JPH07166298A - Tube interior parts - Google Patents
Tube interior partsInfo
- Publication number
- JPH07166298A JPH07166298A JP21062394A JP21062394A JPH07166298A JP H07166298 A JPH07166298 A JP H07166298A JP 21062394 A JP21062394 A JP 21062394A JP 21062394 A JP21062394 A JP 21062394A JP H07166298 A JPH07166298 A JP H07166298A
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- Prior art keywords
- alloy
- precipitation hardening
- added
- annealing
- component
- 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.)
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Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、例えばカラー受像管に
用いられるシャドウマスク、フレーム、インナーシール
ド、バイメタル等の管内部品を成形性良く製造可能な管
内部品に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an in-tube component such as a shadow mask, a frame, an inner shield, and a bimetal used in a color picture tube, which can be manufactured with good moldability.
【０００２】[0002]
【従来の技術】カラー受像管のシャドウマスク、フレー
ム、インナーシールド、バイメタル、電子銃等の所謂管
内部品は、従来よりエッチング性、及び成形性が良く、
また電子ビームの反射軽減に寄与する酸化膜をその表面
に形成しやすい、リムド鋼やＡｌキルド鋼等を素材とし
て形成されている。しかしながら、近年各種のニューメ
ディアに対応するべく、カラー受像管の高品質化、つま
り表示画像の所謂見易さや極細かさが要求され、上述し
たリムド鋼やＡｌキルド鋼にて構成されるシャドウマス
ク、フレーム、インナーシールド、バイメタル等を用い
るには不具合が生じてきた。2. Description of the Related Art So-called in-tube parts such as shadow masks, frames, inner shields, bimetals, and electron guns of color picture tubes have better etching and moldability than before.
Further, it is formed from a material such as rimmed steel or Al-killed steel, which is easy to form an oxide film on its surface that contributes to reduction of electron beam reflection. However, in order to deal with various new media in recent years, high quality of the color picture tube, that is, so-called visibility and extremely fineness of the display image are required, and the shadow mask composed of the above-mentioned rimmed steel or Al killed steel, Problems have arisen in using frames, inner shields, bimetals, and the like.
【０００３】即ち、カラー受像管の動作時には、上記各
部材の温度が３０〜１００℃に上昇し、例えばその熱膨
張によるシャドウマスクの成形形状に歪みに起因した、
所謂ドーミングが生じる。この結果、シャドウマスクと
蛍光面との間の相対的位置関係にずれが生じ、ピュリテ
ィードリフト（ＰＤ）と称される色ずれが発生する。特
に高品位カラー受像管では、前記シャドウマスクの開孔
径及びその開孔ピッチが非常に小さいので、その相対的
ずれ量の割合いが大きくなり、上述したリムド鋼やＡｌ
キルド鋼を素材とする管内部品では実用に耐えなくな
る。That is, when the color picture tube operates, the temperature of each member rises to 30 to 100 ° C., for example, due to distortion in the molding shape of the shadow mask due to its thermal expansion.
So-called doming occurs. As a result, the relative positional relationship between the shadow mask and the fluorescent screen is deviated, and a color misregistration called “purity drift (PD)” is generated. Particularly in a high-quality color picture tube, since the aperture diameter and the aperture pitch of the shadow mask are very small, the relative deviation amount becomes large, and the above-mentioned rimmed steel and Al
In-pipe parts made of killed steel cannot be used practically.
【０００４】そこで従来、この種の管内部品を形成する
素材として、熱膨張係数の小さいＮｉ−Ｆｅ合金、例え
ばアンバー（３６Ｎｉ−Ｆｅ）を用いることが、例えば
特公昭４２−２５４４６号、特開昭５０−５８９７７
号、特開昭５０−６８６５０号等により提唱されてい
る。ところが、この種のＮｉ−Ｆｅ合金は熱伝導性が悪
く、蓄熱し易いことのみならず、通常のシャドウマスク
球面から電子銃側への凹み、所謂スプリングバックを生
じやすい。Therefore, conventionally, a Ni-Fe alloy having a small thermal expansion coefficient, for example, amber (36Ni-Fe), has been used as a material for forming this kind of in-tube component. 50-58977
And Japanese Patent Application Laid-Open No. 50-68650. However, this type of Ni—Fe alloy has a poor thermal conductivity and easily accumulates heat, and is likely to cause a recess from the normal shadow mask spherical surface to the electron gun side, so-called springback.
【０００５】即ち、上記スプリングバックは、その素材
の０．２％耐力値との間で、例えば図１に示すような相
関関係を有している。そしてこの０．２％耐力値が低い
程、スプリングバックが小さくなり、その成形性が良く
なる。逆に上記０．０２％耐力が２０ｋｇ／ｍｍ2 以上
になると、その成形が著しく困難となる。That is, the springback has a correlation with the 0.2% proof stress value of its material, for example, as shown in FIG. The lower the 0.2% proof stress value, the smaller the springback and the better the moldability. On the contrary, if the above-mentioned 0.02% proof stress is 20 kg / mm 2 or more, its molding becomes extremely difficult.
【０００６】そこで従来、上記素材の０．２％耐力を下
げるべく、１０００℃以上で真空焼鈍したり、或いは１
００〜２００℃の範囲で管内部品を成形加工することが
試みられている。しかし、いずれの場合も前記リムド鋼
やＡｌ鋼等が持つエッチング性や成形性には至っていな
いのが実状である。Therefore, conventionally, in order to lower the 0.2% proof stress of the above material, vacuum annealing is performed at 1000 ° C. or higher, or 1
Attempts have been made to mold and process the in-pipe parts within the range of 00 to 200 ° C. However, in any case, in reality, the etching property and formability of the rimmed steel and Al steel have not been reached.
