JP2003129185A - Fe-Ni-BASED ALLOY FOR SHADOW MASKING MATERIAL SUPERIOR IN CORROSION RESISTANCE, AND SHADOW MASKING MATERIAL - Google Patents
Fe-Ni-BASED ALLOY FOR SHADOW MASKING MATERIAL SUPERIOR IN CORROSION RESISTANCE, AND SHADOW MASKING MATERIALInfo
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- JP2003129185A JP2003129185A JP2001323145A JP2001323145A JP2003129185A JP 2003129185 A JP2003129185 A JP 2003129185A JP 2001323145 A JP2001323145 A JP 2001323145A JP 2001323145 A JP2001323145 A JP 2001323145A JP 2003129185 A JP2003129185 A JP 2003129185A
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- alloy
- corrosion resistance
- shadow mask
- thermal expansion
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Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01J—ELECTRIC DISCHARGE TUBES OR DISCHARGE LAMPS
- H01J29/00—Details of cathode-ray tubes or of electron-beam tubes of the types covered by group H01J31/00
- H01J29/02—Electrodes; Screens; Mounting, supporting, spacing or insulating thereof
- H01J29/06—Screens for shielding; Masks interposed in the electron stream
- H01J29/07—Shadow masks for colour television tubes
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01J—ELECTRIC DISCHARGE TUBES OR DISCHARGE LAMPS
- H01J2229/00—Details of cathode ray tubes or electron beam tubes
- H01J2229/07—Shadow masks
- H01J2229/0727—Aperture plate
- H01J2229/0733—Aperture plate characterised by the material
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Electrodes For Cathode-Ray Tubes (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
【0001】[0001]
【発明の属する技術分野】本発明は、カラーテレビブラ
ウン管などの素材として用いられる耐食性に優れるシャ
ドウマスク素材用Fe−Ni系合金およびシャドウマスク材
料に関するものであり、とくに、素材製造工程における
光揮焼鈍後に、大気中にさらされた時でも、錆の発生が
少ない耐食性に優れる高剛性低熱膨張のFe−Ni系合金
と、この合金を用いてなるシャドウマスク材料について
提案する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a Fe-Ni alloy and a shadow mask material for a shadow mask material, which are used as a material for a color television cathode ray tube and have excellent corrosion resistance, and more particularly to a light volatilization annealing in a material manufacturing process. Later, we propose a high-rigidity and low-thermal-expansion Fe-Ni-based alloy that has little corrosion even when exposed to the atmosphere and has excellent corrosion resistance, and a shadow mask material using this alloy.
【0002】[0002]
【従来の技術】従来、シャドウマスク材料としては、低
炭素アルミキルド鋼板が用いられている。この鋼板は、
たとえば、中間冷間圧延後の鋼板を、連続焼鈍炉または
バッチ焼鈍炉によって歪とり中間焼鈍を実施し、その
後、仕上冷間圧延および調質圧延(ダル圧延を含む)を
行うという工程を経て製造されている。2. Description of the Related Art Conventionally, a low carbon aluminum killed steel plate has been used as a shadow mask material. This steel plate is
For example, a steel sheet after intermediate cold rolling is strained by a continuous annealing furnace or a batch annealing furnace to perform intermediate annealing, and then finished cold rolling and temper rolling (including dull rolling) are performed. Has been done.
【0003】一般に、高品位カラーテレビブラウン管や
ディスプレー用の材料というのは、たとえばカラーテレ
ビ受像管の場合であれば、シャドウマスクの開孔を通過
する電子ビームは全体の1/3以下であり、残りの電子ビ
ームはシャドウマスクに射突して、シャドウマスクは時
として80℃にも達する程に加熱されるものである。その
ために、シャドウマスク材料が膨張を起こして歪み、色
純度の低下を招くこととなる。このため、その材質とし
ては熱膨張の小さいものを使用することが有利である。
この意味において近年では、前記アルミキルド鋼鈑の代
わりに熱膨張の影響が少ないFe−36Ni系インバー合金が
使用されるようになっている。Generally, in the case of a high-definition color television picture tube or display material, for example, in the case of a color television picture tube, the electron beam passing through the aperture of the shadow mask is 1/3 or less of the whole. The rest of the electron beam hits the shadow mask, and the shadow mask is sometimes heated to as high as 80 ° C. Therefore, the shadow mask material expands and is distorted, resulting in a decrease in color purity. Therefore, it is advantageous to use a material having a small thermal expansion.
In this sense, in recent years, Fe-36Ni-based Invar alloy, which is less affected by thermal expansion, has been used instead of the aluminum-killed steel plate.
【0004】このFe−Ni系合金板のなかでも、近年で
は、画面のフラット化、大型化にともない、合金元素で
あるMnを低減した低熱膨張Fe−36Ni系合金板(特開平5
−186853号公報)やNbを添加し高強度化をはかった合金
板(特許第3150831号)などが使われている。Among these Fe-Ni alloy plates, in recent years, the flattening of the screen and the increase in size have resulted in a low thermal expansion Fe-36Ni alloy plate in which Mn, which is an alloying element, has been reduced (see Japanese Patent Laid-Open Publication No. Hei 5 (1999) -58).
-186853) and alloy plates with added Nb to increase strength (Patent No. 3150831) and the like are used.
