JP2007146236A - Surface treated steel sheet for liquid crystal front frame, its production method and liquid crystal front frame produced by the production method - Google Patents
Surface treated steel sheet for liquid crystal front frame, its production method and liquid crystal front frame produced by the production method Download PDFInfo
- Publication number
- JP2007146236A JP2007146236A JP2005342829A JP2005342829A JP2007146236A JP 2007146236 A JP2007146236 A JP 2007146236A JP 2005342829 A JP2005342829 A JP 2005342829A JP 2005342829 A JP2005342829 A JP 2005342829A JP 2007146236 A JP2007146236 A JP 2007146236A
- Authority
- JP
- Japan
- Prior art keywords
- liquid crystal
- front frame
- crystal front
- steel sheet
- treated steel
- 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- Withdrawn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
Abstract
Description
本発明は、液晶を固定するために使われる液晶フロントフレーム用表面処理鋼板、その製造方法およびその製造方法により製造された液晶フロントフレームに関する。 The present invention relates to a surface-treated steel sheet for a liquid crystal front frame used for fixing a liquid crystal, a manufacturing method thereof, and a liquid crystal front frame manufactured by the manufacturing method.
現在、ディスプレイとして、ＣＲＴ（Cathode Ray Tube）、ＰＤＰ（Plasma Display Panel）や液晶タイプなどが実用化されている。これらのディスプレイ間では、価格面あるいは特性面での競争が激しくなっている。液晶タイプに使われる液晶フロントフレームは、液晶、ガラス、光学部品及び光学フィルムを固定する枠として使われていて、力を加えても変形しにくい特性が要求されるため、高強度のステンレス鋼板が使われているが、高価であり、不経済である。また、ステンレス鋼板の代わりに冷延鋼板に表面処理した表面処理鋼板を使うことが考えられるが、機械強度の点で問題があり、それなりの強度を選るには板厚を厚くする方法があるが、軽量化できない。機械強度を向上する方法として、再結晶温度以上に加熱した後、急冷する方法が開示されている（例えば、特許文献１参照。）。この場合、急冷するため、急冷後、冷延鋼板にそりが発生し、平坦性の点で問題がある。 Currently, CRT (Cathode Ray Tube), PDP (Plasma Display Panel), liquid crystal type, and the like are put into practical use as displays. Among these displays, competition in terms of price or characteristics is intensifying. The liquid crystal front frame used in the liquid crystal type is used as a frame for fixing liquid crystal, glass, optical components and optical films, and is required to have the property of being difficult to deform even when force is applied. Used, but expensive and uneconomical. Although it is conceivable to use a surface-treated steel sheet that has been surface-treated on a cold-rolled steel sheet instead of a stainless steel sheet, there is a problem in terms of mechanical strength. However, it cannot be reduced in weight. As a method for improving the mechanical strength, a method of rapidly cooling after heating to a recrystallization temperature or higher is disclosed (for example, see Patent Document 1). In this case, because of rapid cooling, warpage occurs in the cold-rolled steel sheet after rapid cooling, and there is a problem in terms of flatness.
本出願に関する先行技術文献情報として次のものがある。
本発明の目的は、安価で、機械的強度に優れかつ軽量な液晶フロントフレーム用表面処理鋼板及び液晶フロントフレームを提供することを目的とする。 An object of the present invention is to provide a surface-treated steel sheet for a liquid crystal front frame and a liquid crystal front frame that are inexpensive, excellent in mechanical strength, and lightweight.