【０００７】一方、上記成形加工が終了した後の素材
（管内部品）についてみれば、その取扱いによって変形
したり、或いはスピーカ等によるハウリングの発生が生
じないことが望まれる。従って上記成形後の素材の０．
２％耐力やその弾性率が十分に高いことが望まれる。換
言すれば、成形処理前には柔らかく、成形処理後には硬
くなる管内部品であることが望ましい。On the other hand, regarding the material (in-tube component) after the above-mentioned molding process is completed, it is desirable that the material is not deformed by handling or howling is caused by a speaker or the like. Therefore, 0.
It is desired that the 2% proof stress and its elastic modulus are sufficiently high. In other words, it is desirable that the in-tube component be soft before the molding process and hard after the molding process.
【０００８】[0008]
【発明が解決しようとする課題】本発明はこのような事
情を考慮してなされたもので、その目的とするところ
は、リムド鋼やＡｌ鋼よりも熱膨張率が低く、またこれ
らの各鋼に近い良好な成形性を有し、しかも成形処理後
には良好なハウリング防止効果と、変形防止効果を呈す
る管理部品とその製造方法を提供することにある。SUMMARY OF THE INVENTION The present invention has been made in view of the above circumstances, and its object is to have a lower coefficient of thermal expansion than rimmed steel and Al steel, and to use each of these steels. It is an object of the present invention to provide a management component having a good moldability close to that of the above, and exhibiting a good howling prevention effect and a good deformation prevention effect after the molding treatment, and a manufacturing method thereof.
【０００９】[0009]
【課題を解決するための手段及び作用】本願第一の発明
は、Ｆｅを主成分とし、総量で０．３〜１０ｗｔ％のＣ
ｒ及びＭｎの少なくとも一種と、２５〜４５ｗｔ％のＮ
ｉと、Ｔｉ，Ｎｂ，Ａｌ，Ｍｏ，Ｖ，Ｚｒ，Ｔａの中か
ら選ばれた少なくとも一種の元素からなる総量で２．５
ｗ％以下の析出硬化成分と、不可避不純物を含有した合
金からなることを特徴とする管内部品である。[Means and Action for Solving the Problems] The first invention of the present application comprises Fe as a main component and a total amount of C of 0.3 to 10 wt%.
At least one of r and Mn and 25 to 45 wt% of N
The total amount of i and at least one element selected from Ti, Nb, Al, Mo, V, Zr, and Ta is 2.5.
It is an internal pipe part characterized by comprising an alloy containing w% or less of a precipitation hardening component and unavoidable impurities.
【００１０】本願第二の発明は、析出硬化成分であるＴ
ｉは０．０５〜２．０ｗｔ％添加されたものである本願
第一の発明の管内部品である。The second invention of the present application is that T which is a precipitation hardening component.
i is the in-pipe component of the first invention of the present application in which 0.05 to 2.0 wt% is added.
【００１１】本願第三の発明は、析出硬化成分であるＮ
ｂは０．０５〜２．０ｗｔ％添加されたものである本願
第一の発明の管内部品である。The third invention of the present application is N which is a precipitation hardening component.
b is the in-pipe component of the first invention of the present application, which is added in an amount of 0.05 to 2.0 wt%.
【００１２】本願第四の発明は、析出硬化成分であるＡ
ｌは０．０５〜１．５ｗｔ％添加されたものである本願
第一の発明の管内部品である。The fourth invention of the present application is A which is a precipitation hardening component.
1 is the in-pipe component of the first invention of the present application, in which 0.05 to 1.5 wt% is added.
【００１３】本願第五の発明は、析出硬化成分であるＴ
ａは０．００５〜２．５ｗｔ％添加されたものである本
願第一の発明の管内部品である。The fifth invention of the present application is that T which is a precipitation hardening component.
a is the in-pipe component of the first invention of the present application, in which 0.005 to 2.5 wt% is added.
【００１４】本願第六の発明は、析出硬化成分であるＭ
ｏは０．００５〜２．５ｗｔ％添加されれたものである
本願第一の発明の管内部品である。The sixth invention of the present application is the precipitation hardening component M.
o is the in-pipe component of the first invention of the present application in which 0.005 to 2.5 wt% is added.
【００１５】本願第七の発明は、析出硬化成分であるＶ
は０．００５〜２．５ｗｔ％添加されれたものである本
願第一の発明の管内部品である。The seventh invention of the present application is the precipitation hardening component V
Is the in-pipe part of the first invention of the present application, in which 0.005 to 2.5 wt% is added.
【００１６】本願第八の発明は、析出硬化成分であるＺ
ｒは０．１〜２．０ｗｔ％添加されたれたものである本
願第一の発明の管内部品である。The eighth invention of the present application is Z which is a precipitation hardening component.
r is the in-pipe component of the first invention of the present application, in which 0.1 to 2.0 wt% is added.
【００１７】そして上記析出硬化成分元素の添加によっ
て、その焼鈍処理による成形加工を容易ならしめ、且つ
その後の時効処理（黒化処理を兼ねた）によって上記析
出硬化成分を析出させて成形加工された管内部品を硬く
するようにしたものである。The addition of the precipitation-hardening component element facilitates the forming process by the annealing treatment, and the aging treatment (also serving as the blackening treatment) thereafter causes the precipitation-hardening component to be deposited to perform the forming process. It is intended to harden the parts inside the pipe.
【００１８】ここで、上記Ｎｉの組成量を２５〜４５ｗ
ｔ％としたのは、その熱膨張係数を９０×１０-7／℃以
下にする為であり、Ｎｉの添加量が上記範囲を外れる
と、本発明が目的とする熱膨張率の低い管内部品が得ら
れなくなる。更にＮｉの添加量が４５ｗｔ％を越える
と、その０．２％耐力の増加が生じ、その成形性が大幅
に劣化する。同時にその耐酸化性の向上によって、通常
その表面に施される黒化膜の生成が著しく困難となる。Here, the composition amount of Ni is 25 to 45 w.
