JP2001172752A - Nonoriented silicon steel sheet for magnet-embedded-type motor, and its manufacturing method - Google Patents
Nonoriented silicon steel sheet for magnet-embedded-type motor, and its manufacturing methodInfo
- Publication number
- JP2001172752A JP2001172752A JP35807299A JP35807299A JP2001172752A JP 2001172752 A JP2001172752 A JP 2001172752A JP 35807299 A JP35807299 A JP 35807299A JP 35807299 A JP35807299 A JP 35807299A JP 2001172752 A JP2001172752 A JP 2001172752A
- Authority
- JP
- Japan
- Prior art keywords
- steel sheet
- oxide layer
- iron
- magnet
- thickness
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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Links
Classifications
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Landscapes
- Manufacturing Of Steel Electrode Plates (AREA)
- Soft Magnetic Materials (AREA)
Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、鉄リサイクルを可
能にする成分系を前提とした、磁石埋設型のモータに最
適な無方向性電磁鋼板に関し、特に、従来の課題であっ
た打ち抜き加工性や磁気特性の向上を図った磁石埋設型
モータ用無方向性電磁鋼板及びその製造方法に係るもの
である。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a non-oriented electrical steel sheet which is optimal for a magnet embedded type motor on the premise of a component system capable of recycling iron, and more particularly to a punching workability which has been a conventional problem. The present invention relates to a non-oriented electrical steel sheet for an embedded magnet type motor with improved magnetic properties and a method for manufacturing the same.
【０００２】[0002]
【従来の技術】地球資源が枯渇するかも知れないとの近
未来的な状況の中で、色々な分野で資源の再利用の動き
が急である。このため、鉄鋼業でも各種の鉄スクラッ
プ、例えば自動車、洗濯機、エアコンなどを製鉄原料と
して利用する必要が生じてきている。このためには、従
来有害とされてきたＣｕ，Ｎｉ，Ｃｒ，Ｓｎなどのスク
ラップに含有する成分を積極利用しなければならない。2. Description of the Related Art In a near-futuristic situation where global resources may be depleted, there is a rapid movement to reuse resources in various fields. For this reason, in the iron and steel industry, it has become necessary to use various iron scraps, for example, automobiles, washing machines, air conditioners, and the like as iron raw materials. For this purpose, components contained in scrap, such as Cu, Ni, Cr, and Sn, which have conventionally been regarded as harmful, must be actively used.
【０００３】一方で、同じ地球資源問題から、エネルギ
ーの無駄使いをなくそうとの動きも強まっている。モー
タの分野でも、例えば一般家庭用のエアコンに見られる
ように、消費電力低下による電気代が安いものが求めら
れている。このため、モータの設計においても消費電力
を少なくすべく改良が計られてきた。従来のモータは殆
どが誘導モータであり、この誘導モータは回転子にアル
ミダイキャストを施し、このアルミに誘導電流を流す方
式であった。しかしながら、近年の日本においては、効
率の観点からインバータ制御化が進み、更には回転子に
永久磁石を埋め込んだ、いわゆる磁石埋設型ＤＣインバ
ータ制御モータと呼ばれる形式に変わりつつある。On the other hand, due to the same problem of earth resources, there is a growing movement to eliminate waste of energy. In the field of motors as well, for example, as seen in general household air conditioners, there is a demand for ones that reduce power consumption due to reduced power consumption. For this reason, improvements have been made in motor design to reduce power consumption. Most conventional motors are induction motors, and this induction motor employs a method in which an aluminum die-cast is applied to a rotor and an induction current is caused to flow through the aluminum. However, in recent years in Japan, inverter control has been advanced from the viewpoint of efficiency, and furthermore, it has been changed to a so-called magnet embedded type DC inverter control motor in which a permanent magnet is embedded in a rotor.
【０００４】ところで、今までこの磁石埋設型回転子に
用いられる無方向性電磁鋼板の第一の課題は、高速回転
での遠心力で磁石が飛び出してモータが破壊されないた
めの必要最低限の強度である。このためには、降伏点強
度で２６０Ｍｐａ以上が必要とされている。高強度にす
るために、従来はＳｉ量を上げて固溶体強化を行う手段
が採用されていた。しかしながらＳｉが増加すると、打
ち抜き金型の摩耗が激しくなって打ち抜き作業性が劣化
していた。これが第二の課題であった。即ち、Ｓｉの活
用によるモータの破壊防止と打抜き性の改善とは二律相
反する現象であった。更に、第三の課題はモータ効率改
善、特に固定子（ステータ）でのインバータ制御での高
周波鉄損の更なる低減である。なお、回転子と固定子は
通常、同一のコイルから打ち抜かれることが多いので、
回転子と固定子との両者を満足させる特性が無方向性電
磁鋼板には要求される。[0004] The first problem of the non-oriented electrical steel sheet used in the magnet-embedded rotor is that it has the minimum necessary strength to prevent the motor from being broken by the centrifugal force of high-speed rotation, which causes the magnet to fly out. It is. For this purpose, a yield point strength of 260 Mpa or more is required. Conventionally, a means for strengthening a solid solution by increasing the amount of Si has been employed to increase the strength. However, when the amount of Si increases, the abrasion of the punching die becomes severe, and the punching workability deteriorates. This was the second task. In other words, prevention of motor destruction and improvement of punching performance by utilizing Si are two mutually exclusive phenomena. Further, a third problem is to improve motor efficiency, particularly to further reduce high-frequency iron loss in inverter control in a stator (stator). Since the rotor and the stator are usually punched from the same coil,
Characteristics that satisfy both the rotor and the stator are required for non-oriented electrical steel sheets.
