JP2016027191A - Soft magnetic steel plate and manufacturing method thereof, and method for manufacturing soft magnetic member - Google Patents
Soft magnetic steel plate and manufacturing method thereof, and method for manufacturing soft magnetic member Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 117
- 239000010959 steel Substances 0.000 title claims abstract description 117
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 34
- 238000000034 method Methods 0.000 title claims description 28
- 238000000137 annealing Methods 0.000 claims abstract description 68
- 239000013078 crystal Substances 0.000 claims abstract description 37
- 239000000203 mixture Substances 0.000 claims abstract description 13
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 238000005097 cold rolling Methods 0.000 claims description 26
- 238000005096 rolling process Methods 0.000 claims description 22
- 230000008569 process Effects 0.000 claims description 20
- 230000009467 reduction Effects 0.000 claims description 19
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 14
- 239000002245 particle Substances 0.000 claims description 13
- 238000005098 hot rolling Methods 0.000 claims description 12
- 239000000463 material Substances 0.000 claims description 12
- 239000002244 precipitate Substances 0.000 claims description 12
- 229910052742 iron Inorganic materials 0.000 claims description 5
- 239000004615 ingredient Substances 0.000 claims description 2
- 229910052717 sulfur Inorganic materials 0.000 abstract description 4
- 229910052748 manganese Inorganic materials 0.000 abstract description 3
- 229910052799 carbon Inorganic materials 0.000 abstract description 2
- 229910052804 chromium Inorganic materials 0.000 abstract description 2
- 229910052757 nitrogen Inorganic materials 0.000 abstract 1
- 229910052698 phosphorus Inorganic materials 0.000 abstract 1
- 230000000694 effects Effects 0.000 description 11
- 238000004080 punching Methods 0.000 description 9
- 238000005452 bending Methods 0.000 description 7
- 238000005259 measurement Methods 0.000 description 7
- 238000000465 moulding Methods 0.000 description 5
- 238000011156 evaluation Methods 0.000 description 4
- 230000004907 flux Effects 0.000 description 4
- 238000012360 testing method Methods 0.000 description 4
- 230000007423 decrease Effects 0.000 description 3
- 238000009864 tensile test Methods 0.000 description 3
- 238000012935 Averaging Methods 0.000 description 2
- 206010013786 Dry skin Diseases 0.000 description 2
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 2
- 238000004458 analytical method Methods 0.000 description 2
- 239000010960 cold rolled steel Substances 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 238000001887 electron backscatter diffraction Methods 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 229910052739 hydrogen Inorganic materials 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 230000005389 magnetism Effects 0.000 description 2
- 238000000611 regression analysis Methods 0.000 description 2
- 230000004043 responsiveness Effects 0.000 description 2
- 238000007788 roughening Methods 0.000 description 2
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 230000005540 biological transmission Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 238000010273 cold forging Methods 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 239000000696 magnetic material Substances 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 239000002436 steel type Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 230000003746 surface roughness Effects 0.000 description 1
- 229910052718 tin Inorganic materials 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
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Abstract
Description
本発明は、自動車、電車、船舶などの電装部品に使用されるソレノイドやリレーなどのケースやカバー、鉄心等として有用な軟磁性部材およびその材料となる軟磁性鋼板に関し、例えば、プレス成形により製造され、磁気特性を必要とする軟磁性部材において、優れたプレス成形性や良好な直流磁気特性を発揮することのできる軟磁性鋼板およびその製造方法、ならびに、軟磁性部材の製造方法に関するものである。 TECHNICAL FIELD The present invention relates to a soft magnetic member useful as a case or cover such as a solenoid or a relay used for electrical parts such as automobiles, trains, ships, and iron cores, and a soft magnetic steel sheet as a material thereof. The present invention relates to a soft magnetic steel sheet that can exhibit excellent press formability and good DC magnetic characteristics in a soft magnetic member that requires magnetic properties, a method for manufacturing the same, and a method for manufacturing a soft magnetic member. .
近年、自動車の燃費向上に対するニーズがますます強くなり、エンジンやトランスミッションその他に使用される電装部品には、よりいっそうの性能向上、たとえば応答性、省電力化、小型化が望まれている。そのためには、磁気特性として、磁化されやすく、保磁力が小さいことが有効である。 In recent years, the need for improving the fuel efficiency of automobiles has become stronger, and electrical components used in engines, transmissions, and the like are desired to have further improved performance, such as responsiveness, power saving, and downsizing. For this purpose, it is effective that the magnetic properties are easily magnetized and the coercive force is small.
さらに製造コストの低減に対するニーズも大きい。すなわち、磁気回路を形成する部材、たとえばソレノイドの外郭を形成するケースやカバー、さらには鉄心にも、従来のように線材や棒鋼を冷間鍛造して切削する方法に代えて、鋼板をプレス成形して部材形状を作製する方法が注目されている。 Furthermore, there is a great need for a reduction in manufacturing costs. In other words, members that form magnetic circuits, such as cases and covers that form the outer shell of solenoids, and iron cores, instead of conventional methods of cold forging and cutting wires and steel bars, are pressed into steel plates. Thus, a method for producing a member shape has attracted attention.
たとえば、特許文献１には、本発明に係る軟磁性鋼板と近似した純鉄系の成分組成を有し、冷間鍛造性と電気伝導性に優れた電気部品用鋼材が開示されている。しかしながら、この電気部品用鋼材は、伸線して製造される線材に関するもので、鋼板に関する記載はない。 For example, Patent Document 1 discloses a steel material for electrical parts that has a pure iron-based component composition similar to that of the soft magnetic steel sheet according to the present invention and is excellent in cold forgeability and electrical conductivity. However, this steel material for electrical parts relates to a wire manufactured by drawing, and there is no description about a steel plate.
また、特許文献２には、成形性と磁気特性に優れた熱延鋼板が開示されている。しかしながら、熱延鋼板は表面状態が悪いため、そのまま電磁気部品に用いることはできない。また、結晶粒径が大きすぎるため、曲げ加工後の肌荒れが懸念される。 Patent Document 2 discloses a hot-rolled steel sheet excellent in formability and magnetic properties. However, the hot-rolled steel sheet cannot be used as an electromagnetic component as it is because of its poor surface condition. Moreover, since the crystal grain size is too large, there is a concern about rough skin after bending.
また、特許文献３には、磁気特性と加工性に優れたＴＶブラウン管マスクフレーム用冷延鋼板が開示されている。しかしながら、このＴＶブラウン管マスクフレーム用冷延鋼板は、Ｃｕ、Ｓｎ、Ｎｉ、Ｃｒ等の不純物元素の相当量の含有を前提とするものであり、純鉄系の成分組成を前提とする、本発明に係る軟磁性鋼板とはそもそも前提が異なる技術である。 Patent Document 3 discloses a cold-rolled steel sheet for a TV CRT mask frame having excellent magnetic properties and workability. However, this cold-rolled steel sheet for a TV CRT mask frame is premised on containing a substantial amount of impurity elements such as Cu, Sn, Ni, Cr, etc., and is premised on a pure iron-based component composition. This is a technology that is originally different from the soft magnetic steel sheet.
本発明は、このような事情を鑑みてなされたものであり、その目的は、優れた磁気特性を有する軟磁性鋼板およびその製造方法、ならびに、軟磁性部材の製造方法を提供することにある。 This invention is made | formed in view of such a situation, The objective is to provide the soft magnetic steel plate which has the outstanding magnetic characteristic, its manufacturing method, and the manufacturing method of a soft magnetic member.
また、本発明の他の目的は、優れた成形性を有する軟磁性鋼板およびその製造方法、ならびに、軟磁性部材の製造方法を提供することにある。 Another object of the present invention is to provide a soft magnetic steel sheet having excellent formability, a method for producing the same, and a method for producing a soft magnetic member.
また、本発明の他の目的は、優れた耐肌荒れ性を有する軟磁性鋼板およびその製造方法、ならびに、軟磁性部材の製造方法を提供することにある。 Another object of the present invention is to provide a soft magnetic steel sheet having excellent skin roughness resistance, a method for producing the same, and a method for producing a soft magnetic member.
また、本発明の他の目的は、優れた被削性を有する軟磁性鋼板およびその製造方法、ならびに、軟磁性部材の製造方法を提供することにある。 Another object of the present invention is to provide a soft magnetic steel sheet having excellent machinability, a method for producing the same, and a method for producing a soft magnetic member.
本発明の前記並びにその他の目的と新規な特徴は、本明細書の記述から明らかになるであろう。 The above and other objects and novel features of the present invention will be apparent from the description of this specification.
