JP2000246640A - Method of polishing surface of steel plate - Google Patents
Method of polishing surface of steel plateInfo
- Publication number
- JP2000246640A JP2000246640A JP11053877A JP5387799A JP2000246640A JP 2000246640 A JP2000246640 A JP 2000246640A JP 11053877 A JP11053877 A JP 11053877A JP 5387799 A JP5387799 A JP 5387799A JP 2000246640 A JP2000246640 A JP 2000246640A
- Authority
- JP
- Japan
- Prior art keywords
- injection
- steel sheet
- pressure
- pressure water
- steel plate
- 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.)
- Withdrawn
Links
Landscapes
- Manufacturing Of Steel Electrode Plates (AREA)
Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、鋼板の表面研磨方
法に関し、特に簡便かつ迅速、さらには低コストの下で
鋼板表面の平滑化を達成しようとするものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for polishing a surface of a steel sheet, and more particularly to a method for achieving smoothness of a steel sheet surface in a simple and quick manner at a low cost.
【０００２】[0002]
【従来の技術】現在、建築用部材、自動車用部材とし
て、ステンレス鋼板や低炭素冷延鋼板、ＩＦ(Interstiti
al Free) 鋼板等が大量に使用されている。また、変圧
器やその他電気器機の鉄芯材料として一方向性珪素鋼板
が広く利用されている。これらの鋼板はいずれも、製
銑、製鋼、連続鋳造、加熱、熱間圧延、冷間圧延および
焼鈍工程を経て製造されているが、その製造過程または
製品板において平滑な表面が必要とされる。例えば、一
方向性珪素鋼板においては、フォルステライト系下地被
膜と地鉄の界面構造の乱れが磁気特性に悪影響を及ぼす
ことが指摘されていることもあって、最近では、このよ
うな下地被膜を形成させないいわゆる膜なし一方向性珪
素鋼板の研究開発が盛んに行われているが、この技術で
は、絶縁被膜形成前に鋼板表面を平滑状態に仕上げてお
くことが重要である。2. Description of the Related Art At present, stainless steel sheets, low-carbon cold-rolled steel sheets, IF (Interstiti
al Free) Steel plates are used in large quantities. Also, unidirectional silicon steel sheets are widely used as iron core materials for transformers and other electric appliances. All of these steel plates are manufactured through ironmaking, steelmaking, continuous casting, heating, hot rolling, cold rolling and annealing processes, but a smooth surface is required in the manufacturing process or product plate. . For example, in unidirectional silicon steel sheets, it has been pointed out that disorder of the interface structure between the forsterite-based undercoat and the ground iron has a bad influence on magnetic properties. Research and development of so-called non-film-oriented unidirectional silicon steel sheets which are not formed are actively performed. In this technique, it is important to finish the steel sheet surface in a smooth state before forming an insulating film.
【０００３】従来、鋼板表面を平滑化する方法として
は、一般に酸洗、機械研磨または電解研磨処理等が使用
されてきた。しかしながら、これらの方法はいずれも、
煩雑で、処理に長時間を要するだけでなく、コスト高と
なるところに問題を残していた。鋼板の製造は、通常、
連続的に行われるため、かような平滑化処理を短時間で
しかも低コストの下に行えれば、その効果ははかり知れ
ない。Conventionally, as a method for smoothing the surface of a steel sheet, pickling, mechanical polishing, electrolytic polishing, or the like has been generally used. However, each of these methods
The problem remains in that it is complicated and takes a long time for processing, and also increases the cost. The manufacture of steel sheets is usually
Since the smoothing process is performed continuously, if the smoothing process can be performed in a short period of time and at low cost, the effect is immeasurable.
【０００４】[0004]
【発明が解決しようとする課題】本発明は、上記の要請
に有利に応えるもので、鋼板の製品段階においては勿
論、製造過程の中途段階で必要とされる表面の平滑化
を、簡便かつ迅速、さらには低コストの下で実現するこ
とができる、新規な鋼板の表面研磨方法を提案すること
を目的とする。SUMMARY OF THE INVENTION The present invention advantageously satisfies the above-mentioned demands, and provides a simple and quick surface smoothing process required not only in the product stage of a steel sheet but also in the middle of a manufacturing process. It is another object of the present invention to propose a novel method for polishing a surface of a steel sheet, which can be realized at a low cost.
【０００５】[0005]
【課題を解決するための手段】製鉄所では、水を大量に
使用することから、その管理、活用に関しては技術レベ
ルが極めて高い。例えば、その一例として、熱間圧延工
程等において鋼板表面に生成したスケールを高圧水で除
去するデスケーラーが挙げられる。また、最近では、超
高圧水を利用して、鋼板表面を研削する方法が提案され
ている（特開平５-31524号公報）。この方法は、予めメ
カニカルな手段によって、帯状金属体の表面に生成した
スケールに亀裂または剥離を助長させる前処理を施した
のち、表面に超高圧水（噴射圧力：1000 kgf/cm2以上）
を噴射して、表面層を20μm 以上研削除去すると共に、
表面をＲmax ≦30μm に仕上げる研削方法である。その
他、超高圧水を利用してモノを切断するという技術（例
えば、 Infondia,1999. p.17、 “製品開発にドラマあ
り”参照）も提案されている。[Means for Solving the Problems] In steel works, a large amount of water is used, so that the technical level of management and utilization thereof is extremely high. For example, as one example, there is a descaler that removes scale generated on the surface of a steel sheet in a hot rolling step or the like with high-pressure water. Recently, a method of grinding the surface of a steel sheet using ultra-high pressure water has been proposed (Japanese Patent Laid-Open No. 5-31524). In this method, the scale formed on the surface of the strip-shaped metal body is pre-treated by mechanical means to promote cracking or peeling, and then the surface is treated with ultra-high pressure water (jet pressure: 1000 kgf / cm 2 or more)
To remove the surface layer by grinding more than 20μm,
This is a grinding method for finishing the surface to R max ≦ 30 μm. Other technologies have been proposed that use ultrahigh-pressure water to cut objects (for example, see Infondia, 1999. p.17, “There is a drama in product development”).
