preferably 2.6% or less.
〈Ｍｎ：０．２０〜０．８％〉
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とは、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０．２０％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: 0.20 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 oxides (hereinafter, these may be abbreviated as “MnS-containing precipitates”). It also has the effect of improving resistance. 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 0.20%. 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 Mn amount 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、冷間鍛造性および交流磁束密度の低下を招く。そこでＰ量は、できる限り低減されていることが好ましい。Ｐ量は、０．０２％以下、好ましくは０．０１％以下であることが推奨される。
<P: 0.02% or less (excluding 0%)>
P segregates at the grain boundaries and causes a decrease in cold forgeability and AC magnetic flux density. Therefore, the P amount is preferably reduced as much as possible. It is recommended that the amount of P is 0.02% or less, preferably 0.01% or less.
〈Ｓ：０．０２〜０．１％〉
Ｓは、ＭｎとＭｎＳ含有析出物を形成して、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、本発明において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、鋼材の冷間鍛造性が劣化する。そこでＳ量の上限を、０．１％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: 0.02-0.1%>
S has a function of improving the AC magnetic flux density of the component by forming Mn and MnS-containing precipitates. In order to fully exhibit this action, the lower limit of the amount of S is set to 0.02% in the present invention. The amount of S is preferably 0.025% or more, more preferably 0.030% or more. However, when the amount of S becomes excessive, the cold forgeability of the steel material deteriorates. Therefore, the upper limit of the amount of S is set to 0.1%. 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ために有用である。この作用を充分に発揮させるために、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％以上である。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 the effect of increasing the electrical resistance, and is useful for improving the alternating magnetic flux density by suppressing the generation of eddy currents. In order to sufficiently exhibit this action, 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：０．２％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。この作用を充分に発揮させるために、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％以上である。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０．２％と定めた。Ｎｉ量は、好ましくは０．１％以下、より好ましくは０．０８％以下である。
<Ni: 0.2% 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 0.2%. The amount of Ni is preferably 0.1% or less, more preferably 0.08% or less.
〈Ｃｒ：１〜３．５％〉
Ｃｒは、鋼中に固溶し、また一部はＣと結びついて炭化物を形成し、電気抵抗を増加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、Ｃｒ量の下限を１％と定めた。Ｃｒ量は、好ましくは１．４％以上、より好ましくは１．６％以上である。しかしＣｒ量が過剰になると、磁気モーメントが低下し、かえって部品の交流磁束密度が低下するおそれがあり、また鋼材の冷間鍛造性も低下する。よってＣｒ量の上限を３．５％と定めた。Ｃｒ量は、好ましくは３．２％以下、より好ましくは３．０％以下である。
<Cr: 1 to 3.5%>
Cr dissolves in the steel, and partly combines with C to form carbides and has an action of increasing electrical resistance. In order to exhibit this effect sufficiently, the lower limit of the Cr content was set to 1%. The amount of Cr is preferably 1.4% or more, more preferably 1.6% or more. However, when the amount of Cr is excessive, the magnetic moment is lowered, and the AC magnetic flux density of the part may be lowered, and the cold forgeability of the steel material is also lowered. Therefore, the upper limit of Cr content is set to 3.5%. The amount of Cr is preferably 3.2% or less, more preferably 3.0% or less.
〈Ａｌ：０．０５〜２．８％〉
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２．８％に定めた。Ａｌ量は、好ましくは２．３％以下、より好ましくは２．０％以下である。
<Al: 0.05 to 2.8%>
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 2.8%. The amount of Al is preferably 2.3% or less, more preferably 2.0% or less.
〈Ｎ：０．００４％以下（０％を含まない）〉
Ｎは、Ａｌ等と窒化物を形成する。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に、交流磁束密度の低下を招く。そこでＮ量（鋼中の全窒素量）の上限を０．００４％と定めた。Ｎ量は、好ましくは０．００３％以下、より好ましくは０．００２５％以下である。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）程度であることが推奨される。
<N: 0.004% or less (excluding 0%)>
N forms a nitride with Al or the like. However, N that does not form nitrides remains in a solid solution N state and distorts the crystal structure, causing a decrease in AC magnetic flux density. Therefore, the upper limit of the N amount (total nitrogen amount in steel) is set to 0.004%. The N amount is preferably 0.003% or less, more preferably 0.0025% or less. On the other hand, the lower limit of the N amount is recommended to be about 0.0010% (industrially general lower limit of the N amount) from the viewpoint of steel production cost.
〈Ｏ：０．０２％以下（０％を含まない）〉
Ｏ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、冷間鍛造性を低下させる。さらに焼鈍工程での結晶粒成長を阻害するため、部品の交流磁束密度を低下させる。そのためＯ量は、できる限り抑制することが好ましく、本発明においてＯ量の上限を０．０２％と定めた。Ｏ量は、好ましくは０．０１％以下、より好ましくは０．００５％以下、さらに好ましくは０．００２％以下である。
<O: 0.02% or less (excluding 0%)>
O hardly dissolves in steel at room temperature, exists as a hard oxide, and decreases cold forgeability. Furthermore, in order to inhibit crystal grain growth in the annealing process, the AC magnetic flux density of the component is reduced. Therefore, the amount of O is preferably suppressed as much as possible. In the present invention, the upper limit of the amount of O is set to 0.02%. The amount of O is preferably 0.01% or less, more preferably 0.005% or less, and still more preferably 0.002% or less.
