JP2007146235A - Surface treated steel sheet for liquid crystal front frame, its manufacturing method, and liquid crystal front frame manufactured by the manufacturing method - Google Patents
Surface treated steel sheet for liquid crystal front frame, its manufacturing method, and liquid crystal front frame manufactured by the manufacturing method Download PDFInfo
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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.
前記目的を達成するため、請求項１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：０．０３〜０．２０％、Ｓｉ：≦０．５％、Ｍｎ：０．５〜３．０％、Ｐ：≦０．１％、Ｓ：≦０．０６％、Ａｌ：≦０．１％、Ｎ：０．００１０〜０．０１６０％、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。この場合、前記鋼板が、重量％で、Ｔｉ：０．０１〜０．２％、Ｎｂ：０．０５〜０．１％およびＢ：０．００１〜０．０１％の内、１種または２種を更に含有することが望ましい。さらに、また、平均粒径が５μｍ〜１２μｍのフェライトと、平均粒径が５μｍ以下のマルテンサイトであって体積率が３０％以下のマルテンサイトからなる組織を有することが望ましい。さらに、前記表面処理層がＺｎまたはＮｉめっきであることが望ましい。
請求項５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：０．０３〜０．２０％、Ｓｉ：≦０．５％、Ｍｎ：０．５〜３．０％、Ｐ：≦０．１％、Ｓ：≦０．０６％、Ａｌ：≦０．１％、Ｎ：０．００１０〜０．０１６０％、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、平均結晶粒径が５μｍ以下になるように熱間圧延し、酸洗後、圧延率が３０〜９０％の冷間圧延を施し、更にその表面に表面処理層を施すことを特徴とする。
In order to achieve the object, the surface-treated steel sheet for a liquid crystal front frame according to claim 1 is, by weight percent, C: 0.03 to 0.20%, Si: ≤ 0.5%, Mn: 0.5 to Steel plate comprising 3.0%, P: ≦ 0.1%, S: ≦ 0.06%, Al: ≦ 0.1%, N: 0.0010 to 0.0160%, balance Fe and inevitable impurities It has a surface treatment layer on the surface. In this case, the steel sheet is, by weight, Ti: 0.01-0.2%, Nb: 0.05-0.1%, and B: 0.001-0.01%, one or two. It is desirable to further contain seeds. Furthermore, it is desirable to have a structure composed of ferrite having an average particle diameter of 5 μm to 12 μm and martensite having an average particle diameter of 5 μm or less and a volume ratio of 30% or less. Furthermore, it is desirable that the surface treatment layer is Zn or Ni plating.
The method for producing a surface-treated steel sheet for a liquid crystal front frame according to claim 5 is, in wt%, C: 0.03 to 0.20%, Si: ≤ 0.5%, Mn: 0.5 to 3.0%. , P: ≦ 0.1%, S: ≦ 0.06%, Al: ≦ 0.1%, N: 0.0010 to 0.0160%, the remaining cast iron and the inevitable impurities. The steel sheet is hot-rolled so that the average crystal grain size is 5 μm or less, pickled, then cold-rolled with a rolling rate of 30 to 90%, and further provided with a surface treatment layer on the surface.
請求項６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：０．０３〜０．２０％、Ｓｉ：≦０．５％、Ｍｎ：０．５〜３．０％、Ｐ：≦０．１％、Ｓ：≦０．０６％、Ａｌ：≦０．１％、Ｎ：０．００１０〜０．０１６０％、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、平均結晶粒径が５μｍ以下になるように熱間圧延し、酸洗後、圧延率が３０〜９０％の冷間圧延を施し、その後７００℃以上の連続焼鈍または５５０℃以上の箱型焼鈍を行い、更に圧延率６０％以下の２次圧延または調質圧延を施し、更にその表面に表面処理層を施すことを特徴とする。
請求項７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：０．０３〜０．２０％、Ｓｉ：≦０．５％、Ｍｎ：０．５〜３．０％、Ｐ：≦０．１％、Ｓ：≦０．０６％、Ａｌ：≦０．１％、Ｎ：０．００１０〜０．０１６０％、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、平均結晶粒径が５μｍ以下になるように熱間圧延し、酸洗後、圧延率が３０〜９０％の冷間圧延を施し、その後連続焼鈍または箱型焼鈍を行い、その後圧延率６０％以下の２次圧延を施し、その後、７００℃以上の連続焼鈍または５５０℃以上の箱型焼鈍を行い、更に、圧延率６０％以下の３次圧延または調質圧延を施し、更にその表面に表面処理層を施すことを特徴とする。この場合、前記鋼板が、重量％で、Ｔｉ：０．０１〜０．２％、Ｎｂ：０．００５〜０．１％およびＢ：０．００１〜０．０１％の内、１種または２種を更に含有することが望ましい。また、前記表面処理層がＺｎまたはＮｉめっきであることを特徴とすることが望ましい。
The method for producing a surface-treated steel sheet for a liquid crystal front frame according to claim 6 is C: 0.03 to 0.20%, Si: ≤ 0.5%, Mn: 0.5 to 3.0% by weight%. , P: ≦ 0.1%, S: ≦ 0.06%, Al: ≦ 0.1%, N: 0.0010 to 0.0160%, the remaining cast iron and the inevitable impurities. , Hot-rolled so that the average grain size is 5 μm or less, pickled, then cold-rolled with a rolling rate of 30 to 90%, and then subjected to continuous annealing at 700 ° C. or higher or box-type annealing at 550 ° C. or higher. Further, secondary rolling or temper rolling with a rolling rate of 60% or less is performed, and a surface treatment layer is further applied to the surface.