上記目的を達成するため、請求項１に記載の液晶フロントフレーム用表面処理鋼板は、重量％で、Ｃ：０．０９〜０．１５％、Ｓｉ：≦０．０３％、Ｍｎ：０．２５〜０．６０％、Ｐ：≦０．０３％、Ｓ：≦０．０５％、Ａｌ：０．０３〜０．１％、Ｎ：０．００１０〜０．０１５０％、残部Ｆｅおよび不可避的な不純物よりなる鋼板の表面に表面処理層を有することを特徴とする。
請求項２に記載の液晶フロントフレーム用表面処理鋼板の製造方法は、重量％で、Ｃ：０．０９〜０．１５％、Ｓｉ：≦０．０３％、Ｍｎ：０．２５〜０．６０％、Ｐ：≦０．０３％、Ｓ：≦０．０５％、Ａｌ：０．０３〜０．１％、Ｎ：０．００１０〜０．０１５０％、残部Ｆｅおよび不可避的な不純物よりなる連続鋳造鋳片を、熱間圧延、酸洗、圧延率が７５％以上の冷間圧延、焼鈍、調質圧延し、更に表面にＺｎまたはＮｉめっきを施すことを特徴とする。
請求項３に記載の液晶フロントフレームは、前記液晶フロントフレーム用表面処理鋼板を用いて製造されることを特徴とする。
請求項４に記載の前記液晶フロントフレーム用表面処理鋼板の製造方法を用いて製造される液晶フロントフレームであることを特徴とする。
In order to achieve the above object, the surface-treated steel sheet for a liquid crystal front frame according to claim 1 is C: 0.09 to 0.15%, Si: ≦ 0.03%, Mn: 0.25 by weight%. ~ 0.60%, P: ≤0.03%, S: ≤0.05%, Al: 0.03-0.1%, N: 0.0010-0.0150%, balance Fe and inevitable It has a surface treatment layer on the surface of a steel plate made of impurities.
The method for producing a surface-treated steel sheet for a liquid crystal front frame according to claim 2 is, in wt%, C: 0.09 to 0.15%, Si: ≤ 0.03%, Mn: 0.25 to 0.60. %, P: ≦ 0.03%, S: ≦ 0.05%, Al: 0.03-0.1%, N: 0.0010-0.0150%, the balance consisting of Fe and unavoidable impurities The cast slab is subjected to hot rolling, pickling, cold rolling with a rolling rate of 75% or more, annealing, temper rolling, and further Zn or Ni plating is performed on the surface.
The liquid crystal front frame according to claim 3 is manufactured using the surface-treated steel sheet for the liquid crystal front frame.
It is a liquid crystal front frame manufactured using the manufacturing method of the surface-treated steel sheet for a liquid crystal front frame according to claim 4.
本発明の液晶フロントフレーム用鋼板は、安価で、機械的強度に優れるため、薄ゲージ化が可能であるため、安価な液晶フロントフレームを提供できる。 Since the steel plate for a liquid crystal front frame of the present invention is inexpensive and excellent in mechanical strength and can be made thinner, an inexpensive liquid crystal front frame can be provided.
以下、本発明の実施の形態を詳細に説明する。 Hereinafter, embodiments of the present invention will be described in detail.
液晶フロントフレーム用表面処理鋼板の鋼成分
本発明の液晶フロントフレーム用表面処理鋼板の鋼成分は、重量％で、Ｃ：０．０９〜０．１５％、Ｓｉ：≦０．０３％、Ｍｎ：０．２５〜０．６０％、Ｐ：≦０．０３％、Ｓ：≦０．０５％、Ａｌ：０．０３〜０．１％、Ｎ：０．００１０〜０．０１５０％、残部Ｆｅおよび不可避的な不純物よりなる。
Steel component of surface-treated steel sheet for liquid crystal front frame The steel composition of the surface-treated steel sheet for liquid crystal front frame of the present invention is C: 0.09 to 0.15%, Si: ≦ 0.03%, Mn: 0.25-0.60%, P: ≦ 0.03%, S: ≦ 0.05%, Al: 0.03-0.1%, N: 0.0010-0.0150%, balance Fe and Consists of inevitable impurities.
Ｃは液晶フロントフレーム表面処理鋼板に高い調質度に加えるため、 Ｃは０．０９重量％以上あることが望ましい。一方でＣ成分が０．１５重量％を超えると炭化物析出量が増大し、鋼板の加工性の低下をもたらすと同時に、冷間圧延の負荷の増大、形状の劣化、連続焼鈍工程での通板性阻害等、生産性低下の原因となる。そのため本発明ではＣ成分の上限値を０．１５重量％とする。 Since C is added to the high tempering degree of the liquid crystal front frame surface-treated steel sheet, C is preferably 0.09% by weight or more. On the other hand, if the C component exceeds 0.15% by weight, the amount of carbide precipitation increases, resulting in a decrease in workability of the steel sheet, and at the same time, an increase in cold rolling load, shape deterioration, and sheet passing in a continuous annealing process. Cause a decrease in productivity. Therefore, in the present invention, the upper limit value of the C component is set to 0.15% by weight.