【0005】[0005]
【発明が解決しようとする課題】しかしながら、低Mn
の低熱膨張Fe−36Ni系合金やNb添加の高強度Fe−36Ni系
合金は、ブラウン管中では、その雰囲気が真空であり腐
食環境にさらされないが、素材製造の中間工程である光
揮焼鈍後の流通、運搬の過程において、大気中に長時間
さらされるために、錆が発生して製品とならないケース
があり、防錆の面で課題を残していた。[Problems to be Solved by the Invention] However, low Mn
The low thermal expansion Fe-36Ni alloy and the Nb-added high-strength Fe-36Ni alloy are not exposed to the corrosive environment because the atmosphere is vacuum in a cathode ray tube, but after light volatilization annealing, which is an intermediate step of material production, In the process of distribution and transportation, there are cases where rust occurs and the product does not become a product because it is exposed to the atmosphere for a long time, which leaves a problem in terms of rust prevention.
【0006】本発明の目的は、素材製造の中間工程であ
る光揮焼鈍後に流通や運搬のために大気中に長時間さら
されたときでも、錆の発生が少ない、高剛性低熱膨張シ
ャドウマスク素材用Fe−Ni系合金とシャドウマスク材料
とを提供することにある。The object of the present invention is to provide a highly rigid and low thermal expansion shadow mask material which causes little rust even when it is exposed to the atmosphere for a long time for distribution and transportation after light volatilization annealing which is an intermediate step of material manufacturing. The present invention is to provide a Fe-Ni based alloy for use and a shadow mask material.
【0007】[0007]
【課題を解決するための手段】上掲の目的に対し、発明
者らは、素材製造の中間工程である光揮焼鈍後に大気中
にさらされた時でも、錆を発生しにくいFe−Ni系合金に
ついて鋭意研究を重ねた結果、次のような知見を得た。
それは、素材(Fe−Ni系合金)に発生する錆は、光揮焼鈍
後に発生しやすく、通常のFe−36Ni合金よりも、Mnを低
減した低熱膨張Fe−36Ni合金の方が発生しやすいという
ことがわかった。この知見について検討したところ、低
MnのFe−Ni系合金板については、その表面から150Åま
での領域におけるS濃度が、バルクよりも著しく高くな
っていることを発見した。一般的に知られているよう
に、このように表層部にSが濃化すると、Sは金属イオン
の溶解を促進させ、錆を誘発させる。なお、こうした現
象は、この合金板の表層部を機械的、化学的に除去すれ
ば解決が可能だが、この処理を商業的規模で対処するこ
とには困難がある。[Means for Solving the Problems] In order to achieve the above object, the inventors of the present invention have developed a Fe-Ni system that is unlikely to generate rust even when exposed to the air after light volatilization annealing, which is an intermediate step of material production. As a result of intensive studies on alloys, the following findings were obtained.
It is said that the rust generated in the material (Fe-Ni alloy) is likely to occur after light annealing, and the low thermal expansion Fe-36Ni alloy with reduced Mn is more likely to occur than the normal Fe-36Ni alloy. I understood it. When we examined this finding, we found that
For the Fe-Ni alloy sheet of Mn, it was discovered that the S concentration in the region from the surface to 150 Å is significantly higher than that in the bulk. As is generally known, when S is concentrated in the surface layer in this manner, S promotes dissolution of metal ions and induces rust. Incidentally, such a phenomenon can be solved by mechanically and chemically removing the surface layer portion of the alloy plate, but it is difficult to deal with this treatment on a commercial scale.
【0008】そこで、発明者らは、合金板の表層に濃化
するSを抑制することで対処することにした。[0008] Therefore, the inventors decided to deal with this by suppressing the S that is concentrated in the surface layer of the alloy plate.
【0009】即ち、発明者らの研究によれば、Fe−36Ni
合金板表層部へのSの濃化は、Mn含有量の高いFe−Ni系
合金では皆無であり、Mn含有量の低い低熱膨張Fe-36Ni
合金において顕著であること、そして、Mn含有量の高い
Fe−Ni系合金中のMn系介在物にはSが取り込まれている
が、Mn含有量の低い低熱膨張Fe−36Ni合金には、Mn含有
量に反比例してSの濃化量が減少していることがわかっ
た。すなわち、Mn含有量の低い低熱膨張Fe-36Ni合金中
には、Mn系介在物に取り込まれないSが多く存在し、こ
のSが光輝焼鈍時に表層近くに拡散し濃化するというこ
とがわかった。That is, according to the research by the inventors, Fe-36Ni
There is no enrichment of S in the surface layer of the alloy plate in Fe-Ni alloys with high Mn content, and low thermal expansion Fe-36Ni with low Mn content.
Notable in alloys and high Mn content
Although S was incorporated in the Mn-based inclusions in the Fe-Ni-based alloy, the low thermal expansion Fe-36Ni alloy with a low Mn content showed a decrease in the concentration of S in inverse proportion to the Mn content. I found out. That is, in the low thermal expansion Fe-36Ni alloy with a low Mn content, there was a large amount of S that was not incorporated into the Mn-based inclusions, and this S was diffused and concentrated near the surface layer during bright annealing. .
【0010】一方で、発明者らは、このような錆の発生
を防止するためには、Mn系介在物生成元素のMnとSの成
分比を制御することが必要になるとの知見を得てさらに
研究をすすめた結果、MnとSとの関係が、Mn/S≧25を満
足するときに錆が発生しにくいことを見い出し、かつ表
面から150Åまでの領域におけるS濃度が、バルクの20倍
程度以下のときに、とくに錆が発生しにくいことがわか
った。On the other hand, the inventors have found that in order to prevent the occurrence of such rust, it is necessary to control the composition ratio of Mn and S of the Mn-based inclusion forming element. As a result of further research, we found that the relationship between Mn and S was less likely to cause rust when Mn / S ≧ 25 was satisfied, and the S concentration in the region from the surface to 150 Å was 20 times that of bulk. It was found that rust was less likely to occur when the amount was below a certain level.
