JPH01119622A - Production of grain oriented electrical steel sheet having excellent magnetic characteristic and glass film characteristic - Google Patents
Production of grain oriented electrical steel sheet having excellent magnetic characteristic and glass film characteristicInfo
- Publication number
- JPH01119622A JPH01119622A JP27501487A JP27501487A JPH01119622A JP H01119622 A JPH01119622 A JP H01119622A JP 27501487 A JP27501487 A JP 27501487A JP 27501487 A JP27501487 A JP 27501487A JP H01119622 A JPH01119622 A JP H01119622A
- Authority
- JP
- Japan
- Prior art keywords
- annealing
- final
- steel sheet
- electrical steel
- cold rolling
- 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.)
- Pending
Links
- 239000011521 glass Substances 0.000 title claims abstract description 13
- 238000004519 manufacturing process Methods 0.000 title claims description 10
- 229910001224 Grain-oriented electrical steel Inorganic materials 0.000 title abstract description 6
- 238000000137 annealing Methods 0.000 claims abstract description 89
- 239000000463 material Substances 0.000 claims abstract description 48
- 238000005261 decarburization Methods 0.000 claims abstract description 26
- 238000005554 pickling Methods 0.000 claims abstract description 19
- 239000010410 layer Substances 0.000 claims abstract description 16
- 229910052739 hydrogen Inorganic materials 0.000 claims abstract description 11
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 claims abstract description 10
- 239000001257 hydrogen Substances 0.000 claims abstract description 10
- 238000005097 cold rolling Methods 0.000 claims abstract description 9
- 239000002344 surface layer Substances 0.000 claims abstract description 8
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 5
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 4
- 239000003795 chemical substances by application Substances 0.000 claims abstract description 4
- 239000012535 impurity Substances 0.000 claims abstract description 4
- 229910000976 Electrical steel Inorganic materials 0.000 claims description 15
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Chemical compound O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 2
- 238000000034 method Methods 0.000 abstract description 49
- 230000008569 process Effects 0.000 abstract description 42
- 238000001953 recrystallisation Methods 0.000 abstract description 25
- 229910000831 Steel Inorganic materials 0.000 abstract description 10
- 238000005121 nitriding Methods 0.000 abstract description 10
- 239000010959 steel Substances 0.000 abstract description 10
- 238000006243 chemical reaction Methods 0.000 abstract description 6
- 238000005098 hot rolling Methods 0.000 abstract description 6
- 229910052717 sulfur Inorganic materials 0.000 abstract description 6
- 239000002253 acid Substances 0.000 abstract description 2
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 abstract 2
- 229910016287 MxOy Inorganic materials 0.000 abstract 1
- 229910052681 coesite Inorganic materials 0.000 abstract 1
- 229910052906 cristobalite Inorganic materials 0.000 abstract 1
- 238000000926 separation method Methods 0.000 abstract 1
- 239000000377 silicon dioxide Substances 0.000 abstract 1
- 235000012239 silicon dioxide Nutrition 0.000 abstract 1
- 229910052682 stishovite Inorganic materials 0.000 abstract 1
- 229910052905 tridymite Inorganic materials 0.000 abstract 1
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 9
- 239000003112 inhibitor Substances 0.000 description 8
- 229910052839 forsterite Inorganic materials 0.000 description 6
- HCWCAKKEBCNQJP-UHFFFAOYSA-N magnesium orthosilicate Chemical compound [Mg+2].[Mg+2].[O-][Si]([O-])([O-])[O-] HCWCAKKEBCNQJP-UHFFFAOYSA-N 0.000 description 6
- 229910052757 nitrogen Inorganic materials 0.000 description 6
- 230000015572 biosynthetic process Effects 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 238000010438 heat treatment Methods 0.000 description 5
- 239000007789 gas Substances 0.000 description 4
- 230000003647 oxidation Effects 0.000 description 4
- 238000007254 oxidation reaction Methods 0.000 description 4
- 230000000087 stabilizing effect Effects 0.000 description 4
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 3
- 238000010521 absorption reaction Methods 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 239000000047 product Substances 0.000 description 3
- 239000011593 sulfur Substances 0.000 description 3
- 239000011248 coating agent Substances 0.000 description 2
- 238000000576 coating method Methods 0.000 description 2
- 239000000470 constituent Substances 0.000 description 2
- 239000011162 core material Substances 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 230000010354 integration Effects 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 239000012071 phase Substances 0.000 description 2
- 230000006641 stabilisation Effects 0.000 description 2
- 238000011105 stabilization Methods 0.000 description 2
- 240000007015 Melilotus indicus Species 0.000 description 1
- NRTOMJZYCJJWKI-UHFFFAOYSA-N Titanium nitride Chemical compound [Ti]#N NRTOMJZYCJJWKI-UHFFFAOYSA-N 0.000 description 1
- 229910052770 Uranium Inorganic materials 0.000 description 1
- 230000002159 abnormal effect Effects 0.000 description 1
- 238000009825 accumulation Methods 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 238000010420 art technique Methods 0.000 description 1
