JP2006307260A - Steel sheet for plasma display fixing plate, method for producing steel sheet for fixing plasma display, and plasma display fixing plate - Google Patents
Steel sheet for plasma display fixing plate, method for producing steel sheet for fixing plasma display, and plasma display fixing plate Download PDFInfo
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Abstract
Description
本発明はプラズマディスプレイ固定板用鋼板、プラズマディスプレイ固定用鋼板の製造方法及びプラズマディスプレイ固定板に関し、特に耐食性あるいは放熱性に優れたプラズマディスプレイ固定板に関する。 The present invention relates to a steel plate for a plasma display fixing plate, a method for manufacturing a steel plate for fixing a plasma display, and a plasma display fixing plate, and more particularly to a plasma display fixing plate excellent in corrosion resistance or heat dissipation.
近年、ディスプレイ分野では、ＣＲＴタイプ、液晶タイプ及びプラズマディスプレイタイプ間で性能面だけでなく、価格面で厳しい競争が行われている。プラズマディスプレイに使われるプラズマディスプレイ固定板は現在アルミニウム合金板使われている。しかし、高強度が要求されるため、厚さが約２ｍｍと厚くしなければならず高コストの原因にもなっている。このため、薄くて、耐食性あるいは放熱性に優れた高強度の材料が求められている。しかし、現在使われているアルミニウム合金板を高強度化することは困難である。従来高強度の鋼板については、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。
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。
In recent years, in the display field, severe competition has been conducted not only in terms of performance but also in price among CRT type, liquid crystal type and plasma display type. The plasma display fixing plate used for the plasma display is currently using an aluminum alloy plate. However, since high strength is required, the thickness has to be increased to about 2 mm, which causes high cost. For this reason, there is a demand for a high-strength material that is thin and excellent in corrosion resistance or heat dissipation. However, it is difficult to increase the strength of currently used aluminum alloy sheets. Conventionally, a method for rapidly cooling a high-strength steel sheet after heating it to the 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.
Prior art document information relating to the present application includes the following.
本発明は、特に薄くて、耐食性あるいは放熱性に優れた高強度のプラズマディスプレイ固定板用鋼板、プラズマディスプレイ固定板用鋼板の製造方法及びプラズマディスプレイ固定板を提供することを目的とする。 An object of the present invention is to provide a steel plate for a plasma display fixing plate that is particularly thin and excellent in corrosion resistance or heat dissipation, a method for manufacturing a steel plate for a plasma display fixing plate, and a plasma display fixing plate.
本発明のプラズマディスプレイ固定板用鋼板（請求項１）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：０．００１〜０．０１６％、Ｔｉ：≦０．２％、Ｎｂ：≦０．１％、Ｂ：≦０．０１％、残部がＦｅおよび不可避的不純物からなることを特徴とする。この場合、プラズマディスプレイ固定板用鋼板の平均結晶粒径が 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が体積率で３０％以下からなる組織を有することが望ましい。
本発明のプラズマディスプレイ固定板用鋼板の製造方法（請求項３）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：０．００１〜０．０１６％、Ｔｉ：≦０．２％、Ｎｂ：≦０．１％、Ｂ：≦０．０１％、残部がＦｅおよび不可避的不純物からなる連続鋳造鋼からなる鋼片を、平均結晶粒径が５μｍ以下のフェライト中にマルテンサイトが分散してなる組織と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、焼鈍を行い、その後、６０％以下の圧延率で２次冷間圧延を施すことを特徴とする。この場合、前記２次冷間圧延後、連続焼鈍では７００℃以上、または箱型焼鈍では５５０℃以上で焼鈍を行い、更に、圧延率６０％以下の３次圧延または調質圧延を施すことが望ましい。
本発明のプラズマディスプレイ固定板（請求項５）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：０．００１〜０．０１６％、Ｔｉ：≦０．２％、Ｎｂ：≦０．１％、Ｂ：≦０．０１％、残部がＦｅおよび不可避的不純物からなる鋼板に、更に表面にＺｎまたはＺｎを主成分としためっき層を有することを特徴とする。この場合、前記ＺｎまたはＺｎを主成分としためっき層の上に、化成処理層を有することが望ましい。
The steel plate for plasma display fixing plate of the present invention (Claim 1) is, by weight, C: 0.03-0.20%, Si: ≦ 0.5%, Mn: 0.5-3.0%, P: ≦ 0.1%, S: ≦ 0.06%, Al: ≦ 0.1%, N: 0.001 to 0.016%, Ti: ≦ 0.2%, Nb: ≦ 0.1% , B: ≦ 0.01%, the balance being Fe and inevitable impurities. In this case, it is desirable that the plasma display fixing plate steel sheet has a structure in which ferrite having an average crystal grain size of 5 μm to 12 μm and martensite having an average grain size of 5 μm or less are 30% or less by volume.