【０００５】一方、上記したように地球環境問題から不
純物とされてきたＣｕ，Ｎｉ，Ｃｒ，Ｓｎなどを積極活
用しなければならないが、上記の磁石埋設型モータ用無
方向性電磁鋼板などの超高級機能性鋼板に、これらのＣ
ｕ，Ｎｉ，Ｃｒ，Ｓｎなどを含有させることは従来、疵
の問題や磁気特性への懸念から不可能と考えられてき
た。その理由の一つとしては、実験室レベルでの研究で
はうまく行っても、実際の工場を通板してみると打抜き
性や高周波鉄損特性に劣化の大きいものがしばしば発生
して、その原因が究明出来ていなかったためである。即
ち、これらの課題を同時に解決する無方向性電磁鋼板は
今まで提案されていなかった。On the other hand, Cu, Ni, Cr, Sn, etc., which have been considered as impurities due to global environmental problems as described above, must be actively utilized. These C
It has heretofore been considered impossible to contain u, Ni, Cr, Sn and the like due to the problem of flaws and concerns about magnetic properties. One of the reasons is that even if the research at the laboratory level works well, when passing through an actual factory, the punching properties and high-frequency iron loss characteristics often deteriorate greatly, Was not ascertained. That is, a non-oriented electrical steel sheet that simultaneously solves these problems has not been proposed.
【０００６】なお特開平８−９７０２３号公報では、Ｓ
ｂを添加することで酸化層を少なくして磁気特性を改善
することが開示されている。しかし、Ｓｂは高価な上、
人体に有害でもあること、また熱延板もしくは熱延板焼
鈍後のスケール残り量が議論されているが、それは最表
層に存在する酸化層のことであり、本発明で重要なイン
バータ制御用の高周波用途には意味のない酸化層であっ
たため、利用されることがなかった。また、K.Matsmura
とB.Fukuda:IEEE Trans.mag.20(1984)1533でも酸化層の
ことが述べられているが、これも最表層から存在する酸
化層のことであった。なお、無方向性電磁鋼板として知
られる製品板厚は０．１〜１mmである。In Japanese Patent Application Laid-Open No. Hei 8-97023, S
It is disclosed that the addition of b improves the magnetic properties by reducing the oxide layer. However, Sb is expensive and
It is also harmful to the human body, and the amount of scale remaining after hot-rolled sheet or hot-rolled sheet annealing is discussed. Since the oxide layer was meaningless for high frequency applications, it was not used. Also, K. Matsmura
And B. Fukuda: IEEE Trans.mag. 20 (1984) 1533 also mentions an oxide layer, but this was also an oxide layer existing from the outermost layer. The thickness of a product known as a non-oriented electrical steel sheet is 0.1 to 1 mm.
【０００７】[0007]
【発明が解決しようとする課題】本発明は上記の点に鑑
み、地球環境問題からの鉄スクラップの積極活用課題を
解決し、更には磁石埋設型モータの固有問題であった無
方向性電磁鋼板の剛性、打抜き性、磁気特性などを抜本
的に解決する無方向性電磁鋼板、及びその製造方法を提
供するものである。SUMMARY OF THE INVENTION In view of the above, the present invention solves the problem of actively utilizing steel scrap from global environmental issues, and furthermore, a non-oriented electrical steel sheet which is an inherent problem of a magnet embedded type motor. The present invention provides a non-oriented electrical steel sheet that fundamentally solves the rigidity, punching property, magnetic characteristics, and the like of a steel sheet, and a method for manufacturing the same.
【０００８】[0008]
【課題を解決するための手段】上記課題を解決するため
に本発明の要旨とするところは以下の通りである。 （１）重量％で、 Ｃ ≦０．００５％、 Ｓｉ：１．６〜２．８％、 Ｍｎ≦０．５％、 Ｐ ≦０．０５％、 Ｓ ≦０．００２％、 Ａｌ：１〜４％、 Ｎ ≦０．００４％、 Ｃｕ：０．０５〜０．７％、 Ｎｉ：０．０１〜０．２％、 Ｃｒ：０．０１〜０．２％、 Ｓｎ：０．００３〜０．１％ を含有し、残部が実質的に鉄からなり、結晶粒径が８０
〜１７０μｍで、内部酸化層厚み≦０．５μｍ、降伏点
強度：２６０〜３７０N/mm2 、であることを特徴とする
磁石埋設型のモータ用無方向性電磁鋼板。 （２）重量％で、 Ｃ ≦０．００５％、 Ｓｉ：１．６〜２．８％、 Ｍｎ≦０．５％、 Ｐ ≦０．０５％、 Ｓ ≦０．００２％、 Ａｌ：１〜４％、 Ｎ ≦０．００４％、 Ｃｕ：０．０５〜０．７％、 Ｎｉ：０．０１〜０．２％、 Ｃｒ：０．０１〜０．２％、 Ｓｎ：０．００３〜０．１％ を含有し、残部が実質的に鉄からなる熱延板を焼鈍し、
冷延を行ってから、焼鈍して、結晶粒径を８０〜１７０
μｍとし、内部酸化層厚み≦０．５μｍ、降伏点強度：
２６０〜３７０N/mm2 とすることを特徴とする磁石埋設
型のモータ用無方向性電磁鋼板の製造方法。The gist of the present invention to solve the above problems is as follows. (1) By weight%, C ≦ 0.005%, Si: 1.6-2.8%, Mn ≦ 0.5%, P ≦ 0.05%, S ≦ 0.002%, Al: 1 4%, N ≦ 0.004%, Cu: 0.05 to 0.7%, Ni: 0.01 to 0.2%, Cr: 0.01 to 0.2%, Sn: 0.003 to 0 0.1%, the balance substantially consisting of iron and having a crystal grain size of 80%.
A non-oriented electrical steel sheet for a motor with an embedded magnet, characterized in that the thickness of the inner oxide layer is 0.5 μm or less and the yield strength is 260 to 370 N / mm 2 . (2) In terms of% by weight, C ≦ 0.005%, Si: 1.6 to 2.8%, Mn ≦ 0.5%, P ≦ 0.05%, S ≦ 0.002%, Al: 1 to 1 4%, N ≦ 0.004%, Cu: 0.05 to 0.7%, Ni: 0.01 to 0.2%, Cr: 0.01 to 0.2%, Sn: 0.003 to 0 A hot-rolled sheet containing 0.1%, with the balance substantially consisting of iron,
After cold rolling, annealing is performed to reduce the crystal grain size to 80 to 170.