本発明に係る第１発明は、
成分組成が、質量％で、
Ｃ：０．００１〜０．０２％、
Ｓｉ：０〜０．０５％、
Ｍｎ：０．０５〜０．５％、
Ｐ：０〜０．０２％、
Ｓ：０〜０．１％、
Ａｌ：０〜０．０１％、
Ｃｒ：０〜０．１％、
Ｎ：０〜０．００５％
であり、残部が鉄および不可避的不純物からなる軟磁性鋼板であって、
平均結晶粒径が５〜５０μｍであり、
さらに、当該軟磁性鋼板のＫＡＭ値Ｋａと、当該軟磁性鋼板を８５０℃で３時間焼鈍した後のＫＡＭ値Ｋｂとの比Ｋａ／Ｋｂが１．２〜４．５である
ことを特徴とする、板厚０．８〜４．０ｍｍの軟磁性鋼板である。
ここに、「ＫＡＭ値」とは、「Ｋｅｒｎｅｌ Ａｖｅｒａｇｅ Ｍｉｓｏｒｉｅｎｔａｔｉｏｎ値」を意味する。
The first invention according to the present invention is:
Ingredient composition is mass%,
C: 0.001 to 0.02%,
Si: 0 to 0.05%,
Mn: 0.05 to 0.5%
P: 0 to 0.02%,
S: 0 to 0.1%,
Al: 0 to 0.01%,
Cr: 0 to 0.1%,
N: 0 to 0.005%
And the balance is a soft magnetic steel plate made of iron and inevitable impurities,
The average crystal grain size is 5-50 μm,
Furthermore, the ratio Ka / Kb between the KAM value Ka of the soft magnetic steel sheet and the KAM value Kb after annealing the soft magnetic steel sheet at 850 ° C. for 3 hours is 1.2 to 4.5. A soft magnetic steel sheet having a thickness of 0.8 to 4.0 mm.
Here, the “KAM value” means a “Kernel Average Mission value”.
本発明に係る第２発明は、上記第１発明において、
前記Ｓの含有量が、Ｓ：０．０１５〜０．１質量％である、軟磁性鋼板である。
According to a second aspect of the present invention, in the first aspect,
It is a soft magnetic steel plate in which the content of S is S: 0.015 to 0.1% by mass.
本発明に係る第３発明は、上記第１発明において、
前記Ｓの含有量が、Ｓ：０〜０．０６質量％である、軟磁性鋼板である。
According to a third aspect of the present invention, in the first aspect,
It is a soft magnetic steel plate in which the content of S is S: 0 to 0.06% by mass.
本発明に係る第４発明は、上記第１〜第３発明のいずれか１つの発明において、
さらに、Ｍｎ／Ｓ原子比が３〜２０であり、
ＭｎＳ析出物の平均粒径が０．０５〜４μｍで、かつ、
粒径０．２μｍ以上のＭｎＳ析出物の個数密度が０．０２〜０．５個／μｍ２である、軟磁性鋼板である。
According to a fourth aspect of the present invention, in any one of the first to third aspects of the invention,
Furthermore, the Mn / S atomic ratio is 3-20,
The average particle size of the MnS precipitate is 0.05-4 μm, and
This is a soft magnetic steel sheet in which the number density of MnS precipitates having a particle size of 0.2 μm or more is 0.02 to 0.5 / μm 2 .
本発明に係る第５発明は、
上記第１〜第３発明のいずれか１つの発明の成分組成を有する鋼材を熱間圧延して熱延板とする熱延工程と、
前記熱延板を圧下率Ｒ１：４０％以上で冷間圧延して冷延板とする粗冷延工程と、
前記冷延板を、下記式１を満足するように、軟化焼鈍温度Ｔ１℃で軟化焼鈍時間Ｈ１秒間保持して軟化焼鈍板とする軟化焼鈍工程と、
さらに、前記軟化焼鈍板を、圧下率Ｒ２：０．５〜１０％で冷間圧延する仕上げ冷延工程と、
を備えたことを特徴とする、軟磁性鋼板の製造方法である。
式１：２１０≦［{１００−Ｒ１＋０．２×（２７３＋Ｔ１)｝２＋Ｈ１×ｅｘｐ｛−１０／（２７３＋Ｔ１）｝］１／２ ≦２６５
ただし、６５０℃≦Ｔ１≦７８０℃である。
The fifth invention according to the present invention is:
A hot rolling step of hot rolling a steel material having the component composition of any one of the first to third inventions into a hot rolled sheet;
A rough cold rolling process in which the hot rolled sheet is cold rolled at a rolling reduction R1: 40% or more to form a cold rolled sheet;
A softening annealing step in which the cold-rolled sheet is held at a softening annealing temperature T1 ° C. and a softening annealing time H1 second so as to satisfy the following formula 1,
Furthermore, a finish cold rolling step of cold rolling the softened annealed plate at a rolling reduction R2: 0.5 to 10%;
A method for producing a soft magnetic steel sheet, comprising:
Formula 1: 210 ≦ [{100−R1 + 0.2 × (273 + T1)} 2 + H1 × exp {−10 / (273 + T1)}] 1/2 ≦ 265
However, it is 650 degreeC <= T1 <= 780 degreeC.
本発明に係る第６発明は、
上記第１〜第３発明いずれか１つの発明の成分組成を有する鋼材を熱間圧延して熱延板とする熱延工程と、
前記熱延板を圧下率Ｒ１：４０％以上で冷間圧延して冷延板とする粗冷延工程と、
前記冷延板を、下記式１を満足するように、軟化焼鈍温度Ｔ１℃で軟化焼鈍時間Ｈ１秒間保持して軟化焼鈍板とする軟化焼鈍工程と、
前記軟化焼鈍板を、さらに、圧下率Ｒ２：０．５〜１０％で冷間圧延することにより軟磁性鋼板を得る仕上げ冷延工程と、
前記軟磁性鋼板を部材形状に成形して成形部材とする成形工程と、
前記成形部材を、下記式２を満足するように、磁気焼鈍温度Ｔ２℃で磁気焼鈍時間Ｈ２秒間保持することにより軟磁性部材を得る磁気焼鈍工程と
を備えたことを特徴とする、軟磁性部材の製造方法である。
式１：２１０≦［{１００−Ｒ１＋０．２×（２７３＋Ｔ１)｝２＋Ｈ１×ｅｘｐ｛−１０／（２７３＋Ｔ１）｝］１／２ ≦２６５
ただし、６５０℃≦Ｔ１≦７８０℃である。
式２：３２０≦［{１００−Ｒ２＋０．２×（２７３＋Ｔ２)｝２＋Ｈ２×ｅｘｐ｛−１０／（２７３＋Ｔ２）｝］１／２
ただし、７５０℃≦Ｔ２≦９００℃である。
The sixth invention according to the present invention is:
A hot rolling step of hot-rolling a steel material having the composition of any one of the first to third inventions into a hot-rolled sheet;
A rough cold rolling process in which the hot rolled sheet is cold rolled at a rolling reduction R1: 40% or more to form a cold rolled sheet;
A softening annealing step in which the cold-rolled sheet is held at a softening annealing temperature T1 ° C. and a softening annealing time H1 second so as to satisfy the following formula 1,
A finish cold rolling step of obtaining a soft magnetic steel sheet by cold rolling the softened annealed plate at a rolling reduction R2 of 0.5 to 10%;
A forming step of forming the soft magnetic steel sheet into a member shape and forming a formed member;
A soft magnetic member comprising: a magnetic annealing step for obtaining a soft magnetic member by holding the molded member at a magnetic annealing temperature T2 ° C. so as to satisfy the following formula 2 and a magnetic annealing time H2 seconds: It is a manufacturing method.
Formula 1: 210 ≦ [{100−R1 + 0.2 × (273 + T1)} 2 + H1 × exp {−10 / (273 + T1)}] 1/2 ≦ 265
However, it is 650 degreeC <= T1 <= 780 degreeC.
Formula 2: 320 ≦ [{100−R2 + 0.2 × (273 + T2)} 2 + H2 × exp {−10 / (273 + T2)}] 1/2
However, 750 ° C. ≦ T2 ≦ 900 ° C.
本願において開示される発明のうち、代表的なものによって得られる効果を簡単に説明すれば以下のとおりである。 Among the inventions disclosed in the present application, effects obtained by typical ones will be briefly described as follows.
本発明の一実施の形態によれば、優れた磁気特性を有する軟磁性鋼板を提供することができる。 According to one embodiment of the present invention, a soft magnetic steel sheet having excellent magnetic properties can be provided.
軟磁性鋼板について高い磁性を得るための要件は、成分組成として添加元素や不純物を適正範囲に制御すること、磁気焼鈍後の部材において十分にひずみ、すなわち塑性変形による転位を除去し、適正範囲の結晶粒径にすることが重要である。一方、成形性については、基本的な特性として、引張試験での伸びが大きいことが重要である。 The requirements for obtaining high magnetism for the soft magnetic steel sheet are to control the additive elements and impurities as appropriate components in the proper range, to sufficiently dissect strain in the member after magnetic annealing, that is, to remove dislocations caused by plastic deformation, It is important to have a crystal grain size. On the other hand, as for the moldability, it is important that the elongation in the tensile test is large as a basic characteristic.