The manufacturing method of the steel plate for plasma display fixing plates of the present invention (Claim 3) is C: 0.03-0.20%, Si: ≦ 0.5%, Mn: 0.5-3. 0%, P: ≦ 0.1%, S: ≦ 0.06%, Al: ≦ 0.1%, N: 0.001 to 0.016%, Ti: ≦ 0.2%, Nb: ≦ 0 0.1%, B: ≦ 0.01%, a steel piece made of continuous cast steel with the balance being Fe and inevitable impurities, and a structure in which martensite is dispersed in ferrite having an average crystal grain size of 5 μm or less; It is characterized in that after hot rolling so that it is pickled, it is cold-rolled with a rolling rate of 30 to 90%, annealed, and then subjected to secondary cold rolling at a rolling rate of 60% or less. To do. In this case, after the secondary cold rolling, annealing is performed at 700 ° C. or more for continuous annealing or 550 ° C. or more for box annealing, and further, tertiary rolling or temper rolling with a rolling rate of 60% or less is performed. desirable.
The plasma display fixing plate of the present invention (Claim 5) 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: 0.001 to 0.016%, Ti: ≦ 0.2%, Nb: ≦ 0.1%, B : ≤0.01%, the balance being Fe and a steel plate made of inevitable impurities, and further having a plating layer mainly composed of Zn or Zn on the surface. In this case, it is desirable to have a chemical conversion treatment layer on the plating layer containing Zn or Zn as a main component.
本発明のプラズマディスプレイ固定板は、板厚が約０．７ｍｍと薄く、しかも高強度な鋼板を用いているため、安価で、耐食性、放熱性などの特性に優れた材料として提供できる。 The plasma display fixing plate of the present invention is a thin plate having a thickness of about 0.7 mm and a high-strength steel plate. Therefore, the plasma display fixing plate is inexpensive and can be provided as a material excellent in characteristics such as corrosion resistance and heat dissipation.
以下、本発明を詳細に説明する。
本発明の原板となる鋼板の鋼成分は、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％、残部が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。
Hereinafter, the present invention will be described in detail.
The steel components of the steel sheet to be the original sheet of the present invention are in weight%, C: 0.03 to 0.20%, Si: ≦ 0.5%, Mn: 0.5 to 3.0%, P: ≦ 0. 0.1%, S: ≦ 0.06%, Al: ≦ 0.1%, N: 0.0010 to 0.0160%, the balance being Fe and inevitable 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は鋼板に高い調質度を付与するため、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。 Since C imparts a high tempering degree to the steel sheet, it is desirable that C is 0.03% by weight or more. 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、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. In terms of material reinforcement, the higher the better, the higher the cold rolling load and the deterioration of the shape, so the upper limit is 0.50% 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、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, in the same manner as C, in order to give a high tempering degree to the original plate, the Mn component is 0.5% 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 set to 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. In the present invention, when P exceeds 0.10% by weight, the corrosion resistance, particularly the hole resistance, is remarkably lowered, so the upper limit 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 it be as small as possible. However, it cannot completely prevent contamination from steel stones, and it is difficult to desulfurize during the process. 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 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、加工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, the anisotropy during processing is significantly deteriorated. Furthermore, 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、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 weight or more is added. Moreover, since the effect is saturated even if it is too much, the upper limit is set to 0.01% by weight for 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℃以上とするのが望ましい。熱間圧延仕上温度をＡｒ3 点以下にすると、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Ａｒ3 点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)
The slab heating temperature in the hot rolling process is not specified in the present invention, but is preferably 1100 ° C. or higher from the standpoint of positive decomposition and dissolution of N and stable securing of the hot finish rolling temperature. If the hot rolling finishing temperature is lower than the Ar3 point, 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 higher than the Ar3 point. .