【0011】さらに、Fe−Ni合金の耐食性は、結晶粒径
にも大きく依存していることがわかった。つまり、光揮
焼鈍後の耐食性は、その素材の結晶粒径に大きく依存
し、とくに結晶粒径が小さく(結晶粒度番号(ASTM)が
大きい)なるにつれて、その材料の耐食性が向上するこ
ともわかった。これは、結晶粒径が小さくなると結晶粒
界の面積が増加し、Sの拡散距離が長くなることによる
ものと考えられる。Further, it has been found that the corrosion resistance of the Fe-Ni alloy also greatly depends on the crystal grain size. In other words, it was also found that the corrosion resistance after light annealing greatly depends on the crystal grain size of the material, and that the corrosion resistance of the material improves as the crystal grain size becomes smaller (the crystal grain size number (ASTM) is larger). It was It is considered that this is because as the crystal grain size becomes smaller, the area of the crystal grain boundary increases and the diffusion distance of S becomes longer.
【0012】さらに、錆の発生を抑えるには、上記の対
処に加えて、非金属介在物を制御することもまた有効で
あることがわかった。それは 酸可溶性のMgO単体介在
物、CaO単体介在物が生成すると、大気中で結露した場
合の耐食性が劣化し、さらにNb含有Fe−36Ni合金では、
アルミナ系介在物を防止した際に生成するMnO−FeO−Si
O2−Nb2O5−MgO−Al2O3−CaO系複合酸化物中に、MgO単
体介在物あるいはCaO単体介在物をともに含有する場
合、やはり耐食性が劣化することがわかった。一方、こ
れらMgO単体介在物やCaO単体介在物を含まない介在物組
成のものは、耐食性に問題がなかったことから、耐食性
向上のためには、MnO−FeO−SiO2−Nb 2O5−MgO−Al2O3
−CaO系複合酸化物の他にさらに、シリカ(SiO2)、ス
ピネル(MgO・Al2O3)、およびニオブ酸化物(Nb2O5)
のうちから選ばれるいずれか1種または2種以上を含むも
のからなる非金属介在物にすることが有効であることが
わかった。Furthermore, in order to suppress the generation of rust, the above
In addition to control, it is also effective to control non-metallic inclusions.
I knew it was. It is mediated by acid soluble MgO
When the inclusions of CaO and CaO are generated, the
Corrosion resistance deteriorates, and in Nb-containing Fe-36Ni alloy,
MnO-FeO-Si formed when alumina inclusions are prevented
O2−Nb2OFive−MgO−Al2O3− In the CaO-based composite oxide, MgO
When both body inclusions or CaO simple substance inclusions are included
However, it was also found that the corrosion resistance deteriorates. On the other hand, this
These inclusions do not include MgO single inclusions or CaO single inclusions
There was no problem in corrosion resistance, so
For improvement, MnO-FeO-SiO2−Nb 2OFive−MgO−Al2O3
− In addition to CaO-based composite oxides, silica (SiO 22),
Pinel (MgO ・ Al2O3), And niobium oxide (Nb2OFive)
Also includes any one or more selected from
It is effective to use non-metallic inclusions consisting of
all right.
【0013】本発明は、これらの知見に基づいて完成し
たものであって、その要旨構成は下記のとおりである。The present invention has been completed based on these findings, and its gist structure is as follows.
【0014】すなわち、本発明は、C≦0.01wt%、Si:0.
01〜0.1wt%、Mn:0.01〜0.1wt%、Ni:35〜37wt%、Cr≦
0.1wt%、Nb:0.01〜1.0wt%、S≦0.0020wt%、Al≦0.005w
t%、残部がFeおよび不可避的不純物からなる耐食性に優
れるシャドウマスク素材用Fe−Ni系合金である。なお、
本発明の合金はまた、上記成分組成に加えて、さらに、
Ti、V、Zr、Ta、HfおよびREMのうちから選ばれるいずれ
か1種または2種以上を、合計量で0.005〜1.0%を含有す
ることが好ましい。That is, according to the present invention, C ≦ 0.01 wt%, Si: 0.
01-0.1wt%, Mn: 0.01-0.1wt%, Ni: 35-37wt%, Cr≤
0.1wt%, Nb: 0.01-1.0wt%, S ≦ 0.0020wt%, Al ≦ 0.005w
It is a Fe-Ni alloy for shadow mask materials, which is excellent in corrosion resistance, consisting of t% and the balance Fe and inevitable impurities. In addition,
The alloy of the present invention also has, in addition to the above composition,
It is preferable to contain any one or more selected from Ti, V, Zr, Ta, Hf and REM in a total amount of 0.005 to 1.0%.
【0015】本発明にかかる上記合金はまた、MnとSと
の関係を、Mn/S≧25にした合金であることが好ましい。The above alloy according to the present invention is also preferably an alloy in which the relationship between Mn and S is Mn / S ≧ 25.
【0016】本発明はまた、この合金の表面から150Å
までの領域は、S濃度の最大値がバルクの20倍以下であ
ることが好ましい。The present invention also provides 150Å from the surface of this alloy.
It is preferable that the maximum concentration of S is 20 times or less that of the bulk.