そこで、本発明者らは、種々の成分組成の鋼板について、その製造条件と組織形態および成形性との関係、さらには磁気焼鈍後の組織形態と磁気特性との関係を詳細に検討した。その結果、鋼板の結晶粒径とひずみ量を適正化することで、成形性を向上させるとともに、磁気焼鈍を実施することによって効果的に組織形態を変化させ、磁気特性も向上させることができることを見出した。上記知見に基づき、さらに検討を進め、本発明を完成するに至った。 Therefore, the present inventors examined in detail the relationship between the manufacturing conditions, the structure morphology, and the formability of the steel sheets having various component compositions, and the relationship between the structure morphology after magnetic annealing and the magnetic properties. As a result, by optimizing the crystal grain size and strain amount of the steel sheet, it is possible to improve the formability and effectively change the form of the structure and improve the magnetic properties by carrying out magnetic annealing. I found it. Based on the above findings, further studies have been made and the present invention has been completed.
以下、まず本発明に係る軟磁性鋼板を特徴づける組織について説明する。 Hereinafter, the structure characterizing the soft magnetic steel sheet according to the present invention will be described first.
〔軟磁性鋼板の組織〕
上述したとおり、本発明に係る軟磁性鋼板は、結晶粒径とひずみ量が制御されている点に特徴を有する。
[Structure of soft magnetic steel sheet]
As described above, the soft magnetic steel sheet according to the present invention is characterized in that the crystal grain size and strain amount are controlled.
＜平均結晶粒径：５〜５０μｍ＞
軟磁性鋼板、すなわち磁気焼鈍前の鋼板ままの平均結晶粒径は、成形性に直接影響し、細かすぎると硬さが増加して伸びが低下するため、その下限は５μｍ、好ましくは６μｍ、さらに好ましくは７μｍとした。一方、上記鋼板ままの平均結晶粒径が大きすぎると、鋼板に対して曲げ加工を行った際に、肌荒れが著しく発生したり、鋼板に対して、打抜き加工を行った際にバリが発生したりするため、その上限は５０μｍ、好ましくは４５μｍ、さらに好ましくは４０μｍとした。
<Average crystal grain size: 5 to 50 μm>
The average crystal grain size of the soft magnetic steel sheet, that is, the steel sheet before magnetic annealing, directly affects the formability, and if it is too fine, the hardness increases and the elongation decreases, so the lower limit is 5 μm, preferably 6 μm. Preferably it was 7 micrometers. On the other hand, if the average crystal grain size of the steel sheet is too large, when the steel sheet is bent, rough skin occurs significantly, or burrs occur when the steel sheet is punched. Therefore, the upper limit is 50 μm, preferably 45 μm, and more preferably 40 μm.
＜当該軟磁性鋼板のＫＡＭ値Ｋａと、当該軟磁性鋼板を８５０℃で３時間焼鈍した後のＫＡＭ値Ｋｂとの比Ｋａ／Ｋｂ：１．２〜４．５＞
ＫＡＭ（Ｋｅｒｎｅｌ Ａｖｅｒａｇｅ Ｍｉｓｏｒｉｅｎｔａｔｉｏｎ）値は、材料は塑性変形したときの塑性ひずみ量に関係する指標である。本発明においては、当該軟磁性鋼板を８５０℃で３時間加熱焼鈍することによって結晶粒径をある程度以上に大きくして、かつ塑性ひずみが概ねなくなった状態におけるＫＡＭ値Ｋｂを基準として、これに対する鋼板ままのＫＡＭ値Ｋａの倍率Ｋａ／Ｋｂを用いて、当該軟磁性鋼板のひずみ量を相対的に評価するようにした。高圧下率の冷間圧延によって塑性ひずみ量が大きくなると、ＫＡＭ値が増大し、成形時における伸びが劣化するため、Ｋａ／Ｋｂの上限を４．５、好ましくは４．０、さらに好ましくは３．５とする。一方、塑性ひずみは後の磁気焼鈍において結晶粒を粗大化させる駆動力にもなること、すなわち、軟磁性鋼板にひずみをある程度導入することによって、良好な磁気特性を確保し、曲げ加工後の肌荒れや、打抜き加工後のバリの発生を抑制することができる。このため、軟磁性鋼板中のひずみ量を適切なレベルにしておく必要があり、Ｋａ／Ｋｂの下限を１．２、好ましくは１．３、さらに好ましくは１．４とする。
<Ratio Ka / Kb of the KAM value Ka of the soft magnetic steel plate and the KAM value Kb after annealing the soft magnetic steel plate at 850 ° C. for 3 hours: 1.2 to 4.5>
The KAM (Kernel Average Misoration) value is an index related to the amount of plastic strain when the material is plastically deformed. In the present invention, the soft magnetic steel sheet is annealed at 850 ° C. for 3 hours to increase the crystal grain size to a certain level and the KAM value Kb in the state in which the plastic strain is almost eliminated is used as a reference. Using the Ka / Kb magnification Ka / Kb of the KAM value Ka, the strain amount of the soft magnetic steel sheet was relatively evaluated. When the amount of plastic strain increases due to cold rolling under high pressure, the KAM value increases and the elongation during molding deteriorates. Therefore, the upper limit of Ka / Kb is 4.5, preferably 4.0, more preferably 3 .5. On the other hand, plastic strain also becomes a driving force that coarsens crystal grains in the subsequent magnetic annealing, that is, by introducing strain to some extent in the soft magnetic steel sheet, ensuring good magnetic properties and roughening after bending Moreover, generation | occurrence | production of the burr | flash after a punching process can be suppressed. For this reason, it is necessary to set the amount of strain in the soft magnetic steel sheet to an appropriate level, and the lower limit of Ka / Kb is set to 1.2, preferably 1.3, and more preferably 1.4.
次に、本発明に係る軟磁性部材を特徴づける組織について説明する。 Next, the structure characterizing the soft magnetic member according to the present invention will be described.
〔軟磁性部材の組織〕
本発明に係る軟磁性部材は、結晶粒径が制御されている点に特徴を有する。
[Structure of soft magnetic material]
The soft magnetic member according to the present invention is characterized in that the crystal grain size is controlled.
＜当該軟磁性部材の全域での平均結晶粒径：３０μｍ以上＞
上記軟磁性鋼板を成形し磁気焼鈍した後の軟磁性部材においては、結晶粒をできるだけ粗大化することによって磁気特性、特に保磁力が小さいという良好な磁気特性が得られるため、当該軟磁性部材の全域での平均結晶粒径を３０μｍ以上、好ましくは４０μｍ以上、さらに好ましくは５０μｍ以上とする。
<Average crystal grain size in the entire area of the soft magnetic member: 30 μm or more>
In the soft magnetic member after the soft magnetic steel sheet is formed and magnetically annealed, the crystal grains are made as coarse as possible to obtain magnetic properties, particularly good magnetic properties with low coercive force. The average crystal grain size in the entire region is 30 μm or more, preferably 40 μm or more, more preferably 50 μm or more.
次に、本発明に係る軟磁性鋼板を構成する成分組成について説明する。以下、化学成分の単位はすべて質量％である。 Next, the component composition constituting the soft magnetic steel sheet according to the present invention will be described. Hereinafter, all the units of chemical components are mass%.
〔軟磁性鋼板の成分組成〕
Ｃ：０．００１〜０．０２％
Ｃは、鋼中に固溶して、あるいは炭化物を形成して磁気特性を劣化させるため、極力低減させるべきであるが、Ｃ含有量が０．００１％を下回っても磁気特性の向上効果は小さいため、その下限を０．００１％とする。一方、Ｃ含有量が０．０２％を超えると急激に磁気特性が劣化するため、その上限を０．０２％、好ましくは０．０１５％、さらに好ましくは０．０１％とする。
[Component composition of soft magnetic steel sheet]
C: 0.001 to 0.02%
C should be reduced as much as possible because it dissolves in steel or forms carbides to deteriorate the magnetic properties. However, even if the C content is less than 0.001%, the effect of improving the magnetic properties is not achieved. Since it is small, the lower limit is made 0.001%. On the other hand, if the C content exceeds 0.02%, the magnetic properties deteriorate rapidly, so the upper limit is made 0.02%, preferably 0.015%, more preferably 0.01%.
Ｓｉ：０〜０．０５％
Ｓｉは、脱酸剤として使用されるが、伸びを低下させる作用があるため、Ｓｉ含有量の上限を０．０５％、好ましくは０．０４％、さらに好ましくは０．０３％とする。
Si: 0 to 0.05%
Si is used as a deoxidizer, but has the effect of reducing elongation, so the upper limit of Si content is 0.05%, preferably 0.04%, and more preferably 0.03%.