本発明の軟磁性鋼材の基本成分組成は上記の通りであり、残部は実質的にＦｅである。但し原料、資材、製造設備等の状況によって持ち込まれる不可避不純物が鋼材中に含まれることは、当然に許容される。さらに本発明の軟磁性鋼材は、必要に応じて、以下の任意元素を含有していても良い。 The basic component composition of the soft magnetic steel material of the present invention is as described above, and the balance is substantially Fe. However, it is naturally allowed that inevitable impurities brought in depending on the situation of raw materials, materials, manufacturing facilities, etc. are contained in the steel material. Furthermore, the soft magnetic steel material of the present invention may contain the following optional elements as necessary.
〈Ｂ：０．００５％以下〉
Ｂは、固溶ＮをＢＮの形で固定して、冷間鍛造時の動的ひずみ時効を抑制し、良好な冷間鍛造性を維持する作用を有する。この作用を充分に発揮させるために、必要に応じてＢを、好ましくは０．０００２％以上、より好ましくは０．００１％以上、さらに好ましくは０．００１５％以上の量で含有させることが推奨される。しかしＢ量が過剰であると、磁気モーメントが低下して、部品の交流磁束密度が低下する。そこでＢを含有させる場合、その上限を０．００５％と定めた。Ｂ量は、好ましくは０．００４％以下、より好ましくは０．００３％以下である。
<B: 0.005% or less>
B has the effect | action which fixes the solid solution N in the form of BN, suppresses the dynamic strain aging at the time of cold forging, and maintains favorable cold forgeability. In order to fully exert this effect, it is recommended that B is contained as necessary in an amount of preferably 0.0002% or more, more preferably 0.001% or more, and further preferably 0.0015% or more. Is done. However, if the amount of B is excessive, the magnetic moment decreases and the AC magnetic flux density of the component decreases. Therefore, when B is contained, the upper limit is set to 0.005%. The amount of B is preferably 0.004% or less, more preferably 0.003% or less.
〈Ｔｉ：０．３５％以下〉
Ｔｉは、固溶ＮをＴｉＮの形で固定し、結晶格子へのひずみに伴う交流磁束密度の低下を防止する作用を有する。またＴｉ4Ｃ2Ｓ2がフェライト中に分散することで、電気抵抗が向上し、交流磁束密度の低下が防止される。これらの作用を充分に発揮させるために、必要に応じてＴｉを、好ましくは０．１０％以上、好ましくは０．１５％以上の量で含有させることが推奨される。しかしＴｉ量が過剰であると、冷間鍛造性が低下する。具体的には過剰なＴｉは、変形抵抗の上昇と変形能の低下を招き、部品寸法精度のばらつきや加工割れの原因となる。さらにＴｉ炭硫化物が過剰に析出すると、かえって交流磁束密度が低下する。そこでＴｉを含有させる場合、その上限を０．３５％と定めた。Ｔｉ量は、好ましくは０．３０％以下、より好ましくは０．２５％以下である。
<Ti: 0.35% or less>
Ti fixes solute N in the form of TiN and has an effect of preventing a decrease in AC magnetic flux density due to strain on the crystal lattice. Further, since Ti 4 C 2 S 2 is dispersed in the ferrite, the electrical resistance is improved and the reduction of the alternating magnetic flux density is prevented. In order to fully exhibit these actions, it is recommended that Ti be contained in an amount of preferably 0.10% or more, preferably 0.15% or more, if necessary. However, when the amount of Ti is excessive, cold forgeability is lowered. Specifically, excessive Ti causes an increase in deformation resistance and a decrease in deformability, causing variations in part dimensional accuracy and processing cracks. Further, when Ti carbon sulfide is excessively precipitated, the alternating magnetic flux density is lowered. Therefore, when Ti is contained, the upper limit is set to 0.35%. The amount of Ti is preferably 0.30% or less, more preferably 0.25% or less.
〈Ｖ：１．５％以下〉
Ｖは、鋼中で炭化物を形成し、電気抵抗を増加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、必要に応じてＶを、好ましくは０．０５％以上、より好ましくは０．１０％以上、さらに好ましくは０．２０％以上の量で含有させることが推奨される。しかしＶ量が過剰であると、鋼材の冷間鍛造性が低下し、また磁気モーメントが低下して部品の交流磁束密度も低下する。そこでＶを含有させる場合、その上限を１．５％と定めた。Ｖ量は、好ましくは１．４％以下、より好ましくは１．３％以下である。
<V: 1.5% or less>
V forms carbides in the steel and has an action of increasing electric resistance. In order to fully exert this action, it is recommended that V is contained as necessary in an amount of preferably 0.05% or more, more preferably 0.10% or more, and further preferably 0.20% or more. Is done. However, if the amount of V is excessive, the cold forgeability of the steel material decreases, the magnetic moment decreases, and the AC magnetic flux density of the component also decreases. Therefore, when V is contained, the upper limit is set to 1.5%. The amount of V is preferably 1.4% or less, more preferably 1.3% or less.