The method for producing a surface-treated steel sheet for a liquid crystal front frame according to claim 7 is, by weight%, C: 0.03 to 0.20%, Si: ≤ 0.5%, Mn: 0.5 to 3.0%. , P: ≦ 0.1%, S: ≦ 0.06%, Al: ≦ 0.1%, N: 0.0010 to 0.0160%, the remaining cast iron and the inevitable impurities. , Hot-rolled so that the average grain size is 5 μm or less, pickled, then cold-rolled with a rolling rate of 30 to 90%, then subjected to continuous annealing or box annealing, and then rolling rate of 60% The following secondary rolling is performed, then continuous annealing at 700 ° C. or higher or box annealing at 550 ° C. or higher is performed, and further, tertiary rolling or temper rolling at a rolling rate of 60% or lower is performed, and the surface is further surfaced. A treatment layer is applied. In this case, the steel sheet is, by weight, Ti: 0.01-0.2%, Nb: 0.005-0.1%, and B: 0.001-0.01%, one or two. It is desirable to further contain seeds. Moreover, it is desirable that the surface treatment layer is Zn or Ni plating.
請求項１０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たことを特徴とする。
請求項１１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の製造方法を用いて製造されたことを特徴とする。
The liquid crystal front frame according to claim 10 is manufactured using the surface-treated steel sheet for the liquid crystal front frame.
The liquid crystal front frame according to claim 11 is manufactured using the method for manufacturing the surface-treated steel sheet for the liquid crystal front frame.
本発明の液晶フロントフレーム用表面処理鋼板は、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 surface-treated steel sheet for a liquid crystal front frame of the present invention is inexpensive and excellent in mechanical strength, it can be made thinner, so that 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.
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：０．０３〜０．２０％、Ｓｉ：≦０．５％、Ｍｎ：０．５〜３．０％、Ｐ：≦０．１％、Ｓ：≦０．０６％、Ａｌ：≦０．１％、Ｎ：０．００１０〜０．０１６０％、残部Ｆｅおよび不可避的な不純物よりなる。また、Ｔｉ：０．０１〜０．２％、Ｎｂ：０．００５〜０．１％およびＢ：０．００１〜０．０１％の内、１種または２種を更に含有するとより望ましい。 The steel components of the surface-treated steel sheet for a liquid crystal front frame according to the present invention are, by weight, C: 0.03 to 0.20%, Si: ≦ 0.5%, Mn: 0.5 to 3.0%, P : ≦ 0.1%, S: ≦ 0.06%, Al: ≦ 0.1%, N: 0.0010 to 0.0160%, balance Fe and unavoidable impurities. Moreover, it is more desirable to further contain one or two of Ti: 0.01 to 0.2%, Nb: 0.005 to 0.1% and B: 0.001 to 0.01%.
Ｃは液晶フロントフレーム用表面処理鋼板に高い調質度のため、０．０３重量％以上であることが望ましい。しかし、Ｃが０．２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。そのため本発明においてはＣ成分の上限値を０．２０重量％とする。 C is preferably 0.03% by weight or more because of the high tempering degree of the surface-treated steel sheet for the liquid crystal front frame. However, if C exceeds 0.2% by weight, the amount of precipitated carbide increases and the workability of the steel sheet decreases, and at the same time, the load of cold rolling increases, the shape deteriorates, and the plate-passability in the continuous annealing process. It causes a decrease in productivity such as inhibition. Therefore, in this invention, the upper limit of C component shall be 0.20 weight%.