Ｍｎ：０．０５〜０．５％
Ｍｎは脱酸作用を有するので、本発明においては、磁気特性とプレス成形性の両立のために、Ｃ、ＳおよびＡｌの各含有量を従来鋼に比べて低めにしている代わりに、Ｍｎが脱酸剤としての役割を果たしており、Ｍｎ含有量を０．０５％以上、好ましくは０．１％以上、さらに好ましくは０．１５％以上としてその効果を発揮させる。一方、Ｍｎを過剰に含有させると伸び、および磁気特性が低下するため、Ｍｎ含有量の上限を０．５％、好ましくは０．４％、さらに好ましくは０．３％とする。
Mn: 0.05 to 0.5%
Since Mn has a deoxidizing action, in the present invention, in order to achieve both magnetic properties and press formability, instead of lowering the contents of C, S and Al as compared with conventional steel, Mn It plays a role as a deoxidizer, and exhibits its effect when the Mn content is 0.05% or more, preferably 0.1% or more, more preferably 0.15% or more. On the other hand, if Mn is contained excessively, elongation and magnetic properties are lowered, so the upper limit of the Mn content is 0.5%, preferably 0.4%, and more preferably 0.3%.
Ｐ：０〜０．０２％
Ｐは伸び、磁気特性ともに低下させるため、Ｐ含有量の上限を０．０２％、好ましくは０．０１５％、さらに好ましくは０．０１％とする。
P: 0 to 0.02%
Since P decreases both elongation and magnetic properties, the upper limit of the P content is 0.02%, preferably 0.015%, and more preferably 0.01%.
Ｓ：０〜０．１％
Ｓは過剰に含まれると、伸び、および磁気特性を低下させるため、Ｓ含有量の上限を０．１％とし、高い磁気特性、または伸びが求められる場合においては、好ましくは０．０６％、さらに好ましくは０．０２％とする。
一方で、Ｓは適量含有させることにより、伸びや磁気特性を若干犠牲にしつつも、Ｍｎとともに鋼中でＭｎＳを形成し、打抜き加工時に応力が負荷されたときに応力集中箇所となって、被削性を向上し、打抜き時のバリ発生を抑制することができる。こうした効果を得るには、Ｓ含有量を０．０１５％以上、好ましくは０．０４％以上とする。
S: 0 to 0.1%
When S is excessively contained, the elongation and magnetic properties are lowered. Therefore, the upper limit of the S content is set to 0.1%, and when high magnetic properties or elongation is required, preferably 0.06%, More preferably, it is 0.02%.
On the other hand, when S is contained in an appropriate amount, MnS is formed in steel together with Mn while sacrificing elongation and magnetic properties, and when stress is applied during punching, it becomes a stress concentration point. The machinability can be improved and the occurrence of burrs during punching can be suppressed. In order to obtain such an effect, the S content is 0.015% or more, preferably 0.04% or more.
Ａｌ：０〜０．０１％
Ａｌは脱酸剤として作用するため、磁気特性に有害なＯ、すなわち酸素と結合して無害化するために有効な元素である。しかしながら、Ａｌを過剰に含有させるとＮと結合してＡｌＮを生成し、結晶粒を微細化して伸びを低下させたり、磁気焼鈍後にも結晶粒が微細なままとなって磁気特性も劣化させるため、Ａｌ含有量の上限を０．０１％、好ましくは０．００７％、さらに好ましくは０．００５％とする。
Al: 0 to 0.01%
Since Al acts as a deoxidizing agent, it is an element effective for detoxifying by combining with O, which is harmful to magnetic properties, that is, oxygen. However, if Al is contained excessively, it combines with N to produce AlN, and the crystal grains are refined to reduce the elongation, or the magnetic grains remain fine even after magnetic annealing and the magnetic properties are deteriorated. The upper limit of the Al content is 0.01%, preferably 0.007%, and more preferably 0.005%.
Ｃｒ：０〜０．１％
Ｃｒは、鋼中に硫化物などの析出物を形成すると磁気特性の劣化を招くため、極力低減すべきであり、Ｃｒ含有量を０．１％以下、好ましくは０．０７％以下、さらに好ましくは０．０５％以下とする。
Cr: 0 to 0.1%
Cr forms a precipitate such as sulfide in the steel, which causes deterioration of magnetic properties. Therefore, Cr should be reduced as much as possible, and the Cr content is 0.1% or less, preferably 0.07% or less, and more preferably. Is 0.05% or less.
Ｎ：０〜０．００５％
Ｎは鋼中に固溶すると磁気特性を劣化させ、またその一部がＡｌＮを形成してもやはり結晶粒が微細化することによって磁気特性が劣化するため、Ｎ含有量を０．００５％以下、好ましくは０．００４％以下、さらに好ましくは０．００３％以下とする。
N: 0 to 0.005%
When N dissolves in steel, the magnetic properties deteriorate, and even if some of them form AlN, the magnetic properties deteriorate due to the refinement of crystal grains, so the N content is 0.005% or less. , Preferably 0.004% or less, more preferably 0.003% or less.
さらに、本発明の軟磁性鋼板では、鋼板の被削性を改善するため、ＭｎとＳの比、およびＭｎＳの形態を以下のように制御することも好ましい。 Furthermore, in the soft magnetic steel sheet of the present invention, in order to improve the machinability of the steel sheet, it is also preferable to control the ratio of Mn and S and the form of MnS as follows.
＜Ｍｎ／Ｓ原子比：３〜２０＞
鋼中に含まれるＭｎとＳが結合しＭｎＳ析出物として微細分散することで被削性が向上し、打抜き時のバリ発生が抑制される。こうした効果を得るため、Ｍｎ／Ｓの原子比で３以上を確保することが必要となる。Ｍｎ／Ｓ原子比のより好ましい範囲は５以上であり、上限は２０である。
<Mn / S atomic ratio: 3-20>
By combining Mn and S contained in the steel and finely dispersing as MnS precipitates, the machinability is improved and the generation of burrs during punching is suppressed. In order to obtain such an effect, it is necessary to secure an Mn / S atomic ratio of 3 or more. A more preferable range of the Mn / S atomic ratio is 5 or more, and the upper limit is 20.
ＭｎＳの形態
＜ＭｎＳ析出物の平均粒径：０．０５〜４μｍ＞
打抜き時のバリ高さを低減するためには、ＭｎＳを分散させることが有効であるが、粗大すぎると磁気特性を低下させてしまうため、上限は４μｍとする。また、微細すぎるとバリ高さ低減効果が発揮されなくなるため、下限を０．０５μｍとする。
ここで、ＭｎＳ粒径とは、圧延板の圧延方向に平行で板面に垂直な断面において観察されるＭｎＳの短径と長径の平均値を意味する。
MnS morphology <MnS precipitate average particle size: 0.05 to 4 μm>
In order to reduce the burr height at the time of punching, it is effective to disperse MnS. However, if it is too coarse, the magnetic properties are deteriorated, so the upper limit is set to 4 μm. On the other hand, if it is too fine, the burr height reduction effect will not be exhibited, so the lower limit is made 0.05 μm.
Here, the MnS grain size means an average value of the minor axis and the major axis of MnS observed in a cross section parallel to the rolling direction of the rolled sheet and perpendicular to the sheet surface.
＜粒径０．２μｍ以上のＭｎＳ析出物：０．０２〜０．５個／μｍ２＞
ＭｎＳ析出物を微細分散させる場合の個数密度も重要であり、０．０２個／μｍ２未満では効果がなく、０．５個／μｍ２超では成形時の割れ発生が顕著になるため、その個数密度は０．０２〜０．５個／μｍ２とする。
<MnS precipitate having a particle size of 0.2 μm or more: 0.02 to 0.5 / μm 2 >
The number density in the case of finely dispersing MnS precipitates is also important. If it is less than 0.02 / μm 2 , there is no effect, and if it exceeds 0.5 / μm 2 , cracking during molding becomes prominent. The number density is 0.02 to 0.5 / μm 2 .
本発明の軟磁性鋼板は、上記記載した以外の成分は、Ｆｅおよび不可避的不純物であることが望ましい。ただし、本発明の効果を害しない範囲内であれば、上記以外の成分の含有を拒むものではない。 In the soft magnetic steel sheet of the present invention, the components other than those described above are desirably Fe and inevitable impurities. However, as long as the effects of the present invention are not impaired, the inclusion of components other than those described above is not rejected.