Ｍｎは不純物であるＳによる熱延中の赤熱脆性を防止するために必要な成分であると同時に、上記のＣと同様に鋼板に高い調質度を与えるため、Ｍｎ成分は０．２５重量％以上とする。しかし、ここでもＣ同様に、多過ぎると冷間圧延の負荷の増大、スラブ圧延中の割れ発生、形状の劣化、連続焼鈍工程での通板性阻害等、生産性低下の原因となるため、上限値を０．６０重量％とする。 Mn is a component necessary for preventing red heat embrittlement during hot rolling due to the impurity S, and at the same time, in the same manner as C, in order to give a high tempering degree to the steel sheet, the Mn component is 0.25% by weight. That's it. However, as is the case with C here, too much load of cold rolling, crack generation during slab rolling, deterioration of shape, threadability hindrance in continuous annealing process, etc., cause productivity reduction, The upper limit is 0.60% by weight.
Ｐは結晶粒微細化成分であり、また鋼板の強度を高めることから一定の割合で添加されるが、一方で耐食性を阻害する。本発明の用途としては、Ｐが０．０３重量％を超えると耐食性、特に耐孔明性が著しく低下するため上限値を０．０３重量％とする。 P is a crystal grain refining component and is added at a certain ratio because it increases the strength of the steel sheet, but it inhibits corrosion resistance. As an application of the present invention, when P exceeds 0.03% by weight, the corrosion resistance, particularly the hole resistance is remarkably lowered, so the upper limit is set to 0.03% by weight.
Ｓは熱延中において赤熱脆性を生じる不純物成分であり、極力少ないことが望ましいが、鉄鋼石等からの混入を完全に防止することができず、工程中の脱硫も困難なことからある程度の残留もやむをえない。少量の残留Ｓによる赤熱脆性はＭｎにより軽減できるため、Ｓ成分の上限値は０．０５重量％とする。 S is an impurity component that causes red-hot brittleness during hot rolling, and it is desirable that S be as small as possible. Unavoidable. Since red heat brittleness due to a small amount of residual S can be reduced by Mn, the upper limit of the S component is set to 0.05% by weight.
Ａｌは製鋼に際し脱酸剤として鋼浴中に添加されるが、０．１重量％を超えると連続鋳造時に酸化抑制剤、および、連続鋳造での鋳型への焼き付き防止剤として使用する鋳型パウダー中の酸素と過剰Ａｌが反応し、本来のパウダー効果を阻害する。したがって、Ａｌ量は０．１０重量％以下とする。 Al is added to the steel bath as a deoxidizer during steelmaking, but if it exceeds 0.1% by weight, it is contained in the mold powder used as an oxidation inhibitor during continuous casting and as an anti-seizure agent on the mold in continuous casting. Oxygen and excess Al react to inhibit the original powder effect. Therefore, the Al amount is 0.10% by weight or less.
ＮはＣ、Ｍｎと同様に鋼板に高い調質度を与える。耐力強化のために必要な成分であるが、０．００１重量％未満とすることは製鋼上の困難を生じ、また一方０．０１５０重量％を超える添加は製鋼時に添加するフェロ窒化物の歩留の低下が著しく、安定性に欠けると同時に、成形時の異方性を著しく劣化させる。さらに連続鋳造片の表面に割れが生じ、鋳造欠陥となるため、本発明においてはＮ成分範囲を０．００１〜０．０１５０重量％とする。より望ましくは０．００２１〜０．０１５０重量％とする。 N, like C and Mn, gives a high tempering degree to the steel sheet. Although it is a necessary component for strengthening the proof stress, if it is less than 0.001% by weight, it will cause difficulty in steelmaking, while if it exceeds 0.0150% by weight, the yield of ferronitride added during steelmaking Is significantly deteriorated, and the stability at the same time is deteriorated. Furthermore, cracks are generated on the surface of the continuous cast piece, resulting in casting defects. Therefore, in the present invention, the N component range is set to 0.001 to 0.0150% by weight. More desirably, the content is 0.0021 to 0.0150% by weight.