【０００６】このように、製鉄所では、水が豊富なだけ
でなく、その制御技術に優れていることから、発明者ら
は、上記したような高圧水技術をうまく活用すれば鋼板
表面の平滑化を短時間でしかも安価に実現できるのでは
ないかと考え、その研究を進めた。まず、従来技術に従
い、板面に対し垂直方向から高圧水を噴射するものと
し、その射出圧を種々に変更することによって鋼板表面
の平滑化を試みたが、射出圧を調整するだけではどのよ
うにしても、満足いくほどの表面粗さに仕上げることは
できなかった。そこで、次に、発明者らは、射出圧以外
の要件についても鋭意研究を進めた結果、表面平滑化の
ためには高圧水を噴射する時の射出角が重要で、この角
度を適正の範囲に調整することによって、所期した目的
が有利に達成されることの知見を得た。本発明は、上記
の知見に立脚するものである。[0006] As described above, since steelworks are not only abundant in water but also excellent in control technology, the present inventors have proposed that if the above-mentioned high-pressure water technology is used well, the surface of the steel sheet can be smoothed. We thought that it could be realized in a short time and at low cost, and proceeded with the research. First, according to the prior art, it was assumed that high-pressure water was injected from the direction perpendicular to the plate surface, and the injection pressure was variously changed to try to smooth the steel plate surface. However, it was not possible to achieve a satisfactory surface roughness. Then, the inventors next conducted intensive research on requirements other than the injection pressure. As a result, the injection angle when high-pressure water is injected is important for smoothing the surface. It has been found that the desired objective can be advantageously achieved by adjusting to. The present invention is based on the above findings.
【０００７】[0007]
【課題を解決するための手段】すなわち、本発明は、鋼
板の表面に対し、射出圧が 500〜5000気圧の高圧水を、
板面に対し30〜70°傾斜した射出角で噴射することを特
徴とする鋼板の表面研磨方法である。That is, according to the present invention, high pressure water having an injection pressure of 500 to 5000 atm is applied to the surface of a steel sheet.
This is a method for polishing the surface of a steel sheet, wherein the injection is performed at an injection angle inclined by 30 to 70 ° with respect to the plate surface.
【０００８】また、本発明を適用して好適な被処理鋼板
としては、ステンレス鋼板、低炭素冷延鋼板、 ＩＦ鋼板
および一方向性珪素鋼板等が挙げられる。[0008] Examples of the steel sheet to be processed according to the present invention include a stainless steel sheet, a low-carbon cold-rolled steel sheet, an IF steel sheet, and a unidirectional silicon steel sheet.
【０００９】[0009]
【発明の実施の形態】以下、本発明の解明経緯について
説明する。さて、発明者らは、まず最初に、高圧水の射
出圧を調整することによって鋼板表面の平滑化を試み
た。試料（30×300 mm）としては次の４種類の鋼板を準
備した。 ステンレス鋼板（SUS430） Ｃ：0.03wt％、Si：0.25wt％、Mn：0.16wt％、Ｐ：0.01
2 wt％、Ｓ：0.011 wt％およびCr：16.7wt％を含有し、
残部は実質的にFeの組成になる連続鋳造スラブを、熱間
圧延後、冷間圧延して0.25mm厚の冷延板としたのち、 H2
ガス雰囲気中で光輝焼鈍(Bright Annealing)したもの。 低炭素冷延鋼板 Ｃ：0.046 wt％、Si：0.012 wt％、Mn：0.35wt％、Ｐ：
0.007 wt％、Ｓ：0.009 wt％およびAl：0.003 wt％を含
有し、残部は実質的にFeの組成になる連続鋳造スラブ
を、熱間圧延後、冷間圧延して0.80mm厚の冷延板とした
のち、連続焼鈍したもの。 ＩＦ鋼 Ｃ： 0.002wt％、Si：0.002 wt％、Mn：0.009 wt％、
Ｐ：0.002 wt％、Ｓ：0.002 wt％、Al：0.001 wt％、
Ｎ：0.0009wt％およびＯ：0.0013wt％を含有し、残部は
実質的にFeの組成になる連続鋳造スラブを、熱間圧延
後、冷間圧延して 1.2mm厚の冷延板としたのち、連続焼
鈍したもの。 一方向性珪素鋼板（膜なし） Ｃ：0.068 wt％、Si：3.33wt％、Mn：0.067 wt％、Se：
0.020 wt％、Sb：0.025 wt％、Al：0.20wt％、Ｎ：0.00
76wt％およびMo：0.013 wt％を含有し、残部は実質的に
Feの組成になる連続鋳造スラブを、熱間圧延後、中間焼
鈍を挟む２回の冷間圧延を施して板厚：0.23mmの最終板
厚に仕上げたのち、線状溝を付与する磁区細分化処理
（幅：200 μm 、深さ：20μm 、間隔：４mm）を施し、
ついで、840 ℃の湿H2中で脱炭・１次再結晶焼鈍を行っ
たのち、鋼板表面に MgO（20wt％),Al2O3（75wt％), C
aSiO3（５wt％) の組成になる焼鈍分離剤をスラリー塗
布してから、850 ℃で15時間の焼鈍後、850 ℃から10℃
／h の速度で1150℃まで昇温してゴス方位に強く集積し
た2 次再結晶粒を発達させたのち、 1200℃の乾H2中で純
化処理を施したもの。DESCRIPTION OF THE PREFERRED EMBODIMENTS The details of the invention will be described below. The inventors first tried to smooth the steel sheet surface by adjusting the injection pressure of high-pressure water. The following four types of steel plates were prepared as samples (30 × 300 mm). Stainless steel plate (SUS430) C: 0.03wt%, Si: 0.25wt%, Mn: 0.16wt%, P: 0.01
2 wt%, S: 0.011 wt% and Cr: 16.7 wt%,
After the balance of the continuously cast slab consisting essentially composition Fe, after hot rolling, was 0.25mm thick cold-rolled sheet by cold rolling, H 2