μm, internal oxide layer thickness ≦ 0.5 μm, yield point strength:
A method for producing a non-oriented electrical steel sheet for a motor with embedded magnets, wherein the non-oriented electrical steel sheet has a thickness of 260 to 370 N / mm 2 .
【０００９】本発明のポイントは３点ある。一つは、打
抜き性の金型摩耗を少なくするには鋼板の降伏点を小さ
くすべきこと、このためにはＳｉよりもＡｌを積極活用
したほうが良いこと、更には、Ｃｕ，Ｎｉ，Ｃｒ，Ｓｎ
の４種を含有する鋼板で発生しやすい内部酸化層を少な
くすることが重要である。二点目は、鉄損を改善するに
は、従来公知の結晶粒径制御以外に内部酸化層も効いて
いること、特に高周波鉄損にこの内部酸化層が重要であ
る。三点目は、これらの降伏点、内部酸化層などを制御
することは、工業的に充分可能なことである。There are three points of the present invention. One is that the yield point of the steel sheet should be reduced in order to reduce the die wear of the punching property. For this purpose, it is better to utilize Al rather than Si. Sn
It is important to reduce the internal oxide layer that is likely to be generated in a steel sheet containing the above four types. Secondly, in order to improve iron loss, an internal oxide layer is effective in addition to the conventionally known control of crystal grain size, and this internal oxide layer is particularly important for high-frequency iron loss. Third, it is industrially sufficiently possible to control these yield points, internal oxide layers, and the like.
【００１０】[0010]
【発明の実施の形態】以下、本発明の限定理由について
説明する。成分含有量は重量％である。Ｃ量は、０．０
０５％以下とする。Ｃ量が０．００５％を超えると、磁
気時効問題があるため低周波鉄損が増加するためであ
る。DESCRIPTION OF THE PREFERRED EMBODIMENTS The reasons for limiting the present invention will be described below. Component content is% by weight. C content is 0.0
It shall be not more than 05%. If the C content exceeds 0.005%, there is a problem of magnetic aging, so that low-frequency iron loss increases.
【００１１】Ｓｉ量は、１．６〜２．８％に制限する。
Ｓｉは鋼板剛性を増加させるのに有効で、１．６％未満
では降伏点が低すぎて不満で、また２．８％超では、降
伏点が高すぎ金型摩耗が大きく不可である。The amount of Si is limited to 1.6 to 2.8%.
Si is effective in increasing the rigidity of the steel sheet. If it is less than 1.6%, the yield point is too low and it is unsatisfactory, and if it is more than 2.8%, the yield point is too high and mold wear is too large.
【００１２】Ｍｎ量は、０．５％以下とする。Ｍｎは熱
間割れを防止する効果があるが、多すぎると添加コスト
の問題があるので０．５％以下とする。[0012] The amount of Mn is 0.5% or less. Mn has an effect of preventing hot cracking, but if it is too much, there is a problem of addition cost, so Mn is made 0.5% or less.
【００１３】Ｐ量は、０．０５％以下に制限する。Ｐも
結晶粒成長を阻害して、製品結晶粒径を細粒化するため
少ない方が好ましいが、この限界が０．０５％である。The amount of P is limited to 0.05% or less. P is also preferably small in order to inhibit the crystal grain growth and reduce the product crystal grain size, but the limit is 0.05%.
【００１４】Ｓ量は、０．００２％以下とする。Ｓは硫
化物を形成して鉄損を劣化させる。この限界が、０．０
０２％である。The amount of S is set to 0.002% or less. S forms sulfides and deteriorates iron loss. This limit is 0.0
02%.
【００１５】Ａｌ量は、１〜４％とする。Ａｌは鋼板剛
性を増加させるのに有効で、１％未満では降伏点が不満
であり、また４％超では添加コストが大きくなるため、
避けなければならない。The amount of Al is set to 1 to 4%. Al is effective in increasing the rigidity of the steel sheet. If it is less than 1%, the yield point is unsatisfactory, and if it exceeds 4%, the addition cost becomes large.
Must be avoided.
【００１６】Ｎ量は、０．００４％以下とする。Ｎは窒
化物を形成して鉄損を劣化させる。この限界が０．００
４％である。The N content is set to 0.004% or less. N forms nitrides and deteriorates iron loss. This limit is 0.00
4%.
【００１７】Ｃｕ量は、０．０５〜０．７％とする。鉄
スクラップの有効活用の意味は０．０５％以上のＣｕで
あり、また０．７％を超えるとＣｕへげと称される熱延
での鋼板表面割れが発生するので、避けなければならな
い。The amount of Cu is 0.05-0.7%. The meaning of the effective use of iron scrap is 0.05% or more of Cu, and if it exceeds 0.7%, a steel plate surface crack in hot rolling called Cu-hage occurs, so it must be avoided.
【００１８】Ｎｉ量は、０．０１〜０．２％とする。鉄
スクラップの有効活用の意味は０．０１％以上のＮｉで
あり、また０．２％を超えると結晶粒成長が阻害される
ため不可とする。The amount of Ni is 0.01-0.2%. The meaning of the effective use of iron scrap is 0.01% or more of Ni, and if it exceeds 0.2%, crystal grain growth is inhibited, so that it is not possible.
【００１９】Ｃｒ量は、０．０１〜０．２％とする。鉄
スクラップの有効活用の意味は、０．０１％以上のＣｒ
であり、また、実用上、鉄スクラップから０．２％を超
えることはないので、０．０１〜０．２％とする。The amount of Cr is 0.01-0.2%. The meaning of effective use of iron scrap is 0.01% or more of Cr
In addition, since it does not exceed 0.2% from iron scrap in practical use, the content is set to 0.01 to 0.2%.
【００２０】Ｓｎ量は、０．００３〜０．１％とする。
鉄スクラップの有効活用の意味は０．００３％以上のＳ
ｎであり、また実用上、鉄スクラップから０．１％を超
えることはないので、０．０１〜０．１％とする。The amount of Sn is 0.003 to 0.1%.