Ｓｉは多く含まれると耐食性の点で問題があり、０，０３重量％以下とする。 If a large amount of Si is contained, there is a problem in terms of corrosion resistance, and the content is made 0.03 wt% or less.
熱間圧延
熱間圧延工程における鋼片加熱温度は本発明において特定するものではないが、Ｎの積極的分解固溶および熱間仕上圧延温度の安定的確保の見地から８００℃以上とするのが望ましい。熱間圧延仕上温度を８００℃未満にすると、熱間鋼帯の結晶組織が混粒化するとともに粗大化し、目的の強度が得られないので熱間圧延仕上温度は８００℃以上とするのが望ましい。
Hot rolling Steel slab heating temperature in the hot rolling process is not specified in the present invention, but it should be 800 ° C. or higher from the standpoint of positive decomposition and dissolution of N and stable securing of the hot finish rolling temperature. desirable. When the hot rolling finishing temperature is less than 800 ° C., the crystal structure of the hot steel strip is mixed and coarsened, and the desired strength cannot be obtained. Therefore, the hot rolling finishing temperature is preferably 800 ° C. or more. .
巻き取り温度は４００℃〜６５０℃とする。熱延時のコイルの幅方向および長手方向の品質安定性を考慮して４００℃を下限とする。また、巻取温度が６５０℃を超えると、熱延時および連続焼鈍時で結晶粒径が大きくなり、加工時の不良原因となるため、巻取温度は６５０℃以下とするのが望ましい。 The winding temperature is 400 ° C to 650 ° C. In consideration of the quality stability in the width direction and the longitudinal direction of the coil during hot rolling, 400 ° C. is set as the lower limit. Further, if the coiling temperature exceeds 650 ° C., the crystal grain size becomes large during hot rolling and continuous annealing, which causes a defect during processing. Therefore, the coiling temperature is preferably 650 ° C. or less.
冷間圧延
上記の成分系で熱延された鋼板を冷間圧延するが、この冷間圧延率は、成分とともに本発明の重要な強度因子であり、目的の強度を得るために、７５％以上で行う。７５％未満では、強度不足となりやすい。
Cold Rolling A steel sheet hot-rolled with the above component system is cold-rolled, and this cold rolling rate is an important strength factor of the present invention together with the components. In order to obtain the desired strength, 75% or more To do. If it is less than 75%, the strength tends to be insufficient.
焼鈍
上記のように冷間圧延率７５％以上の冷間圧延を施した材料は、クリーニング工程で脱脂を施した後、６００〜７２０℃で３０秒から１０分連続焼鈍を行う。または、５００〜５８０℃で１〜８時間箱型焼鈍を行う。これらの焼鈍時間は再結晶される範囲内であれば十分である。特に板厚０．６ｍｍ以下の場合は、連続焼鈍が望ましく、板厚０．６ｍｍを超えた場合、箱型焼鈍が望ましい。
Annealing The material subjected to cold rolling with a cold rolling ratio of 75% or more as described above is subjected to degreasing in the cleaning step, and then subjected to continuous annealing at 600 to 720 ° C. for 30 seconds to 10 minutes. Alternatively, box annealing is performed at 500 to 580 ° C. for 1 to 8 hours. It is sufficient that these annealing times are within the range to be recrystallized. In particular, when the thickness is 0.6 mm or less, continuous annealing is desirable, and when the thickness exceeds 0.6 mm, box annealing is desirable.
調質圧延
焼鈍後に圧延率１〜２％の調質圧延を施す。調質圧延の際、必要により表面粗度を付与する。圧延率が１％未満だと、ストレッチャーストレインが発生しやすく、逆に２％を超えると、加工性が劣化し、問題がある。
Temper Rolling After annealing, temper rolling with a rolling rate of 1-2% is performed. During temper rolling, surface roughness is imparted if necessary. If the rolling rate is less than 1%, stretcher strain tends to occur. Conversely, if it exceeds 2%, the workability deteriorates and there is a problem.