Ｓｉは、鋼中では大きな固溶強化機能を持ち、強靱性を得るのに有効な元素である。従って、０．１重量％以上は必要である。また、Ｓｉは、材質強化面では、多いほど良いが、冷間圧延の負荷の増大、形状の劣化を招くため上限値を０．５０重量％とする。 Si has a large solid solution strengthening function in steel and is an effective element for obtaining toughness. Therefore, 0.1% by weight or more is necessary. Further, Si is better in terms of material strengthening, but the upper limit is set to 0.50% by weight because it causes an increase in cold rolling load and deterioration of the shape.
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、前記のＣと同様に原板に高い調質度を与えるため、Ｍｎ成分は０．５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、Ｍｎ成分は上限値を３．０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, as in the case of C, the Mn component is 0.5% by weight in order to give a high tempering degree to the original plate. 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 Mn component has an upper limit of 3.0% by weight.
Ｐは結晶粒微細化成分であり、また原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０．１０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Ｐ成分の上限値を０．１０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 original plate, but it inhibits corrosion resistance. As an application of the present invention, when P exceeds 0.10% by weight, the corrosion resistance, particularly the hole resistance, is remarkably lowered, so the upper limit of the P component is set to 0.10% 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０．０６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 0.06% 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、０．１０重量％以上にな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 when it exceeds 0.10% by weight, it is used as an oxidation inhibitor during continuous casting and as a mold powder used as an anti-seizure agent for 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と同様に原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％より少なくすることは製鋼上の困難を生じ、また一方０．０１６０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、プレス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ではＮ成分範囲を０．００１〜０．０１６０重量％とする。 N, like C and Mn, gives a high degree of tempering to the original plate. 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 0.0160% by weight, the yield of ferronitride added during steelmaking Is significantly deteriorated and lacks stability, and at the same time, anisotropy during press molding is significantly deteriorated. Further, since cracks are generated on the surface of the continuous cast piece, resulting in casting defects, the N component range is set to 0.001 to 0.0160% by weight in the present invention.
Ｔｉ、Ｎｂは炭窒化化合物を形成しやすく、結晶粒を微細化する効果ある。Ｎｂは下限を０．００５重量％、Ｔｉは０．０１重量％とする。また、いずれの元素も多すぎると再結晶温度を上昇させ、連続焼鈍温度を上げなければならず、コスト増である。そこで、Ｔｉの上限は０．２重量％、Ｎｂの上限を０．１重量％とする。 Ti and Nb are easy to form a carbonitride compound and have the effect of refining crystal grains. Nb has a lower limit of 0.005% by weight, and Ti has 0.01% by weight. Moreover, when there are too many any elements, the recrystallization temperature must be raised and the continuous annealing temperature must be raised, resulting in an increase in cost. Therefore, the upper limit of Ti is 0.2% by weight, and the upper limit of Nb is 0.1% by weight.
Ｂは本発明の重要な組織であるマルテンサイトを得るために必要な元素であることと粒界に偏析しやすく、結晶粒粗大化を低減し結晶粒を微細化する効果があるため、必要に応じて０．００１重量％以上を添加する。また、多過ぎてもその効果が飽和するため、コストなどの理由から、Ｂ成分の上限を０．０１重量％とする。 B is an element necessary for obtaining martensite, which is an important structure of the present invention, and is easily segregated at grain boundaries, and has the effect of reducing crystal grain coarsening and refining crystal grains. Accordingly, 0.001% by weight or more is added. Moreover, since the effect will be saturated even if too much, the upper limit of B component shall be 0.01 weight% from reasons, such as cost.
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１１００℃以下とするのが望ましい。熱間圧延仕上温度を８５０℃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８５０℃以上とするのが望ましい。
熱延仕上圧延における圧延率、冷却条件は特定するものではないが、高強度を得るためには、平均結晶粒径が５μｍ以下となるようにできるだけ高圧下、急冷することが望ましい。また、平均粒径が５μｍ以下のフエライト中にマルテンサイトが分散してなる組織であることが望ましい。
巻き取り温度は本発明において特定するものではないが、結晶粒粗大化を抑制するために巻取温度は７００℃以下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 is 1100 ° C. or less from the viewpoint 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 850 ° 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 850 ° C. or more. .