The meaning of effective use of iron scrap is 0.003% or more S
n, and practically does not exceed 0.1% from iron scrap, so it is set to 0.01 to 0.1%.
【００２１】その他の元素として、集合組織を改善する
ための公知のＢ，Ｍｏなどを添加しても本発明として有
害なものではない。但し添加コストの問題があるので、
それぞれ０．１％以下が好ましい。また、公知の有害元
素、Ｔｉ，Ｎｂは０．０１％以下が好ましい。また本発
明では高価なＳｂは添加しないので、製鋼作業の不可避
的不純物としての量である０．０１％未満である。As other elements, addition of known B, Mo or the like for improving the texture is not harmful to the present invention. However, there is a problem of addition cost,
Each is preferably 0.1% or less. The known harmful elements Ti and Nb are preferably 0.01% or less. Further, in the present invention, since expensive Sb is not added, the amount is less than 0.01% which is an inevitable impurity in the steel making operation.
【００２２】製鋼で上記の成分に調整された連続鋳造ス
ラブは、通常の熱間圧延を行われて熱延板とされる。熱
延板は、次いで焼鈍される。熱延板焼鈍は、通常の８０
０〜１２００℃であって磁束密度改善のためには高温の
ほうが好ましい。なお熱延板焼鈍温度は高い方が若干で
あるが、製品の降伏点は低めとなる傾向になる。The continuous cast slab adjusted to the above components by steelmaking is subjected to ordinary hot rolling to form a hot rolled sheet. The hot rolled sheet is then annealed. Hot-rolled sheet annealing is usually 80
0 to 1200 ° C., and a higher temperature is more preferable for improving the magnetic flux density. Although the higher the hot-rolled sheet annealing temperature is, the higher the yield point of the product tends to be.
【００２３】次いで、冷延を行ってから焼鈍を実施す
る。焼鈍後の鋼板の平均結晶粒径は、８０μｍ以上、１
７０μｍ以下とする。８０μｍ未満では、低周波鉄損が
不満足で、また１７０μｍ超では高周波鉄損が不満であ
る。結晶粒径を制御するためには、通常の温度×時間制
御をすればよい。Next, annealing is performed after performing cold rolling. The average grain size of the steel sheet after annealing is 80 μm or more,
70 μm or less. If it is less than 80 μm, the low-frequency iron loss is unsatisfactory, and if it exceeds 170 μm, the high-frequency iron loss is unsatisfactory. In order to control the crystal grain size, normal temperature × time control may be performed.
【００２４】また、内部酸化層の厚みは０．５μｍ以下
でなければならない。内部酸化層が０．５μｍを超える
と、高周波鉄損の劣化が大きいためである。特に、本発
明のＣｕ，Ｓｎ，Ｎｉ，Ｃｒ複合含有系では、内部酸化
層が生じ易いので注意しなければならない。The thickness of the internal oxide layer must be 0.5 μm or less. This is because if the internal oxide layer exceeds 0.5 μm, the deterioration of high-frequency iron loss is large. In particular, in the Cu, Sn, Ni, Cr composite-containing system of the present invention, care must be taken because an internal oxide layer is easily formed.
【００２５】ここで言う内部酸化層とは、最表層がＳｉ
またはＡｌが若干少なくなった鉄メタル層の下層に形成
された、Ｓｉ，Ａｌ，Ｍｎなどがリッチの酸化層のこと
である。即ち表面構造としては、最表層の第一層が鉄メ
タルで、第二層が内部酸化層、第三層が地鉄である三層
構造が形成されている。内部酸化層が厚くなると、最表
層の鉄メタル層厚みも増加する傾向にあるが、例えば内
部酸化層が０．５μｍの場合は、鉄メタル層厚みは０．
８μｍ程度である。なお、最表層の鉄メタル層は殆どの
場合、内部酸化層の上にフィルム（膜）状に観察され
る。しかし、まれなケースとしては、この最表層の鉄メ
タル部分がなく、内部酸化層の上層部分に、鉄メタルが
断続的な島状のものとして観察されることもある。この
場合の内部酸化層厚みは、島状の鉄メタル厚みの平均化
したものを全体の酸化層厚みから引いたものとして定義
する。内部酸化層の下層は地鉄である。The internal oxide layer referred to here means that the outermost layer is Si
Alternatively, it is an oxide layer rich in Si, Al, Mn, etc., formed under the iron metal layer in which Al is slightly reduced. That is, as the surface structure, a three-layer structure is formed in which the first layer of the outermost layer is iron metal, the second layer is an internal oxide layer, and the third layer is ground iron. As the internal oxide layer becomes thicker, the thickness of the outermost iron metal layer also tends to increase. For example, when the internal oxide layer is 0.5 μm, the thickness of the iron metal layer is 0.1 μm.
It is about 8 μm. In most cases, the outermost iron metal layer is observed as a film on the internal oxide layer. However, in rare cases, there is no iron metal portion on the outermost layer, and the iron metal is observed as an intermittent island in the upper layer portion of the internal oxide layer. In this case, the thickness of the internal oxide layer is defined as a value obtained by subtracting the average of the thickness of the island-shaped iron metal from the total thickness of the oxide layer. The lower layer of the inner oxide layer is ground iron.
【００２６】この内部酸化層は地鉄との境界面の凹凸が
大きいので、磁束の流れを阻害して高周波鉄損を著しく
劣化させるので、特に注意しなければならない。なお、
この内部酸化層は、鋼板断面の研磨面を５０００倍以上
の倍率でＳＥＭ−ＥＤＸ測定することで観察することが
できるが、ＳＥＭ像は通常の二次電子ではなく、反射電
子像の方が内部酸化層厚みを明瞭に見ることができる。
内部酸化層厚みは、最表層の鉄メタル界面と下層の地鉄
界面との中間層の厚みであるが、上下それぞれの界面の
凹凸中心線（凹凸曲線の平均線に平行な直線を引いたと
き、この直線と凹凸曲線で囲まれる面積が、この直線の
両側で等しくなる直線を中心線とする）同士の差として
定義される。Since the internal oxide layer has a large unevenness at the boundary surface with the ground iron, it obstructs the flow of the magnetic flux and remarkably deteriorates the high-frequency iron loss. In addition,
This internal oxide layer can be observed by measuring the polished surface of the steel plate cross section at a magnification of 5000 times or more by SEM-EDX measurement. However, the SEM image is not a normal secondary electron, but the reflected electron image is more internal. The oxide layer thickness can be clearly seen.