- SJKRCWUQJZIWQB-UHFFFAOYSA-N azane;chromium Chemical compound N.[Cr] SJKRCWUQJZIWQB-UHFFFAOYSA-N 0.000 description 1
- SKKMWRVAJNPLFY-UHFFFAOYSA-N azanylidynevanadium Chemical compound [V]#N SKKMWRVAJNPLFY-UHFFFAOYSA-N 0.000 description 1
- 230000004888 barrier function Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 230000004907 flux Effects 0.000 description 1
- 238000009413 insulation Methods 0.000 description 1
- 230000002452 interceptive effect Effects 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 230000005389 magnetism Effects 0.000 description 1
- 238000012423 maintenance Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 230000000116 mitigating effect Effects 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 239000011224 oxide ceramic Substances 0.000 description 1
- 229910052574 oxide ceramic Inorganic materials 0.000 description 1
- 230000001376 precipitating effect Effects 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000002250 progressing effect Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 230000000630 rising effect Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 238000007789 sealing Methods 0.000 description 1
- 238000005245 sintering Methods 0.000 description 1
- 238000003746 solid phase reaction Methods 0.000 description 1
- 239000007858 starting material Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 150000003464 sulfur compounds Chemical class 0.000 description 1
- 125000000101 thioether group Chemical group 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- 239000010936 titanium Substances 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- 239000002023 wood Substances 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Abstract
Description
【発明の詳細な説明】
(産業上の利用分野)
本発明は、一方向性電磁鋼板の製造プロセスの脱炭焼鈍
工程において得られる材料表面の酸化膜層の改質に関す
るものであり、特に最終仕上焼鈍時の材料の二次再結晶
の安定化とグラス皮膜の特性の向上の双方を同時に満た
す一方向性電磁鋼板の製造方法に関するものである。Detailed Description of the Invention (Field of Industrial Application) The present invention relates to the modification of an oxide film layer on the surface of a material obtained in the decarburization annealing step of the manufacturing process of unidirectional electrical steel sheets, and in particular, The present invention relates to a method for producing grain-oriented electrical steel sheets that simultaneously stabilizes secondary recrystallization of the material during final annealing and improves the properties of the glass coating.
(従来の技術)
一方向性電磁鋼板は、圧延方向に(110) (00
1)方位を持つ結晶粒(ゴス方位粒)により構成される
、通常、4.5重量%以下のSiを含有する、板厚が0
. 1 0〜0.35圓の鋼板である。その表面は、絶
縁性を確保する等の目的で、通常、フォルステライトで
覆われている。(Prior art) A unidirectional electrical steel sheet has (110) (00
1) A plate with a thickness of 0, usually containing 4.5% by weight or less of Si, consisting of oriented crystal grains (Goss-oriented grains)
.. 10 to 0.35 round steel plate. Its surface is usually covered with forsterite for the purpose of ensuring insulation.
即ち、一方向性電磁鋼板は、極めて集積度の高い(11
0) (001)集合組織(ゴス組織)を持ったSt
含有薄鋼板と、表層部の0.1〜数μmの酸化物系セラ
ミックスであるフォルステライトからなる複合材料であ
る。In other words, the unidirectional electrical steel sheet has an extremely high degree of integration (11
0) (001) St with collective texture (Goss texture)
It is a composite material consisting of a thin steel plate and a surface layer of forsterite, which is an oxide ceramic with a thickness of 0.1 to several μm.
このような、ゴス組織の極めて高い集積度の達成と、材
料表層部の薄いフォルステライト絶縁皮膜の生成という
2つの異質の過程は、現在の一方向性電磁鋼板製造工程
においては、最終仕上焼鈍という一つの箱焼鈍工程中に
おいて、はぼ時期を同じくして行なわれる。前者の、ゴ
ス組織の集積度向上には、二次再結晶と呼ばれるゴス方
位粒のカタストロフィツタな粒成長(異常粒成長)が、
工業的に利用されている。The two distinct processes of achieving an extremely high degree of Goss structure integration and forming a thin forsterite insulating film on the surface of the material are achieved through a process called final annealing in the current manufacturing process of grain-oriented electrical steel sheets. During one box annealing process, these are performed at approximately the same time. In the former case, the increase in the degree of accumulation of the Goss structure is due to catastrophic grain growth (abnormal grain growth) of Goss-oriented grains called secondary recrystallization.
Used industrially.
一方、後者の、材料表層部の薄いフォルステライト絶縁
皮膜の生成は、材料(鋼板)表面に予め形成された酸化
皮膜中のSiO□と、その上に塗布された焼鈍分離剤中
のMgOとの固相反応によってなされる。On the other hand, the latter formation of a thin forsterite insulating film on the surface of the material is due to the combination of SiO□ in the oxide film previously formed on the surface of the material (steel plate) and MgO in the annealing separator applied thereon. It is made by solid phase reaction.
これら、二次再結晶とフォルステライトの生成という木
質的に全く異なる2つの現象は、脱炭焼鈍過程で材料表
面に形成される酸化膜の構造や厚さ等を決定する脱炭焼
鈍条件や焼鈍分離剤の影響を受は易い。また、これら2
つの現象は、実際には、材料(liiI板)内部と表層
部具面とで相互に干渉しあいながら反応が進行する結果
であると考えられる。These two phenomena, secondary recrystallization and the formation of forsterite, which are completely different in wood quality, are caused by the decarburization annealing conditions and annealing conditions that determine the structure and thickness of the oxide film formed on the material surface during the decarburization annealing process. Easily affected by separating agents. Also, these 2
It is thought that this phenomenon is actually the result of a reaction progressing while mutually interfering between the inside of the material (III plate) and the surface layer part surface.
かかる観点から、これまで、脱炭焼鈍条件や焼鈍分離剤
について多くの研究がなされてきた。From this point of view, many studies have been conducted on decarburization annealing conditions and annealing separators.