The reason why t% is set is that the coefficient of thermal expansion thereof is set to 90 × 10 −7 / ° C. or less. Will not be obtained. Further, if the added amount of Ni exceeds 45 wt%, the 0.2% proof stress increases, and the formability thereof deteriorates significantly. At the same time, the improvement of its oxidation resistance makes it extremely difficult to form a blackened film, which is usually applied to the surface.
【００１９】またエッチング性に関しても、Ｎｉ量が多
くなると微細エッチングが困難となり、そのエッチング
孔の内壁が所謂ガサ穴となったり、エッチング液中への
Ｎｉの多量の溶け込みによって、そのエッチング速度の
低下を招く等の問題が生じる。Regarding the etching property, if the amount of Ni increases, it becomes difficult to perform fine etching, the inner wall of the etching hole becomes a so-called rough hole, and a large amount of Ni dissolved in the etching solution lowers the etching rate. And other problems occur.
【００２０】またＣｒまたはＭｎは、一般的にはＦｅ−
Ｎｉ合金の熱膨張係数を上昇させるが、その反面上記
０．２％耐力を減少させ、その成形性の向上に大きく寄
与する。つまり管内部品用素材にエッチングし、多数の
穴を開けたフラットマスクを得た後の管内部品の焼鈍工
程において上記Ｃｒが重要な役割を果たす。Further, Cr or Mn is generally Fe-
Although the coefficient of thermal expansion of the Ni alloy is increased, on the other hand, the 0.2% proof stress is decreased, which greatly contributes to the improvement of the formability. That is, the Cr plays an important role in the step of annealing the in-pipe part after the flat mask having a large number of holes is obtained by etching the in-pipe part material.
【００２１】即ち一般に、３６Ｎｉ−Ｆｅ合金にＣｒま
たはＭｎを添加し、再結晶温度以上で焼鈍しない場合、
その結晶粒が微細であるので室温での０．２％耐力の増
大を招き、例えばシャドウマスクとしての曲率を保つこ
とが困難となる。この為、上記ＣｒまたはＭｎの添加に
よって、その素材の高強度化が図られるだけである。し
かし本発明の如くＣｒまたはＭｎを添加した３６Ｎｉ−
Ｆｅ合金に特定の焼鈍処理を施した場合、その０．２％
耐力の減少量は、ＣｒまたはＭｎが無添加の３６Ｎｉ−
Ｆｅ合金に比較して著しく多くなる。つまり素材に含ま
れるＣｒまたはＭｎは、その焼鈍工程において素材の
０．２％耐力を大きく減少させる上で重要な作用を呈す
る。That is, in general, when Cr or Mn is added to a 36Ni-Fe alloy and annealing is not performed at a recrystallization temperature or higher,
Since the crystal grains are fine, 0.2% proof stress at room temperature is increased, and it becomes difficult to maintain the curvature as a shadow mask, for example. Therefore, the addition of Cr or Mn only enhances the strength of the material. However, as in the present invention, 36Ni- with Cr or Mn added
When Fe alloy is subjected to specific annealing treatment, its 0.2%
The amount of decrease in yield strength is 36Ni- with no addition of Cr or Mn.
It is remarkably large as compared with the Fe alloy. That is, Cr or Mn contained in the material has an important effect in greatly reducing the 0.2% proof stress of the material in the annealing process.
【００２２】ところで、ＣｒまたはＭｎの添加量が０．
３ｗｔ％未満であると、ＣｒまたはＭｎの無添加の３６
Ｎｉ−Ｆｅ合金と同様に焼鈍温度を１２００℃と高くし
ても、その０．２％耐力が２４ｋｇ／ｍｍ2 以下になる
ことはない。またその添加量が１０ｗｔ％を越えた場
合、熱膨張係数が９０×１０-7／℃以上となり、色ずれ
の原因となるので高精細度カラー受像管への採用には不
適当である。またＣｒまたはＭｎの添加量が１０ｗｔ％
を越えた場合、その表面にＣｒ2 Ｏ3 （Ｍｎ3 Ｏ4 ）の
保護膜が形成され易く、表面黒化速度の低下を招く等、
黒化処理に不都合を生じる。尚、ＣｒまたはＭｎの添加
量は低膨張性、エッチング性、および廃液中の低クロム
化を考慮した場合、１〜４ｗｔ％とすることが望まし
い。更に、上記ＣｒとＭｎとを複合添加しても、これら
の特性が劣化することはない。By the way, the addition amount of Cr or Mn is less than 0.1.
If it is less than 3 wt%, 36 without addition of Cr or Mn
As with the Ni-Fe alloy, even if the annealing temperature is increased to 1200 ° C, the 0.2% proof stress does not fall below 24 kg / mm 2 . If the amount added exceeds 10 wt%, the coefficient of thermal expansion becomes 90 × 10 −7 / ° C. or more, which causes color misregistration and is not suitable for use in a high definition color picture tube. The addition amount of Cr or Mn is 10 wt%
If it exceeds the range, a protective film of Cr 2 O 3 (Mn 3 O 4 ) is likely to be formed on the surface, resulting in a decrease in the surface blackening rate.
This causes inconvenience to the blackening process. The amount of Cr or Mn added is preferably 1 to 4 wt% in consideration of low expansion property, etching property, and low chromium content in the waste liquid. Further, even if the above Cr and Mn are added in combination, these characteristics do not deteriorate.