＜板厚０．８〜４．０ｍｍ＞
本発明の軟磁性鋼板の板厚は、適用する部品形状やサイズに応じて選定すればよいが、本発明の対象となる自動車、電車、船舶などの電装部品に使用されるソレノイドやリレーなどのケースやカバー、鉄心等では、磁気回路を形成するため、板厚が薄すぎると部材を通る磁束が不足して吸引力や応答性などの部品特性が低下してしまう。また部品に必要な強度が確保できなくなるため、その下限は０．８ｍｍとする。また、厚すぎると部品サイズの小型化ニーズに対応できなくなるため、その上限は４ｍｍとする。
<Thickness 0.8-4.0mm>
The thickness of the soft magnetic steel sheet of the present invention may be selected according to the shape and size of the parts to be applied, but the solenoids and relays used for the electrical parts such as automobiles, trains, ships, etc. that are the subject of the present invention. Since a case, a cover, an iron core, etc. form a magnetic circuit, if the plate thickness is too thin, the magnetic flux passing through the member is insufficient, and the component characteristics such as attractive force and responsiveness deteriorate. Moreover, since the strength required for the components cannot be secured, the lower limit is set to 0.8 mm. Further, if it is too thick, it becomes impossible to meet the needs for downsizing of the component size, so the upper limit is set to 4 mm.
次に、本発明に係る軟磁性鋼板の製造方法について述べる。特に製造方法を限定するものではないが、たとえば下記のように製造することができる。 Next, a method for producing a soft magnetic steel sheet according to the present invention will be described. Although a manufacturing method in particular is not limited, For example, it can manufacture as follows.
〔軟磁性鋼板の好ましい製造方法〕
上記のような軟磁性鋼板を製造するには、まず、上記成分組成を有する鋼を溶製し、造塊または連続鋳造によりスラブとしてから熱間圧延を行い、熱延材とする。この工程を熱延工程と呼ぶ。熱間圧延時の温度条件などは特に限定する必要はないが、例えば、９５０℃以下の圧延終了温度で、熱間圧延を行えばよい。
次いで、この熱延材を圧下率Ｒ１：４０％以上で冷間圧延して冷延板とする。この工程を粗冷延工程と呼ぶ。その後、この冷延板を、式１：２１０≦［{１００−Ｒ１＋０．２×（２７３＋Ｔ１)｝２＋Ｈ１×ｅｘｐ｛−１０／（２７３＋Ｔ１）｝］１／２≦２６５、ただし、６５０℃≦Ｔ１≦７８０℃を満足するように、軟化焼鈍温度Ｔ１℃で軟化焼鈍時間Ｈ１秒間保持して軟化焼鈍板とする。この工程を軟化焼鈍工程と呼ぶ。そして、この軟化焼鈍板を、さらに、圧下率Ｒ２：０．５〜１０％で冷間圧延することも好ましい。この工程を仕上げ冷延工程と呼ぶ。これらの工程を経ることにより軟磁性鋼板を得ることができる。
[Preferred production method of soft magnetic steel sheet]
In order to produce the soft magnetic steel sheet as described above, first, a steel having the above component composition is melted and formed into a hot-rolled material by hot rolling after forming a slab by ingot forming or continuous casting. This process is called a hot rolling process. Although the temperature conditions at the time of hot rolling need not be particularly limited, for example, hot rolling may be performed at a rolling end temperature of 950 ° C. or lower.
Next, this hot-rolled material is cold-rolled at a rolling reduction R1: 40% or more to obtain a cold-rolled sheet. This process is called a rough cold rolling process. Then, this cold-rolled sheet is expressed by the formula 1: 210 ≦ [{100−R1 + 0.2 × (273 + T1)} 2 + H1 × exp {−10 / (273 + T1)}] 1/2 ≦ 265, where 650 ° C. ≦ T1 In order to satisfy ≦ 780 ° C., the soft annealing temperature is T1 ° C. and the soft annealing time is maintained for H 1 second to obtain a soft annealing plate. This process is called a soft annealing process. And it is also preferable to cold-roll this softening annealing board further by rolling reduction R2: 0.5-10%. This process is called a finish cold rolling process. A soft magnetic steel sheet can be obtained through these steps.
＜圧下率Ｒ１：４０％以上＞
粗冷延工程における圧下率Ｒ１は、その後の軟化焼鈍工程における平均結晶粒径の制御のために重要である。圧下率Ｒ１が４０％未満では鋼板上がりの結晶粒径が十分に大きくなりにくく、軟化焼鈍条件との組合せで所定の結晶粒径に制御することが難しいため、圧下率Ｒ１の下限を４０％、より好ましくは５０％、特に好ましくは６０％とする。
<Rolling ratio R1: 40% or more>
The rolling reduction R1 in the rough cold rolling process is important for controlling the average crystal grain size in the subsequent softening annealing process. When the rolling reduction R1 is less than 40%, the crystal grain size of the steel sheet is not sufficiently large, and it is difficult to control to a predetermined crystal grain size in combination with the soft annealing condition, so the lower limit of the rolling reduction R1 is 40%. More preferably, it is 50%, and particularly preferably 60%.
＜式１：２１０≦［{１００−Ｒ１＋０．２×（２７３＋Ｔ１)｝２＋Ｈ１×ｅｘｐ｛−１０／（２７３＋Ｔ１）｝］１／２ ≦２６５、ただし、６５０℃≦Ｔ１≦７８０℃を満足するように、軟化焼鈍温度Ｔ１℃で軟化焼鈍時間Ｈ１秒間保持＞
上記粗冷延工程における圧下率Ｒ１の調整と併せて軟化焼鈍条件が上記式１を満たすように組み合わせることによって平均結晶粒径を５〜５０μｍに制御できる。上記式１の中辺の値が２１０未満では平均結晶粒径が小さすぎ、一方２６５を超えると平均結晶粒径が大きくなりすぎる。
なお、上記式１は以下のようにして導出したものである。すなわち、フェライト単相温度域での焼鈍時における再結晶および粒成長挙動は、冷間圧延のひずみ量と焼鈍温度と焼鈍時間の兼ね合いで決まるという一般論がある。そこで、ひずみ量が大きいほど、また焼鈍温度が低いほど再結晶粒径が小さくなり、その後の粒成長による結晶粒径を半径で表したｒは、初期粒径を半径で表したｒ０と、焼鈍温度Ｔと、焼鈍時間ｔとの関数として、ｒ２−ｒ０ ２＝ｋ×ｔの関係式が成り立つと仮定した。ここで速度定数ｋはアレニウスの式である∝ｅｘｐ（−Ａ／ＲＴ）に従うと仮定した。なお、Ｔの単位はＫである。上記関係式は、たとえば、西沢泰二：「単相鋼と二相鋼における結晶粒成長」，鉄と鋼（１９８４）第１５号，ｐ．１９４−２０２０に詳しい。この一般論において、特別な粒成長抑制要因である析出物を極力減らした本発明の成分系の鋼板に対してはひずみの影響が通常より小さいとの仮説を当てはめ、粗冷延工程における圧下率Ｒ１と、軟化焼鈍条件であるＴ１およびＨ１との組合せを種々変更して実験を行い、プレス成形性と後の焼鈍後の磁気特性との関係を調査して回帰分析により上記式１を導出した。
<Formula 1: 210 ≦ [{100−R1 + 0.2 × (273 + T1)} 2 + H1 × exp {−10 / (273 + T1)}} 1/2 ≦ 265, provided that 650 ° C. ≦ T1 ≦ 780 ° C. is satisfied. In addition, the soft annealing time T1 ° C. and the soft annealing time H1 second hold>
The average grain size can be controlled to 5 to 50 μm by combining the softening annealing conditions so as to satisfy the above formula 1 together with the adjustment of the rolling reduction R1 in the rough cold rolling step. If the value of the middle side of the above formula 1 is less than 210, the average crystal grain size is too small, whereas if it exceeds 265, the average crystal grain size becomes too large.
The above equation 1 is derived as follows. That is, there is a general theory that the recrystallization and grain growth behavior during annealing in the ferrite single phase temperature range is determined by the balance between the strain amount of cold rolling, the annealing temperature, and the annealing time. Therefore, the larger the amount of strain and the lower the annealing temperature, the smaller the recrystallized grain size. The r representing the crystal grain size by the subsequent grain growth by the radius is r 0 representing the initial grain size by the radius, As a function of the annealing temperature T and the annealing time t, it was assumed that the relational expression r 2 −r 0 2 = k × t was established. Here, it is assumed that the rate constant k follows ア レ exp (−A / RT) which is an Arrhenius equation. The unit of T is K. For example, Nishizawa Yoji: “Grain growth in single-phase and dual-phase steels”, Iron and Steel (1984) No. 15, p. Detailed on 194-2020. In this general theory, the hypothesis that the effect of strain is smaller than usual for steel sheets of the component system of the present invention in which precipitates, which are a special grain growth inhibiting factor, are reduced as much as possible, is applied, and the rolling reduction rate in the rough cold rolling process is applied. Experiments were carried out with various combinations of R1 and soft annealing conditions T1 and H1, and the relationship between the press formability and the magnetic properties after the subsequent annealing was investigated and the above formula 1 was derived by regression analysis. .