一方、生産性を向上させる目的で、最終仕上焼鈍工程に
おいて取り扱うストリップコイルの単重は増大する傾向
にあり、このことに起因してストリップ長さ方向、幅方
向における温度或は雰囲気組成(露点等)のバラツキ、
特に昇温時におけるバラツキは避けられない実情にある
。このような、最終仕上焼鈍過程における材料(ストリ
ップコイル)内部での温度、雰囲気条件の不均一性を可
及的に緩和するためにも、脱炭焼鈍過程で材料表面に形
成する酸化膜層や焼鈍分離剤は重要であり、この分野の
研究を進める動機となってきた。On the other hand, for the purpose of improving productivity, the unit weight of strip coils handled in the final annealing process tends to increase. ) variation,
In particular, variations in temperature cannot be avoided. In order to alleviate as much as possible the non-uniformity of temperature and atmospheric conditions inside the material (strip coil) during the final finish annealing process, the oxide film layer formed on the material surface during the decarburization annealing process, Annealing separators are important and have motivated research in this area.
脱炭焼鈍過程で材料表面に形成する酸化膜層の効果は、
太き(分けて2つある。The effect of the oxide film layer formed on the material surface during the decarburization annealing process is
Thick (There are two parts.
1つは、材料表面におけるグラス皮膜(フォルステライ
ト皮膜)の安定形成であり、もう1つは、二次再結晶の
安定化である。One is stable formation of a glass film (forsterite film) on the material surface, and the other is stabilization of secondary recrystallization.
前者の場合、材料表面の酸化層の厚さ、構成成分等が重
要であり、後者の場合、材質的にどのようなメカニズム
で二°次再結晶を行わせるかということが重要である。In the former case, the thickness of the oxidized layer on the surface of the material, its constituent components, etc. are important, and in the latter case, it is important to determine the mechanism by which secondary recrystallization is performed in terms of the material.
これらが、脱炭焼純条件選択の重要な基準となる。These are important criteria for selecting decarburization and sintering conditions.
周知の如く、最終仕上焼鈍過程で材料の二次再結晶を進
行せしめるためには、インヒビターと呼ばれる微細析出
物の存在が必須である。通常、前記微細析出物の分散相
を、最終仕上焼鈍過程の高温域まで強化・維持すること
により二次再結晶は安定するので、インヒビターが窒化
物を主体としている場合は、焼鈍雰囲気中の窒素(N2
)分圧を、硫化物を主体としている場合は、硫黄分圧を
適当に維持する。As is well known, the presence of fine precipitates called inhibitors is essential for the secondary recrystallization of the material to proceed in the final annealing process. Normally, secondary recrystallization is stabilized by strengthening and maintaining the dispersed phase of the fine precipitates up to the high temperature range of the final annealing process. (N2
) If the main component is sulfide, maintain the sulfur partial pressure appropriately.
最終仕上焼鈍過程における焼鈍雰囲気中の窒素(N2)
分圧を適当に維持することに関しては、たとえば、特公
昭46−937号公報に、含M珪素鋼板を窒素雲囲気下
で焼鈍することの有用性が開示されており、この方法は
、引続き/U、 Ti、 Zr、 V等を含有する珪
素鋼板を種々の方法で窒化することを提案した特公昭4
6−40855号公報に開示されたプロセスに発展した
。Nitrogen (N2) in the annealing atmosphere during the final annealing process
Regarding maintaining an appropriate partial pressure, for example, Japanese Patent Publication No. 46-937 discloses the usefulness of annealing a M-containing silicon steel sheet under a nitrogen cloud, and this method is Tokuko Sho 4 proposed nitriding silicon steel sheets containing U, Ti, Zr, V, etc. by various methods.
The process was developed into the process disclosed in Publication No. 6-40855.
また、特公昭49−6455号公報には、含M珪素鋼板
の表層部を選択的に窒化することの有用性が指摘されて
おり、さらに、特公昭54−19850号公報には、適
切な窒化吸収を行わせるため、最終仕上焼鈍時の雰囲気
の露点を、−20℃〜+30℃の範囲にすることが提案
されている。Furthermore, Japanese Patent Publication No. 49-6455 points out the usefulness of selectively nitriding the surface layer of M-containing silicon steel sheets, and Japanese Patent Publication No. 54-19850 also states that appropriate nitriding is necessary. In order to cause absorption, it has been proposed that the dew point of the atmosphere during final annealing be in the range of -20°C to +30°C.
さらに、特公昭54−22408号公報には、最終仕上
焼鈍を水素20%以下の水素・窒素混合雰囲気下に行う
ことが提案されている。Furthermore, Japanese Patent Publication No. 54-22408 proposes that final annealing be performed in a hydrogen/nitrogen mixed atmosphere containing 20% or less hydrogen.