【００２３】図２（ａ）は本発明に係る管内部品用素材
である、Ｍｎを添加した３６Ｎｉ−Ｆｅ合金からなる管
内部品の、上記Ｍｎの添加量に対する熱膨張係数の変化
を特性Ａとして示すもので、特性Ｂはその０．２％耐力
の変化である。また図２（ｂ）は、Ｃｒを添加した３６
Ｎｉ−Ｆｅ合金における上記Ｃｒの添加量に対する熱膨
張係数の変化を特性Ｃとして示すもので、特性Ｄはその
０．２％耐力の変化である。但し、これらの特性は９０
０℃で１時間の焼鈍処理を行った管内部品についての特
定結果である。これらの図に示されるように、５ｗｔ％
までのＣｒまたはＭｎの添加によって、その０．２％耐
力が大幅に低下し、この結果その成形性が向上すること
がわかる。FIG. 2 (a) shows, as a characteristic A, a change in the coefficient of thermal expansion with respect to the amount of Mn added, of a pipe internal part made of a 36Ni—Fe alloy containing Mn, which is a material for a pipe internal part according to the present invention. Characteristic B is the change in its 0.2% proof stress. Further, FIG. 2B shows that 36 with Cr added.
The change in the coefficient of thermal expansion with respect to the amount of addition of Cr in the Ni-Fe alloy is shown as the characteristic C, and the characteristic D is the change in the 0.2% proof stress thereof. However, these characteristics are 90
It is a specific result about a part in a pipe annealed at 0 ° C for 1 hour. As shown in these figures, 5 wt%
It can be seen that the addition of Cr or Mn up to 10% significantly lowers the 0.2% proof stress, and as a result, the formability thereof is improved.
【００２４】尚、上記ＣｒまたはＭｎの添加は３０〜３
５％のＮｉと７％までのＣｏを含むスーパーアンバーに
対しても有効である。The addition of Cr or Mn is 30 to 3
It is also effective for Super Amber containing 5% Ni and up to 7% Co.
【００２５】次に析出硬化成分元素の添加による管内部
品の特性について説明する。Next, the characteristics of the in-pipe component due to the addition of the precipitation hardening component element will be described.
【００２６】析出硬化成分元素の添加量の上限を２．５
ｗｔ％としたのは、それ以上の量を添加した場合、黒化
処理等の時効処理において管内部品の変形を招来した
り、その溶体化を兼ねた焼鈍処理において管内部品が不
本意に硬くなることを防止する為である。The upper limit of the addition amount of the precipitation hardening component element is set to 2.5.
The reason why the content is set to wt% is that when an amount of more than that is added, deformation of the pipe parts is caused in the aging treatment such as blackening treatment, or the pipe parts become unintentionally hardened in the annealing treatment that also serves as solution treatment. This is to prevent this.
【００２７】具体的には、析出硬化成分元素であるＴｉ
は、時効処理によって析出し、合金の強度を向上させる
が、その添加量が０．０５ｗｔ％未満では十分な硬化作
用を呈しない。つまり合金の強度が十分に高くならな
い。また添加量が２．０ｗｔ％を越えると成形性が悪く
なる。従って、望ましくは０．２〜１．０ｗｔ％の範囲
で上記Ｔｉを添加することが望ましい。Specifically, Ti which is a precipitation hardening component element
Is precipitated by aging treatment and improves the strength of the alloy, but if the addition amount is less than 0.05 wt%, it does not exhibit a sufficient hardening effect. That is, the strength of the alloy is not sufficiently high. Further, if the addition amount exceeds 2.0 wt%, the moldability becomes poor. Therefore, it is desirable to add Ti in the range of 0.2 to 1.0 wt%.
【００２８】また析出硬化成分元素であるＡｌは、上記
Ｔｉと同様に時効処理によって析出し、合金の強度を向
上させるに有用な元素である。しかしその添加量が０．
０５ｗｔ％未満では十分な硬化作用を呈しない、つまり
合金の強度が十分に高くならない。また添加量が１．５
ｗｔ％を越えると成形性が悪くなる。Al, which is a precipitation hardening component element, is an element useful for improving the strength of the alloy by being precipitated by an aging treatment as in the case of Ti. However, the addition amount is 0.
If it is less than 05 wt%, a sufficient hardening action is not exhibited, that is, the strength of the alloy is not sufficiently increased. The addition amount is 1.5
If it exceeds wt%, the moldability becomes poor.
【００２９】また析出硬化成分元素であるＺｒは、上記
ＴｉおよびＡｌとの複合添加によってその強度向上に大
きく寄与する。尚、単独の添加によっても、合金の強度
を向上させるに有用であることは言うまでもない。しか
しその添加量が０．０５ｗｔ％未満では十分な硬化作用
が得られず、またその添加量が２．０ｗｔ％を越える
と、その成形性を著しく悪くする。Zr, which is a precipitation-hardening component element, contributes greatly to the improvement of strength by the combined addition of Ti and Al. Needless to say, addition alone is also useful for improving the strength of the alloy. However, if the added amount is less than 0.05 wt%, a sufficient curing action cannot be obtained, and if the added amount exceeds 2.0 wt%, the moldability is remarkably deteriorated.
【００３０】またＮｂを添加する場合には、Ｚｒと同様
な理由により、その添加量を０．０５〜２．０ｗｔ％と
することが望ましい。更にＭｏおよびＶも上記各元素と
同様な効果を奏するが、その添加量をＴｉ，Ａｌ，Ｚ
ｒ，Ｎｂに比較して多くする必要がある。またその添加
量を０．０５ｗｔ％未満とすると十分な強度が得られ
ず、２．５ｗｔ％を越えると成形性が悪くなる。When Nb is added, it is desirable that the addition amount be 0.05 to 2.0 wt% for the same reason as Zr. Further, Mo and V also have the same effects as the above-mentioned elements, but the addition amounts thereof are Ti, Al, Z.