【0017】さらにまた、本発明の合金は、結晶粒度が
ASTM粒度番号の No.9以上の大きさのものであることが
好ましい。Furthermore, the alloy of the present invention has a grain size of
It is preferable that the size is ASTM No. 9 or larger.
【0018】さらにまた、本発明の合金は、MnO−FeO−
SiO2−Nb2O5−MgO−Al2O3−CaO系複合酸化物の他、さら
にシリカ(SiO2)スピネル(MgO・Al2O3)およびニオブ
酸化物(Nb2O5)のうちのいずれか1種または2種以上を
含むものからなる非金属介在物を含有することが好まし
い。Furthermore, the alloy of the present invention is MnO-FeO-
In addition to SiO 2 —Nb 2 O 5 —MgO—Al 2 O 3 —CaO composite oxide, among silica (SiO 2 ) spinel (MgO · Al 2 O 3 ) and niobium oxide (Nb 2 O 5 ). It is preferable to contain a nonmetallic inclusion consisting of any one of the above or two or more.
【0019】本発明はまた、上記Fe−Ni系合金からな
り、この合金の0.2%耐力が300N/mm2以上でかつ30〜100
℃の熱膨張係数が1.0×10−6/℃以下の特性を有する高
耐食高剛性低熱膨張のシャドウマスク材料を提案する。The present invention also comprises the above Fe-Ni alloy, which has a 0.2% proof stress of 300 N / mm 2 or more and 30 to 100.
We propose a high-corrosion, high-rigidity, low-thermal-expansion shadow mask material that has a thermal expansion coefficient of 1.0 x 10 -6 / ° C or less.
【0020】[0020]
【発明の実施の形態】以下、本発明に係るFe−Ni系合金
の組成を上記のように規定した理由について説明する。C≦0.01wt%
Cは、固溶および加工硬化作用による材質の強化に寄与
する元素である。その含有量が、0.01wt%を超えると炭
化物が多く析出してエッチング性、プレス成形性、黒化
性および低熱膨張特性を悪くする。そのため、Cの含有
量は、0.01wt%以下に限定する。好ましくは0.005wt%以
下とする。BEST MODE FOR CARRYING OUT THE INVENTION Fe-Ni alloy according to the present invention
The reason for defining the composition of as described above will be described.C ≦ 0.01 wt%
C contributes to strengthening the material by solid solution and work hardening action
It is an element that does. If the content exceeds 0.01 wt%, charcoal
Of a large amount of compounds precipitate, resulting in etchability, press moldability, and blackening
And low thermal expansion characteristics are deteriorated. Therefore, the content of C
The amount is limited to 0.01 wt% or less. Preferably 0.005 wt% or less
Below.
【0021】Si:0.01〜0.1wt%
Siは、合金の精錬に際して、脱酸材として0.01wt%以上
の添加が必要となるが、0.1wt%を超えて添加すると熱膨
張を増大させるので、0.01〜0.1wt%の範囲に定めた。好
ましくは0.02〜0.05wt%である。[0021]Si: 0.01-0.1wt%
Si is 0.01 wt% or more as a deoxidizing material when refining alloys.
Is required, but if added over 0.1 wt%, thermal expansion
Since the tensile strength is increased, the range is set to 0.01 to 0.1 wt%. Good
It is preferably 0.02 to 0.05 wt%.
【0022】Mn:0.01〜0.1wt%
Mnは、固溶強化元素として有用であり、さらに合金の精
錬に際して、脱酸材として0.01wt%以上の添加が必要で
ある。しかし、その含有量が0.1wt%を超えて添加される
と熱膨張を増大させるので、0.01〜0.1wt%の範囲に定め
た。好ましくは0.01〜0.05wt%である。また、このMnを
添加することにより、Mn系介在物が生成し、これが光揮
焼鈍時に拡散してくるSを固着するので、一定量のMn系
介在物が必要である。よって、このMnはSの関係におい
て、耐食性の面でMn/S≧25を満足するように制御するこ
とが必要である。[0022]Mn: 0.01-0.1wt%
Mn is useful as a solid solution strengthening element,
It is necessary to add 0.01 wt% or more as a deoxidizing material during smelting.
is there. However, its content exceeds 0.1 wt%
And increase the thermal expansion, so set it in the range of 0.01 to 0.1 wt%.
It was It is preferably 0.01 to 0.05 wt%. Also, this Mn
When added, Mn-based inclusions are generated, which are
Since S that diffuses during annealing is fixed, a certain amount of Mn-based
Inclusions are required. Therefore, this Mn is in the relationship of S
Control in terms of corrosion resistance so that Mn / S ≧ 25 is satisfied.
And are required.
【0023】Ni:35〜37wt%
Niは、Fe−Ni合金の熱膨張特性に大きな影響を及ぼす元
素である。このNiの含有量が36wt%のとき、熱膨張が最
小となるため、Niは35〜37wt%に限定した。[0023]Ni: 35-37wt%
Ni has a large effect on the thermal expansion characteristics of the Fe-Ni alloy.
It is plain. When the Ni content is 36 wt%, the thermal expansion is maximum.
Since it is small, Ni is limited to 35 to 37 wt%.
【0024】Cr≦0.1wt%
Crは、耐食性を著しく向上させる元素であるが0.1wt%を
超えると熱膨張係数が高くなり、また、黒化性も劣化す
るため、0.1wt%以下に限定する。[0024]Cr ≦ 0.1wt%
Cr is an element that significantly improves corrosion resistance.
If it exceeds, the coefficient of thermal expansion will be high and the blackening property will be deteriorated.
Therefore, it is limited to 0.1 wt% or less.