The thickness of the internal oxide layer is the thickness of the intermediate layer between the iron metal interface on the outermost layer and the ground iron interface on the lower layer. The center line of the unevenness at the upper and lower interfaces (when a straight line parallel to the average line of the unevenness curve is drawn) , The area surrounded by the straight line and the concave-convex curve is defined as a center line where the straight line becomes equal on both sides of the straight line).
【００２７】この内部酸化層は、焼鈍の加熱過程などで
酸化された場合に生じるため、例えば加熱ラジアントチ
ューブでの割れや直火無酸化炉での空燃比に十分注意し
なければならない。即ち、焼鈍の加熱過程で酸化される
と、次いで高温での還元ガスで均熱焼鈍されても内部酸
化層まで還元されることはない。なお、この内部酸化層
は、従来のＨ2 ＋Ｎ2 ＋Ｈ2 Ｏ混合の湿潤ガス中での均
熱焼鈍で、最表面から酸化される現象を意味しない。こ
の表面酸化は高周波鉄損に悪影響しない。Since this internal oxide layer is formed when it is oxidized during the heating process of annealing, it is necessary to pay sufficient attention to, for example, cracking in a heated radiant tube and air-fuel ratio in a direct-fired non-oxidizing furnace. In other words, if it is oxidized in the annealing heating process, it is not reduced to the internal oxide layer even if it is soaked with a reducing gas at a high temperature. Note that this internal oxide layer does not mean a phenomenon of being oxidized from the outermost surface by conventional soaking annealing in a wet gas of a mixture of H 2 + N 2 + H 2 O. This surface oxidation does not adversely affect high frequency iron loss.
【００２８】また実験室レベルでは、加熱から均熱、冷
却まで非酸化性ガス中で焼鈍することが容易であるが、
鉄鋼メーカでの実炉では加熱帯に直火バーナーやラジア
ントチューブを用いることが多いので、特にＣｕ，Ｓ
ｎ，Ｎｉ，Ｃｒ複合含有系では、この内部酸化層には注
意を払わなければならない。均熱帯で例えば１００％Ｈ
2 の露点−５０℃ドライ雰囲気として高温均熱しても、
この内部酸化層までは還元されないので注意を要する。At the laboratory level, heating, soaking, and cooling
It is easy to anneal in a non-oxidizing gas until
In an actual furnace at a steel manufacturer, an open flame burner or
In particular, Cu, S
In the system containing n, Ni, and Cr composites,
You have to pay attention. 100% H
TwoDew point of -50 ° C
Care must be taken because this internal oxide layer is not reduced.
【００２９】上記、再結晶焼鈍の後は通常の絶縁皮膜が
塗布乾燥されて出荷される。出荷された後は、打ち抜き
加工され、積層固定され、そのまま、または焼鈍されて
（特に固定子が磁性改善のために焼鈍される場合があ
る）磁石埋設型モータコアとなる。以下、実施例で説明
する。After the recrystallization annealing, a normal insulating film is applied and dried before shipment. After being shipped, it is punched, laminated and fixed, and as it is or is annealed (particularly, the stator may be annealed to improve magnetism) to provide a magnet embedded type motor core. Hereinafter, an embodiment will be described.
【００３０】（実施例１）表１に示す各種の成分系を真
空溶解で溶解して、インゴットを作成した。これを１０
３０℃に加熱してから、１０mm厚の鋼片に分塊した。次
いで、更に１０００℃に加熱してから、１．７mmの熱延
板を作成した。次いで１１００℃で３０秒均熱の窒素中
焼鈍を行ってから大気中放冷した。酸洗後、冷延して
０．３５mm厚とした。次いで脱脂して、１０００℃で５
秒の水素中焼鈍を実施した。(Example 1) Various components shown in Table 1 were melted by vacuum melting to prepare ingots. This is 10
After heating to 30 ° C., it was lumped into 10 mm thick slabs. Next, after further heating to 1000 ° C., a 1.7 mm hot-rolled sheet was prepared. Next, annealing was performed in nitrogen at 1100 ° C. for 30 seconds soaking, and then allowed to cool in the air. After pickling, it was cold rolled to a thickness of 0.35 mm. Then, degrease and at 1000 ° C for 5
A second annealing in hydrogen was performed.
【００３１】これらから、引張試験片を圧延方向とそれ
と直角の方向に切り出し、降伏点（ＹＰ）を測定して平
均化した値を表１に併記した。なお、降伏点は上降伏点
より、読み取り精度の高い下降伏点とした。また、１０
０mm角の試料を切り出してから、圧延方向とそれと直角
の方向の４００Hz鉄損を測定し、平均して表１に示し
た。また、鋼板断面の平均結晶粒径を厚み方向にカウン
トとして求めた。なお、内部酸化層も調査したが存在し
なかった。From these, tensile test pieces were cut out in the rolling direction and a direction perpendicular to the rolling direction, and the yield points (YP) were measured and averaged. The yield point was a lower yield point with higher reading accuracy than the upper yield point. Also, 10
After cutting out a 0 mm square sample, the 400 Hz iron loss in the rolling direction and the direction perpendicular thereto was measured, and the results are shown in Table 1 on average. Further, the average grain size of the cross section of the steel sheet was determined as a count in the thickness direction. In addition, although the internal oxide layer was examined, it was not found.
【００３２】表１に示すように、本発明の成分範囲を外
れるものは、降伏点の下限・上限を外れ、また鉄損特性
が不満となった。なお、製品での成分分析も実施した
が、インゴットでの分析結果と同じであった。As shown in Table 1, those out of the component range of the present invention were out of the lower limit and upper limit of the yield point, and were unsatisfactory in iron loss characteristics. In addition, the component analysis of the product was also performed, but the result was the same as the analysis result of the ingot.