It is necessary to increase the number compared with r and Nb. If the addition amount is less than 0.05 wt%, sufficient strength cannot be obtained, and if it exceeds 2.5 wt%, the formability deteriorates.
【００３１】そしてＴａについては、上述したＭｏとほ
ぼ同様な特性を示すので、その添加量を０．０５〜２．
５ｗｔ％とすれば、その強度向上を望むことが可能とな
る。Since Ta exhibits substantially the same characteristics as Mo described above, the addition amount of Ta is 0.05 to 2.
If it is 5 wt%, it is possible to expect the strength to be improved.
【００３２】さてこのような成分からなる管内部品は次
のようにして製造される。Now, the in-tube component made of such components is manufactured as follows.
【００３３】この製造方法をシャドウマスクの製作を例
に説明すると、先ず、真空または不活性ガス雰囲気中で
上述した組成からなる合金を、溶解し、そのインゴット
を製作する。次にこのインゴットを繰返し熱延した後、
酸洗して冷延処理を施す。その後の最終圧延における圧
延率は、次の工程であるエッチング処理における液組
成、液温度に依存して変更することができるが、通常４
０％以上とすることが望ましい。This manufacturing method will be described by taking the production of a shadow mask as an example. First, an alloy having the above-mentioned composition is melted in a vacuum or an inert gas atmosphere to produce an ingot. Next, after repeatedly hot rolling this ingot,
Pickled and cold rolled. The rolling ratio in the subsequent final rolling can be changed depending on the liquid composition and liquid temperature in the etching process which is the next step, but it is usually 4
It is desirable to set it to 0% or more.
【００３４】しかる後、焼鈍温度、焼鈍時間の調整によ
って結晶粒径を制御し、最終圧延によって管内部品の形
状保持を行う。この場合、管内部品の素材の結晶粒度を
ＪＩＳ−Ｇ０５５１に規定されるところの８〜１２に設
定することが好ましい。また最終の調整圧延は、結晶の
集合組織を崩さないように、３０％以下の圧延率で行う
ことが望ましい。更にエッチングに望ましい結晶面は通
常（１００）であることから、この結晶面を主面として
管内部品を製作するようにすれば良い。Thereafter, the grain size is controlled by adjusting the annealing temperature and the annealing time, and the shape of the in-pipe part is maintained by the final rolling. In this case, it is preferable to set the crystal grain size of the material of the in-pipe component to 8 to 12 as specified in JIS-G0551. Further, it is desirable that the final adjustment rolling is performed at a rolling rate of 30% or less so as not to destroy the crystal texture. Further, since the crystal plane desired for etching is usually (100), the in-pipe part may be manufactured with this crystal plane as the main surface.
【００３５】しかる後、エッチング工程を経て多数の孔
を開けたフラットマスクを作成し、前述した析出硬化成
分をそのマトリックス中に固溶させるべく、溶体化処理
を兼ねた焼鈍を行う。この焼鈍は７００〜１３００℃の
温度で、且つ不活性ガス中で行う。但し、ＣｒまたはＭ
ｎの添加量が３〜８ｗｔ％のときは、焼鈍温度を７００
〜９００℃にすることが望ましい。またその添加量が３
ｗｔ％以下、または６〜１０ｗｔ％の時には、９００℃
以上に設定することが望ましい。After that, a flat mask having a large number of holes formed is formed through an etching process, and an annealing process which also serves as a solution treatment is carried out in order to form a solid solution of the precipitation hardening component in the matrix. This annealing is performed at a temperature of 700 to 1300 ° C. and in an inert gas. However, Cr or M
When the added amount of n is 3 to 8 wt%, the annealing temperature is 700
It is desirable to set the temperature to 900 ° C. The addition amount is 3
900 ° C when less than 6% by weight or 6% by weight
It is desirable to set the above.
【００３６】この焼鈍処理時に重要なことは、冷却速度
を可能な限り速くすることであり、溶体化処理にとって
不可決なことである。ちなみに冷却速度が遅いと、析出
硬化成分の不本意な析出が始まり、フラットマスクの
０．２％耐力が増大する。従って、その後の成形加工が
困難となる。またこの冷却は、室温以下に冷却された不
活性ガスを焼鈍炉内に充満させる等して行われる。What is important in this annealing treatment is to make the cooling rate as fast as possible, which is inevitable for the solution treatment. By the way, when the cooling rate is slow, incipient precipitation of the precipitation hardening component starts, and the 0.2% proof stress of the flat mask increases. Therefore, the subsequent molding process becomes difficult. Further, this cooling is performed by filling the inside of the annealing furnace with an inert gas cooled to room temperature or lower.
【００３７】このようにして焼鈍処理した後、その素材
（フラットマスク）をプレス成形し、所定の曲面を有す
るシャドウマスクとする。そしてこのシャドウマスク
を、例えばトリクロロエチレンの蒸気で洗浄した後、以
下に示すように黒化処理を兼ねた時効処理を施す。After the annealing treatment as described above, the material (flat mask) is press-molded to obtain a shadow mask having a predetermined curved surface. Then, after the shadow mask is washed with, for example, trichloroethylene vapor, it is subjected to an aging treatment which also serves as a blackening treatment as described below.
【００３８】この時効処理ではシャドウマスクの黒化を
兼ねることから、そのガス雰囲気として、例えば空気、
水蒸気、炭酸ガスが用いられる。この際、時効処理温度
を５００℃未満とすることは、黒化処理が遅くなり、時
効析出も遅くなることから不適当である。また時効処理
温度を８００℃以上にすると、添加した析出硬化成分が
合金組織のマトリックス内に固溶していまい、成形後の
管内部品が硬くならないので不適当である。尚、この時
効処理温度とその処理時間は、合金中に添加した析出硬
化成分元素の種類に応じて適宜定められることは勿論の
ことである。Since this aging treatment also serves to blacken the shadow mask, its gas atmosphere is, for example, air,
Steam and carbon dioxide are used. At this time, if the aging temperature is less than 500 ° C., the blackening process is delayed and the aging precipitation is also delayed, which is inappropriate. Further, if the aging treatment temperature is 800 ° C. or higher, the added precipitation hardening component will not dissolve into the matrix of the alloy structure as a solid solution, and the parts in the tube after forming will not be hard, which is not suitable. It is needless to say that the aging treatment temperature and the aging treatment time are appropriately determined according to the type of the precipitation hardening component elements added to the alloy.