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）
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、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 is performed at 30 to 90% in order to obtain the desired strength. .
（焼鈍）
上記のように圧延率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７００〜８３０℃または、バッチ焼鈍では５５０〜７００℃の温度で焼鈍する。
(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 to 830 ° C. in continuous annealing or 550 to 700 ° C. in batch 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。
(Secondary cold rolling)
In secondary cold rolling after annealing, the strength increases and is desirable when the rolling rate increases, but the elongation decreases. Therefore, when secondary cold rolling is performed, the rolling rate is set to 60% or less. Then, if necessary, surface roughness is imparted by temper rolling.
（２次焼鈍及び３次冷間圧延）
前記２次冷間圧延後、連続焼鈍では７００℃以上、または箱型焼鈍では５５０℃以上で焼鈍を行い、更に、圧延率６０％以下の３次圧延または調質圧延を施しても良い。
(Secondary annealing and third cold rolling)
After the secondary cold rolling, annealing may be performed at 700 ° C. or more for continuous annealing or 550 ° C. or more for box annealing, and further, tertiary rolling or temper rolling with a rolling rate of 60% or less may be performed.
本発明のプラズマディスプレイ固定板素材となる鋼板としては、板厚が０．５〜０．８ｍｍ、抗張力が５５０〜１０００ＭＰａ、伸びが１０〜３０％である鋼板が好ましい。
これらの鋼板は以下のようにして得られる。すなわち、鋼成分が重量％で、Ｃ：０．０３〜０．２０％、Ｓｉ：≦０．５％、Ｍｎ：０．５〜３．０％、Ｐ：≦０．１％、Ｓ：≦０．０６％、Ａｌ：≦０．１％、Ｎ：０．００１〜０．０１６％、Ｔｉ：≦０．２％、Ｎｂ：≦０．１％、Ｂ：≦０．０１％、残部がＦｅおよび不可避的不純物からなる連続鋳造鋼からなる鋼片を、加熱温度：≧１１００℃、仕上温度：≧Ａｒ３点以上の条件で熱間圧延する。熱間圧延に際しては、平均粒径が５μｍ以下のフェライト中にマルテンサイトが分散してなる組織となるように、高圧下率で圧延した後に急冷し、巻取温度：≦７００℃でコイルとして巻取り、長尺帯状の熱延板とする。次いでこの熱延板を３０〜９０％の圧延率で１次冷間圧延し、クリーニングして脱脂した後、焼鈍する。焼鈍を連続焼鈍で行う場合は７００〜８３０℃に加熱し、箱型焼鈍で行う場合は５５０〜７００℃に加熱する。次いで６０％以下の圧延率で２次冷間圧延する。さらに、その後、連続焼鈍では７００℃以上、または箱型焼鈍では５５０℃以上で焼鈍を行い、更に、圧延率６０％以下の３次圧延または調質圧延を施しても良い。、
As a steel plate used as the plasma display fixing plate material of the present invention, a steel plate having a plate thickness of 0.5 to 0.8 mm, a tensile strength of 550 to 1000 MPa, and an elongation of 10 to 30% is preferable.