【0025】Nb:0.01〜1.0wt%
Nbは、これを合金中に添加すると、0.2%耐力が増大す
る。また、結晶粒度を著しく微細化し、結晶粒界の面積
を増加させ、光揮焼鈍時に、Sの拡散距離を長くして表
面のSの濃化を抑制する効果がある。また、靭性、エッ
チング性、プレス成形性をともに向上させるとともに黒
化性をも向上させる。従って、Nbは、上記の効果を得る
ために、とくに耐食性、0.2%耐力を付与するために、少
なくとも0.01wt%以上の添加を必要とする。好ましくは
0.10wt%以上を添加した方がよい。しかし、1.0wt%を超
えて添加すると、靭性、プレス成形性、低熱膨張特性を
却って低下させるため、0.01〜1.0wt%に限定する。[0025]Nb: 0.01-1.0wt%
Nb increases the 0.2% proof stress when it is added to the alloy.
It In addition, the crystal grain size has been significantly reduced, and the grain boundary area
Is increased and the diffusion distance of S is lengthened during light annealing.
It has the effect of suppressing the enrichment of S on the surface. Also, toughness, essence
Improves both chingability and press formability, and is black
It also improves the chemical conversion property. Therefore, Nb obtains the above effect
In order to provide corrosion resistance and 0.2% proof stress.
At least 0.01 wt% or more must be added. Preferably
It is better to add 0.10 wt% or more. However, above 1.0 wt%
If added, the toughness, press formability, and low thermal expansion properties can be improved.
On the contrary, since it lowers, it is limited to 0.01 to 1.0 wt%.
【0026】S≦0.0020wt%
Sは、本発明に係る合金を特徴づける元素であり、耐食
性に大きな影響を及ぼす元素である。このSの含有量が
0.0020wt%を超えると、光揮焼鈍後にSが表面近傍まで拡
散し、表面から150ÅまでのS濃度がバルクに対し著しく
上昇し、耐食性を低下させる。そのためSの含有量は0.0
020wt%以下とし、好ましくは0.0010wt%以下とした。た
だし、このSは、Mnとの関係において、Mn/S≧25を満足
させることが必要である。[0026]S ≦ 0.0020wt%
S is an element that characterizes the alloy according to the present invention, and corrosion resistance
It is an element that greatly affects the properties. The content of this S is
If it exceeds 0.0020 wt%, S spreads near the surface after light annealing.
Scattered, and the S concentration from the surface to 150 Å is remarkable for bulk
Increases and reduces corrosion resistance. Therefore, the S content is 0.0
The content is 020 wt% or less, preferably 0.0010 wt% or less. Was
However, this S satisfies Mn / S ≧ 25 in relation to Mn.
It is necessary to let
【0027】Al≦0.005wt%
Alは、比較的活性な元素であるから、多量に含まれる
と、鋼鈑表面での優先酸化しを生じて黒化性を阻害す
る。さらにAl系酸化物を増加してエッチング性を阻害す
る。とくに、0.005wt%を超えると低熱膨張特性を低下さ
せるので、0.005wt%に限定した。[0027]Al ≦ 0.005wt%
Al is a relatively active element, so it is contained in large amounts.
And causes preferential oxidation on the surface of the steel plate and hinders blackening.
It Furthermore, it increases the Al-based oxide and hinders the etching property.
It In particular, if it exceeds 0.005 wt%, the low thermal expansion properties deteriorate.
Therefore, it was limited to 0.005 wt%.
【0028】Ti、V、Zr、Ta、HfおよびREM
Ti、V、Zr、Ta、HfおよびREMは、CおよびNと結合して炭
化物、窒化物を形成し結晶粒微細化に寄与する元素であ
り、Sと結合し硫化物を形成し耐食性にも寄与する。T
i、V、Zr、Ta、Hf及びREM(希土類元素)の中から選ば
れるいずれか1種または2種以上が、単独または合計で0.
005wt%未満では、上記効果が不十分になる。一方、1.0w
t%より多いと、これら元素の固溶量が多くなりすぎて、
低熱膨張特性を低下させるため、0.005〜1.0wt%に限定
した。[0028]Ti, V, Zr, Ta, Hf and REM
Ti, V, Zr, Ta, Hf and REM combine with C and N
Is an element that forms oxides and nitrides and contributes to grain refinement.
It also combines with S to form sulfides and contributes to corrosion resistance. T
Selected from i, V, Zr, Ta, Hf and REM (rare earth elements)
Any one or two or more of them are 0 alone or in total.
If it is less than 005 wt%, the above effect becomes insufficient. On the other hand, 1.0w
If it is more than t%, the solid solution amount of these elements becomes too large,
Limited to 0.005-1.0wt% to reduce low thermal expansion properties
did.
【0029】Mn/S≧25
本発明に係るFe−Ni合金おいては、MnとSとは、次式;
Mn/S≧25
の関係を満足する範囲内に収まるように調整する必要が
ある。すなわち、Sの含有量に応じてMnの含有量を調整
し、耐食性に悪影響を及ぼすS含有量をMnで制御するこ
とが肝要である。つまり、Mn/Sの比が25未満では、Mn系
介在物中に取り込まれるS量が少なく、光輝焼鈍時にSが
表層近くまで拡散、濃化し、錆が発生しやすくなる。[0029]Mn / S ≧ 25
In the Fe-Ni alloy according to the present invention, Mn and S are represented by the following formulas;
Mn / S ≧ 25
Need to be adjusted to be within the range that satisfies the relationship
is there. That is, the content of Mn is adjusted according to the content of S
However, the S content that adversely affects the corrosion resistance can be controlled with Mn.