一方、焼鈍分離剤中に金属窒化物を添加することにより
、最終仕上焼鈍過程での材料(ストリップコイル)長さ
方向、幅方向での雰囲気のバラツキの影響を緩和する方
法が、特公昭54−14568号公報に開示されている
。具体的には、焼鈍分離剤中に窒化クロム、窒化チタン
、窒化バナジウムを添加することにより、最終仕上焼鈍
過程でのストリップコイルのストリップ幅方向における
雰囲気の窒素分圧を均一にし、二次再結晶の安定性を実
現せんとするものである。On the other hand, a method of mitigating the effects of atmospheric variations in the length and width directions of the material (strip coil) during the final annealing process was developed by adding metal nitrides to the annealing separator. It is disclosed in Japanese Patent No. 14568. Specifically, by adding chromium nitride, titanium nitride, and vanadium nitride to the annealing separator, the nitrogen partial pressure in the atmosphere in the strip width direction of the strip coil during the final annealing process is made uniform, and secondary recrystallization is achieved. The aim is to achieve the stability of
他方、最終仕上焼鈍過程での雰囲気中の硫黄分圧の確保
を目的としたものに、特開昭53−50008号公報に
提案されている方法がある。これは、sbと、Sおよび
/またはSeを主体とする析出分散相をインヒビターと
して用いる成分系の珪素鋼の二次再結晶の安定化を図る
ために、FezS等硫黄化合物を焼鈍分離剤中に添加し
たり、H,Sを含有する雰囲気中で最終仕上焼鈍する方
法である。On the other hand, there is a method proposed in Japanese Patent Laid-Open No. 53-50008 for the purpose of ensuring the sulfur partial pressure in the atmosphere during the final annealing process. This is because sulfur compounds such as FezS are added to the annealing separator in order to stabilize the secondary recrystallization of silicon steel, which uses sb and a precipitated dispersed phase mainly composed of S and/or Se as an inhibitor. In this method, final annealing is performed in an atmosphere containing H and S.
これらの先行技術にみられるように、珪素鋼の二次再結
晶は、最終仕上焼鈍過程での窒素分圧や硫黄分圧の確保
により安定する方向に向い、焼鈍分離剤中の添加物もこ
の目的のために加えられることが多い。As seen in these prior art techniques, the secondary recrystallization of silicon steel tends to be stabilized by ensuring nitrogen partial pressure and sulfur partial pressure in the final annealing process, and the additives in the annealing separator also stabilize this process. Often added for a purpose.
上に述べたように、脱炭焼鈍過程で材料表面に形成され
る酸化膜の機能の1つであるグラス皮膜形成は、焼鈍分
離剤中のMgOと酸化膜中のSiO□との反応で生じる
ものであり、酸化膜の構成成分としてSi0gリッチで
あることおよび一定以上の膜厚さが確保されていること
が重要である。As mentioned above, the glass film formation, which is one of the functions of the oxide film formed on the material surface during the decarburization annealing process, is caused by the reaction between MgO in the annealing separator and SiO□ in the oxide film. Therefore, it is important that the oxide film is rich in SiOg as a constituent component and that the film thickness is above a certain level.
脱炭焼鈍過程で材料表面に形成される酸化膜の第2の機
能である、最終仕上焼鈍過程での二次再結晶の安定化に
ついては、従来の、鋼中インヒビターとしてMnS 、
MnSe、 /VN等を用いる場合は、最終仕上焼鈍
の昇温過程での雰囲気ガスとの反応によるインヒビター
の変化を防止するために、雰囲気ガスに対して安定な酸
化膜、即ちシール性のよい(バリヤーとして機能し得る
)酸化膜であることが要求されてきた。Regarding the stabilization of secondary recrystallization in the final annealing process, which is the second function of the oxide film formed on the material surface during the decarburization annealing process, conventional inhibitors such as MnS and
When using MnSe, /VN, etc., in order to prevent changes in the inhibitor due to reaction with the atmospheric gas during the temperature raising process during final annealing, an oxide film that is stable against the atmospheric gas, that is, a film with good sealing properties ( There has been a demand for an oxide film that can function as a barrier.
この目的のために、たとえば、特公昭57−1575号
公報には、脱炭焼鈍過程前段領域における雰囲気の酸化
度(P工2゜/ P M□)を0.15以上とし、引き
続く後段領域における雰囲気の酸化度を0,75以下か
つ前段領域におけるそれよりも小さくすることが開示さ
れている。For this purpose, for example, Japanese Patent Publication No. 57-1575 states that the degree of oxidation of the atmosphere (P2°/P M□) in the first stage region of the decarburization annealing process is set to be 0.15 or more, and that It is disclosed that the oxidation degree of the atmosphere is set to 0.75 or less and smaller than that in the former region.
処で、近年、スラブ加熱過程でインヒビターを完全に溶
体化することなく、比較的低い温度に加熱する一方向性
電磁鋼板の製造プロセスが試みられている。In recent years, attempts have been made to produce grain-oriented electrical steel sheets in which the slab is heated to a relatively low temperature without completely solutionizing the inhibitor in the slab heating process.
かかるプロセスにあっては、熱延板焼鈍過程以外の過程
でインヒビターを析出分散させることが必要となってく
る。そのような、インヒビター析出分散手段の1つに最
終仕上焼鈍における二次再結晶以前の段階で、たとえば
、鋼中のMを窒化析出させる手段がある。In such a process, it is necessary to precipitate and disperse the inhibitor in a process other than the hot-rolled sheet annealing process. One of such means for dispersing inhibitor precipitation is a means for precipitating M in steel by nitriding, for example, at a stage before secondary recrystallization in final finish annealing.
かかる手段を採るときは、脱炭焼鈍過程で材料表面に形
成する酸化膜の機能が一変する。即ち、脱炭焼鈍過程で
材料表面に形成する酸化膜は、上に述べた如き最終仕上
焼鈍での雰囲気ガスに対して安定な酸化膜であってはな
らない。When such a measure is adopted, the function of the oxide film formed on the material surface during the decarburization annealing process changes completely. That is, the oxide film formed on the material surface during the decarburization annealing process must not be an oxide film that is stable against the atmospheric gas in the final finish annealing as described above.