These steel plates are obtained as follows. That is, the steel component 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: 0.001 to 0.016%, Ti: ≦ 0.2%, Nb: ≦ 0.1%, B: ≦ 0.01%, the balance being A steel slab made of continuously cast steel made of Fe and inevitable impurities is hot-rolled under conditions of a heating temperature: ≧ 1100 ° C. and a finishing temperature: ≧ Ar 3 points or more. In hot rolling, the steel is rolled as a coil at a coiling temperature of ≦ 700 ° C. after rolling at a high-pressure rate so as to obtain a structure in which martensite is dispersed in ferrite having an average particle size of 5 μm or less. Take a long strip-shaped hot-rolled sheet. Next, the hot-rolled sheet is subjected to primary cold rolling at a rolling rate of 30 to 90%, cleaned and degreased, and then annealed. When performing annealing by continuous annealing, it heats to 700-830 degreeC, and when performing by box type annealing, it heats to 550-700 degreeC. Next, secondary cold rolling is performed at a rolling rate of 60% or less. Furthermore, after that, annealing may be performed at 700 ° C. or higher for continuous annealing or 550 ° C. or higher for box annealing, and further, tertiary rolling or temper rolling at a rolling rate of 60% or less may be performed. ,
このようにして、０．５〜０．８ｍｍの板厚を有し、平均結晶粒径が５〜１２μｍのフェライトと平均結晶粒径が５μｍ以下のマルテンサイトからなり、マルテンサイトの体積率が３０％以下の組織の冷延鋼板からなる基板が得られる。平均結晶粒径が３〜１０μｍのフェライトと平均粒径が５μｍ以下のマルテンサイトからなり、マルテンサイトの体積率が８〜３０％からなる組織とすることが望ましい。強度を重視する場合は、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。加工性を重視する場合、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、強度を重視した鋼板には、より微細な組織とし、加工性を重視した鋼板には粒径を大きくすることで必要な特性を得ることが可能である。 Thus, it has a plate thickness of 0.5 to 0.8 mm, consists of ferrite having an average crystal grain size of 5 to 12 μm and martensite having an average crystal grain size of 5 μm or less, and the volume ratio of martensite is 30. A substrate made of a cold-rolled steel sheet having a structure of% or less is obtained. It is desirable to have a structure comprising ferrite having an average crystal grain size of 3 to 10 μm and martensite having an average grain size of 5 μm or less, and having a martensite volume ratio of 8 to 30%. When emphasizing strength, it is more desirable to have a structure in which 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 volume ratio of 6% to 30%. When emphasizing workability, it is more desirable to have a structure comprising 5% or less of ferrite having an average particle diameter of 3 μm to 12 μm and martensite having an average particle diameter of 5 μm or less. In this way, by controlling the ferrite grain size and martensite volume ratio in combination with the cold rolling rate and annealing conditions, steel sheets that emphasize strength have a finer structure and steel sheets that emphasize workability. The required characteristics can be obtained by increasing the particle size.
次いで、以上のようにして得られる基板に耐食性を付与するためにめっきを施す。めっき金属としては、Ｓｎ、Ｚｎ、Ｃｕ、Ｎｉ、Ａｇ、Ａｕ、またはこれらの２種以上からなる合金を用いることができるが、廉価であることからＺｎまたはＺｎを主成分とする合金を用いることが好ましい。また、Ｚｎ−Ｃｏ−Ｍｏからなる電気めっき鋼板を用いても良い。Ｚｎめっき方法として、溶融めっき法または電気めっき法のいずれを用いてもよい。電気めっき法を用いる場合、めっき量としては５〜５０ｇ／ｍ２であることが好ましい。 Next, plating is performed to impart corrosion resistance to the substrate obtained as described above. As the plating metal, Sn, Zn, Cu, Ni, Ag, Au, or an alloy composed of two or more of these can be used. However, since it is inexpensive, an alloy containing Zn or Zn as a main component should be used. Is preferred. Moreover, you may use the electroplated steel plate which consists of Zn-Co-Mo. As the Zn plating method, either a hot dipping method or an electroplating method may be used. When the electroplating method is used, the plating amount is preferably 5 to 50 g / m 2 .
引き続いてめっき層上にクロムを含まず、耐食性及び放熱性を向上させる化成処理層を設ける。化成処理層としては、次の組成を有する処理液を用いて、浸漬法、ロールコート法、カーテンフローコート法、スプレーコート法などのいずれかの塗布方法を用いて塗布し、乾燥することにより形成させる。塗布厚さは乾燥後の厚さ０．０５〜１０μｍであることが好ましい。
（１）アクリル系処理液
水系アクリル樹脂や水系ウレタン樹脂などの水系有機樹脂に水分散性シリカおよび防錆剤、さらにフラックス性を付与するために水溶化ロジンを含有したもの処理液を用いる。
Subsequently, a chemical conversion treatment layer that does not contain chromium and improves corrosion resistance and heat dissipation is provided on the plating layer. The chemical conversion treatment layer is formed by applying and drying using a treatment liquid having the following composition, using any of the application methods such as dipping, roll coating, curtain flow coating, and spray coating. Let The coating thickness is preferably 0.05 to 10 μm after drying.