Bright annealed in a gas atmosphere. Low carbon cold rolled steel sheet C: 0.046 wt%, Si: 0.012 wt%, Mn: 0.35 wt%, P:
A continuous cast slab containing 0.007 wt%, S: 0.009 wt% and Al: 0.003 wt%, with the balance being substantially Fe, is hot rolled, then cold rolled and cold rolled to 0.80 mm thickness After being made into a plate, it is continuously annealed. IF steel C: 0.002 wt%, Si: 0.002 wt%, Mn: 0.009 wt%,
P: 0.002 wt%, S: 0.002 wt%, Al: 0.001 wt%,
A continuous cast slab containing N: 0.0009 wt% and O: 0.0013 wt%, with the balance being substantially Fe, was hot rolled and then cold rolled into a 1.2 mm thick cold rolled sheet. , Continuously annealed. Unidirectional silicon steel sheet (without film) C: 0.068 wt%, Si: 3.33 wt%, Mn: 0.067 wt%, Se:
0.020 wt%, Sb: 0.025 wt%, Al: 0.20 wt%, N: 0.00
Contains 76 wt% and Mo: 0.013 wt%, with the balance being substantially
A continuous cast slab having a Fe composition is hot-rolled and then subjected to two cold rolling steps with intermediate annealing to finish to a final thickness of 0.23 mm, and then a magnetic domain subdivision providing linear grooves. Processing (width: 200 μm, depth: 20 μm, interval: 4 mm)
Then, after decarburization and primary recrystallization annealing in 840 ° C. wet H 2 , MgO (20 wt%), Al 2 O 3 (75 wt%), C
a SiO 3 and annealing separating agent consisting of the composition of (5 wt%) from the slurry application, after annealing for 15 hours at 850 ° C., 10 ° C. from 850 ° C.
/ H speed was heated to 1150 ° C. in the mixture was allowed to develop secondary recrystallized grains accumulated strongly Goss orientation, which was subjected to purification treatment in dry of H 2 1200 ° C..
【００１０】実験例１ これら〜のサンプルを、図１に示すように配置した
のち、射出圧が4000気圧の高圧水のウォータージェット
を、鋼板表面に対し垂直に噴射しながら矢印の方向に移
動させた（移動速度：3000mm／min 、噴射幅：２mm) 。
かような処理を施す前後の鋼板表面の表面粗さＲa およ
び表面状況を比較して表１に示す。 Experimental Example 1 After arranging these samples as shown in FIG. 1, a water jet having an injection pressure of 4000 atm was moved in the direction of the arrow while being jetted perpendicularly to the steel sheet surface. (Moving speed: 3000 mm / min, injection width: 2 mm).
Table 1 shows a comparison between the surface roughness Ra and the surface condition of the steel sheet surface before and after such treatment.
【００１１】[0011]
【表１】 [Table 1]
【００１２】同表から明らかなように、高圧水を鋼板表
面に対し垂直に噴射した場合には、いずれの鋼板につい
ても、噴射後に表面粗さが大きくなり、また強力な水圧
のため鋼板の表面に凹凸が出ることが判明した。As is clear from the table, when high-pressure water is injected perpendicularly to the surface of the steel sheet, the surface roughness of any steel sheet becomes large after the injection, and the surface of the steel sheet is intense due to strong water pressure. It was found that irregularities appeared.
【００１３】実験例２ そこで、次に、射出圧を1500気圧に低減し、実験１と同
様に、鋼板表面に対し垂直方向から噴射しながら矢印の
方向に移動させた（移動速度：3000mm／min 、噴射幅：
２mm) 。この場合における、処理前後の鋼板表面の表面
粗さＲa および表面状況について調べた結果を表１に併
記する。同表に示したとおり、射出圧を1500気圧まで低
減すると、鋼板の表面粗さや表面状況は4000気圧の場合
よりも幾分改善されたけれども、やはり満足いくほど良
好な成果を得ることはできなかった。 Experimental Example 2 Then, as in Experiment 1, the injection pressure was reduced to 1500 atm, and the steel sheet was moved in the direction of the arrow while spraying from the vertical direction (moving speed: 3000 mm / min). , Injection width:
2mm). In this case, the results of the examination of the surface roughness Ra and the surface condition of the steel sheet surface before and after the treatment are also shown in Table 1. As shown in the table, when the injection pressure was reduced to 1500 atm, the surface roughness and surface condition of the steel sheet were somewhat improved compared to the case of 4000 atm, but still no satisfactory results could be obtained. Was.