And are essential. That is, if the ratio of Mn / S is less than 25,
The amount of S incorporated in inclusions is small, and S
Diffuses and thickens near the surface layer, and rust easily occurs.
【0030】次に、本発明に係るFe−Ni合金において
は、合金板表面から150Åまでの領域におけるS濃度をバ
ルクの20倍程度以下とする。この理由は、表層中におけ
るSの濃化の程度が、バルク(基地)のS濃度の20倍を超
えると、金属イオンの溶解を促進し、錆を誘発させるか
らである。なお、このS濃度は、より好ましくは18倍以
下である。Next, in the Fe-Ni alloy according to the present invention, the S concentration in the region from the alloy plate surface to 150 Å is set to about 20 times the bulk or less. The reason for this is that if the concentration of S in the surface layer exceeds 20 times the concentration of S in the bulk (base), it promotes the dissolution of metal ions and induces rust. The S concentration is more preferably 18 times or less.
【0031】結晶粒度
本発明は、上記成分設計に加えて、結晶粒度をASTM 粒
度番号でNo.9以上の大きさとすることが有効である。本
発明者らの研究によると、Fe−Ni系合金の光揮焼鈍後の
耐食性は、素材の結晶粒径に大きく依存し、とくに結晶
粒径が小さく(結晶粒度番号が大きい)なるにつれて、
その材料の耐食性が向上することがわかった。また、0.
2%耐力も結晶粒径に大きく依存することから優れた耐食
性、剛性を得るには結晶粒度がASTM No.9以上とするこ
とが望ましい。[0031]Grain size
In addition to the above component design, the present invention uses the grain size of ASTM grain
It is effective to set the size to No. 9 or above. Book
According to the research conducted by the inventors, the Fe-Ni alloys after light-annealing
Corrosion resistance greatly depends on the crystal grain size of the material,
As the grain size decreases (grain size number increases),
It has been found that the corrosion resistance of the material is improved. Also, 0.
Excellent corrosion resistance as the 2% proof stress also largely depends on the grain size.
The grain size must be ASTM No. 9 or more to obtain the property and rigidity.
And is desirable.
【0032】非金属介在物
上記成分設計と結晶粒度調整に加えて本発明では、さら
に非金属介在物の制御を行う。すなわち、本発明合金中
に含まれる非金属介在物は、MnO−FeO−SiO2−Nb2O5−M
gO−Al2O3−CaO系複合酸化物の他にさらに、SiO2、MgO
・Al2O3、Nb2O5のうちのいずれか1種または2種以上を含
有するものからなる非金属介在物とする必要がある。発
明者らの研究によると、酸可溶性のMgO単体介在物、CaO
単体介在物が生成すると、大気中で結露した場合の耐食
性が劣化することがわかった。さらにNb含有Fe-36Ni合
金では、アルミナ系介在物を防止した際に生成するMnO
−FeO−SiO2−Nb2O5−MgO−Al2O3−CaO系複合酸化物中
に、MgO単体介在物あるいはCaO単体介在物をともに含有
する場合、やはり耐食性が劣化することがわかった。一
方、これらMgO単体介在物、CaO単体介在物を含まない介
在物組成のものは耐食性に問題を起こさなかったことか
ら、上記介在物の組成にすることとした。[0032]Non-metallic inclusion
In addition to the above component design and grain size adjustment, the present invention further
Control non-metallic inclusions. That is, in the alloy of the present invention
The non-metallic inclusions contained in MnO-FeO-SiO2−Nb2OFive−M
gO-Al2O3− In addition to CaO-based composite oxide, SiO2, MgO
・ Al2O3, Nb2OFiveOne or more of
It is necessary to make it a non-metallic inclusion made up of. Departure
According to the study by the authors, CaO, which is an acid-soluble MgO simple substance inclusion,
Corrosion resistance when condensation occurs in the atmosphere when single inclusions are generated
It was found that the property deteriorates. Furthermore, Nb-containing Fe-36Ni alloy
In gold, MnO generated when alumina inclusions are prevented
-FeO-SiO2−Nb2OFive−MgO−Al2O3− In CaO-based complex oxide
Contains both MgO simple substance inclusions and CaO simple substance inclusions
However, it was found that the corrosion resistance was deteriorated. one
However, these MgO single inclusions and CaO single inclusions are not included.
Did the composition of existing materials cause no problem in corrosion resistance?
The composition of the above inclusions was decided.
【0033】[0033]
【実施例】以下、実施例をもって本発明に係る合金の作
用効果について具体的に説明するが、本発明はこの実施
例に限定されるものではない。供試材は、後述する表1
に示す成分組成となるように、合金の各成分を調整して
試験材を製造し、その試験材を大気誘導炉で溶解してイ
ンゴットを製作し、次いでこのインゴットを1000〜1150
℃の温度で熱間鍛造加工を施し、圧延率80%以上で圧延
加工を行い、そして900℃−60秒、30%H2+N2、露点−40
℃の雰囲気で固溶化熱処理を行った。その後、徐冷して
厚さ0.12mmのFe−Ni合金板を得た。EXAMPLES The working effects of the alloy according to the present invention will be specifically described below with reference to examples, but the present invention is not limited to these examples. The test materials are listed in Table 1 below.