(1) Acrylic treatment liquid A treatment liquid containing water-dispersible silica and a rust preventive agent and a water-soluble rosin for imparting flux properties to an aqueous organic resin such as an aqueous acrylic resin or an aqueous urethane resin is used.
処理液の水系樹脂として水系アクリル樹脂を用いる場合は、１００〜８００ｇ／Ｌの濃度のものを用い、処理液中に５０〜６００ｇ／Ｌの濃度で水溶化ロジン、１０〜２００ｇ／Ｌで濃度の水分散性シリカ、および１０〜２００ｇ／Ｌの濃度で防錆剤を含有させることが好ましい。 When an aqueous acrylic resin is used as the aqueous resin for the treatment liquid, one having a concentration of 100 to 800 g / L is used, the water-solubilized rosin at a concentration of 50 to 600 g / L in the treatment liquid, and the concentration of 10 to 200 g / L. It is preferable to contain a water-dispersible silica and a rust inhibitor at a concentration of 10 to 200 g / L.
処理液の水系樹脂として水系ウレタン樹脂を用いる場合は、１００〜９００ｇ／Ｌの濃度のものを用い、処理液中に１０〜４００ｇ／Ｌで濃度の水分散性シリカ、および１０〜１００ｇ／Ｌの濃度で防錆剤を含有させることが好ましい。 When using a water-based urethane resin as the water-based resin for the treatment liquid, a resin having a concentration of 100 to 900 g / L is used, water-dispersible silica having a concentration of 10 to 400 g / L in the treatment liquid, and 10 to 100 g / L. It is preferable to contain a rust inhibitor at a concentration.
これらの処理液中に含有させる水分散性シリカは、シリカ表面にアルミニウムをコーティングしたものが分散性に優れており好ましい。シリカの粒径としては１００ｎｍ以下であることが好ましい。 The water-dispersible silica contained in these treatment liquids is preferably one in which the silica surface is coated with aluminum because of excellent dispersibility. The particle size of silica is preferably 100 nm or less.
防錆剤としては、クロムを含まずアミンを含む化合物またはスチレン・無水マレイン酸共重合体のいずれかもしくは両方を含むものを用いることが好ましい。アミンを含む化合物としては、ドデシルアミン、オレオイルイミダゾリン、アミノプロピル牛脂アミン、ロジンアミンなどの有機アミン石けんを単独でまたは混合して使用する。スチレン・無水マレイン酸共重合体としてはスチレン・無水マレイン酸共重合アルキルエステル・アンモニウム塩を用いる。 As the rust preventive agent, it is preferable to use a compound containing either or both of a compound containing no amine and an amine and a styrene / maleic anhydride copolymer. As the amine-containing compound, organic amine soaps such as dodecylamine, oleoyl imidazoline, aminopropyl tallow amine, and rosin amine are used alone or in combination. As the styrene / maleic anhydride copolymer, styrene / maleic anhydride copolymer alkyl ester / ammonium salt is used.
処理液の水系樹脂として水系アクリル樹脂を用いる場合に含有させる水溶化ロジンとしては、ロジンの主成分であるアビエチン酸分子内のカルボン酸基をアミン塩などで中和し、ロジン石けんとしたものを用いることが好ましい。 The water-solubilized rosin to be included when using an aqueous acrylic resin as the aqueous resin for the treatment liquid is a rosin soap obtained by neutralizing the carboxylic acid group in the abietic acid molecule, which is the main component of the rosin, with an amine salt. It is preferable to use it.