【００３３】[0033]
【表１】 [Table 1]
【００３４】（実施例２）表２に示すように、ＳｉとＡ
ｌ量とを調整した連続鋳造スラブを供試材として用い
た。その他の成分としては、実験No．１〜９について
は、０．００１％Ｃ、０．２％Ｍｎ、０．０２％Ｐ、
０．０００２％Ｓ、０．０００７％Ｎ、０．２５％Ｃ
ｕ、０．０４％Ｓｎ、０．０５％Ｎｉ、０．０５％Ｃｒ
に固定した。また、実験No．１０と１１のみ、０．００
１％Ｃ、０．２％Ｍｎ、０．０２％Ｐ、０．０００２％
Ｓ、０．０００７％Ｎで、Ｃｕ，Ｓｎ，Ｎｉ，Ｃｒにつ
いてはそれぞれ０．０００２％以下とした。このスラブ
を１１００℃で加熱してから、１．５mm厚の熱延コイル
を製造した。次いで９００℃で１５秒の焼鈍をＮ2 中で
実施した。酸洗してから０．２５mmまで冷延した。この
冷延板で表層酸化層を観察調査したが、酸化層は存在し
なかった。Example 2 As shown in Table 2, Si and A
A continuously cast slab having the adjusted l amount was used as a test material. Other components include Experiment No. For 1 to 9, 0.001% C, 0.2% Mn, 0.02% P,
0.0002% S, 0.0007% N, 0.25% C
u, 0.04% Sn, 0.05% Ni, 0.05% Cr
Fixed to. Experiment No. 10 and 11 only, 0.00
1% C, 0.2% Mn, 0.02% P, 0.0002%
S, 0.0007% N, and Cu, Sn, Ni, Cr were each set to 0.0002% or less. After heating the slab at 1100 ° C., a hot-rolled coil having a thickness of 1.5 mm was manufactured. Then annealing at 900 ° C. for 15 seconds was performed in N 2 . After pickling, it was cold rolled to 0.25 mm. Observation of the surface oxide layer on the cold-rolled sheet revealed no oxide layer.
【００３５】脱脂後、１１００℃×１０秒の均熱焼鈍を
実施した。この時、加熱を無酸化炉（直火雰囲気、空燃
比＝０．９）で行い、無酸化炉出側の板温を制御して、
内部酸化層の厚みを変更した。無酸化炉を出てからは、
電気ヒータゾーンで４０％Ｈ 2 ＋６０％Ｎ2 雰囲気で焼
鈍した。絶縁皮膜（クロム酸、マグネシュウム、アクリ
ル系の半有機皮膜）を約１．５μｍ厚焼き付けた。After degreasing, soak at 1100 ° C. for 10 seconds.
Carried out. At this time, heating is performed in a non-oxidizing furnace (open flame atmosphere, air-fuel
Ratio = 0.9), controlling the sheet temperature on the exit side of the non-oxidizing furnace,
The thickness of the internal oxide layer was changed. After leaving the non-oxidizing furnace,
40% H in electric heater zone Two+ 60% NTwoBaked in the atmosphere
Slowed down. Insulation film (chromic acid, magnesium, acrylic)
(A semi-organic film of a metal system) was baked to a thickness of about 1.5 μm.
【００３６】このコイルから、打抜き性の評価は、リン
グ試料（２０mmφ×３０mmφ）の最大かえり量を測定
し、かえりが５／１００mmとなる打抜き回数を表２に記
した。なお、金型はＳＫＤを使用した。初回のかえりは
いずれも２／１００mmであった。また、エプスタイン試
験片で磁気特性を測定した。引張試験片を圧延方向とそ
れと直角の方向に切り出し、下降伏点を測定して平均化
して表２に載せた。製品の平均結晶粒径は、いずれも１
５０〜１５５μｍであった。For evaluation of the punching property of this coil, the maximum burr amount of a ring sample (20 mmφ × 30 mmφ) was measured. Table 2 shows the number of punchings at which the burr was 5/100 mm. The mold used was SKD. The initial burr was 2/100 mm. In addition, magnetic properties were measured on Epstein test pieces. Tensile test specimens were cut out in the rolling direction and in a direction perpendicular to the rolling direction. The average crystal grain size of each product is 1
It was 50 to 155 μm.
【００３７】[0037]
【表２】 [Table 2]
【００３８】表２に示すように、成分、内部酸化層、降
伏点とを本発明範囲に制御したものは、優れた打抜き回
数および鉄損特性を示した。なお、最終の鋼板の成分を
チェックしたが、スラブ成分と同一であった。No．１０
と１１とは、Ｃｕ，Ｓｎ，Ｎｉ，Ｃｒを含まない成分系
であるが、内部酸化層は生成されにくい傾向にあること
が実験No．２と１０との比較で、また実験No．５と１１
との比較で分かる。その原因については、未だ不明確な
部分があって今後の調査に待たなければならないが、表
層をＧＤＳなどでスパッターしながら調査すると、Ｃ
ｕ，Ｓｎ，Ｎｉ，Ｃｒなどは表層に濃化する傾向がある
ため、これが原因の一つと推定している。As shown in Table 2, the composition, the internal oxide layer, and the yield point controlled within the range of the present invention exhibited excellent punching times and iron loss characteristics. In addition, the components of the final steel sheet were checked and found to be the same as the slab components. No. 10
And No. 11 are component systems that do not contain Cu, Sn, Ni, and Cr, but it was found in Experiment Nos. That an internal oxide layer was less likely to be formed. In comparison between Nos. 2 and 10, and in Experiment No. 5 and 11
You can see by comparing with. The cause is still unclear and we have to wait for further investigation.
Since u, Sn, Ni, Cr and the like tend to be concentrated in the surface layer, this is presumed to be one of the causes.