【００１４】実験例３ そこで、次に、発明者らは、射出圧以外の要件について
種々検討した結果、表面平滑化のためには高圧水の射出
角が極めて重要であることが究明されたのである。表２
に、射出圧が4000気圧および2000気圧の各場合におい
て、高圧水の噴射角を板面に対して45°傾斜させ、実験
１，２と同様に移動速度：3000mm／min 、噴射幅：２mm
の条件で高圧水噴射を行った場合の表面粗さＲa および
表面状況について調べた結果を示す。 EXPERIMENTAL EXAMPLE 3 Next, as a result of various studies on requirements other than the injection pressure, the inventors have found that the injection angle of high-pressure water is extremely important for surface smoothing. is there. Table 2
In addition, when the injection pressure is 4000 atm and 2000 atm, the injection angle of the high-pressure water is inclined by 45 ° with respect to the plate surface, and the moving speed is 3000 mm / min and the injection width is 2 mm as in Experiments 1 and 2.
The results of examining the surface roughness Ra and the surface condition when high-pressure water injection is performed under the conditions described above are shown.
【００１５】[0015]
【表２】 [Table 2]
【００１６】同表から明らかなように、射出圧が4000気
圧および2000気圧いずれの場合においても、高圧水の噴
射を45°傾斜させて行った場合には、鋼板の表面粗さが
格段に改善され、また鋼板の形状は噴射前と全く変わら
ず平坦であった。そこで、本発明では、高圧水の噴射に
よる鋼板の表面研磨に際し、高圧水の射出角を幾分傾斜
させることにしたのである。なお、ステンレス鋼板や一
方向性珪素鋼板のように比較的硬い鋼種の場合には4000
気圧という高い射出圧の方が、一方低炭素冷延鋼板やＩ
Ｆ鋼板のように比較的軟らかい鋼種の場合には2000気圧
という比較的低い射出圧の方が一層良好な結果が得られ
た。As is clear from the table, the surface roughness of the steel sheet is significantly improved when the injection of high-pressure water is performed at an inclination of 45 °, regardless of the injection pressure of 4000 or 2000 atm. In addition, the shape of the steel plate was flat as it was before the injection. Therefore, in the present invention, the injection angle of the high-pressure water is slightly inclined when the surface of the steel plate is polished by the injection of the high-pressure water. In the case of relatively hard steel types such as stainless steel sheets and unidirectional silicon steel sheets, 4000
Higher injection pressure, on the other hand, is better for low carbon cold rolled steel sheets and I
In the case of a relatively soft steel type such as an F steel plate, better results were obtained with a relatively low injection pressure of 2000 atm.
【００１７】実験例４ 次に、の膜なし一方向性珪素鋼板に、射出圧：4000気
圧、射出角：45°の条件で表面平滑化処理を施したもの
について、以下の条件で絶縁被膜を被成し、そのときの
磁気特性について調査した。 (1) マグネトロン・スパッタ法を用いて、SiＮX 膜を
0.8μm 厚成膜した。 (2) 中空陰極法（ＨＣＤ法）を用いて、TiＮ膜を1.00μ
m 厚成膜した。 また、比較のため、3vol％ＨＦとH2O2で化学研磨したの
ち、(1), (2)のセラミック膜を成膜した場合、および5v
ol％HCl で酸洗処理したのち、(1), (2)のセラミック膜
を成膜した場合についても調査した。得られた結果を表
３に示す。 EXPERIMENTAL EXAMPLE 4 Next, a film-free unidirectional silicon steel sheet which had been subjected to a surface smoothing treatment under the conditions of an injection pressure of 4000 atm and an injection angle of 45 ° was coated with an insulating film under the following conditions. The magnetic properties at that time were investigated. (1) using a magnetron sputtering method, a SiN X film
A 0.8 μm thick film was formed. (2) Using a hollow cathode method (HCD method), the TiN film is 1.00 μm thick.
m thick film was formed. For comparison, 3 vol% HF and H 2 O 2 were chemically polished, and then the ceramic films (1) and (2) were formed.
After the pickling treatment with ol% HCl, the cases where the ceramic films (1) and (2) were formed were also investigated. Table 3 shows the obtained results.
【００１８】[0018]
【表３】 [Table 3]
【００１９】同表に示したとおり、 (a) 本発明の高圧水
噴射による平滑化および (b)従来の化学研磨を施した後
にセラミック膜を被覆した場合の磁気特性はほとんど差
異がなく、極めて良好な鉄損値を呈していた。As shown in the table, (a) smoothing by high-pressure water jetting of the present invention and (b) magnetic properties when a ceramic film is coated after conventional chemical polishing are hardly different. A good iron loss value was exhibited.
【００２０】[0020]
【作用】本発明において、被処理材の鋼種については特
に限定されることはないが、製品段階および製造過程の
中途段階で平滑な表面が必要とされるステンレス鋼板、
低炭素冷延鋼板、 ＩＦ鋼板および一方向性珪素鋼板等が
有利に適合する。In the present invention, the steel type of the material to be treated is not particularly limited, but a stainless steel sheet which requires a smooth surface in the product stage and in the middle of the production process,
Low carbon cold rolled steel sheets, IF steel sheets and unidirectional silicon steel sheets are advantageously suitable.