（２）黒色系（放熱性を有する処理液）
処理液としては、上記水系アクリル樹脂や水系ウレタン樹脂に、黒色顔料を５０〜３００ｇ／Ｌ添加した液を用いる。黒色顔料としては、カーボンブラック、アセチレンブラック、ケッチェンブラック、天然黒鉛、人造黒鉛などの無機顔料、あるいはアニリン黒などの有機顔料が適用できる。５０ｇ／Ｌ未満では放熱性の効果が小さく、３００ｇ／Ｌを超えると皮膜の製膜性が悪くなる。
以上のようにして素材となる鋼板にめっきを施し、次いでめっき層上に耐食性あるいは放熱性を向上させる化成処理層を設けることにより、本発明のプラズマディスプレイ固定板用材料を得ることができる。
(2) Black system (treatment solution with heat dissipation)
As the treatment liquid, a liquid obtained by adding 50 to 300 g / L of a black pigment to the water-based acrylic resin or water-based urethane resin is used. As black pigments, inorganic pigments such as carbon black, acetylene black, ketjen black, natural graphite and artificial graphite, or organic pigments such as aniline black can be applied. If it is less than 50 g / L, the effect of heat dissipation is small, and if it exceeds 300 g / L, the film-forming property of the film is deteriorated.
As described above, the material for the plasma display fixing plate of the present invention can be obtained by plating the steel plate as a raw material and then providing a chemical conversion treatment layer for improving the corrosion resistance or heat dissipation on the plating layer.
以下、実施例を示して本発明をさらに詳細に説明する。
[供試板の作成］
表１に示す鋼板の化学成分、冷間圧延条件、焼鈍条件を示す。
Hereinafter, the present invention will be described in more detail with reference to examples.
[Create test plate]
The chemical composition, cold rolling conditions, and annealing conditions of the steel sheet shown in Table 1 are shown.
この鋼板に、下記に示すめっき浴とめっき条件を用いてＺｎめっきを施した後、下記にに示す液組成の処理液を用いて耐食性を向上させる化成処理層をＺｎめっき皮膜上に形成し、特性評価用の基板とした。 めっき条件、化成処理の種類は表２に示す。 After applying Zn plating to this steel sheet using the plating bath and plating conditions shown below, a chemical conversion treatment layer for improving corrosion resistance is formed on the Zn plating film using a treatment liquid having the following liquid composition, It was set as the board | substrate for characteristic evaluation. Table 2 shows the plating conditions and types of chemical conversion treatment.
[Ｚｎめっき］
めっき浴 硫酸亜鉛 ２５０ｇ／Ｌ
硫酸アンモニウム ３０ｇ／Ｌ
ｐＨ ３．０
浴温 ４０℃
電流密度 ２０Ａ／ｄｍ２
めっき量 ２０ｇ／ｍ２
[Zn plating]
Plating bath Zinc sulfate 250g / L
Ammonium sulfate 30g / L
pH 3.0
Bath temperature 40 ℃
Current density 20A / dm 2
Plating amount 20 g / m 2
[耐食性を向上させる化成処理］
浴組成 水系ウレタン樹脂 ７００ｇ／Ｌ
水分散性シリカ ２００ｇ／Ｌ
ロジン−アミン系防錆剤 ５０ｇ／Ｌ
塗布方法 ロールコート
塗布厚さ（乾燥後） １μｍ
[Chemical conversion treatment to improve corrosion resistance]
Bath composition Aqueous urethane resin 700g / L
Water-dispersible silica 200g / L
Rosin-amine rust inhibitor 50g / L
Application method Roll coat Application thickness (after drying) 1μm
[放熱性を向上させる化成処理］
浴組成 水系ウレタン樹脂 ６００ｇ／Ｌ
水分散性シリカ １００ｇ／Ｌ
ロジン−アミン系防錆剤 ５０ｇ／Ｌ
カーボンブラック ２００ｇ／Ｌ
塗布方法 ロールコート
塗布厚さ（乾燥後） １μｍ
また、比較用の供試板として、表２に示す厚み２ｍｍのＡｌ合金板（試料番号８）を用いた。なお、表２において、耐食性を向上させる化成処理はＡ、放熱性を向上させる化成処理はＢで示した。
[Chemical conversion treatment to improve heat dissipation]
Bath composition Aqueous urethane resin 600g / L
Water-dispersible silica 100g / L
Rosin-amine rust inhibitor 50g / L
Carbon black 200g / L
Application method Roll coat Application thickness (after drying) 1μm
Further, as a test plate for comparison, an Al alloy plate (sample number 8) having a thickness of 2 mm shown in Table 2 was used. In Table 2, chemical conversion treatment for improving corrosion resistance is indicated by A, and chemical conversion treatment for improving heat dissipation is indicated by B.