かかる条件を満たしかつ、グラス皮膜の特性の向上と二
次再結晶の安定化を図らねばならない。These conditions must be met, and the properties of the glass film must be improved and secondary recrystallization stabilized.
(発明が解決しようとする問題点)
本発明は、スラブ加熱温度を1280℃未満の低い水準
とする一方向性電磁鋼板製造プロセスを採るときに、最
終仕上焼鈍過程における材料の窒化反応の安定化による
二次再結晶の安定化とグラス皮膜の安定形成が図れる一
方向性電磁鋼板の製造方法を提供することを目的として
なされた。(Problems to be Solved by the Invention) The present invention aims at stabilizing the nitriding reaction of the material during the final annealing process when using a unidirectional electrical steel sheet manufacturing process in which the slab heating temperature is at a low level of less than 1280°C. The purpose of this work is to provide a method for producing grain-oriented electrical steel sheets that can stabilize secondary recrystallization and stably form a glass film.
(問題点を解決するための手段)
本発明の要旨とするところは、重量%で、C:0.00
10〜0.10%、Si:2.5〜4.0%、酸可溶性
A1: 0.010〜0.06%、S≦0.014%、
残部:Feおよび不可避的不純物からなる一方向性電磁
鋼板用スラブを1280℃を超えない温度に加熱した後
、熱間圧延および熱延板焼鈍を施し、次いで1回または
焼鈍を介挿する2回以上の冷間圧延を行って最終板厚と
した後、湿水素雰囲気中で脱炭焼鈍し、次いで焼鈍分離
剤を塗布した後最終仕上焼鈍する一方向性電磁鋼板の製
造方法において、最終冷間圧延後の材料を、水素分圧に
対する水蒸気分圧の比PH2゜/ P ozが0.25
〜0.60の湿水素雰囲気中800〜900℃の温度域
で脱炭焼鈍した後、材料最表面層に形成されたSiO□
以外のMXoy層のみを、材料表面1m2当り0.02
〜2g軽酸洗によって除去し、次いで焼鈍分離剤を塗布
し、さらに最終仕上焼鈍することを特徴とする特許よび
グラス皮膜特性に優れた一方向性電磁鋼板の製造方法に
ある。(Means for solving the problems) The gist of the present invention is that C: 0.00% by weight
10-0.10%, Si: 2.5-4.0%, acid-soluble A1: 0.010-0.06%, S≦0.014%,
Remaining portion: After heating a unidirectional electrical steel plate slab consisting of Fe and unavoidable impurities to a temperature not exceeding 1280°C, hot rolling and hot rolled plate annealing are performed, and then once or twice with intervening annealing. In the method for manufacturing unidirectional electrical steel sheets, the final cold rolling is performed to achieve the final thickness, followed by decarburization annealing in a wet hydrogen atmosphere, followed by applying an annealing separator and final finish annealing. The material after rolling is adjusted to a ratio of water vapor partial pressure to hydrogen partial pressure, PH2°/Poz, of 0.25.
After decarburizing annealing in a temperature range of 800 to 900°C in a wet hydrogen atmosphere of ~0.60, SiO□ formed on the outermost surface layer of the material
0.02 per m2 of material surface only for the MXoy layer other than
The patent and method for producing a unidirectional electrical steel sheet with excellent glass film properties include removing ~2g by light pickling, then applying an annealing separator, and further final annealing.
以下に、本発明の詳細な説明する。The present invention will be explained in detail below.
本発明は、前述のように、脱炭焼純過程で形成される酸
化膜の、極く最表面層のみを軽酸洗によって除去し、最
終仕上焼鈍過程における雰囲気条件を特定のものとする
ことで材料の窒化反応の安定化による二次再結晶の安定
化とグラス皮膜の安定形成を図ることを目的とする。As mentioned above, the present invention removes only the outermost layer of the oxide film formed in the decarburization annealing process by light pickling, and specifies the atmospheric conditions in the final finish annealing process. The aim is to stabilize the secondary recrystallization by stabilizing the nitriding reaction of the material and to stably form a glass film.
本発明の発明者等は、出発材料として、重量%で、C:
0.055%、Si:3.30%、Mn : 0.1
5%、酸可溶性AZ : 0.030%、N : 0.
0070%、残部:実質的にFeからなるスラブを、熱
間圧延−熱延板焼鈍一酸洗一冷間圧延の工程で処理して
0.30閣の最終板厚とし、この材料を、P□2゜/P
□を変えて脱炭焼鈍し、軽酸洗条件を変えて材料表面の
酸化層の除去を行った。こうして得られた材料の酸化層
を、GDS分析および電位差カーブの測定によって解析
した。The inventors of the present invention have determined that as starting materials, in weight %, C:
0.055%, Si: 3.30%, Mn: 0.1
5%, acid soluble AZ: 0.030%, N: 0.
0070%, remainder: A slab consisting essentially of Fe was processed through the steps of hot rolling, hot rolling plate annealing, pickling, and cold rolling to a final thickness of 0.30%, and this material was □2゜/P
Decarburization annealing was performed by changing □, and the oxidation layer on the material surface was removed by changing the light pickling conditions. The oxidation layer of the material thus obtained was analyzed by GDS analysis and measurement of potential difference curves.
その結果、軽酸洗処理材にはその表面にM、O。As a result, the lightly pickled material has M and O on its surface.