【００２１】本発明では、高圧水の噴射に際し、射出圧
を 500〜5000気圧とすることおよび射出角を30〜70°に
することが不可欠であるが、その理由は次のとおりであ
る。まず、射出圧については、その値が 500気圧に満た
ないと表面研磨に長時間を有し、本発明の目的から逸脱
し、一方5000気圧を超えると射出角を如何に調整しよう
とも所期したほどの平滑性が得られなくなるからであ
る。また、射出角が30°に満たないと高圧水が鋼板上を
滑るようになって表面研磨効果がなくなるためであり、
一方70°を超えると射出圧を如何に調整しても良好な表
面状態が得られないからである。より好適な射出角は40
〜60°の範囲である。なお、前述したような、従来の高
圧水を用いた表面研削技術や切断技術では、高圧水の噴
射はほとんどの場合板面に対しほぼ垂直の方向から行わ
れ、若干傾斜させたとしても板面垂線に対し±15°程度
すなわち板面に対し75°以上傾斜させて行われていた。In the present invention, when injecting high-pressure water, it is essential to set the injection pressure to 500 to 5000 atm and the injection angle to 30 to 70 °, for the following reasons. First, as for the injection pressure, if the value is less than 500 atm, the surface polishing has a long time, deviating from the purpose of the present invention, while if it exceeds 5,000 atm, it is intended to adjust the injection angle no matter how. This is because such smoothness cannot be obtained. Also, if the injection angle is less than 30 °, high-pressure water will slide on the steel plate and the surface polishing effect will be lost,
On the other hand, if it exceeds 70 °, a good surface state cannot be obtained no matter how the injection pressure is adjusted. A better exit angle is 40
It is in the range of ~ 60 °. In the conventional surface grinding and cutting techniques using high-pressure water as described above, high-pressure water is almost always injected from a direction substantially perpendicular to the plate surface, and even if the plate surface is slightly inclined, It was performed at an angle of about ± 15 ° to the perpendicular, that is, at an angle of 75 ° or more to the plate surface.
【００２２】本発明に従い、射出角を鋼板に対し30〜70
°の範囲に調整することによって、極めて良好な平滑性
が得られる理由について、発明者らは次のように考えて
いる。すなわち、高圧水を板面に対し傾斜させて噴射す
ると、噴射水流の衝突面積が増大して衝突圧が緩和され
るだけでなく、噴射水流による切削力が鋼板表面の微小
凹凸部の山部に集中するためと考えている。また、高圧
水を傾斜させて噴射する際には、射出側および／または
被処理体を移動させることが好ましい。両者を移動させ
る場合、これらの移動方向がとくに限定されることはな
く、互いに同じ方向または逆方向であっても良く、また
互いに全く異なる方向に移動させても良い。さらに、鋼
板と高圧水の射出位置との間隔は50〜300 mm程度とする
のが好ましい。According to the present invention, the injection angle is set to 30 to 70 with respect to the steel plate.
The inventors consider the reason why extremely good smoothness can be obtained by adjusting the angle in the range of ° as follows. In other words, when high-pressure water is sprayed at an angle to the plate surface, not only the collision area of the jet water flow increases and the collision pressure is relieved, but also the cutting force due to the jet water flow is applied to the peaks of the minute irregularities on the steel sheet surface. Think to focus. When the high-pressure water is injected while being inclined, it is preferable to move the injection side and / or the object to be processed. When both are moved, their moving directions are not particularly limited, and they may be moved in the same direction or opposite directions, or may be moved in completely different directions. Further, the distance between the steel plate and the injection position of the high-pressure water is preferably about 50 to 300 mm.
【００２３】上記のようにして表面を平滑化した鋼板
は、そのまま使用してもよいし、またその上に腐食防
止、装飾用に各種のコーティングを施して良い。例え
ば、の膜なし一方向性珪素鋼板については、その後、
平滑表面に極薄のSi, Mn, Cr, Ni, Mo, Ｗ, Ｖ, Ti, N
b, Ta, Hf, Al, Cu, ZrおよびＢの窒化物、炭化物 、酸
化物のうちから選んだ１種または２種以上の張力付与型
のセラミック被膜を被成し、さらにはその上に重ねて張
力絶縁被膜を被成させることもできる。The steel sheet whose surface has been smoothed as described above may be used as it is, or may be coated thereon with various coatings for corrosion prevention and decoration. For example, for a film-oriented unidirectional silicon steel sheet,
Ultra-thin Si, Mn, Cr, Ni, Mo, W, V, Ti, N on smooth surface
b, Ta, Hf, Al, Cu, Zr and B nitride, carbide, oxide selected from the group consisting of oxides or oxides of two or more types, and further overlaid thereon To form a tension insulating coating.