＜圧下率Ｒ２：０．５〜１０％＞
また、軟化焼鈍後に圧下率Ｒ２＝０．５〜１０％で仕上げ冷間圧延することも好ましい。仕上げ冷間圧延をすることで、曲げ加工後の肌荒れや、打抜き加工後のバリを防止し、伸びを確保することができるとともに、成形後の磁気焼鈍の後の結晶粒成長を促進させて磁気特性の向上に寄与する。これらの効果を発揮させるためには、圧下率Ｒ２は０．５％以上とする。ただし、１０％を超えると伸びが低下する。
<Rolling ratio R2: 0.5 to 10%>
It is also preferable to perform finish cold rolling at a rolling reduction R2 = 0.5 to 10% after the soft annealing. Finishing cold rolling prevents roughening after bending and burrs after punching to ensure elongation, and promotes grain growth after magnetic annealing after molding to increase magnetism. Contributes to improved characteristics. In order to exert these effects, the rolling reduction R2 is 0.5% or more. However, if it exceeds 10%, the elongation decreases.
次に、本発明に係る軟磁性部材の製造方法について述べる。特に製造方法を限定するものではないが、たとえば下記のように製造することができる。 Next, a method for manufacturing a soft magnetic member according to the present invention will be described. Although a manufacturing method in particular is not limited, For example, it can manufacture as follows.
〔軟磁性部材の好ましい製造方法〕
上記のような軟磁性部材を製造するには、まず、上記推奨の製造方法で製造された上記軟磁性鋼板を部材形状に成形して成形部材とする。この工程を成形工程と呼ぶ。次いで、この成形部材を、式２：３２０≦［{１００−Ｒ２＋０．２×（２７３＋Ｔ２)｝２＋Ｈ２×ｅｘｐ｛−１０／（２７３＋Ｔ２）｝］１／２（ただし、７５０℃≦Ｔ２≦９００℃）を満足するように、磁気焼鈍温度Ｔ２℃で磁気焼鈍時間Ｈ２秒間保持することにより軟磁性部材を得ることができる。この工程を磁気焼鈍工程と呼ぶ。
[Preferable manufacturing method of soft magnetic member]
In order to manufacture the soft magnetic member as described above, first, the soft magnetic steel sheet manufactured by the recommended manufacturing method is formed into a member shape to obtain a formed member. This process is called a molding process. Then, this molded member is expressed by the formula 2: 320 ≦ [{100−R2 + 0.2 × (273 + T2)} 2 + H2 × exp {−10 / (273 + T2)}] 1/2 (however, 750 ° C. ≦ T2 ≦ 900 ° C. ), A soft magnetic member can be obtained by holding the magnetic annealing temperature T2 ° C. and the magnetic annealing time H2 seconds. This process is called a magnetic annealing process.
＜式２：３２０≦［{１００−Ｒ２＋０．２×（２７３＋Ｔ２)｝２＋Ｈ２×ｅｘｐ｛−１０／（２７３＋Ｔ２）｝］１／２（ただし、７５０℃≦Ｔ２≦９００℃）を満足するように、磁気焼鈍温度Ｔ２℃で磁気焼鈍時間Ｈ２秒間保持＞
上記式２の右辺の値が３２０未満では磁気特性が劣化する。
なお、上記式２は以下のようにして導出したものである。すなわち、成形によって各部位に付与されるひずみ量が大きく変わるなかで、ひずみ量の大小によらず、安定的に所定の磁気焼鈍後の磁気特性が得られるような、仕上げ冷延工程における圧化率Ｒ２と磁気焼鈍条件のＴ２およびＨ２との適正な組合せ条件を求めるために、本発明の対象鋼種について、Ｒ２とＴ２およびＨ２の組合せを種々変更して実験を行い、回帰分析により上記式２を導出した。
<Formula 2: 320 ≦ [{100−R2 + 0.2 × (273 + T2)} 2 + H2 × exp {−10 / (273 + T2)}] 1/2 (however, 750 ° C. ≦ T2 ≦ 900 ° C.) , Magnetic annealing temperature T2 ° C. and magnetic annealing time H2 seconds hold>
If the value on the right side of Equation 2 is less than 320, the magnetic characteristics deteriorate.
The above equation 2 is derived as follows. In other words, while the amount of strain imparted to each part changes significantly due to molding, pressure in the finish cold rolling process can stably obtain the magnetic characteristics after the prescribed magnetic annealing regardless of the amount of strain. In order to obtain an appropriate combination condition of the rate R2 and the magnetic annealing conditions T2 and H2, with respect to the target steel type of the present invention, experiments were performed with various combinations of R2, T2 and H2, and the above equation 2 was obtained by regression analysis. Was derived.
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もちろん可能であり、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, but may be appropriately modified within a range that can meet the purpose described above and below. Of course, it is possible to implement them, and they are all included in the technical scope of the present invention.
〔実施例１〕
下記表１に示す成分の鋼材を熱間圧延して所定厚さの熱延板とした。この熱延板を酸洗した後、下記表２に示す条件で、粗冷延、軟化焼鈍、仕上げ冷延の順に処理を施して最終板厚１．０ｍｍの軟磁性鋼板とした。なお、表２には、上記磁気焼鈍の条件を規定する上記式２の右辺の値を併記した。
[Example 1]
The steel materials having the components shown in Table 1 below were hot-rolled to obtain hot-rolled sheets having a predetermined thickness. After this hot-rolled sheet was pickled, it was processed in the order of rough cold rolling, soft annealing, and finish cold rolling under the conditions shown in Table 2 below to obtain a soft magnetic steel sheet having a final thickness of 1.0 mm. In Table 2, the value on the right side of the above equation 2 that defines the conditions for the magnetic annealing is also shown.
この各軟磁性鋼板について、成形性を評価するために、ＪＩＳ １３Ｂ試験片に加工して引張試験を実施し、伸びを測定して、それを成形性の評価指標とした。 In order to evaluate the formability of each soft magnetic steel sheet, it was processed into a JIS 13B test piece, a tensile test was performed, the elongation was measured, and this was used as an evaluation index for formability.
また、曲げ加工時の肌荒れを評価するために、曲げ試験として、内径Ｒ：２ｍｍ、曲げ角度：１８０°に曲げ加工してＲ外側の表面粗さをカットオフ０．８μｍ、測定長５ｍｍで測定し、それを肌荒れの評価指標とした。 In addition, in order to evaluate the rough skin during bending, as a bending test, the inner surface R was bent to 2 mm and the bending angle was 180 °, and the outer surface roughness of R was measured with a cutoff of 0.8 μm and a measurement length of 5 mm. It was used as an evaluation index for rough skin.
また、磁気焼鈍後の軟磁性部材の磁気特性を評価するために、上記各軟磁性鋼板を６０ｍｍ×６０ｍｍに切断して、Ｔ２：８５０℃×Ｈ２：３時間の条件で、水素中で磁気焼鈍した後、単板測定枠を用い、ＪＩＳ Ｃ２５５６に準じて直流磁気特性を評価した。なお、磁束密度および保磁力は印加磁場３００Ａ／ｍにて測定した。 Further, in order to evaluate the magnetic properties of the soft magnetic member after the magnetic annealing, each of the soft magnetic steel sheets is cut into 60 mm × 60 mm, and magnetic annealing is performed in hydrogen under conditions of T2: 850 ° C. × H2: 3 hours. After that, DC magnetic characteristics were evaluated according to JIS C2556 using a single plate measurement frame. The magnetic flux density and coercive force were measured with an applied magnetic field of 300 A / m.
また、鋼板ままの軟磁性鋼板と８５０℃×３時間磁気焼鈍した鋼板である軟磁性部材のそれぞれについて、以下のようにして、平均結晶粒径およびＫＡＭ値を測定した。 Moreover, the average crystal grain size and the KAM value were measured as follows for each of the soft magnetic steel plate as a steel plate and the soft magnetic member which was a steel plate magnetically annealed at 850 ° C. for 3 hours.