〈Ｂｉ：０．３％以下〉
Ｂｉは、鋼材の被削性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、必要に応じてＢｉを、０．０１％以上、より好ましくは０．０５％以上の量で含有させることが推奨される。しかしＢｉ量が過剰であると、部品の交流磁束密度が低下するので、含有させる場合、その上限を０．３％と定めた。Ｂｉ量は、好ましくは０．２％以下、より好ましくは０．１％以下である。
<Bi: 0.3% or less>
Bi has the effect | action which improves the machinability of steel materials. In order to sufficiently exhibit this effect, it is recommended that Bi be contained in an amount of 0.01% or more, more preferably 0.05% or more, as necessary. However, if the amount of Bi is excessive, the AC magnetic flux density of the component is lowered. Therefore, when it is contained, the upper limit is set to 0.3%. The Bi amount is preferably 0.2% or less, more preferably 0.1% or less.
〈Ｆ＝９７．０［Ｃ］＋１０．９［Ｓｉ］＋４．２［Ｍｎ］＋２３．８［Ｐ］
＋１７２．０［Ｓ］＋１５．０［Ｃｕ］−０．０３［Ｎｉ］＋５．１［Ｃｒ］
＋８．６［Ａｌ］＋３４［Ｎ］−１２０［Ｂ］−０．２［Ｔｉ］
＋４．５［Ｖ］＋２．９［Ｂｉ］＋８．３８ ・・・ （６）〉
本発明の軟磁性鋼材は、鋼材の冷間鍛造性、およびそれから得られる部品の交流磁束密度を向上させるために、各成分量を適正範囲に調整することを特徴とする。しかし各成分量を適正範囲に調整するだけでは、より高い交流磁束密度を達成することが難しい。そこで本発明者らは、部品の交流磁束密度を一層向上させるために、部品の電気抵抗に着目し、当該電気抵抗を表すパラメーターとしてＦ値を規定した。部品の電気抵抗を向上させれば、渦電流を抑制することができる。そして鉄損は、ヒステリシス損と渦電流損との和であるから、渦電流が抑制されれば、鉄損も抑制することができ、その結果、交流磁束密度の低下も防止できる。
<F = 97.0 [C] +10.9 [Si] +4.2 [Mn] +23.8 [P]
+172.0 [S] +15.0 [Cu] -0.03 [Ni] +5.1 [Cr]
+8.6 [Al] +34 [N] -120 [B] -0.2 [Ti]
+4.5 [V] +2.9 [Bi] +8.38 (6)>
The soft magnetic steel material of the present invention is characterized in that the amount of each component is adjusted to an appropriate range in order to improve the cold forgeability of the steel material and the AC magnetic flux density of the parts obtained therefrom. However, it is difficult to achieve a higher AC magnetic flux density simply by adjusting the amount of each component to an appropriate range. In view of this, the present inventors have focused on the electrical resistance of the component in order to further improve the AC magnetic flux density of the component, and defined the F value as a parameter representing the electrical resistance. If the electrical resistance of the component is improved, eddy current can be suppressed. And since an iron loss is the sum of a hysteresis loss and an eddy current loss, if an eddy current is suppressed, an iron loss can also be suppressed and the fall of alternating current magnetic flux density can also be prevented as a result.