【００３９】この場合、黒化膜としては主としてＣｒx
Ｎｉy Ｆｅ3-x-y Ｏ4 （０＜ｘ，ｙ＜３）、またはＭｎ
x Ｎｉy Ｆ3-x-yＯ4 が生成し、その密着性が保たれ
る。また析出硬化成分元素は、主として黒化膜と金属と
の界面に濃縮するが、その添加量が上述したように少な
いこと、および同時に添加されたＣｒまたはＮｎによる
効果とが相俟って、上述した密着性に悪影響を及ぼすこ
とがない。In this case, the blackening film is mainly Cr x.
Ni y Fe 3-xy O 4 (0 <x, y <3), or Mn
x Ni y F 3-xy O 4 is produced, the adhesion is maintained. The precipitation hardening component element is mainly concentrated at the interface between the blackening film and the metal, but the addition amount thereof is small as described above, and the effect of Cr or Nn added at the same time is taken into consideration. It does not adversely affect the adherence.
【００４０】かくして本発明によれば、所定のＮｉ−Ｆ
ｅ系合金にＣｒを添加して、その０．２％耐力を低減
し、且つその成形性を改善することができる。しかも従
来の３２Ｎｉ−５Ｃｏ−Ｆｅ合金のように、高温で真空
焼鈍する必要がなくなり、温間プレスする等の手間がな
くなる。そして１２００℃以下の焼鈍によって、十分に
その成形加工が可能となる。更には、その形成後の黒化
処理を兼ねた時効処理によってその形成部品を十分に硬
くすることができ、取扱いの容易化を図り得る。またそ
の強度を十分に高くすることができるので、ハウリング
防止にも効果的である等の効果が奏せられる。Thus, according to the present invention, a predetermined Ni-F
By adding Cr to the e-based alloy, its 0.2% proof stress can be reduced and its formability can be improved. Moreover, unlike the conventional 32Ni-5Co-Fe alloy, there is no need to perform vacuum annealing at a high temperature, and the trouble of warm pressing is eliminated. Then, by annealing at 1200 ° C. or less, the forming process can be sufficiently performed. Furthermore, the formed part can be made sufficiently hard by the aging treatment that also serves as the blackening treatment after the formation, and the handling can be facilitated. Further, since the strength can be sufficiently increased, the effect of preventing howling can be obtained.
【００４１】尚、ここではＮｉ−Ｆｅ系合金を例に説明
したが、Ｆｅ−Ｎｉ−Ｃｏ系合金についても適用可能な
ことはいうまでもない。Although the Ni--Fe based alloy has been described as an example here, it is needless to say that the present invention is also applicable to the Fe--Ni--Co based alloy.
【００４２】[0042]
【実施例】次に本発明の実施例をシャドウマスクの製作
を例に挙げて説明する。EXAMPLES Next, examples of the present invention will be described by taking the production of a shadow mask as an example.
【００４３】実施例１ 先ず、３６％ＮｉとＦｅを主成分とし、Ｃｒを２ｗｔ
％、その他附随的成分を含む合金に、析出硬化成分の元
素としてＴｉを添加した合金のインゴットを真空溶解に
より製作準備し、このインゴットを熱間加工して厚さ１
０ｍｍの板材とした。この板材を繰返し焼鈍・冷間加工
して厚み０．２ｍｍのコイルを製作した。ここでは最終
圧延率を８０％、調整圧延率を１０％として行い、上記
コイルの結晶粒度を、ＪＩＳ−Ｇ０５５１で規定される
１０の粒度とした。このようにして製作された管内部品
用素材を用いて、次のようにしてシャドウマスクを製作
した。先ず、素材の両表面にフォトレジストを塗布し、
これを乾燥させた後、スロット或いはドット形状の基準
パターンを形成したフィルムをその両面に密着させて、
前記フォトレジストを露光・現像した。この現像によっ
て未露光部分のフォトレジストが溶解除去される。しか
る後、残されたフォトレジストをバーニングして硬化さ
せた後、塩化第二鉄溶液でエッチング処理し、その後そ
の残存レジストを熱アルカリによって除去してシャドウ
マスクの原板となるフラットマスクを作製した。Example 1 First, 36% Ni and Fe were the main components, and 2 wt% of Cr was used.
%, An alloy containing Ti and other incidental components, to which Ti is added as an element of a precipitation hardening component, is prepared by vacuum melting, and this ingot is hot-worked to a thickness of 1
The plate material was 0 mm. This plate material was repeatedly annealed and cold worked to produce a coil having a thickness of 0.2 mm. Here, the final rolling rate was 80% and the adjusted rolling rate was 10%, and the grain size of the coil was set to 10 grain sizes specified in JIS-G0551. A shadow mask was manufactured in the following manner using the material for the in-pipe parts thus manufactured. First, apply photoresist to both surfaces of the material,
After this is dried, a film with a slot or dot-shaped reference pattern is adhered to both sides,
The photoresist was exposed and developed. By this development, the photoresist in the unexposed portion is dissolved and removed. Thereafter, the remaining photoresist was burned and hardened, and then an etching treatment with a ferric chloride solution was performed. Then, the remaining resist was removed by a hot alkali to prepare a flat mask as a master plate for the shadow mask.