つぎに、このようにして作成した本発明の鋼板としては、シ−ト状およびコイル状の鋼板に表面処理を施したものがあげられる。特に、表面処理として、亜鉛めっき、ニッケル、コバルト、鉄、アルミニウム、マグネシウムあるいはモリブデンの１種あるいは２種以上含んだ亜鉛合金めっき、ニッケルめっき、ニッケル合金めっきを施したもの、あるいは更にこれらのめっき表面に有機物あるいは無機物を含んだ処理液で処理したものが使える。亜鉛または亜鉛合金めっき方法として電気めっき法、溶融めっき法あるいは真空蒸着めっき法が適用できる。 Next, examples of the steel sheet of the present invention thus prepared include those obtained by surface-treating sheet-shaped and coil-shaped steel sheets. In particular, as surface treatment, zinc plating, nickel alloy plating containing one or more of nickel, cobalt, iron, aluminum, magnesium or molybdenum, nickel plating, nickel alloy plating, or further these plating surfaces Those treated with a treatment solution containing organic or inorganic substances can be used. As the zinc or zinc alloy plating method, an electroplating method, a hot dipping method or a vacuum deposition plating method can be applied.
有機物を含んだ処理液として、ウレタン系樹脂、ポリテトラフルオロエチレン及びコロイダルシリカを含んだ溶液、あるいはウレタン系樹脂、アミン系防腐剤及びコロイダルシリカを含んだ溶液を用いることができる。下層が金属クロム、上層がクロム水和酸化物の２層構造をもつ電解クロム酸処理鋼板あるいは錫めっき鋼板も適用できる。
無機物を含んだ処理液として、ケイ酸またはケイ酸塩と水酸化リチウムを含んだ溶液、リン酸亜鉛などのリン酸塩を含んだ溶液あるいはクロム酸を含んだ溶液を用いることができる。
有機物あるいは無機物を含んだ処理液を用いて処理する場合、浸漬方法、浸漬後絞りを行う方法、ロールコート方法、スプレーコート法等公知の処理方法が適用できる。クロム酸を含んだ溶液で処理する場合、電解処理により行っても良い。
As the treatment liquid containing an organic substance, a solution containing a urethane resin, polytetrafluoroethylene and colloidal silica, or a solution containing a urethane resin, an amine preservative and colloidal silica can be used. An electrolytic chromic acid-treated steel sheet or tin-plated steel sheet having a two-layer structure in which the lower layer is metallic chromium and the upper layer is chromium hydrated oxide can also be applied.
As the treatment liquid containing an inorganic substance, a solution containing silicic acid or silicate and lithium hydroxide, a solution containing a phosphate such as zinc phosphate, or a solution containing chromic acid can be used.
When processing using the processing liquid containing an organic substance or an inorganic substance, a known processing method such as an immersion method, a method of drawing after immersion, a roll coating method, or a spray coating method can be applied. When processing with a solution containing chromic acid, it may be performed by electrolytic treatment.
本発明である実施例と比較例について、表１に鋼成分と圧延率などの製造条件を示し、表２にその特性評価結果を示す。実施例１〜４と比較例１は鋼片を熱間圧延、酸洗、冷間圧延、連続焼鈍、調質圧延して、表面処理を行った。表１において、仕上温度及び巻取温度は、熱間圧延条件であり、圧延率は、冷間圧延時の圧延率であり、加熱温度は連続焼鈍時の均熱温度である。均熱温度は５０秒間保持した。表面処理として、亜鉛ー１重量％コバルトー０．１重量％モリブデンめっきを両面に１０ｇ／ｍ２行い、水系ウレタン樹脂を固形分として３００ｇ／Ｌ、アミン系防錆剤を５０ｇ／Ｌ、水分散シリカを２５０ｇ／Ｌを含んだ処理液に亜鉛ー１重量％コバルトー０．１重量％モリブデンめっきした鋼板を浸漬した。浸漬後ロールで絞って、乾燥後の厚みが０．５μｍとなるように９０℃で乾燥し、表面処理鋼板を得た。 About the Example and comparative example which are this invention, Table 1 shows manufacturing conditions, such as a steel component and a rolling rate, and Table 2 shows the characteristic evaluation result. In Examples 1 to 4 and Comparative Example 1, the steel pieces were subjected to surface treatment by hot rolling, pickling, cold rolling, continuous annealing, and temper rolling. In Table 1, the finishing temperature and the coiling temperature are hot rolling conditions, the rolling rate is the rolling rate during cold rolling, and the heating temperature is the soaking temperature during continuous annealing. The soaking temperature was maintained for 50 seconds. As surface treatment, zinc 1wt% cobalt-0.1wt% molybdenum plating is performed on both sides at 10g / m2, 300g / L of water-based urethane resin as solid content, 50g / L of amine-based rust inhibitor, water-dispersed silica A steel plate plated with zinc-1 wt% cobalt-0.1 wt% molybdenum was immersed in a treatment solution containing 250 g / L. After dipping, the film was squeezed with a roll and dried at 90 ° C. so that the thickness after drying was 0.5 μm to obtain a surface-treated steel sheet.