【００２４】[0024]
【実施例】被処理材としては、次の４種類の鋼板（30×
300 mm）を準備した。 ステンレス鋼板（SUS430） Ｃ：0.02wt％、Si：0.20wt％、Mn：0.12wt％、Ｐ：0.01
1 wt％、Ｓ：0.014 wt％およびCr：18.7wt％を含有し、
残部は実質的にFeの組成になる連続鋳造スラブを、熱間
圧延後、冷間圧延して0.25mm厚の冷延板としたのち、 H2
ガス雰囲気中で光輝焼鈍したもの。 低炭素冷延鋼板 Ｃ：0.038 wt％、Si：0.016 wt％、Mn：0.43wt％、Ｐ：
0.009 wt％、Ｓ：0.012 wt％およびAl：0.004 wt％を含
有し、残部は実質的にFeの組成になる連続鋳造スラブ
を、熱間圧延後、冷間圧延して0.70mm厚の冷延板とした
のち、連続焼鈍したもの。 ＩＦ鋼 Ｃ： 0.003wt％、Si：0.004 wt％、Mn：0.011 wt％、
Ｐ：0.006 wt％、Ｓ：0.003 wt％、Al：0.001 wt％、
Ｎ：0.0012wt％およびＯ：0.0018wt％を含有し、残部は
実質的にFeの組成になる連続鋳造スラブを、熱間圧延
後、冷間圧延して 1.0mm厚の冷延板としたのち、連続焼
鈍したもの。 一方向性珪素鋼板（膜なし） Ｃ：0.072 wt％、Si：3.39wt％、Mn：0.073 wt％、Se：
0.020 wt％、Sb：0.025 wt％、Al：0.20wt％、Ｎ：0.00
77wt％およびMo：0.013 wt％を含有し、残部は実質的に
Feの組成になる連続鋳造スラブを、熱間圧延後、中間焼
鈍を挟む２回の冷間圧延を施して板厚：0.23mmの最終板
厚に仕上げたのち、線状溝を付与する磁区細分化処理
（幅：200 μm 、深さ：20μm 、間隔：４mm）を施し、
ついで、830 ℃の湿H2中で脱炭・１次際結晶焼鈍を行っ
たのち、鋼板表面に MgO（15wt％),Al2O3 (80wt％), C
aSiO3（５wt％) の組成になる焼鈍分離剤をスラリー塗
布してから、850 ℃で15時間の焼鈍後、850 ℃から12℃
／h の速度で1150℃まで昇温してゴス方位に強く集積し
た2 次再結晶粒を発達させたのち、 1220℃の乾H2中で純
化処理を施したもの。EXAMPLE The following four types of steel plates (30 ×
300 mm). Stainless steel plate (SUS430) C: 0.02wt%, Si: 0.20wt%, Mn: 0.12wt%, P: 0.01
1 wt%, S: 0.014 wt% and Cr: 18.7 wt%,
After the balance of the continuously cast slab consisting essentially composition Fe, after hot rolling, was 0.25mm thick cold-rolled sheet by cold rolling, H 2
Bright annealed in a gas atmosphere. Low carbon cold rolled steel sheet C: 0.038 wt%, Si: 0.016 wt%, Mn: 0.43 wt%, P:
A continuous cast slab containing 0.009 wt%, S: 0.012 wt% and Al: 0.004 wt%, with the balance being substantially Fe, is hot rolled, then cold rolled and cold rolled to 0.70 mm thick. After being made into a plate, it is continuously annealed. IF steel C: 0.003 wt%, Si: 0.004 wt%, Mn: 0.011 wt%,
P: 0.006 wt%, S: 0.003 wt%, Al: 0.001 wt%,
A continuously cast slab containing N: 0.0012 wt% and O: 0.0018 wt%, with the balance being substantially Fe, is hot-rolled and then cold-rolled into a cold-rolled sheet having a thickness of 1.0 mm. , Continuously annealed. Unidirectional silicon steel sheet (without film) C: 0.072 wt%, Si: 3.39 wt%, Mn: 0.073 wt%, Se:
0.020 wt%, Sb: 0.025 wt%, Al: 0.20 wt%, N: 0.00
Contains 77 wt% and Mo: 0.013 wt%, with the balance being substantially
A continuous cast slab having a Fe composition is hot-rolled and then subjected to two cold rolling steps with intermediate annealing to finish to a final thickness of 0.23 mm, and then to provide a magnetic domain subdivision for providing linear grooves. Processing (width: 200 μm, depth: 20 μm, interval: 4 mm)
Then, after performing the crystallization annealing decarburization and primary time in humidity of H 2 830 ℃, MgO (15wt%) on the surface of the steel sheet, Al 2 O 3 (80wt% ), C
After applying the annealed separating agent to the composition of aSiO 3 (5 wt%) in slurry, annealing at 850 ° C for 15 hours, then from 850 ° C to 12 ° C
/ And velocity heated to 1150 ° C. in a h After developed a secondary recrystallized grains accumulated strongly Goss orientation, the ones subjected to purification treatment in dry of H 2 1220 ° C..
【００２５】これら〜のサンプルを、前掲図１に示
すように配置した後、射出圧が3500気圧の高圧水のウォ
ータージェットを、板面に対し55°傾斜した射出角で噴
射しながら矢印の方向に移動させた（移動速度：3000mm
／min 、噴射幅：２mm) 。かような処理を施した後の鋼
板表面の表面粗さＲa および表面状況を、処理前の値と
比較して表４に示す。After arranging these samples as shown in FIG. 1 above, a high-pressure water jet having an injection pressure of 3500 atm was sprayed at an injection angle of 55 ° with respect to the plate surface in the direction of the arrow. (Moving speed: 3000mm
/ Min, injection width: 2 mm). Table 4 shows the surface roughness Ra and the surface condition of the steel sheet surface after such treatment in comparison with the values before the treatment.
【００２６】[0026]
【表４】 [Table 4]
【００２７】同表から明らかなように、本発明に従い、
高圧水の噴射を55°傾斜させて行った場合には、鋼板の
表面粗さが処理前に比べて格段に改善され、また鋼板の
形状は噴射前と全く変わらず良好な鋼板形状が得られて
いる。As is clear from the table, according to the present invention,
When the high-pressure water injection is performed at an angle of 55 °, the surface roughness of the steel sheet is remarkably improved compared to before the treatment, and the shape of the steel sheet is not changed at all, and a good steel sheet shape is obtained. ing.