【００４４】その後、このフラットマスクを箱形の真空
加熱炉に入れ、１０-4ｔｏｒｒ、１０００℃の雰囲気で
焼鈍し、歪取りとその加工性の改善を行った。この焼鈍
後のフラットマスクをレベラーに通して板歪を除去し、
同時に成形工程におけるストレッチャーストレインを減
少させた。尚、この真空焼鈍は、フラットマスク中の溶
存Ｃ量の減少と、その結晶粒度の低減を目的として行っ
た。これによって、その後のプレス成形の容易化を図っ
た。Thereafter, this flat mask was placed in a box-shaped vacuum heating furnace and annealed in an atmosphere of 10 -4 torr and 1000 ° C. to remove strain and improve its workability. The flat mask after this annealing is passed through a leveler to remove plate distortion,
At the same time, the stretcher strain in the molding process was reduced. The vacuum annealing was performed for the purpose of reducing the amount of dissolved C in the flat mask and reducing the crystal grain size. This facilitated the subsequent press molding.
【００４５】次に上記フラットマスクをプレス成形し、
所定の曲面を有するシャドウマスクを得た。この際、
０．２％耐力が小さく、その成形性が極めて良好で、ス
プリングバックが生じないことが確認された。同時にシ
ャドウマスクの幅方向および長手方向の特性が均一であ
り、特性の所謂バラツキに起因する成形性不良の発生が
ないことが確認された。Next, the flat mask is press-molded,
A shadow mask having a predetermined curved surface was obtained. On this occasion,
It was confirmed that the 0.2% proof stress was small, the moldability was extremely good, and springback did not occur. At the same time, it was confirmed that the characteristics of the shadow mask in the width direction and the length direction were uniform, and there was no occurrence of defective moldability due to so-called variations in the characteristics.
【００４６】その後、上記シャドウマスクをトリクロロ
エチレンの蒸気で洗浄し、７００℃に保持された連続黒
化炉で２０分間加熱して密着性の良い黒化膜を、厚み
１．５ｍｍ成長させてシャドウマスクを完成させた。こ
の際、析出硬化が生じ、その硬さがビッカース硬度で１
０３Ｈｖから１５０Ｈｖに向上した。Then, the shadow mask was washed with trichloroethylene vapor and heated in a continuous blackening furnace kept at 700 ° C. for 20 minutes to grow a blackened film having good adhesion to a thickness of 1.5 mm. Was completed. At this time, precipitation hardening occurs, and the hardness is 1 in Vickers hardness.
It was improved from 03Hv to 150Hv.
【００４７】実施例２〜８ 実施例１における合金の成分と共に表１で示すような組
成成分の合金を用い、実施例１と同様な手法でシャドウ
マスクをそれぞれ製作した。Examples 2 to 8 Using the alloys having the composition components shown in Table 1 together with the alloy components in Example 1, shadow masks were manufactured in the same manner as in Example 1.
【００４８】[0048]
【表１】 尚、この表では、黒化処理を兼ねた時効処理前後の素材
の硬さと、機械的強度の向上の度合いが併記されてい
る。[Table 1] In this table, the hardness of the material before and after the aging treatment that also serves as the blackening treatment and the degree of improvement in mechanical strength are also shown.
【００４９】これらの各実施例でも、先の実施例と同様
な効果が得られることが確認された。It was confirmed that the same effects as those of the previous examples were obtained in each of these examples.
【００５０】このようにして得られた各実施例のシャド
ウマスクを組込んだカラー受像管について、その四隅の
ＰＤ値について調べたところ、従来のリムド鋼やＡｌキ
ルド鋼を素材とするシャドウマスクを組込んだカラー受
像管のＰＤ値に比較して、１／２に減少していることが
認められた。またアンバー系の素材で形成されたシャド
ウマスクを用いた場合のようなハウリングの発生もない
ことが確認された。The PD values at the four corners of the color picture tube incorporating the shadow mask of each of the embodiments thus obtained were examined, and it was found that the shadow masks made of conventional rimmed steel or Al-killed steel were used. It was confirmed that the value was reduced to 1/2 as compared with the PD value of the color picture tube incorporated. It was also confirmed that howling did not occur as in the case of using a shadow mask formed of an amber material.
【００５１】ちなみに参考として示した比較例１〜３に
おいては、その硬さがビッカース硬度で１２０以上にな
ると０．２％耐力が約２４ｋｇ／ｍｍ2 となり、プレス
成形が困難となった。その熱膨張係数も大きくなり、不
具合が生じた。By the way, in Comparative Examples 1 to 3 shown as a reference, when the hardness was 120 or more in Vickers hardness, the 0.2% proof stress was about 24 kg / mm 2 , and press molding became difficult. The coefficient of thermal expansion also increased, causing a problem.
【００５２】尚、ここではシャドウマスクの形成を例に
説明したが、インナーシールドやフレーム、バイメタル
等を同様に製作してカラー受像管を得ることも可能であ
る。その他、本発明はその要旨を逸脱しない範囲で種々
変形して実施することができる。Although the formation of the shadow mask has been described as an example here, it is also possible to obtain the color picture tube by similarly manufacturing the inner shield, the frame, the bimetal and the like. In addition, the present invention can be variously modified and implemented without departing from the scope of the invention.
【００５３】[0053]
【発明の効果】上述したように、本発明によれば熱膨張
率が低く、良好な成形性を有し、しかも成形処理後には
良好なハウリング防止効果と変形防止効果を呈する管内
部品を得ることが可能となる。As described above, according to the present invention, it is possible to obtain a pipe part having a low coefficient of thermal expansion, a good moldability, and a good howling prevention effect and a deformation prevention effect after the molding treatment. Is possible.
【図１】 ０．２％耐力とスプリングバックとの関係を
示す図。FIG. 1 is a diagram showing the relationship between 0.2% proof stress and springback.