系の酸化物は見られず、電位差カーブの結果でも最表層
には酸洗なし材に見られるタイトな酸化物は確認できな
かった。No system oxides were observed, and the tight oxides seen in the non-pickled material were not confirmed in the outermost layer even in the results of the potential difference curve.
この軽酸洗処理による材料表面状況の変化は、脱炭焼鈍
におけるPo。/Pug が高くても低くても同様で
あった。軽酸洗後の材料表層部所面を第1図に模式的に
示す。The change in the material surface condition due to this light pickling treatment is due to Po in decarburization annealing. The results were similar whether /Pug was high or low. Figure 1 schematically shows the surface layer of the material after light pickling.
次いで、この材料に焼鈍分離剤を塗布し、昇温過程でN
2 +Hz雰囲気を使用して最終仕上焼鈍を行ない、昇
温過程における材料の窒化状況ならびに最終仕上焼鈍完
了後の製品の特性を調査した。Next, an annealing separator is applied to this material, and N is added during the heating process.
Final annealing was performed using a 2+Hz atmosphere, and the nitridation status of the material during the temperature raising process and the characteristics of the product after final annealing were investigated.
その結果、最終仕上焼鈍の昇温過程900℃での鋼中の
Ni!には、軽酸洗量が所定条件内では100〜150
ppmの増加が認められ、磁気特性、皮膜特性とも軽酸
洗量が所定条件以下の領域で著しく改善できることが判
った。As a result, Ni in the steel during final annealing at 900°C! The amount of light pickling is 100 to 150 within the specified conditions.
An increase in ppm was observed, and it was found that both the magnetic properties and film properties could be significantly improved when the amount of light pickling was below the predetermined conditions.
次に、本発明の要件の軽酸洗条件の限定理由について述
べる。Next, the reason for limiting the light pickling conditions, which is a requirement of the present invention, will be described.
脱炭焼鈍過程におけるP nzo / P utは、0
.25〜0.60の範囲内であればよい。P nzo
/ P Hzが0.25未満では、脱炭性と酸化膜形成
能の点で不利であり、0.60mではM、O,層が著し
く増大し軽酸洗条件を強くしなければならず、材料表面
の肌荒れからくる磁性、皮膜への悪影響やこれらのバラ
ツキが大きくなるという問題がある。P nzo / P ut in the decarburization annealing process is 0
.. It may be within the range of 25 to 0.60. P nzo
/P Hz is less than 0.25, which is disadvantageous in terms of decarburization and oxide film formation ability, and at 0.60 m, the M, O, and layers increase significantly and the light pickling conditions must be strengthened. There are problems in that the roughness of the material surface has an adverse effect on magnetism and the film, and that variations in these factors become large.
軽酸洗では、最終仕上焼鈍過程での材料の適切な窒化反
応の促進と、焼鈍分離剤中のMgOとの反応によるグラ
ス形成の促進およびグラス形成量の観点から、5iOd
i!以外の最表面層のM、O,層のみを除去することが
重要である。In light pickling, 5iOd
i! It is important to remove only the outermost M, O, and other layers.
このM、O,@の量は、当然のことながら脱炭焼鈍にお
けるP Hzo / P Illによって変わるから、
上記P Hgo / P oxの範囲内では、軽酸洗量
は、0.02〜2g/m”の範囲であれば、グラス皮膜
、二次再結晶の安定化に寄与する。The amounts of M, O, and @ naturally vary depending on P Hzo / P Ill in decarburization annealing, so
Within the above range of P Hgo / P ox , if the light pickling amount is in the range of 0.02 to 2 g/m'', it contributes to stabilizing the glass film and secondary recrystallization.
最終仕上焼鈍過程における雰囲気条件は、本発明におけ
る成分条件下では特に重要であり、特公昭54−145
68号公報に開示されている技術におけるような窒化剤
を用いるとき以外は、N2を含む焼鈍雰囲気であること
が重要である。The atmospheric conditions in the final annealing process are particularly important in terms of the component conditions in the present invention.
It is important that the annealing atmosphere contains N2, except when using a nitriding agent as in the technique disclosed in Japanese Patent No. 68.
最終仕上焼鈍の昇温過程における雰囲気ガスとしては、
N!単独、N、+l1zSN、+Ar、NZ+H2+^
r等であれば良い。The atmospheric gas during the temperature increase process of final annealing is as follows:
N! Single, N, +l1zSN, +Ar, NZ+H2+^
It is sufficient if it is r, etc.
素材成分の限定理由についてのべる。本発明が2次再結
晶に必要な析出物として、(St、 /V) Nを使う
ことから5tSAlの含有が必須である。Siが2.5
%未満では素材の固有抵抗が低すぎ、トランス鉄心材料
として必要な低鉄損が得られないので2.5%以上とし
た。また、4.0%を超えると冷延時の割れが著しくな
るので4.0%以下とした。IVNは2次再結晶の安定
化に必要なjVNもしくは(Si、jV)Nを確保する
ため酸可溶性Mとして0.010%以上が必要である。Describe the reasons for limiting the material components. Since the present invention uses (St, /V) N as a precipitate necessary for secondary recrystallization, the inclusion of 5tSAl is essential. Si is 2.5
If it is less than 2.5%, the specific resistance of the material will be too low and the low core loss required as a transformer core material cannot be obtained, so it is set to 2.5% or more. Moreover, if it exceeds 4.0%, cracking during cold rolling becomes significant, so the content was set at 4.0% or less. IVN requires an acid-soluble M content of 0.010% or more in order to secure jVN or (Si, jV)N necessary for stabilizing secondary recrystallization.