機械特性の評価
実施例１〜４と比較例１〜２について、ＪＩＳ５号試験片にして、表２に示すＹｐ（降伏点強度）、ＴＳ（抗張力）、ＴＥｌ（伸び）を測定した。
硬度（ＨＲ−３０Ｔ）の測定
ロックウエル硬度計でＨＲ−３０Ｔを測定した。
Evaluation of Mechanical Properties For Examples 1-4 and Comparative Examples 1-2, Yp (yield point strength), TS (tensile strength), and TEl (elongation) shown in Table 2 were measured using JIS No. 5 test pieces.
Measurement of Hardness (HR-30T) HR-30T was measured with a Rockwell hardness meter.
表１と表２より、実施例１〜４は、従来材ステンレス鋼板（比較例２）と比べてＴＳ（抗張力）が同等であり、高強度で優れた材料特性を有する。従って、実施例１〜４は液晶フロントフレームとして適用できる。比較例１は、強度（ＴＳ）が従来のステンレス鋼板である比較例２より小さく、液晶フロントフレームとして適用できない。比較例２は従来材であるステンレス鋼板の場合を示す。 From Table 1 and Table 2, Examples 1-4 have equivalent TS (tensile strength) compared with the conventional stainless steel plate (Comparative Example 2), and have high strength and excellent material properties. Therefore, Examples 1 to 4 can be applied as a liquid crystal front frame. Comparative Example 1 has a lower strength (TS) than Comparative Example 2, which is a conventional stainless steel plate, and cannot be applied as a liquid crystal front frame. The comparative example 2 shows the case of the stainless steel plate which is a conventional material.
本発明の液晶フロントフレーム用表面処理鋼板は機械的特性に優れ、液晶フロントフレームとして使用できる。高価なステンレス鋼板の代替として使用可能なので、安価な液晶フロントフレームが提供できる。
The surface-treated steel sheet for a liquid crystal front frame of the present invention is excellent in mechanical properties and can be used as a liquid crystal front frame. Since it can be used as an alternative to an expensive stainless steel plate, an inexpensive liquid crystal front frame can be provided.
Claims (4)
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2005342829A JP2007146236A (en) | 2005-11-28 | 2005-11-28 | Surface treated steel sheet for liquid crystal front frame, its production method and liquid crystal front frame produced by the production method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2005342829A JP2007146236A (en) | 2005-11-28 | 2005-11-28 | Surface treated steel sheet for liquid crystal front frame, its production method and liquid crystal front frame produced by the production method |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JP2007146236A true JP2007146236A (en) | 2007-06-14 |
Family
ID=38207994
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2005342829A Withdrawn JP2007146236A (en) | 2005-11-28 | 2005-11-28 | Surface treated steel sheet for liquid crystal front frame, its production method and liquid crystal front frame produced by the production method |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2007146236A (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100982387B1 (en) * | 2009-04-30 | 2010-09-14 | 삼성전자주식회사 | Bottom chassis for thin film transistor liquid crystal display device |
| KR100982382B1 (en) * | 2009-04-30 | 2010-09-14 | 삼성전자주식회사 | Thin film transistor liquid crystal display device |
| CN106521311A (en) * | 2016-10-28 | 2017-03-22 | 首钢总公司 | Bell-annealing tin plate and preparation method thereof |
| CN114058946A (en) * | 2021-10-14 | 2022-02-18 | 首钢集团有限公司 | Low-anisotropy high-strength high-elongation steel substrate, tin-plated plate and preparation method of tin-plated plate |
-
2005
- 2005-11-28 JP JP2005342829A patent/JP2007146236A/en not_active Withdrawn
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100982387B1 (en) * | 2009-04-30 | 2010-09-14 | 삼성전자주식회사 | Bottom chassis for thin film transistor liquid crystal display device |
| KR100982382B1 (en) * | 2009-04-30 | 2010-09-14 | 삼성전자주식회사 | Thin film transistor liquid crystal display device |
| JP2010262286A (en) * | 2009-04-30 | 2010-11-18 | Hyundai Hysco | Thin film transistor liquid crystal display |
| JP2010266863A (en) * | 2009-04-30 | 2010-11-25 | Hyundai Hysco | Bottom chassis for thin film transistor liquid crystal display element and method for manufacturing the same |