【００３９】（実施例３）重量％で、０．００３５％
Ｃ、２．２％Ｓｉ、０．１８％Ｍｎ、０．０１％Ｐ、
０．００３５％Ｓ、２．１％Ａｌ、０．００１５％Ｎ、
０．００３％Ｎｂ、０．５％Ｃｕ、０．０８％Ｓｎ、
０．０８％Ｎｉ、０．１１％Ｃｒ、０．００２％Ｏ、
０．００１％Ｔｉ、０．００２％Ｍｏ、０．００１％
Ｖ、０．０００１％Ｂ、０．０００２％Ｓｂを含むスラ
ブを１０５０℃で加熱してから、２．５mm厚の熱延コイ
ルを製造した。次いで８５０℃×１０秒の窒素中焼鈍を
して、酸洗した。酸化層を調査したが、認められなかっ
た。次いで０．２mmまで冷延し、脱脂後、均熱温度を表
３のように変更して１０秒均熱の３０％Ｈ2 ＋７０％Ｎ
2 中の焼鈍を実施した。この時、均熱温度に到達するま
での加熱雰囲気をＮ2 とし、その酸素を０．０１％とし
た。次いで有機、無機混合の絶縁皮膜を１μｍ厚で焼き
付けした。(Example 3) 0.0035% by weight
C, 2.2% Si, 0.18% Mn, 0.01% P,
0.0035% S, 2.1% Al, 0.0015% N,
0.003% Nb, 0.5% Cu, 0.08% Sn,
0.08% Ni, 0.11% Cr, 0.002% O,
0.001% Ti, 0.002% Mo, 0.001%
A slab containing V, 0.0001% B, and 0.0002% Sb was heated at 1050 ° C., and then a hot-rolled coil having a thickness of 2.5 mm was manufactured. Then, the resultant was annealed in nitrogen at 850 ° C. × 10 seconds and pickled. The oxidized layer was examined, but was not found. Then, it was cold-rolled to 0.2 mm, and after degreasing, the soaking temperature was changed as shown in Table 3 and 30% H 2 + 70% N of soaking for 10 seconds.
Annealing in 2 was performed. At this time, the heating atmosphere until reaching the soaking temperature was N 2 , and the oxygen was 0.01%. Next, an insulating film of a mixture of organic and inorganic was baked to a thickness of 1 μm.
【００４０】この鋼板表面を調査したところ、いずれも
内部酸化層は、０．２μｍ厚であった。次いでエプスタ
イン試料に切断してから磁気特性を測定した。引張試験
片を圧延方向とそれと直角の方向に切り出し、下降伏点
を測定して平均化した。また結晶粒径も測定して、表３
に示した。表３に示すように、本発明範囲の結晶粒径で
優れた磁気特性・機械的性質が得られた。When the surface of this steel sheet was examined, the inner oxide layer was 0.2 μm thick in each case. Next, after cutting into Epstein samples, the magnetic properties were measured. Tensile test pieces were cut out in the rolling direction and a direction perpendicular to the rolling direction, and the drop yield points were measured and averaged. The crystal grain size was also measured, and Table 3
It was shown to. As shown in Table 3, excellent magnetic and mechanical properties were obtained with a crystal grain size within the range of the present invention.
【００４１】[0041]
【表３】 [Table 3]
【００４２】[0042]
【発明の効果】地球環境問題からの鉄スクラップの積極
活用課題を解決し、磁石埋設型モータの回転子の固有問
題であった、無方向性電磁鋼板の剛性、打抜き性、磁気
特性などの課題も解決した無方向性電磁鋼板およびその
製造方法を提供することができた。The present invention solves the problem of actively utilizing iron scrap from global environmental issues, and issues inherent in the rotor of a magnet embedded type motor, such as rigidity, punching properties, and magnetic properties of non-oriented electrical steel sheets. Thus, a non-oriented electrical steel sheet and a method for manufacturing the same can be provided.
Claims (2)
〜１７０μｍで、内部酸化層厚み≦０．５μｍ、降伏点
強度：２６０〜３７０N/mm2 であることを特徴とする磁
石埋設型のモータ用無方向性電磁鋼板。1. Weight%, C ≦ 0.005%, Si: 1.6-2.8%, Mn ≦ 0.5%, P ≦ 0.05%, S ≦ 0.002%, Al: 1 to 4%, N ≦ 0.004%, Cu: 0.05 to 0.7%, Ni: 0.01 to 0.2%, Cr: 0.01 to 0.2%, Sn: 0.003 0.1%, the balance being substantially iron and having a crystal grain size of 80%.
A non-oriented electrical steel sheet for a motor with embedded magnets, characterized by having a thickness of up to 170 µm, an internal oxide layer thickness of 0.5 µm, and a yield point strength of 260 to 370 N / mm 2 .
冷延を行ってから、焼鈍して、結晶粒径を８０〜１７０
μｍとし、内部酸化層厚み≦０．５μｍ、降伏点強度：
２６０〜３７０N/mm2 とすることを特徴とする磁石埋設
型のモータ用無方向性電磁鋼板の製造方法。2. In% by weight, C ≦ 0.005%, Si: 1.6-2.8%, Mn ≦ 0.5%, P ≦ 0.05%, S ≦ 0.002%, Al: 1 to 4%, N ≦ 0.004%, Cu: 0.05 to 0.7%, Ni: 0.01 to 0.2%, Cr: 0.01 to 0.2%, Sn: 0.003 ~ 0.1%, the balance is substantially annealed hot rolled plate consisting of iron,
After cold rolling, annealing is performed to reduce the crystal grain size to 80 to 170.
μm, internal oxide layer thickness ≦ 0.5 μm, yield point strength:
A method for producing a non-oriented electrical steel sheet for a motor with embedded magnets, wherein the non-oriented electrical steel sheet has a thickness of 260 to 370 N / mm 2 .