しかし0.06%を超えると熱延板のjVNが不適切と
なり、2次再結晶が不安定になるので0.06%以下と
した。However, if it exceeds 0.06%, the jVN of the hot rolled sheet becomes inappropriate and secondary recrystallization becomes unstable, so the content was set to 0.06% or less.
Sを0.014%以下としたのは、Sが高いと線状細粒
と呼ばれる2次再結晶不良部が発生する傾向にあり、こ
れを予防するためには窒化処理が十分であれば0.01
4%以下であることが望ましい。Sがこの量を超えると
、如何に窒化処理により(St、 AJ) Nを鋼中に
作りインヒビターを強化しても2次再結晶不良部が発生
する確率が高くなり好ましくない。The reason for setting the S content to 0.014% or less is that if the S content is high, secondary recrystallization defects called linear fine grains tend to occur, and to prevent this, if the nitriding treatment is sufficient, the .01
It is desirable that it is 4% or less. If S exceeds this amount, no matter how much (St, AJ) N is created in the steel through nitriding treatment to strengthen the inhibitor, there is a high probability that secondary recrystallization defects will occur, which is undesirable.
Cは0.0010%未満になると2次再結晶が不安定に
なり、かつ2次再結晶した場合でも低磁束密度しか得ら
れないので0.0010%以上とした。一方、Cが多く
なり過ぎると、脱炭焼鈍時間が長くなり経済的でないの
で0.10%以下とした。If C is less than 0.0010%, secondary recrystallization becomes unstable, and even if secondary recrystallization is performed, only a low magnetic flux density can be obtained, so it is set to 0.0010% or more. On the other hand, if the amount of C is too large, the decarburization annealing time becomes long and it is not economical, so it is set to 0.10% or less.
以下、実施例により本発明をさらに詳細に説明する。Hereinafter, the present invention will be explained in more detail with reference to Examples.
(実施例)
重量%で、C: 0.048%、Si:3.30%、s
: o、 o o s%、N : O,OO75%、
Mn :0.15%、残部Fe及び不可避的不純物から
なる溶鋼を、連続鋳造−熱間圧延一熱延板焼鈍一酸洗一
冷間圧延して、0.29mmの最終板厚とした後、脱炭
焼鈍を、Nt25%+H275%の雰囲気中で、P *
zo / P Hzを(A):0.44、(B) :
0.34として850℃×150秒間で行った。(Example) In weight%, C: 0.048%, Si: 3.30%, s
: o, o o s%, N: O, OO75%,
Molten steel consisting of Mn: 0.15%, balance Fe and unavoidable impurities was subjected to continuous casting, hot rolling, hot rolling plate annealing, pickling, and cold rolling to a final plate thickness of 0.29 mm. Decarburization annealing was performed in an atmosphere of 25% Nt + 75% H2.
zo/P Hz (A): 0.44, (B):
The temperature was set to 0.34 at 850° C. for 150 seconds.
次いで、1lzs045%溶液中で、脱炭焼鈍過程で形
成された酸化層の最表面層のみを、時間を変えて酸洗し
た。然る後、この材料に焼鈍分離剤を塗布し、最終仕上
焼鈍を、昇温過程での雰囲気N225%+H!75%、
1200℃X20hrの高温保定時の雰囲気82100
%ドライの条件で行い、このときの昇温過程での鋼中の
N含有量を調査した。Next, only the outermost layer of the oxide layer formed during the decarburization annealing process was pickled in a 1lzs045% solution for different times. After that, an annealing separator is applied to this material, and final annealing is performed in an atmosphere of N225%+H! during the temperature raising process. 75%,
Atmosphere when maintaining high temperature at 1200℃ x 20hrs 82100
% dry conditions, and the N content in the steel during the temperature rising process was investigated.
その結果ならびに最終仕上焼鈍完了後の製品の磁気特性
およびグラス皮膜特性を、表1に示す。Table 1 shows the results and the magnetic properties and glass film properties of the product after final annealing.
軽酸洗なしの比較材では、最終仕上焼鈍昇温過程におけ
るN吸収量が少なく、磁性、皮膜特性ともに不良である
のに対し、本発明になる軽酸洗材は、何れもN吸収量が
増加し、製品の磁気特性が著しく改善されるとともにグ
ラス皮膜も均一化し、密着性の改善が見られた。Comparative materials without light pickling had a small amount of N absorption during the final finish annealing temperature raising process, and were poor in both magnetic properties and film properties, whereas the light pickling materials of the present invention had a low amount of N absorption. The magnetic properties of the product were significantly improved, the glass coating became more uniform, and the adhesion was improved.
(発明の効果)
本発明は、以上述べたように構成しかつ、作用せしめる
ようにしたから、スラブ加熱温度を1280℃未満と低
い水準にしてなお、最終仕上焼鈍過程における二次再結
晶を安定化し、最終製品の磁気特性、皮膜特性ともに優
れたものとすることができるから、スラブ加熱のための
エネルギを大幅に減少せしめ得、設備のメンテナンス、
設備稼働率、作業性の面で多大の効果を奏する。(Effects of the Invention) Since the present invention is configured and operated as described above, secondary recrystallization in the final finish annealing process is stabilized even when the slab heating temperature is set to a low level of less than 1280°C. The final product has excellent magnetic properties and film properties, which greatly reduces the energy required to heat the slab, reducing equipment maintenance and
It has a great effect on equipment utilization rate and work efficiency.