鋼板ままの平均結晶粒径については、各鋼板の縦断面をナイタール腐食した後、板厚をｔとしたときのｔ／４位置を顕微鏡観察し、写真撮影した。そして、ＪＩＳ Ｇ０５５１の標準図との比較法により粒度番号を求め、平均結晶粒径に換算した。一方、上記磁気焼鈍後の鋼板の平均結晶粒径については、当該軟磁性鋼板の全域での平均結晶粒径を評価するため、各鋼板の縦断面をナイタール腐食した後、最表面から２００μｍ深さの表面部、板厚をｔとしたときのｔ／４、およびｔ／２の各位置を顕微鏡観察し、写真撮影した。そして、ＪＩＳ Ｇ０５５１の標準図との比較法により粒度番号を求め、平均結晶粒径に換算し、３つの位置のうち最小の値を上記磁気焼鈍後の鋼板の平均結晶粒径とした。 The average crystal grain size of the steel plates was photographed by observing a microscope at the t / 4 position when the plate thickness was t after corroding the longitudinal section of each steel plate. And the particle size number was calculated | required with the comparison method with the standard figure of JISG0551, and it converted into the average crystal grain size. On the other hand, with respect to the average crystal grain size of the steel plate after the magnetic annealing, in order to evaluate the average crystal grain size in the entire area of the soft magnetic steel plate, the depth of 200 μm from the outermost surface is obtained after the longitudinal section of each steel plate is subjected to nital corrosion. The surface portion of each and the positions of t / 4 and t / 2 when the plate thickness is t were observed with a microscope and photographed. And the particle size number was calculated | required by the comparison method with the standard figure of JISG0551, it converted into the average crystal grain size, and let the minimum value among three positions be the average crystal grain size of the steel plate after the said magnetic annealing.
ＫＡＭ値については、各鋼板を鏡面研磨し、走査型電子顕微鏡としてＪＥＯＬ社製 ＪＳＭ−５４１０を用いて、板厚をｔとしたときのｔ／４位置において、１ｓｔｅｐ ０．２μｍで５００μｍ×５００μｍの領域の電子線後方散乱回折像を測定し、それを解析ソフトとしてＴＳＬ社製 ＯＩＭ ａｎａｌｙｓｉｓ ６を用いて、各測定点におけるＫＡＭ値を求め、それらを算術平均してＫＡＭ値とした。 For the KAM value, each steel plate is mirror-polished, using JSMOL 5410 made by JEOL as a scanning electron microscope, and at a t / 4 position when the plate thickness is t, 1 step 0.2 μm is 500 μm × 500 μm The electron backscatter diffraction image of the region was measured, and the KAM value at each measurement point was obtained using OIM analysis 6 manufactured by TSL as analysis software, and the KAM value was obtained by arithmetically averaging them.
下記表３に測定結果を示す。 Table 3 below shows the measurement results.
同表において、鋼Ｎｏ．１〜４および９〜１２は、保磁力３５Ａ／ｍ以下、磁界の強さ３００Ａ／ｍにおける磁束密度１．３５Ｔ以上の優れた磁気特性を有し、さらに伸び３５％以上の高い成形性、および曲げ加工後のＲａ２．５μｍ以下の優れた耐肌荒れ性を有していることを確認した。 In the table, Steel No. 1-4 and 9-12 have excellent magnetic properties such as a coercive force of 35 A / m or less, a magnetic flux density of 1.35 T or more at a magnetic field strength of 300 A / m, and a high formability of 35% or more in elongation. It was confirmed that it had excellent skin roughness resistance of Ra 2.5 μm or less after bending.
また、推奨の製造条件で製造することで、本発明に係る軟磁性鋼板が確実に得られ、さらにその軟磁性鋼板を推奨の磁気焼鈍条件で磁気焼鈍することで、本発明に係る軟磁性部材が確実に得られることが確認された。 Moreover, the soft magnetic steel sheet according to the present invention can be reliably obtained by manufacturing under the recommended manufacturing conditions, and the soft magnetic steel sheet according to the present invention can be obtained by magnetic annealing under the recommended magnetic annealing conditions. Was confirmed to be obtained reliably.
〔実施例２〕
下記表４に示す成分の鋼材を熱間圧延して所定厚さの熱延板とした。この熱延板を酸洗した後、下記表５に示す条件で、粗冷延、軟化焼鈍、仕上げ冷延の順に処理を施して最終板厚１．０ｍｍの軟磁性鋼板とした。
[Example 2]
The steel materials having the components shown in Table 4 below were hot-rolled to obtain hot-rolled sheets having a predetermined thickness. After this hot-rolled sheet was pickled, it was processed in the order of rough cold rolling, soft annealing, and finish cold rolling under the conditions shown in Table 5 below to obtain a soft magnetic steel sheet having a final thickness of 1.0 mm.
この各軟磁性鋼板について、成形性を評価するために、ＪＩＳ １３Ｂ試験片に加工して引張試験を実施し、伸びを測定して、それを成形性の評価指標とした。 In order to evaluate the formability of each soft magnetic steel sheet, it was processed into a JIS 13B test piece, a tensile test was performed, the elongation was measured, and this was used as an evaluation index for formability.
また、打抜き加工時の打抜き性の評価として、直径１０ｍｍのパンチと、直径１０．２０ｍｍでクリアランス０．１０ｍｍのダイスを用いて打抜き、穴の周囲に生成したバリの最大高さを測定した。 Further, as an evaluation of punchability at the time of punching, punching was performed using a punch having a diameter of 10 mm and a die having a diameter of 10.20 mm and a clearance of 0.10 mm, and the maximum height of the burr generated around the hole was measured.
また、磁気焼鈍後の軟磁性部材の磁気特性を評価するために、上記各軟磁性鋼板を６０ｍｍ×６０ｍｍに切断して、Ｔ２：８５０℃×Ｈ２：３時間の条件で、水素中で磁気焼鈍した後、単板測定枠を用い、ＪＩＳ Ｃ２５５６に準じて直流磁気特性を評価した。なお、磁束密度および保磁力は印加磁場３００Ａ／ｍにて測定した。 Further, in order to evaluate the magnetic properties of the soft magnetic member after the magnetic annealing, each of the soft magnetic steel sheets is cut into 60 mm × 60 mm, and magnetic annealing is performed in hydrogen under conditions of T2: 850 ° C. × H2: 3 hours. After that, DC magnetic characteristics were evaluated according to JIS C2556 using a single plate measurement frame. The magnetic flux density and coercive force were measured with an applied magnetic field of 300 A / m.
鋼板ままの平均結晶粒径については、各鋼板の縦断面をナイタール腐食した後、板厚をｔとしたときのｔ／４位置を顕微鏡観察し、写真撮影した。そして、ＪＩＳ Ｇ０５５１の標準図との比較法により粒度番号を求め、平均結晶粒径に換算した。一方、上記磁気焼鈍後の鋼板の平均結晶粒径については、当該軟磁性鋼板の全域での平均結晶粒径を評価するため、各鋼板の縦断面をナイタール腐食した後、最表面から２００μｍ深さの表面部、板厚をｔとしたときの、およびｔ／２の各位置を顕微鏡観察し、写真撮影した。そして、ＪＩＳＧ０５５１の標準図との比較法により粒度番号を求め、平均結晶粒径に換算し、３つの位置のうち最小の値を上記磁気焼鈍後の鋼板の平均結晶粒径とした。 The average crystal grain size of the steel plates was photographed by observing a microscope at the t / 4 position when the plate thickness was t after corroding the longitudinal section of each steel plate. And the particle size number was calculated | required with the comparison method with the standard figure of JISG0551, and it converted into the average crystal grain size. On the other hand, with respect to the average crystal grain size of the steel plate after the magnetic annealing, in order to evaluate the average crystal grain size in the entire area of the soft magnetic steel plate, the depth of 200 μm from the outermost surface is obtained after the longitudinal section of each steel plate is subjected to nital corrosion. The surface portion of each plate and the thickness of the plate at t and each position at t / 2 were observed with a microscope and photographed. And the particle size number was calculated | required by the comparison method with the standard figure of JISG0551, it converted into an average crystal grain size, and let the minimum value among three positions be the average crystal grain size of the steel plate after the said magnetic annealing.
ＫＡＭ値については、各鋼板を鏡面研磨し、走査型電子顕微鏡としてＪＥＯＬ社製 ＪＳＭ−５４１０を用いて、板厚をｔとしたときのｔ／４位置において、１ｓｔｅｐ ０．２μｍで５００μｍ×５００μｍの領域の電子線後方散乱回折像を測定し、それを解析ソフトとしてＴＳＬ社製 ＯＩＭ ａｎａｌｙｓｉｓ ６を用いて、各測定点におけるＫＡＭ値を求め、それらを算術平均してＫＡＭ値とした。 For the KAM value, each steel plate is mirror-polished, using JSMOL 5410 made by JEOL as a scanning electron microscope, and at a t / 4 position when the plate thickness is t, 1 step 0.2 μm is 500 μm × 500 μm The electron backscatter diffraction image of the region was measured, and the KAM value at each measurement point was obtained using OIM analysis 6 manufactured by TSL as analysis software, and the KAM value was obtained by arithmetically averaging them.