このような着想の下で、以下の実施例で示す軟磁性鋼材Ｎｏ．１〜２５の各元素の含有量（質量％）を説明変数とし、軟磁性部品Ｎｏ．１〜２５の電気抵抗率（μΩｃｍ）を目的変数として、重回帰分析を行った。その結果、自由度調整済み寄与率Ｒ2＝０．９９３で、下記式（７）で表される重回帰式が得られた：
電気抵抗率＝９７．０［Ｃ］＋１０．９［Ｓｉ］＋４．２［Ｍｎ］＋２３．８［Ｐ］
＋１７２．０［Ｓ］＋１５．０［Ｃｕ］−０．０３［Ｎｉ］
＋５．１［Ｃｒ］＋８．６［Ａｌ］＋３４［Ｎ］−１２０［Ｂ］
−０．２［Ｔｉ］＋４．５［Ｖ］＋２．９［Ｂｉ］
＋８．３８ ・・・ （７）
Under such an idea, soft magnetic steel No. 1 shown in the following examples. The content (mass%) of each element of 1 to 25 was used as an explanatory variable, and the soft magnetic component No. A multiple regression analysis was performed using an electrical resistivity (μΩcm) of 1 to 25 as an objective variable. As a result, a multiple regression equation represented by the following equation (7) was obtained with the degree of freedom adjusted contribution R 2 = 0.993:
Electrical resistivity = 97.0 [C] +10.9 [Si] +4.2 [Mn] +23.8 [P]
+172.0 [S] +15.0 [Cu] -0.03 [Ni]
+5.1 [Cr] +8.6 [Al] +34 [N] -120 [B]
−0.2 [Ti] +4.5 [V] +2.9 [Bi]
+8.38 (7)
上記式（６）および上記の重回帰式（７）を対比すれば分かるように、パラメーターＦ値は、部品の電気抵抗率（μΩｃｍ）に対応するものであり、式（６）の各元素（変数）の各係数は、重回帰式（７）の偏回帰係数に対応するものである。さらに実施例の軟磁性鋼材Ｎｏ．１〜２５において、上記式（６）により計算されるＦ値をｘとし、軟磁性部品Ｎｏ．１〜２５の電気抵抗率（μΩｃｍ）をｙとしたグラフを図１に示す。図１のグラフには、ｘ（Ｆ値）を説明変数とし、ｙ（電気抵抗率）を目的変数として回帰分析して得られた回帰式も示す。図１に示されるように、広範囲で、Ｆ値と部品の電気抵抗率とは良好に一致しており、ｙ（電気抵抗率（μΩｃｍ））≒ｘ（Ｆ値）の関係にある。 As can be seen by comparing the above equation (6) and the multiple regression equation (7), the parameter F value corresponds to the electrical resistivity (μΩcm) of the component, and each element of the equation (6) ( Each coefficient of (variable) corresponds to the partial regression coefficient of the multiple regression equation (7). Furthermore, soft magnetic steel material No. 1 to 25, the F value calculated by the above equation (6) is x, and the soft magnetic part No. A graph in which the electrical resistivity (μΩcm) of 1 to 25 is y is shown in FIG. The graph of FIG. 1 also shows a regression equation obtained by regression analysis with x (F value) as an explanatory variable and y (electric resistivity) as an objective variable. As shown in FIG. 1, over a wide range, the F value and the electrical resistivity of the component are in good agreement, and y (electric resistivity (μΩcm)) ≈x (F value).
よってＦ値が６０以上となるように、軟磁性鋼材の各元素量（＝軟磁性部品の各元素量）を調整することにより、軟磁性部品の電気抵抗率を、ほぼ６０μΩｃｍ以上に設定することができる。このように各元素量を調整して、高い電気抵抗率を達成することにより、優れた交流磁束密度を達成することができる。Ｆ値は、より好ましくは６５以上であり、さらに好ましくは７０以上である。 Therefore, by adjusting the amount of each element of the soft magnetic steel material (= the amount of each element of the soft magnetic component) so that the F value is 60 or more, the electric resistivity of the soft magnetic component is set to approximately 60 μΩcm or more. Can do. Thus, the outstanding alternating current magnetic flux density can be achieved by adjusting each element amount and achieving a high electrical resistivity. The F value is more preferably 65 or more, and still more preferably 70 or more.
本発明の軟磁性鋼材は、成分組成に特徴を有するので、その製造方法には特に限定は無く、上記の成分組成の要件を満たすように常法で製造すればよい。しかし本発明の軟磁性鋼材の冷間鍛造性をより向上させるために、また本発明の軟磁性鋼材を焼鈍して得られる軟磁性部品の磁気特性をより向上させるために、本発明の軟磁性鋼材の製造に際して、以下の条件で熱間圧延することが推奨される。 Since the soft magnetic steel material of the present invention is characterized by the component composition, the production method is not particularly limited, and may be produced by a conventional method so as to satisfy the requirements for the above component composition. However, in order to further improve the cold forgeability of the soft magnetic steel material of the present invention and to further improve the magnetic properties of the soft magnetic parts obtained by annealing the soft magnetic steel material of the present invention, In the production of steel materials, it is recommended to perform hot rolling under the following conditions.
合金成分を母相に完全に固溶させるために、圧延前の加熱温度は高いほうが好ましい。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。さらに加熱温度が低すぎると、異なる相が局所的に生成し、圧延時に割れが発生するおそれがある。そこで加熱温度は、１０００℃以上とすることが推奨される。しかし加熱温度が高くなりすぎると、フェライト結晶粒の粗大化が顕著となって、鋼材の冷間鍛造性が低下し得る。そこで加熱温度を１２００℃以下とすることが推奨される。 In order to completely dissolve the alloy components in the matrix, it is preferable that the heating temperature before rolling is higher. Moreover, when heating temperature is low, the roll load at the time of rolling will rise and productivity will fall. Further, if the heating temperature is too low, different phases are locally generated, and cracking may occur during rolling. Therefore, it is recommended that the heating temperature be 1000 ° C. or higher. However, if the heating temperature becomes too high, the ferrite crystal grains become prominent and the cold forgeability of the steel material can be reduced. Therefore, it is recommended that the heating temperature is 1200 ° C. or lower.
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℃以上であることが推奨される。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。 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 is 850 ° C. or higher. 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.