【００２８】実施例２ Ｃ：0.076 wt％、Si：3.58wt％、Mn：0.078 wt％、Se：
0.020 wt％、Sb：0.025 wt％、Al：0.020 wt％、Ｎ：0.
076 wt％およびMo：0.012 wt％を含有し、残部は実質的
にFeの組成になる珪素鋼連鋳スラブを、 1340℃で５時間
の加熱処理後、熱間圧延を施して厚み：2.2 mmの熱延板
とした。ついで1000℃の均一化焼鈍を施した後、 1050℃
の中間焼鈍を挟む２回の冷間圧延を施して0.23mm厚の最
終冷延坂とした。ついで、最終冷延坂の表面に、アルキ
ド系樹脂を主成分とするエッチングレジストインキをグ
ラビアオフセット印刷により、非塗布部が圧延方向とほ
ぼ直角な方向に幅：200 μm 、圧延方向の間隔：４mmで
線状に残存するように塗布したのち、 200℃で約20秒間
焼付けた。このときのレジスト厚は２μm であった。こ
のようにしてエッチングレジストを塗布した鋼板に、電
解エッチングを施すことにより、幅：200 μm 、 深さ：
20μm の線状の溝を形成し、ついで有機溶剤中に浸漬し
てレジストを除去した。この時の電解エッチングは, Na
Cl電解液中で電流密度：10 A／dm2 、処理時間：20秒間
の条件で行った。ついで、 840℃の湿H2中で脱炭・１次
再結晶焼鈍を行った後、綱板表面にMgO（15wt％), A12
03 (75wt ％), CaSiO3 (10wt％) の組成になる焼鈍分
離剤をスラリー塗布し、ついで 850℃で15時間の焼鈍
後、 850℃から12℃／h の速度で1160℃まで昇温してゴ
ス方位に強く集積した２次再結晶粒を発達させた後、 12
20℃の乾H2中で純化処理を施した。Example 2 C: 0.076 wt%, Si: 3.58 wt%, Mn: 0.078 wt%, Se:
0.020 wt%, Sb: 0.025 wt%, Al: 0.020 wt%, N: 0.
A continuous cast steel slab containing 076 wt% and Mo: 0.012 wt%, with the balance being substantially Fe, was heated at 1340 ° C. for 5 hours and then hot-rolled to a thickness of 2.2 mm. Hot rolled sheet. Then, after subjecting to 1000 ° C uniform annealing, 1050 ° C
Was subjected to cold rolling twice with intermediate annealing being performed to obtain a final cold-rolled slope having a thickness of 0.23 mm. Then, on the surface of the final cold rolled hill, an etching resist ink containing an alkyd resin as a main component is gravure offset printed so that the non-applied portion has a width of approximately 200 μm in a direction almost perpendicular to the rolling direction, and a distance between the rolling directions of 4 mm. Then, it was baked at 200 ° C. for about 20 seconds. At this time, the resist thickness was 2 μm. By subjecting the steel sheet coated with the etching resist to electrolytic etching in this manner, the width: 200 μm and the depth:
A 20 μm linear groove was formed and then immersed in an organic solvent to remove the resist. The electrolytic etching at this time is
In a Cl electrolyte, the current density was 10 A / dm 2 , and the treatment time was 20 seconds. Then, after the decarburization and primary recrystallization annealing in wet of H 2 840 ℃, MgO (15wt%) on the steel plate surface, A1 2
A slurry of an annealing separator having a composition of 0 3 (75 wt%) and CaSiO 3 (10 wt%) is applied by slurry, and after annealing at 850 ° C. for 15 hours, the temperature is raised from 850 ° C. to 1160 ° C. at a rate of 12 ° C./h. To develop secondary recrystallized grains strongly integrated in the Goss orientation.
Purification was performed in dry H 2 at 20 ° C.
【００２９】かくして得られた膜なし珪素鋼板に対し、
射出圧が3000気圧の高圧水のウォータージェットを、板
面に対し60°傾斜した射出角で噴射しながら移動させた
（移動速度：3000mm／min 、噴射幅：２mm) 。その後、
マグネトロン・スパッタ法、ＨＣＤ法およびプラズマＣ
ＶＤ法を用いて、鋼板表面に種々のセラミック膜（0.7
〜1.1 μm)を被成した。また、比較のため、鋼板表面の
平滑化を従来法に従い、化学研磨および酸洗で行ったの
ち、同様の処理を行った。かくして得られた製品の磁気
特性について調べた結果を表５にまとめて示す。With respect to the silicon steel sheet without film thus obtained,
A water jet having an injection pressure of 3000 atm was moved while jetting at an injection angle of 60 ° with respect to the plate surface (moving speed: 3000 mm / min, jetting width: 2 mm). afterwards,
Magnetron sputtering method, HCD method and plasma C
Using the VD method, various ceramic films (0.7
1.11.1 μm). For comparison, the surface of the steel sheet was smoothed by chemical polishing and pickling according to a conventional method, and then subjected to the same treatment. Table 5 summarizes the results obtained by examining the magnetic properties of the products thus obtained.
【００３０】[0030]
【表５】 [Table 5]
【００３１】同表から明らかなように、この発明に従っ
て表面を研磨した場合は、従来の化学研磨を施した場合
と遜色のない優れた磁気特性が得られている。As is clear from the table, when the surface is polished according to the present invention, excellent magnetic properties are obtained, which are comparable to those obtained by conventional chemical polishing.