ＭｎＳ析出物の粒径は、鋼板の圧延方向に平行で板面に垂直な断面において倍率１０００倍でＳＥＭ観察し、１０視野について、ＭｎＳの長径と短径を測定してそれらの算術平均値を粒径と定義した。また、粒径０．２μｍ以上のＭｎＳ析出物の個数を測定し、個数密度を算出した The particle size of the MnS precipitate was observed by SEM at a magnification of 1000 times in a cross section parallel to the rolling direction of the steel sheet and perpendicular to the plate surface, and the major and minor diameters of MnS were measured for 10 fields of view and their arithmetic average values were calculated. The particle size was defined. Further, the number density of MnS precipitates having a particle size of 0.2 μm or more was measured, and the number density was calculated.
下記表６に測定結果を示す。 The measurement results are shown in Table 6 below.
同表において、鋼Ｎｏ．１０１〜１０４および１１０〜１１３は、保磁力３５Ａ／ｍ以下、磁界の強さ３００Ａ／ｍ における磁束密度１．３５Ｔ以上となり、優れた磁気特性を有していることを確認した。さらに、これらの鋼板は、伸び３３％以上、打抜き試験後のバリ高さ１ｍｍ以下となり、優れた成形性、および被削性を有することを確認した。 In the table, Steel No. Nos. 101 to 104 and 110 to 113 had a magnetic force density of 1.35 T or more at a coercive force of 35 A / m or less and a magnetic field strength of 300 A / m 2, and were confirmed to have excellent magnetic properties. Further, these steel sheets had an elongation of 33% or more and a burr height of 1 mm or less after the punching test, and it was confirmed that they had excellent formability and machinability.
Claims (6)
Ｃ：０．００１〜０．０２％、
Ｓｉ：０〜０．０５％、
Ｍｎ：０．０５〜０．５％、
Ｐ：０〜０．０２％、
Ｓ：０〜０．１％、
Ａｌ：０〜０．０１％、
Ｃｒ：０〜０．１％、
Ｎ：０〜０．００５％
であり、残部が鉄および不可避的不純物からなる軟磁性鋼板であって、
平均結晶粒径が５〜５０μｍであり、
さらに、当該軟磁性鋼板のＫＡＭ値Ｋａと、当該軟磁性鋼板を８５０℃で３時間焼鈍した後のＫＡＭ値Ｋｂとの比Ｋａ／Ｋｂが１．２〜４．５である
ことを特徴とする、板厚０．８〜４．０ｍｍの軟磁性鋼板。
ここに、「ＫＡＭ値」とは、「Ｋｅｒｎｅｌ Ａｖｅｒａｇｅ Ｍｉｓｏｒｉｅｎｔａｔｉｏｎ値」を意味する。 Ingredient composition is mass%,
C: 0.001 to 0.02%,
Si: 0 to 0.05%,
Mn: 0.05 to 0.5%
P: 0 to 0.02%,
S: 0 to 0.1%,
Al: 0 to 0.01%,
Cr: 0 to 0.1%,
N: 0 to 0.005%
And the balance is a soft magnetic steel plate made of iron and inevitable impurities,
The average crystal grain size is 5-50 μm,
Furthermore, the ratio Ka / Kb between the KAM value Ka of the soft magnetic steel sheet and the KAM value Kb after annealing the soft magnetic steel sheet at 850 ° C. for 3 hours is 1.2 to 4.5. A soft magnetic steel sheet having a thickness of 0.8 to 4.0 mm.
Here, the “KAM value” means a “Kernel Average Mission value”.
請求項１に記載の軟磁性鋼板。 The S content is S: 0.015 to 0.1 mass%.
The soft magnetic steel sheet according to claim 1.
請求項１に記載の軟磁性鋼板。 The content of S is S: 0 to 0.06% by mass.
The soft magnetic steel sheet according to claim 1.
ＭｎＳ析出物の平均粒径が０．０５〜４μｍで、かつ、
粒径０．２μｍ以上のＭｎＳ析出物の個数密度が０．０２〜０．５個／μｍ２である、
請求項１〜３のいずれか１項に記載の軟磁性鋼板。 Furthermore, the Mn / S atomic ratio is 3-20,
The average particle size of the MnS precipitate is 0.05-4 μm, and
The number density of MnS precipitates having a particle size of 0.2 μm or more is 0.02 to 0.5 / μm 2 .
The soft magnetic steel plate according to any one of claims 1 to 3.
前記熱延板を圧下率Ｒ１：４０％以上で冷間圧延して冷延板とする粗冷延工程と、
前記冷延板を、下記式１を満足するように、軟化焼鈍温度Ｔ１℃で軟化焼鈍時間Ｈ１秒間保持して軟化焼鈍板とする軟化焼鈍工程と、
さらに、前記軟化焼鈍板を、圧下率Ｒ２：０．５〜１０％で冷間圧延する仕上げ冷延工程と、
を備えたことを特徴とする、軟磁性鋼板の製造方法。
式１：２１０≦［{１００−Ｒ１＋０．２×（２７３＋Ｔ１)｝２＋Ｈ１×ｅｘｐ｛−１０／（２７３＋Ｔ１）｝］１／２ ≦２６５
ただし、６５０℃≦Ｔ１≦７８０℃である。 A hot rolling step of hot rolling a steel material having the component composition according to any one of claims 1 to 3 to obtain a hot rolled sheet;
A rough cold rolling process in which the hot rolled sheet is cold rolled at a rolling reduction R1: 40% or more to form a cold rolled sheet;
A softening annealing step in which the cold-rolled sheet is held at a softening annealing temperature T1 ° C. and a softening annealing time H1 second so as to satisfy the following formula 1,
Furthermore, a finish cold rolling step of cold rolling the softened annealed plate at a rolling reduction R2: 0.5 to 10%;
A method for producing a soft magnetic steel sheet, comprising:
Formula 1: 210 ≦ [{100−R1 + 0.2 × (273 + T1)} 2 + H1 × exp {−10 / (273 + T1)}] 1/2 ≦ 265
However, it is 650 degreeC <= T1 <= 780 degreeC.
前記熱延板を圧下率Ｒ１：４０％以上で冷間圧延して冷延板とする粗冷延工程と、
前記冷延板を、下記式１を満足するように、軟化焼鈍温度Ｔ１℃で軟化焼鈍時間Ｈ１秒間保持して軟化焼鈍板とする軟化焼鈍工程と、
前記軟化焼鈍板を、さらに、圧下率Ｒ２：０．５〜１０％で冷間圧延することにより軟磁性鋼板を得る仕上げ冷延工程と、
前記軟磁性鋼板を部材形状に成形して成形部材とする成形工程と、
前記成形部材を、下記式２を満足するように、磁気焼鈍温度Ｔ２℃で磁気焼鈍時間Ｈ２秒間保持することにより軟磁性部材を得る磁気焼鈍工程と
を備えたことを特徴とする、軟磁性部材の製造方法。
式１：２１０≦［{１００−Ｒ１＋０．２×（２７３＋Ｔ１)｝２＋Ｈ１×ｅｘｐ｛−１０／（２７３＋Ｔ１）｝］１／２ ≦２６５
ただし、６５０℃≦Ｔ１≦７８０℃である。
式２：３２０≦［{１００−Ｒ２＋０．２×（２７３＋Ｔ２)｝２＋Ｈ２×ｅｘｐ｛−１０／（２７３＋Ｔ２）｝］１／２
ただし、７５０℃≦Ｔ２≦９００℃である。 A hot rolling step of hot rolling a steel material having the component composition according to any one of claims 1 to 3 to obtain a hot rolled sheet;
A rough cold rolling process in which the hot rolled sheet is cold rolled at a rolling reduction R1: 40% or more to form a cold rolled sheet;
A softening annealing step in which the cold-rolled sheet is held at a softening annealing temperature T1 ° C. and a softening annealing time H1 second so as to satisfy the following formula 1,
A finish cold rolling step of obtaining a soft magnetic steel sheet by cold rolling the softened annealed plate at a rolling reduction R2 of 0.5 to 10%;
A forming step of forming the soft magnetic steel sheet into a member shape and forming a formed member;
A soft magnetic member comprising: a magnetic annealing step for obtaining a soft magnetic member by holding the molded member at a magnetic annealing temperature T2 ° C. so as to satisfy the following formula 2 and a magnetic annealing time H2 seconds: Manufacturing method.
Formula 1: 210 ≦ [{100−R1 + 0.2 × (273 + T1)} 2 + H1 × exp {−10 / (273 + T1)}] 1/2 ≦ 265
However, it is 650 degreeC <= T1 <= 780 degreeC.
Formula 2: 320 ≦ [{100−R2 + 0.2 × (273 + T2)} 2 + H2 × exp {−10 / (273 + T2)}] 1/2
However, 750 ° C. ≦ T2 ≦ 900 ° C.
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