本発明は、上記の成分組成の要件、即ち各成分の含有量およびＦ値の要件を満たし、且つ鋼組織がフェライト単相組織であり、ＪＩＳ Ｇ ０５５２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部品も提供する。なお本発明において、「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。そして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 present invention satisfies the requirements of the above component composition, that is, the content of each component and the F value, and the steel structure is a ferrite single phase structure, and the ferrite crystal grain size number specified by JIS G 0552 is 3 or less. A soft magnetic component is also provided. In the present invention, it is intended that the “ferrite single-phase structure” includes, 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. And by making it a ferrite single phase structure, a magnetic moment increases and an alternating current magnetic flux density can be improved.
軟磁性部品の交流磁束密度は、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。そこで本発明の軟磁性部品は、優れた交流磁束密度を達成するために、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部品は、３以下、好ましくは２．５以下、より好ましくは２．０以下のフェライト結晶粒度番号を有することを特徴とする。 The AC magnetic flux density of the soft magnetic component is related to the amount of energy for fixing the magnetic flux moving inside the component (steel material), and is affected by the size of the ferrite crystal grains. Therefore, if the ferrite crystal grains are coarsened and the grain boundary area is reduced, the coercive force can be reduced and the alternating magnetic flux density can be increased, so that it can be used as a component part of electrical parts such as solenoids, relays, or iron cores of solenoid valves. Suitable magnetic characteristics can be ensured. Therefore, the soft magnetic component of the present invention is characterized by having coarse ferrite crystal grains in order to achieve an excellent alternating magnetic flux density. Specifically, the soft magnetic component of the present invention is characterized by having a ferrite grain size number of 3 or less, preferably 2.5 or less, more preferably 2.0 or less.
本発明の軟磁性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。該焼鈍温度が低すぎると、中に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℃以上であ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。 In order to produce the soft magnetic 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. If the annealing temperature is too low, the nitride precipitated therein inhibits the growth of crystal grains, and it becomes difficult to form coarse crystal grains having a ferrite 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、２時間以上であることが必要である。好ましい焼鈍時間の下限は２．５時間である。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 above annealing temperature needs to be 2 hours or more. The lower limit of the preferable annealing time is 2.5 hours. 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.
以下、実施例を挙げて本発明をより具体的に説明するが、本発明は以下の実施例によって制限を受けるものではなく、上記・下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勿論可能であり、それらはいずれも本発明の技術的範囲に包含される。 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, and appropriate modifications are made within a range that can meet the above and the following purposes. Of course, it is possible to implement them, and both are included in the technical scope of the present invention.
実験例１
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および冷間鍛造性を、下記の方法で測定した。その結果も、表２に示す。
Experimental example 1
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 and the cold forgeability were measured by the following methods. The results are also shown in Table 2.
〈フェライト結晶粒度番号の測定〉
鋼材の横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、ＪＩＳＧ ０５５２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。
<Measurement of ferrite grain size number>
The steel material is embedded in a supporting substrate in a state in which the cross section of the steel material is exposed, and after polishing, is immersed in a 5% picric acid alcohol solution for 15 to 30 seconds to be corroded, and then D / 4 (D is a diameter) with an optical microscope. The structure of the part was photographed at 10 magnifications at 10 fields, the ferrite grain size number defined by JISG 0552 was examined, and the average value was determined as the ferrite grain size number.
〈鋼材の冷間鍛造性の測定〉
鋼材の冷間鍛造性の指標として、圧縮加工で割れが発生しない最大の圧縮率を測定した。具体的には、試料として直径２０ｍｍ×高さ３０ｍｍの鋼材を用い、ひずみ速度１０／秒で端面拘束圧縮して、割れが発生しない最大の圧縮率を測定した。最大圧縮率が５０％以上のものを合格（○）とし、５０％未満のものを不合格（×）とした。
<Measurement of cold forgeability of steel>
As an index of the cold forgeability of the steel material, the maximum compression ratio at which no cracking occurs during compression processing was measured. Specifically, a steel material having a diameter of 20 mm and a height of 30 mm was used as a sample, and end face restraint compression was performed at a strain rate of 10 / second, and the maximum compression ratio at which no cracks occurred was measured. Those having a maximum compression ratio of 50% or more were evaluated as pass (◯), and those having a maximum compression ratio of less than 50% were determined as reject (x).
上記のようにして得られた鋼材Ｎｏ．１〜２５を、下記表３に示す条件で焼鈍して、軟磁性部品Ｎｏ．１〜２５を製造した。部材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の鋼組織は、全て、フェライト単相組織であった。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）を測定した。それらの結果も表３に示す。 The steel material No. obtained as described above. 1 to 25 were annealed under the conditions shown in Table 3 below, and soft magnetic part No. 1-25 were produced. The ferrite crystal grain size number and structure of the member were measured in the same manner as the method for measuring the ferrite crystal grain size number of the steel material. The obtained ferrite grain size number results are shown in Table 3. In addition, member No. All the steel structures 1 to 25 were ferrite single phase structures. Further, the electrical resistivity and magnetic properties (DC magnetic flux density and AC magnetic flux density) of the member were measured. The results are also shown in Table 3.