To prepare the test material by adjusting each component of the alloy so as to have the composition shown in Fig. 1, the test material is melted in an atmospheric induction furnace to produce an ingot, and then this ingot is 1000 to 1150
Hot forged at a temperature of ℃, rolled at a rolling rate of 80% or more, and 900 ℃ for 60 seconds, 30% H 2 + N 2 , dew point of -40
Solution heat treatment was performed in an atmosphere of ° C. Then, it was gradually cooled to obtain a Fe-Ni alloy plate having a thickness of 0.12 mm.
【0034】表中の熱膨張係数は、常温から300℃まで
の範囲で測定し、30〜100℃の平均熱膨張係数を求め、
0.2%耐力は引張試験により測定した。また、板表面から
150Åにおける領域のS濃化量の最大値は、オージェ電子
分光分析装置を用い、表面から50Å間隔でスパッタリン
グを行い、その都度元素分析を実施し、Sの原子濃度を
算出し、バルク(バルクとは本件では、素材全体を化学
的に分析した値である。)との比で表わした。耐食性
は、屋外大気暴露試験にて、暴露後の腐食状況を発錆面
積率にて評価した。なお、発錆面積率が0.5%以上のも
のは素材製造の中間工程である光輝焼鈍後、大気に長時
間さらされると錆を発生するので、素材としては不適当
であった。これらの結果を表2に示す。The coefficient of thermal expansion in the table is measured from room temperature to 300 ° C., and the average coefficient of thermal expansion of 30 to 100 ° C. is obtained.
The 0.2% proof stress was measured by a tensile test. Also, from the board surface
The maximum amount of S concentration in the region of 150 Å is calculated by using Auger electron spectroscopy at 50 Å intervals from the surface, performing elemental analysis each time, calculating the atomic concentration of S, and measuring the bulk (bulk and bulk). Is the value obtained by chemically analyzing the entire material in this case). The corrosion resistance was evaluated by the outdoor air exposure test, and the corrosion state after exposure was evaluated by the rusting area ratio. It should be noted that a material having a rusting area ratio of 0.5% or more was unsuitable as a material because it would generate rust after being exposed to the atmosphere for a long time after bright annealing, which is an intermediate step of manufacturing the material. The results are shown in Table 2.
【0035】表2から明らかなように、本発明に適合す
る合金は、耐食性、剛性および低熱膨張特性の面におい
て十分な特性を有しているといえる。すなわち、本発明
に係る試験材は、0.2%耐力が300N/mm2以上であり、高剛
性を有し、熱膨張係数が1.0×10-6/℃以下で低熱膨張で
ある。また、大気暴露試験後の発錆面積率が0.5%以下で
あり、優れた耐食性を有する。これに対して、比較材1
9、20は、バルクのS量が多いため耐食性に劣る。また、
比較材21、22は介在物形態がMgO単体、CaO単体を含むた
め耐食性に劣っている。比較材23は、結晶粒径が大きい
ために耐食性、剛性に劣っている。比較例24は、板表面
から150Åにおける領域のS濃化量の最大値が20以上であ
るため、耐食性に劣っている。なお、本発明の上記Fe−
Ni系合金を、シャドウマスク材料として製造したもの
は、光揮焼鈍後に錆の発生なく製造することができた。
とくに、素材の品質としてマスク成形前の0.2%耐力が30
0N/mm2以上であり、熱膨張係数が1.0×10−6/℃以下で
高剛性でかつ低熱膨張のシャドウマスク素材を製造する
ことができた。As is clear from Table 2, it can be said that the alloys conforming to the present invention have sufficient characteristics in terms of corrosion resistance, rigidity and low thermal expansion characteristics. That is, the test material according to the present invention has a 0.2% proof stress of 300 N / mm 2 or more, high rigidity, and a low thermal expansion coefficient of 1.0 × 10 −6 / ° C. or less. Further, the rusted area ratio after the atmospheric exposure test is 0.5% or less, and it has excellent corrosion resistance. On the other hand, comparative material 1
9 and 20 are inferior in corrosion resistance due to the large amount of S in bulk. Also,
The comparative materials 21 and 22 are inferior in corrosion resistance because the inclusion forms include MgO simple substance and CaO simple substance. Comparative material 23 is inferior in corrosion resistance and rigidity because of its large crystal grain size. Comparative Example 24 is inferior in corrosion resistance because the maximum S concentration amount in the region 150 Å from the plate surface is 20 or more. The Fe-
The Ni-based alloy produced as a shadow mask material could be produced without rusting after light annealing.
Especially, 0.2% proof stress before mask molding is 30 as material quality.
A shadow mask material having a thermal expansion coefficient of 0 N / mm 2 or more and a thermal expansion coefficient of 1.0 × 10 −6 / ° C. or less and high rigidity and low thermal expansion could be manufactured.