| CN106521311A (en) * | 2016-10-28 | 2017-03-22 | 首钢总公司 | Bell-annealing tin plate and preparation method thereof |
| CN114058946A (en) * | 2021-10-14 | 2022-02-18 | 首钢集团有限公司 | Low-anisotropy high-strength high-elongation steel substrate, tin-plated plate and preparation method of tin-plated plate |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| TWI467027B (en) | High strength galvanized steel sheet | |
| JP4804996B2 (en) | Method for producing alloyed hot-dip galvanized steel sheet with good workability, powdering property and slidability | |
| WO2013047810A1 (en) | Alloyed hot-dip galvanized steel sheet | |
| JP2022514847A (en) | High-strength galvanized steel sheet with excellent electrical resistance spot weldability and its manufacturing method | |
| WO2018220873A1 (en) | HIGH-STRENGTH Zn-Al-Mg-BASED SURFACE-COATED STEEL SHEET AND METHOD FOR PRODUCING SAME | |
| JP2017133080A (en) | Oriented electromagnetic steel sheet and manufacturing method therefor | |
| WO2017110030A1 (en) | High strength hot dip hot-rolled steel sheet and manufacturing method therefor | |
| WO2018142849A1 (en) | High-strength molten zinc plating hot-rolled steel sheet, and production method therefor | |
| JP2009249714A (en) | Method for producing hot-rolled steel sheet excellent in surface-processing property | |
| JP2007146236A (en) | Surface treated steel sheet for liquid crystal front frame, its production method and liquid crystal front frame produced by the production method | |
| JP4720618B2 (en) | Alloyed hot-dip galvanized steel sheet and method for producing the same | |
| JP2006283070A (en) | Method for producing galvannealed steel sheet having good workability | |
| JP2019026893A (en) | High strength steel sheet excellent in delayed fracture resistance and corrosion resistance | |
| JP5309862B2 (en) | Steel material excellent in chemical conversion treatment after member processing and manufacturing method thereof | |
| JP2003328099A (en) | Production method for high-strength hot-dip galvanized steel sheet | |
| JP6137436B2 (en) | Steel plate for can and manufacturing method thereof | |
| JP2007321180A (en) | Surface-treated steel sheet for cover material for optical pickup parts, its manufacturing method, and cover material for optical pickup parts manufactured by the manufacturing method | |
| JP2007146235A (en) | Surface treated steel sheet for liquid crystal front frame, its manufacturing method, and liquid crystal front frame manufactured by the manufacturing method | |
| JP2007146234A (en) | Surface treated steel sheet for liquid crystal front frame, its production method and liquid crystal front frame produced by the production method | |
| JP6436268B1 (en) | Method for producing high-strength hot-dip galvanized steel sheet with excellent plating adhesion | |
| JP5434040B2 (en) | Manufacturing method of high formability and high strength steel sheet with excellent chemical conversion | |
| JP2007169732A (en) | Surface treated steel sheet for gasket material of plasma television, method for manufacturing the same, and gasket material for plasma television manufactured by the manufacturing method | |
| JP2006307260A (en) | Steel sheet for plasma display fixing plate, method for producing steel sheet for fixing plasma display, and plasma display fixing plate | |
| JP2019031728A (en) | HIGH STRENGTH Zn-Al-Mg BASED SURFACE COATED STEEL SHEET FOR BUILDING COMPONENT AND BUILDING COMPONENT USING THE SAME | |
| JP2019031727A (en) | HIGH-STRENGTH Zn-Al-Mg-BASED SURFACE-COATED STEEL SHEET FOR AUTOMOBILE COMPONENTS AND AUTOMOBILE COMPONENTS USING THE SAME |
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: 20090203 |