〈部品の磁気特性の測定〉
前記鋼材を外径１０ｍｍ×内径５ｍｍ×厚さ０．５ｍｍ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磁束密度および交流磁束密度を求めた。なお鉄損に伴う発熱によって、試料温度が上昇するのを防止するため、試料は絶縁処理した上で、２０℃の水中に浸漬して磁気測定を実施した。磁界振幅：８００Ａ／ｍ、周波数：１０ｋＨｚでの交流磁束密度が、５００ｍＴ以上のものを合格（○）とし、５００ｍＴ未満のものを不合格（×）とした。
<Measurement of magnetic properties of parts>
The steel material was processed into a ring shape having an outer diameter of 10 mm, an inner diameter of 5 mm, and a thickness of 0.5 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 magnetic flux density and the alternating magnetic flux density were determined. In order to prevent the temperature of the sample from rising due to heat generated by iron loss, the sample was insulated and immersed in water at 20 ° C. for magnetic measurement. Magnetic flux amplitude: 800 A / m, Frequency: 10 kHz AC magnetic flux density of 500 mT or more was accepted (◯), and less than 500 mT was rejected (x).
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Ｎｏ．１〜１２は、良好な冷間鍛造性を示すこと、および鋼材Ｎｏ．１〜１２により製造された部品Ｎｏ．１〜１２は、高い交流磁束密度を示すことが分かる。しかし本発明の要件を満たさない鋼材ないし部品Ｎｏ．１３〜２５は、以下に示す理由により、冷間鍛造性または交流磁束密度が劣っている。 As shown in Tables 1 to 3, a steel material No. 1 that satisfies the requirements of the component composition of the present invention. Nos. 1-12 show good cold forgeability and Parts No. 1 to 12 manufactured according to No. 1-12. It turns out that 1-12 shows a high alternating current magnetic flux density. However, the steel material or part No. which does not satisfy the requirements of the present invention. 13 to 25 are inferior in cold forgeability or AC magnetic flux density for the following reasons.
鋼材Ｎｏ．１３は、Ｓｉ量が過剰であるため、冷間鍛造性が低下している。なお鋼材Ｎｏ．１３のＦ値は６０未満であり、部品Ｎｏ．１３の交流磁束密度は悪いと予想されるが、反対の結果となっている。これはＦ値が低いことによる交流磁束密度の低下分が、交流磁束密度を向上させる作用を有するＳｉが過剰であることによって補われているためであると考えられる。
鋼材Ｎｏ．１４は、Ａｌ量が過剰であるため、冷間鍛造性が低下している。
鋼材Ｎｏ．１５は、Ｔｉ量が過剰であるため、粗大なＴｉＮが生成し、その結果、冷間鍛造性が低下している。
Steel No. In No. 13, since the Si amount is excessive, the cold forgeability is lowered. Steel No. 13 has an F value of less than 60. The AC magnetic flux density of 13 is expected to be bad, but the opposite result. This is thought to be because the decrease in the AC magnetic flux density due to the low F value is compensated by the excess of Si having the effect of improving the AC magnetic flux density.
Steel No. In No. 14, since the Al amount is excessive, the cold forgeability is lowered.
Steel No. In No. 15, since the Ti amount is excessive, coarse TiN is generated, and as a result, the cold forgeability is lowered.
鋼材Ｎｏ．１６は、Ｐ量が過剰であるため、Ｐが粒界に偏析し、その結果、冷間鍛造性が低下している。
鋼材Ｎｏ．１７は、電磁ステンレスに相当する鋼材であり、Ｃｒを多量に含有しているため、冷間鍛造性が低下している。
Steel No. In No. 16, since the amount of P is excessive, P segregates at the grain boundaries, and as a result, cold forgeability is reduced.
Steel No. 17 is a steel material corresponding to electromagnetic stainless steel, and since it contains a large amount of Cr, cold forgeability is reduced.
部品Ｎｏ．１８は、Ｓｉ、Ｓ、ＣｒおよびＡｌ量が過少であるため、交流磁束密度が低下している。
部品Ｎｏ．１９は、ＭｎおよびＡｌ量が過少であるため、交流磁束密度が低下している。
部品Ｎｏ．２０および２１は、Ｃｒ量が過少であるため、交流磁束密度が低下している。
Part No. In No. 18, since the amounts of Si, S, Cr and Al are too small, the AC magnetic flux density is lowered.
Part No. In No. 19, since the amounts of Mn and Al are too small, the AC magnetic flux density is lowered.
Part No. In 20 and 21, the amount of Cr is too small, so the alternating magnetic flux density is low.
部品Ｎｏ．２２は、Ｍｎ量が過剰であるため、Ｍｎの電気抵抗の向上作用よりも、磁気モーメントを低下させる作用が大きく影響し、その結果、交流磁束密度が低下している。
部品Ｎｏ．２３は、Ｃｒ量が過少であり、Ｎｉ量が過剰であるため、交流磁束密度が低下している。
部品Ｎｏ．２４および２５は、鋼材の各成分量は適正範囲に調整されているが、Ｆ値が６０未満であるため、交流磁束密度が低下している。
Part No. Since the amount of Mn is excessive, the effect of lowering the magnetic moment is more greatly affected than the effect of improving the electrical resistance of Mn. As a result, the alternating magnetic flux density is lowered.