【００３２】[0032]
【発明の効果】かくして、本発明によれば、従来に比
べ、鋼板表面の研磨・平滑化を、極めて安価にしかも高
生産性の下で達成することができる。As described above, according to the present invention, polishing and smoothing of the surface of a steel sheet can be achieved at a very low cost and with high productivity as compared with the prior art.
【図１】鋼板表面に対する高圧水噴射流の移動要領を示
す模式図を示す図である。FIG. 1 is a diagram showing a schematic view showing a moving point of a high-pressure water jet flow with respect to a steel plate surface.
Claims (2)
気圧の高圧水を、板面に対し30〜70°傾斜した射出角で
噴射することを特徴とする鋼板の表面研磨方法。1. An injection pressure of 500 to 5000 against the surface of a steel sheet.
A method for polishing a surface of a steel sheet, wherein high-pressure water at an atmospheric pressure is injected at an injection angle inclined by 30 to 70 ° with respect to the plate surface.
が、ステンレス鋼板、低炭素冷延鋼板、 ＩＦ鋼板および
一方向性珪素鋼板のいずれかである鋼板の表面研磨方
法。2. The method for polishing a surface of a steel sheet according to claim 1, wherein the steel sheet to be treated is any one of a stainless steel sheet, a low-carbon cold-rolled steel sheet, an IF steel sheet, and a unidirectional silicon steel sheet.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP11053877A JP2000246640A (en) | 1999-03-02 | 1999-03-02 | Method of polishing surface of steel plate |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP11053877A JP2000246640A (en) | 1999-03-02 | 1999-03-02 | Method of polishing surface of steel plate |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JP2000246640A true JP2000246640A (en) | 2000-09-12 |
Family
ID=12954989
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP11053877A Withdrawn JP2000246640A (en) | 1999-03-02 | 1999-03-02 | Method of polishing surface of steel plate |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2000246640A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105150109A (en) * | 2015-08-24 | 2015-12-16 | 安徽正和橡塑合金有限公司 | Polyurethane screen framework sand blasting process |
-
1999
- 1999-03-02 JP JP11053877A patent/JP2000246640A/en not_active Withdrawn
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105150109A (en) * | 2015-08-24 | 2015-12-16 | 安徽正和橡塑合金有限公司 | Polyurethane screen framework sand blasting process |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| WO1986004929A1 (en) | Process for producing unidirectional silicon steel plate with extraordinarily low iron loss | |
| JP2000246640A (en) | Method of polishing surface of steel plate | |
| JPH0699824B2 (en) | Thermally stable ultra-low iron loss unidirectional silicon steel sheet and method for producing the same | |
| CN113166875B (en) | Electrical steel sheet and method for manufacturing same | |
| JPH02243754A (en) | Production of grain-oriented silicon steel sheet reduced in iron loss | |
| JP4016756B2 (en) | Method for producing grain-oriented electrical steel sheet | |
| JP4300604B2 (en) | Ultra-low iron loss unidirectional silicon steel sheet and manufacturing method thereof | |
| JPH1112755A (en) | Super-low core loss grain-oriented silicon steel sheet | |
| JP2004060029A (en) | Method for manufacturing super low core loss grain oriented magnetic steel sheet having excellent film adhesion | |
| JPH11286775A (en) | Production of ultralow core loss grain-oriented silicon steel sheet | |
| JPH11343579A (en) | Extremely low iron loss grain-oriented silicon steel sheet and its production | |
| JPH11329819A (en) | Ultra-small core loss unidirectional silicon steel plate | |
| JPS621820A (en) | Grain oriented silicon steel sheet having thermal stability and ultra-low iron loss | |
| JPS63192855A (en) | Production of low carbon steel sheet and stainless steel sheet coated with ceramic film having superior adhesion, uniformity and corrosion resistance | |
| JPH0375354A (en) | Production of grain-oriented silicon steel sheet with superlow iron loss free from deterioration in characteristic due to stress relief annealing | |
| JP4042202B2 (en) | Unidirectional silicon steel sheet | |
| JPH08283866A (en) | Production of grain-oriented silicon steel sheet and coater for separation agent for annealing | |
| JPS6230302A (en) | Manufacture of super-low iron loss unidirectional silicon steel plate | |
| JP3280898B2 (en) | Ultra-low iron loss unidirectional silicon steel sheet | |
| JPS621822A (en) | Production of grain oriented silicon steel sheet having thermal stability and ultra-low iron loss | |
| JP2004027348A (en) | Method for manufacturing ultra-low-iron loss grain-oriented silicon steel plate having excellent film adhesion property | |
| JP2002080959A (en) | Method for producing extra-low core loss grain oriented silicon steel plate excellent in film stickness without deteriorating characteristic after stress relieving annealing | |
| JPH0327633B2 (en) | ||
| JP2002129309A (en) | Single directional, ultra low iron loss silicon steel sheets and strips eliminating deterioration of iron loss after strain annealing and having superior coating adhesion and manufacturing method for the same | |
| JP2001303235A (en) | ULTRA LOW CORE-LOSS GRAIN ORIENTED SILICON STEEL SHEET HAVING SiNX CERAMIC THIN FILM EXCELLENT IN FILM CHARACTERISTIC, AND ITS MANUFACTURING METHOD |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A300 | Withdrawal of application because of no request for examination |
Free format text: JAPANESE INTERMEDIATE CODE: A300 Effective date: 20060509 |