【図２】 （ａ）はＭｎを添加した３６Ｎｉ−Ｆｅ合金
におけるＭｎの添加量に対する０．２％耐力とスプリン
グバックとの関係を示す図。（ｂ）はＣｒを添加した３
６Ｎｉ−Ｆｅ合金におけるＣｒの添加量に対する０．２
％耐力とスプリングバックとの関係を示す図。FIG. 2A is a diagram showing the relationship between 0.2% proof stress and springback with respect to the amount of Mn added in a 36Ni—Fe alloy containing Mn. (B) is Cr-added 3
0.2 with respect to the amount of addition of Cr in the 6Ni-Fe alloy
The figure which shows the relationship between% yield strength and spring back.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 大竹 康久 埼玉県深谷市幡羅町１丁目９番２号 株式 会社東芝深谷ブラウン管工場内 ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Yasuhisa Otake 1-9-2 Hararacho, Fukaya-shi, Saitama, Ltd. Inside the Fukaya CRT factory of Toshiba Corporation
Claims (8)
ｗｔ％のＣｒ及びＭｎの少なくとも一種と、２５〜４５
ｗｔ％のＮｉと、Ｔｉ，Ｎｂ，Ａｌ，Ｍｏ，Ｖ，Ｚｒ，
Ｔａの中から選ばれた少なくとも一種の元素からなる総
量で２．５ｗｔ％以下の析出硬化成分と、不可避不純物
を含有した合金からなることを特徴とする管内部品。1. A total amount of 0.3 to 10 containing Fe as a main component.
wt% of at least one of Cr and Mn, and 25 to 45
wt% Ni, Ti, Nb, Al, Mo, V, Zr,
A pipe part comprising an alloy containing an unavoidable impurity and a precipitation hardening component in a total amount of 2.5 wt% or less composed of at least one element selected from Ta.
２．０ｗｔ％添加されたものである特許請求の範囲第１
項記載の管内部品。2. The precipitation hardening component Ti is 0.05 to
Claim 1 wherein 2.0 wt% is added
In-pipe parts described in paragraph.
２．０ｗｔ％添加されたものである特許請求の範囲第１
項記載の管内部品。3. Nb which is a precipitation hardening component is 0.05 to
Claim 1 wherein 2.0 wt% is added
In-pipe parts described in paragraph.
１．５ｗｔ％添加されたものである特許請求の範囲第１
項記載の管内部品。4. The precipitation hardening component of Al is 0.05 to
Claim 1 in which 1.5 wt% is added
In-pipe parts described in paragraph.
２．５ｗｔ％添加されたものである特許請求の範囲第１
項記載の管内部品。5. The precipitation hardening component Ta is 0.005 to 0.005.
Claim 1 in which 2.5 wt% is added
In-pipe parts described in paragraph.
２．５ｗｔ％添加されたものである特許請求の範囲第１
項記載の管内部品。6. Mo as a precipitation hardening component is 0.005-
Claim 1 in which 2.5 wt% is added
In-pipe parts described in paragraph.
２．５ｗｔ％添加されたものである特許請求の範囲第１
項記載の管内部品。7. The precipitation hardening component V is 0.005 to 0.005.
Claim 1 in which 2.5 wt% is added
In-pipe parts described in paragraph.
０ｗｔ％添加されたものである特許請求の範囲第１項記
載の管内部品。8. Zr which is a precipitation hardening component is 0.1 to 2.
The in-pipe component according to claim 1, wherein 0 wt% is added.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6210623A JP2669789B2 (en) | 1994-08-11 | 1994-08-11 | In-pipe parts |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6210623A JP2669789B2 (en) | 1994-08-11 | 1994-08-11 | In-pipe parts |
Related Parent Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP60016790A Division JPH0798982B2 (en) | 1985-01-31 | 1985-01-31 | Manufacturing method of in-pipe parts |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH07166298A true JPH07166298A (en) | 1995-06-27 |
| JP2669789B2 JP2669789B2 (en) | 1997-10-29 |
Family
ID=16592398
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP6210623A Expired - Lifetime JP2669789B2 (en) | 1994-08-11 | 1994-08-11 | In-pipe parts |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2669789B2 (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0765950A1 (en) * | 1995-08-25 | 1997-04-02 | Inco Alloys International, Inc. | High strength low thermal expansion alloy |
| US5688471A (en) * | 1995-08-25 | 1997-11-18 | Inco Alloys International, Inc. | High strength low thermal expansion alloy |
| US6824625B2 (en) | 2000-07-24 | 2004-11-30 | Dai Nippon Printing Co., Ltd. | Magnetostriction control alloy sheet, a part of a braun tube, and a manufacturing method for a magnetostriction control alloy sheet |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5959861A (en) * | 1982-09-29 | 1984-04-05 | Toshiba Corp | Parts in electron tube |
-
1994
- 1994-08-11 JP JP6210623A patent/JP2669789B2/en not_active Expired - Lifetime
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5959861A (en) * | 1982-09-29 | 1984-04-05 | Toshiba Corp | Parts in electron tube |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0765950A1 (en) * | 1995-08-25 | 1997-04-02 | Inco Alloys International, Inc. | High strength low thermal expansion alloy |
| US5688471A (en) * | 1995-08-25 | 1997-11-18 | Inco Alloys International, Inc. | High strength low thermal expansion alloy |
| US6824625B2 (en) | 2000-07-24 | 2004-11-30 | Dai Nippon Printing Co., Ltd. | Magnetostriction control alloy sheet, a part of a braun tube, and a manufacturing method for a magnetostriction control alloy sheet |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2669789B2 (en) | 1997-10-29 |
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| Date | Code | Title | Description |
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| EXPY | Cancellation because of completion of term |