Part No. In No. 23, the amount of Cr is too small and the amount of Ni is too large, so the alternating magnetic flux density is lowered.
Part No. In 24 and 25, the amount of each component of the steel material is adjusted to an appropriate range, but the F value is less than 60, so the AC magnetic flux density is reduced.
実験例２
本発明の鋼材を焼鈍することで交流磁束密度が向上することを示すために、上記の鋼材Ｎｏ．７の電気抵抗率、直流磁束密度および交流磁束密度を測定した。鋼材Ｎｏ．７（焼鈍なし）および部品Ｎｏ．７（焼鈍あり）の電気抵抗率、直流磁束密度および交流磁束密度の結果を、下記表４にまとめる。表４に示す結果から、焼鈍することで部品Ｎｏ．７の交流磁束密度が向上していることが分かる。
Experimental example 2
In order to show that the AC magnetic flux density is improved by annealing the steel material of the present invention, the above steel material No. 7 electrical resistivity, DC magnetic flux density and AC magnetic flux density were measured. Steel No. 7 (no annealing) and part no. The results of electrical resistivity, DC magnetic flux density and AC magnetic flux density of 7 (with annealing) are summarized in Table 4 below. From the results shown in Table 4, the part no. 7 shows that the AC magnetic flux density is improved.
Claims (7)
Ｓｉ：１．８〜３．０％、
Ｍｎ：０．２０〜０．８％、
Ｐ：０．０２％以下（０％を含まない）、
Ｓ：０．０２〜０．１％、
Ｃｕ：０．１％以下（０％を含まない）、
Ｎｉ：０．２％以下（０％を含まない）、
Ｃｒ：１〜３．５％、
Ａｌ：０．０５〜２．８％、
Ｎ：０．００４％以下（０％を含まない）、および
Ｏ：０．０２％以下（０％を含まない）
を含有し、残部がＦｅおよび不可避不純物からなり、
下記式（１）で計算されるＦ１値が６０以上であることを特徴とする軟磁性鋼材。
Ｆ１＝９７．０［Ｃ］＋１０．９［Ｓｉ］＋４．２［Ｍｎ］＋２３．８［Ｐ］
＋１７２．０［Ｓ］＋１５．０［Ｃｕ］−０．０３［Ｎｉ］＋５．１［Ｃｒ］
＋８．６［Ａｌ］＋３４．０［Ｎ］＋８．３８ ・・・ （１）
〔式中、［ ］は、それぞれ軟磁性鋼材中の各元素の含有量（質量％）を表す。〕 C: 0.005-0.05% (meaning mass%, the same shall apply hereinafter)
Si: 1.8-3.0%,
Mn: 0.20 to 0.8%,
P: 0.02% or less (excluding 0%),
S: 0.02-0.1%,
Cu: 0.1% or less (excluding 0%),
Ni: 0.2% or less (excluding 0%),
Cr: 1 to 3.5%,
Al: 0.05 to 2.8%,
N: 0.004% or less (not including 0%), and O: 0.02% or less (not including 0%)
And the balance consists of Fe and inevitable impurities,
A soft magnetic steel material having an F1 value calculated by the following formula (1) of 60 or more.
F1 = 97.0 [C] +10.9 [Si] +4.2 [Mn] +23.8 [P]
+172.0 [S] +15.0 [Cu] -0.03 [Ni] +5.1 [Cr]
+8.6 [Al] +34.0 [N] +8.38 (1)
[In formula, [] represents content (mass%) of each element in a soft-magnetic steel material, respectively. ]
Ｆ２＝９７．０［Ｃ］＋１０．９［Ｓｉ］＋４．２［Ｍｎ］＋２３．８［Ｐ］
＋１７２．０［Ｓ］＋１５．０［Ｃｕ］−０．０３［Ｎｉ］＋５．１［Ｃｒ］
＋８．６［Ａｌ］＋３４［Ｎ］−１２０［Ｂ］＋８．３８ ・・・ （２）
〔式中、［ ］は、それぞれ軟磁性鋼材中の各元素の含有量（質量％）を表す。〕 The soft magnetic steel material according to claim 1, further comprising B: 0.005% or less (excluding 0%) and having an F2 value calculated by the following formula (2) of 60 or more.
F2 = 97.0 [C] +10.9 [Si] +4.2 [Mn] +23.8 [P]
+172.0 [S] +15.0 [Cu] -0.03 [Ni] +5.1 [Cr]
+8.6 [Al] +34 [N] -120 [B] +8.38 (2)
[In formula, [] represents content (mass%) of each element in a soft-magnetic steel material, respectively. ]
Ｆ３＝９７．０［Ｃ］＋１０．９［Ｓｉ］＋４．２［Ｍｎ］＋２３．８［Ｐ］
＋１７２．０［Ｓ］＋１５．０［Ｃｕ］−０．０３［Ｎｉ］＋５．１［Ｃｒ］
＋８．６［Ａｌ］＋３４［Ｎ］−１２０［Ｂ］−０．２［Ｔｉ］
＋８．３８ ・・・ （３）
〔式中、［ ］は、それぞれ軟磁性鋼材中の各元素の含有量（質量％）を表す。〕 The soft magnetic steel material according to claim 1 or 2, further comprising Ti: 0.35% or less (excluding 0%) and having an F3 value calculated by the following formula (3) of 60 or more.