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP35807299A JP4116748B2 (en) | 1999-12-16 | 1999-12-16 | Magnet buried type non-oriented electrical steel sheet for motor |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP35807299A JP4116748B2 (en) | 1999-12-16 | 1999-12-16 | Magnet buried type non-oriented electrical steel sheet for motor |
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| Publication Number | Publication Date |
|---|---|
| JP2001172752A true JP2001172752A (en) | 2001-06-26 |
| JP4116748B2 JP4116748B2 (en) | 2008-07-09 |
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| Application Number | Title | Priority Date | Filing Date |
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| JP35807299A Expired - Fee Related JP4116748B2 (en) | 1999-12-16 | 1999-12-16 | Magnet buried type non-oriented electrical steel sheet for motor |
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| WO2004050934A1 (en) * | 2002-12-05 | 2004-06-17 | Jfe Steel Corporation | Non-oriented magnetic steel sheet and method for production thereof |
| US7922834B2 (en) | 2005-07-07 | 2011-04-12 | Sumitomo Metal Industries, Ltd. | Non-oriented electrical steel sheet and production process thereof |
| JP2011089167A (en) * | 2009-10-22 | 2011-05-06 | Nippon Steel Corp | Composite panel having excellent stretch rigidity |
| JP2018135556A (en) * | 2017-02-21 | 2018-08-30 | 新日鐵住金株式会社 | Electromagnetic steel sheet, and method for producing the same |
| JP2018141206A (en) * | 2017-02-28 | 2018-09-13 | 新日鐵住金株式会社 | Electromagnetic steel sheet, and method for producing the same |
| WO2020149405A1 (en) * | 2019-01-17 | 2020-07-23 | 日本製鉄株式会社 | Non-oriented electrical steel sheet, segmented stator, and dynamo-electric machine |
| CN111556904A (en) * | 2017-12-26 | 2020-08-18 | Posco公司 | Non-oriented electrical steel sheet and method for manufacturing the same |
| JP2021532257A (en) * | 2018-07-18 | 2021-11-25 | ポスコPosco | Non-oriented electrical steel sheet and its manufacturing method |
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1999
- 1999-12-16 JP JP35807299A patent/JP4116748B2/en not_active Expired - Fee Related
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| WO2004050934A1 (en) * | 2002-12-05 | 2004-06-17 | Jfe Steel Corporation | Non-oriented magnetic steel sheet and method for production thereof |
| EP1580289A1 (en) * | 2002-12-05 | 2005-09-28 | JFE Steel Corporation | Non-oriented magnetic steel sheet and method for production thereof |
| EP1580289A4 (en) * | 2002-12-05 | 2006-02-01 | Jfe Steel Corp | Non-oriented magnetic steel sheet and method for production thereof |
| KR100709056B1 (en) * | 2002-12-05 | 2007-04-18 | 제이에프이 스틸 가부시키가이샤 | Non-oriented magnetic steel sheet and method for production thereof |
| US7513959B2 (en) | 2002-12-05 | 2009-04-07 | Jfe Steel Corporation | Non-oriented electrical steel sheet and method for manufacturing the same |
| EP2489753A1 (en) * | 2002-12-05 | 2012-08-22 | JFE Steel Corporation | Non-oriented magnetic steel sheet and method for production thereof |
| US7922834B2 (en) | 2005-07-07 | 2011-04-12 | Sumitomo Metal Industries, Ltd. | Non-oriented electrical steel sheet and production process thereof |
| US8157928B2 (en) | 2005-07-07 | 2012-04-17 | Sumitomo Metal Industries, Ltd. | Non-oriented electrical steel sheet and production process thereof |
| JP2011089167A (en) * | 2009-10-22 | 2011-05-06 | Nippon Steel Corp | Composite panel having excellent stretch rigidity |
| JP2018135556A (en) * | 2017-02-21 | 2018-08-30 | 新日鐵住金株式会社 | Electromagnetic steel sheet, and method for producing the same |
| JP2018141206A (en) * | 2017-02-28 | 2018-09-13 | 新日鐵住金株式会社 | Electromagnetic steel sheet, and method for producing the same |
| CN111556904A (en) * | 2017-12-26 | 2020-08-18 | Posco公司 | Non-oriented electrical steel sheet and method for manufacturing the same |
| EP3733907A4 (en) * | 2017-12-26 | 2020-11-04 | Posco | Non-oriented electrical steel sheet and method for preparing same |
| JP2021509153A (en) * | 2017-12-26 | 2021-03-18 | ポスコＰｏｓｃｏ | Non-oriented electrical steel sheet and its manufacturing method |
| CN111556904B (en) * | 2017-12-26 | 2022-05-17 | Posco公司 | Non-oriented electrical steel sheet and method for manufacturing the same |
| JP7142094B2 (en) | 2017-12-26 | 2022-09-26 | ポスコ | Non-oriented electrical steel sheet and manufacturing method thereof |
| US11492678B2 (en) | 2017-12-26 | 2022-11-08 | Posco | Non-oriented electrical steel sheet and method for preparing same |
| JP2021532257A (en) * | 2018-07-18 | 2021-11-25 | ポスコPosco | Non-oriented electrical steel sheet and its manufacturing method |
| JP7273945B2 (en) | 2018-07-18 | 2023-05-15 | ポスコ カンパニー リミテッド | Non-oriented electrical steel sheet and manufacturing method thereof |
| WO2020149405A1 (en) * | 2019-01-17 | 2020-07-23 | 日本製鉄株式会社 | Non-oriented electrical steel sheet, segmented stator, and dynamo-electric machine |
| JPWO2020149405A1 (en) * | 2019-01-17 | 2021-09-30 | 日本製鉄株式会社 | Non-oriented electrical steel sheets, split stators and rotary electric machines |
| EP3913079A4 (en) * | 2019-01-17 | 2022-08-31 | Nippon Steel Corporation | Non-oriented electrical steel sheet, segmented stator, and dynamo-electric machine |
| JP7192887B2 (en) | 2019-01-17 | 2022-12-20 | 日本製鉄株式会社 | Non-oriented electrical steel sheet, split type stator and rotating electric machine |
| US11952641B2 (en) | 2019-03-20 | 2024-04-09 | Nippon Steel Corporation | Non oriented electrical steel sheet |
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