上記のようにして得られた供試板について、ＴＳ（抗張力）とＴ．ＥＬ．（伸び）はＪＩＳ５号試験片とした供試板を引張試験により測定した。
放熱性は、放射率計（ＡＥＲＤ放射率計（ＤＥＶＩＣＥＳ ＆ ＳＥＲＶＩＣＥＳ ＣＯＭＰＡＮＹ製））を用いて供試板の放射率を測定し、下記の基準で熱放射性を評価した。熱放射性は熱放射率が０．４以上（下記評価基準で◎と○に相当する）を合格とした。
◎：放射率≧０．７
○：放射率≧０．４でかつ＜０．７
△：放射率≧０．１でかつ＜０．４
×：放射率＜０．１
これらの評価結果を表２に示す。
About the test plate obtained as described above, TS (tensile strength) and T.I. EL. (Elongation) was measured by a tensile test of a test plate used as a JIS No. 5 test piece.
For the heat dissipation, the emissivity of the test plate was measured using an emissometer (AERD emissometer (manufactured by DEVICES & SERVICES COMPANY)), and the thermal emissivity was evaluated according to the following criteria. Thermal emissivity was determined to be acceptable when the thermal emissivity was 0.4 or more (corresponding to ◎ and ○ in the following evaluation criteria).
A: Emissivity ≧ 0.7
○: Emissivity ≧ 0.4 and <0.7
Δ: Emissivity ≧ 0.1 and <0.4
×: Emissivity <0.1
These evaluation results are shown in Table 2.
その結果、表２に示すように、鋼板上にＺｎめっきを施し、その上に耐食性あるいは放熱性を向上させる化成処理層を形成してなる本発明のプラズマディスプレイ固定板は、プラズマディスプレイ固定板として充分適用できることが判明した。 As a result, as shown in Table 2, the plasma display fixing plate of the present invention obtained by applying Zn plating on the steel plate and forming a chemical conversion treatment layer on the steel plate to improve corrosion resistance or heat dissipation is used as a plasma display fixing plate. It has been found that it can be applied sufficiently.
本発明のプラズマディスプレイ固定板は、安価な鋼板に安価なＺｎめっきとその上に耐食性または放熱性を向上させる化成処理層を形成したものであり、プラズマディスプレイ固定板として充分適用できることが判明した。また、従来材より薄いため、コンパクトなプラズマディスプレイが製造可能となる。 The plasma display fixing plate of the present invention is obtained by forming an inexpensive Zn plating on a cheap steel plate and a chemical conversion treatment layer for improving corrosion resistance or heat dissipation thereon, and can be sufficiently applied as a plasma display fixing plate. Moreover, since it is thinner than the conventional material, a compact plasma display can be manufactured.
Claims (6)
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2010248626A (en) * | 2009-03-27 | 2010-11-04 | Kobe Steel Ltd | High thermal conductivity heat radiation steel sheet |
| WO2014156671A1 (en) * | 2013-03-26 | 2014-10-02 | 日新製鋼株式会社 | High-strength plated steel sheet for welded structural member and method for manufacturing said sheet |
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Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2010248626A (en) * | 2009-03-27 | 2010-11-04 | Kobe Steel Ltd | High thermal conductivity heat radiation steel sheet |
| WO2014156671A1 (en) * | 2013-03-26 | 2014-10-02 | 日新製鋼株式会社 | High-strength plated steel sheet for welded structural member and method for manufacturing said sheet |
| JP2014189812A (en) * | 2013-03-26 | 2014-10-06 | Nisshin Steel Co Ltd | High strength plated steel sheet for weld structure member and manufacturing method therefor |
| CN105121681A (en) * | 2013-03-26 | 2015-12-02 | 日新制钢株式会社 | High-strength plated steel sheet for welded structural member and method for manufacturing said sheet |
| US10100395B2 (en) | 2013-03-26 | 2018-10-16 | Nisshin Steel Co., Ltd. | High-strength plated steel plate for welded structural member, and method for producing the same |
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Free format text: JAPANESE INTERMEDIATE CODE: A300 Effective date: 20080701 |