第1図は、脱炭焼鈍後の材料最表層部を軽酸洗によって
除去した後の、材料表要部段面を模式的に ・示す図で
ある。
第1図
腎欽洗荊 軽峡洗使FIG. 1 is a diagram schematically showing the step surface of the main part of the material surface after the outermost layer of the material after decarburization annealing was removed by light pickling. Diagram 1: Kidokin Senji Karukyo Senshi
Claims (1)
5〜4.0%、酸可溶性Al:0.010〜0.06%
、S≦0.014%、残部:Feおよび不可避的不純物
からなる一方向性電磁鋼板用スラブを1280℃を超え
ない温度に加熱した後、熱間圧延および熱延板焼鈍を施
し、次いで1回または焼鈍を介挿する2回以上の冷間圧
延を行って最終板厚とした後、湿水素雰囲気中で脱炭焼
鈍し、次いで焼鈍分離剤を塗布した後最終仕上焼鈍する
一方向性電磁鋼板の製造方法において、最終冷間圧延後
の材料を、水素分圧に対する水蒸気分圧の比P_H_Z
_O/P_H_Zが0.25〜0.60の湿水素雰囲気
中800〜900℃の温度域で脱炭焼鈍した後、材料最
表面層に形成されたSiO_2以外のM_xO_y層の
みを、材料表面1m^2当り0.02〜2g軽酸洗によ
って除去し、次いで焼鈍分離剤を塗布し、さらに最終仕
上焼鈍することを特徴とする磁気特性およびグラス皮膜
特性に優れた一方向性電磁鋼板の製造方法。In weight%, C: 0.0010 to 0.10%, Si: 2.
5-4.0%, acid-soluble Al: 0.010-0.06%
, S≦0.014%, remainder: Fe and unavoidable impurities A slab for unidirectional electrical steel sheets is heated to a temperature not exceeding 1280°C, then hot rolled and hot rolled plate annealed, and then once Or, after cold rolling two or more times with intervening annealing to achieve the final thickness, decarburization annealing in a wet hydrogen atmosphere, then applying an annealing separator and final finish annealing is performed on a unidirectional electrical steel sheet. In the manufacturing method, the material after final cold rolling is heated to a ratio of water vapor partial pressure to hydrogen partial pressure P_H_Z
After decarburizing annealing at a temperature range of 800 to 900°C in a wet hydrogen atmosphere with _O/P_H_Z of 0.25 to 0.60, only the M_xO_y layer other than SiO_2 formed on the outermost surface layer of the material was removed from the surface of the material by 1 m^. 1. A method for producing a unidirectional electrical steel sheet with excellent magnetic properties and glass film properties, characterized by removing 0.02 to 2 g per 2 g by light pickling, then applying an annealing separating agent, and further final annealing.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP27501487A JPH01119622A (en) | 1987-10-30 | 1987-10-30 | Production of grain oriented electrical steel sheet having excellent magnetic characteristic and glass film characteristic |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP27501487A JPH01119622A (en) | 1987-10-30 | 1987-10-30 | Production of grain oriented electrical steel sheet having excellent magnetic characteristic and glass film characteristic |
Publications (1)
Publication Number | Publication Date |
---|---|
JPH01119622A true JPH01119622A (en) | 1989-05-11 |
Family
ID=17549676
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP27501487A Pending JPH01119622A (en) | 1987-10-30 | 1987-10-30 | Production of grain oriented electrical steel sheet having excellent magnetic characteristic and glass film characteristic |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPH01119622A (en) |
Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO1991016462A1 (en) * | 1990-04-13 | 1991-10-31 | Nippon Steel Corporation | Process for producing unidirectional magnetic steel sheet excellent in magnetic characteristics |
US5620533A (en) * | 1995-06-28 | 1997-04-15 | Kawasaki Steel Corporation | Method for making grain-oriented silicon steel sheet having excellent magnetic properties |
KR100340500B1 (en) * | 1997-09-26 | 2002-07-18 | 이구택 | A Method for Manufacturing Oriented Electrical Steel Sheets Having Superior Decarburization within Shot Annealing-time |
KR100345709B1 (en) * | 1997-12-24 | 2002-09-18 | 주식회사 포스코 | A method of manufacturing grain oriented electrical steel sheet with high permeability |
-
1987
- 1987-10-30 JP JP27501487A patent/JPH01119622A/en active Pending
Cited By (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO1991016462A1 (en) * | 1990-04-13 | 1991-10-31 | Nippon Steel Corporation | Process for producing unidirectional magnetic steel sheet excellent in magnetic characteristics |
US5597424A (en) * | 1990-04-13 | 1997-01-28 | Nippon Steel Corporation | Process for producing grain oriented electrical steel sheet having excellent magnetic properties |
US5620533A (en) * | 1995-06-28 | 1997-04-15 | Kawasaki Steel Corporation | Method for making grain-oriented silicon steel sheet having excellent magnetic properties |
KR100340500B1 (en) * | 1997-09-26 | 2002-07-18 | 이구택 | A Method for Manufacturing Oriented Electrical Steel Sheets Having Superior Decarburization within Shot Annealing-time |
KR100345709B1 (en) * | 1997-12-24 | 2002-09-18 | 주식회사 포스코 | A method of manufacturing grain oriented electrical steel sheet with high permeability |
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