F3 = 97.0 [C] +10.9 [Si] +4.2 [Mn] +23.8 [P]
+172.0 [S] +15.0 [Cu] -0.03 [Ni] +5.1 [Cr]
+8.6 [Al] +34 [N] -120 [B] -0.2 [Ti]
+8.38 (3)
[In formula, [] represents content (mass%) of each element in a soft-magnetic steel material, respectively. ]
Ｆ４＝９７．０［Ｃ］＋１０．９［Ｓｉ］＋４．２［Ｍｎ］＋２３．８［Ｐ］
＋１７２．０［Ｓ］＋１５．０［Ｃｕ］−０．０３［Ｎｉ］＋５．１［Ｃｒ］
＋８．６［Ａｌ］＋３４［Ｎ］−１２０［Ｂ］−０．２［Ｔｉ］
＋４．５［Ｖ］＋８．３８ ・・・ （４） The soft magnetic steel material according to any one of claims 1 to 3, further comprising V: 1.5% or less (excluding 0%) and having an F4 value calculated by the following formula (4) of 60 or more. .
F4 = 97.0 [C] +10.9 [Si] +4.2 [Mn] +23.8 [P]
+172.0 [S] +15.0 [Cu] -0.03 [Ni] +5.1 [Cr]
+8.6 [Al] +34 [N] -120 [B] -0.2 [Ti]
+4.5 [V] +8.38 (4)
Ｆ５＝９７．０［Ｃ］＋１０．９［Ｓｉ］＋４．２［Ｍｎ］＋２３．８［Ｐ］
＋１７２．０［Ｓ］＋１５．０［Ｃｕ］−０．０３［Ｎｉ］＋５．１［Ｃｒ］
＋８．６［Ａｌ］＋３４［Ｎ］−１２０［Ｂ］−０．２［Ｔｉ］
＋４．５［Ｖ］＋２．９［Ｂｉ］＋８．３８ ・・・ （５）
〔式中、［ ］は、それぞれ軟磁性鋼材中の各元素の含有量（質量％）を表す。〕 The soft magnetic steel material according to any one of claims 1 to 4, further comprising Bi: 0.3% or less (not including 0%) and having an F5 value calculated by the following formula (5) of 60 or more. .
F5 = 97.0 [C] +10.9 [Si] +4.2 [Mn] +23.8 [P]
+172.0 [S] +15.0 [Cu] -0.03 [Ni] +5.1 [Cr]
+8.6 [Al] +34 [N] -120 [B] -0.2 [Ti]
+4.5 [V] +2.9 [Bi] +8.38 (5)
[In formula, [] represents content (mass%) of each element in a soft-magnetic steel material, respectively. ]
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| CN104465002A (en) * | 2013-09-20 | 2015-03-25 | 太阳诱电株式会社 | Magnetic body and electronic component using the same |
| US11248283B2 (en) | 2016-12-08 | 2022-02-15 | Nippon Steel Corporation | Steel material for soft magnetic part, soft magnetic part, and method for producing soft magnetic part |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2000313944A (en) * | 1999-04-28 | 2000-11-14 | Sanyo Special Steel Co Ltd | Free-cutting corrosion-resistant soft magnetic material excellent in magnetic property |
| JP2001040456A (en) * | 1999-07-29 | 2001-02-13 | Sanyo Special Steel Co Ltd | Electromagnetic material having excellent cold forgeability and weat resistance |
| JP2001073101A (en) * | 1999-09-01 | 2001-03-21 | Sanyo Special Steel Co Ltd | Electromagnetic material having high magnetic flux density and high specific resistance and excellent in machinability and cold forgeability |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2000313944A (en) * | 1999-04-28 | 2000-11-14 | Sanyo Special Steel Co Ltd | Free-cutting corrosion-resistant soft magnetic material excellent in magnetic property |
| JP2001040456A (en) * | 1999-07-29 | 2001-02-13 | Sanyo Special Steel Co Ltd | Electromagnetic material having excellent cold forgeability and weat resistance |
| JP2001073101A (en) * | 1999-09-01 | 2001-03-21 | Sanyo Special Steel Co Ltd | Electromagnetic material having high magnetic flux density and high specific resistance and excellent in machinability and cold forgeability |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104465002A (en) * | 2013-09-20 | 2015-03-25 | 太阳诱电株式会社 | Magnetic body and electronic component using the same |
| US11248283B2 (en) | 2016-12-08 | 2022-02-15 | Nippon Steel Corporation | Steel material for soft magnetic part, soft magnetic part, and method for producing soft magnetic part |
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