Although the rolling rate and cooling conditions in hot rolling finish rolling are not specified, in order to obtain high strength, it is desirable to quench rapidly under high pressure as much as possible so that the average crystal grain size is 5 μm or less. Further, a structure in which martensite is dispersed in ferrite having an average particle diameter of 5 μm or less is desirable.
The coiling temperature is not specified in the present invention, but the coiling temperature is preferably 700 ° C. or lower in order to suppress the coarsening of crystal grains.
冷間圧延
前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、３０〜９０％で行う。
Cold rolling The steel sheet hot-rolled in 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, and in order to obtain the desired strength, 30 to 90 %.
焼鈍
前記のように圧延率３０〜９０％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、連続焼鈍では７００℃以上または、バッチ焼鈍では５５０℃以上の温度で焼鈍する。上限温度は、連続焼鈍では８３０℃、箱型焼鈍では７００℃とする。
Annealing The material subjected to cold rolling at a rolling rate of 30 to 90% as described above is degreased in the cleaning process, and then annealed at a temperature of 700 ° C. or higher for continuous annealing or 550 ° C. or higher for batch annealing. The upper limit temperature is 830 ° C. for continuous annealing and 700 ° C. for box annealing.
２次冷間圧延
焼鈍後の２次冷間圧延は圧延率が高くなると強度は増し、望ましいが、伸びが小さくなるので、２次冷間圧延を行う場合は、圧延率を６０％以下とする。その後、必要により調質圧延により表面粗度を付与する。
以上のように作製した冷延鋼板は、平均粒径が５μｍ〜１２μｍ以下のフェライトと、平均粒径が５μｍ以下のマルテンサイトであって体積率が３０％以下のマルテンサイトからなる組織を有することが望ましい。ばね用途では、平均粒径が２μｍ以下のフェライトと、平均粒径が５μｍ以下のマルテンサイトが体積率で６％〜３０％以下からなる組織を有することがより望ましい。加工用途では、平均粒径が３μｍ〜１２μｍのフェライトと、平均粒径が５μｍ以下のマルテンサイトが体積率で５％以下からなる組織を有することがより望ましい。このようにフェライトの結晶粒径とマルテンサイトの体積比率を冷延率と焼鈍条件を組み合わせて制御することにより、強靱性が重要な冷延鋼板には、より微細な組織とし、加工性を求められる冷延鋼板には粒径を大きくすることで、それぞれに最適な特性を得ることが可能である。
Secondary cold rolling The secondary cold rolling after annealing increases the strength when the rolling rate is high, which is desirable, but the elongation is small, so when performing the secondary cold rolling, the rolling rate is set to 60% or less. . Then, if necessary, surface roughness is imparted by temper rolling.
The cold-rolled steel sheet produced as described above has a structure composed of ferrite having an average particle diameter of 5 μm to 12 μm and martensite having an average particle diameter of 5 μm or less and a volume ratio of 30% or less. Is desirable. For spring applications, it is more desirable that ferrite having an average particle diameter of 2 μm or less and martensite having an average particle diameter of 5 μm or less have a structure composed of 6% to 30% by volume. In processing applications, it is more desirable to have a structure in which ferrite having an average particle diameter of 3 μm to 12 μm and martensite having an average particle diameter of 5 μm or less have a volume ratio of 5% or less. In this way, by controlling the ferrite grain size and the volume ratio of martensite in combination with the cold rolling rate and the annealing conditions, the cold rolled steel sheet, which is important for toughness, has a finer structure and requires workability. It is possible to obtain optimum characteristics for each cold rolled steel sheet by increasing the particle size.
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 the surface treatment, zinc 1 wt% cobalt-0.1 wt% molybdenum plating is performed on both sides at 10 g / m 2 , 300 g / L of water-based urethane resin as a solid content, 50 g / L of amine-based anticorrosive agent, 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）とＹｐ（降伏点強度）が大きく、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 larger TS (tensile strength) and Yp (yield point strength) than 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 smaller strength (TS) than Comparative Example 2, which is a conventional stainless steel plate, and cannot be applied as a liquid crystal front frame. Comparative Example 2 shows the case of a stainless steel plate that 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 (11)
A liquid crystal front frame produced by using the method for producing a surface-treated steel sheet for a liquid crystal front frame according to any one of claims 5 to 9.
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| 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 |
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| 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 |
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