【0036】[0036]
【表1】 [Table 1]
【0037】[0037]
【表2】 [Table 2]
【0038】[0038]
【発明の効果】以上説明したように本発明によれば、素
材製造の中間工程である光揮焼鈍後の流通や運搬の過程
において大気中にさらされたときでも、錆が発生しづら
い高耐食高剛性低熱膨張のシャドウマスク用Fe−Ni系合
金を提供することができる。従って、映像のきれいなカ
ラーブラウン管やディスプレー用のシャドウマスク材料
を確実にかつ高い収率で提供することができる。As described above, according to the present invention, even when exposed to the atmosphere in the process of distribution or transportation after light volatilization annealing, which is an intermediate step of material production, rust hardly occurs and high corrosion resistance It is possible to provide an Fe—Ni-based alloy for a shadow mask having high rigidity and low thermal expansion. Therefore, it is possible to reliably provide a color cathode ray tube with a clear image and a shadow mask material for a display in a high yield.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 小林 裕 神奈川県川崎市川崎区小島町4番2号 日 本冶金工業株式会社技術研究所内 Fターム(参考) 5C031 EE05 ─────────────────────────────────────────────────── ─── Continued front page (72) Inventor Yutaka Kobayashi 4-2 Kojima-cho, Kawasaki-ku, Kawasaki-shi, Kanagawa Inside the Technical Research Laboratory, Honkin Kogyo Co., Ltd. F-term (reference) 5C031 EE05
Claims (7)
01〜0.1wt%、Ni:35〜37wt%、Cr≦0.1wt%、Nb:0.01〜
1.0wt%、S≦0.0020wt%、Al≦0.005wt%、残部がFeおよび
不可避的不純物からなる耐食性に優れるシャドウマスク
素材用Fe−Ni系合金。1. C ≦ 0.01 wt%, Si: 0.01 to 0.1 wt%, Mn: 0.
01-0.1wt%, Ni: 35-37wt%, Cr ≦ 0.1wt%, Nb: 0.01-
Fe-Ni alloy for shadow mask materials, which is 1.0 wt%, S ≤ 0.0020 wt%, Al ≤ 0.005 wt%, the balance being Fe and unavoidable impurities and having excellent corrosion resistance.
の関係を、Mn/S≧25にしたことを特徴とするシャドウマ
スク素材用Fe−Ni系合金。2. The Fe-Ni alloy for a shadow mask material according to claim 1, wherein the relationship between Mn and S is Mn / S ≧ 25.
V、Zr、Ta、HfおよびREMのうちから選ばれるいずれか1
種または2種以上を、合計量で0.005〜1.0%を含有するこ
とを特徴とする請求項1または2に記載のシャドウマス
ク素材用Fe−Ni系合金。3. In addition to the above component composition, Ti,
Any one selected from V, Zr, Ta, Hf and REM 1
The Fe-Ni-based alloy for a shadow mask material according to claim 1 or 2, characterized in that it contains 0.005 to 1.0% in total of two or more kinds.
組成を有する合金は、その表面から150Åまでの領域
は、S濃度の最大値がバルクの20倍以下に制御されてい
ることを特徴とする請求項1〜3のいずれか1項に記載
のシャドウマスク素材用Fe−Ni系合金。4. The alloy having the composition of any one of claims 1 to 3 has a maximum S concentration controlled to 20 times or less that of the bulk in the region from the surface to 150 Å. The Fe-Ni-based alloy for a shadow mask material according to any one of claims 1 to 3, which is characterized in that.
ある請求項1〜4のいずれか1項に記載のシャドウマス
ク素材用Fe−Ni系合金。5. The Fe-Ni-based alloy for a shadow mask material according to any one of claims 1 to 4, which has a grain size of ASTM No. 9 or more.
aO系複合酸化物の他、さらにシリカ(SiO2)スピネル
(MgO・Al2O3)およびニオブ酸化物(Nb2O5)のうちの
いずれか1種または2種以上を含有するものからなる非金
属介在物を含有することを特徴とする請求項1〜5のい
ずれか1項に記載の耐食性に優れるシャドウマスク素材
用Fe−Ni系合金。6. MnO-FeO-SiO 2 -Nb 2 O 5 -MgO-Al 2 O 3 -C
In addition to aO-based complex oxide, it contains one or more of silica (SiO 2 ) spinel (MgO.Al 2 O 3 ) and niobium oxide (Nb 2 O 5 ). The Fe-Ni alloy for a shadow mask material having excellent corrosion resistance according to any one of claims 1 to 5, which contains a non-metallic inclusion.
−Ni系合金からなり、この合金の0.2%耐力が300N/mm2以
上でかつ30〜100℃の熱膨張係数が1.0×10− 6/℃以下
の特性を有することを特徴とする高耐食高剛性低熱膨張
のシャドウマスク材料。7. Fe according to any one of claims 1 to 6.
Consists -Ni system alloy, the thermal expansion coefficient of 0.2% proof stress of the alloy is 300N / mm 2 or more and 30 to 100 ° C. is 1.0 × 10 - high corrosion resistance and high, characterized in that it has a characteristic of 6 / ° C. or less Rigid low thermal expansion shadow mask material.
Priority Applications (6)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2001323145A JP3854121B2 (en) | 2001-10-22 | 2001-10-22 | Fe-Ni alloy for shadow mask material with excellent corrosion resistance and shadow mask material |
PCT/JP2002/010718 WO2003035920A1 (en) | 2001-10-22 | 2002-10-16 | Fe-Ni BASE ALLOY FOR SHADOW MASK RAW MATERIAL EXCELLENT IN CORROSION RESISTANCE AND SHADOW MASK MATERIAL |
US10/488,257 US20040238076A1 (en) | 2001-10-22 | 2002-10-16 | Fe-ni based alloy for shadow mask raw material excellent in corrosion resistance and shadow mask material |
KR1020047005785A KR100595393B1 (en) | 2001-10-22 | 2002-10-16 | FeNi BASE ALLOY FOR SHADOW MASK RAW MATERIAL EXCELLENT IN CORROSION RESISTANCE AND SHADOW MASK MATERIAL |
EP02777848A EP1445341A4 (en) | 2001-10-22 | 2002-10-16 | Fe-Ni BASED ALLOY FOR SHADOW MASK HAVING EXCELLENT CORROSION RESISTANCE AND SHADOW MASK MATERIAL |
CNB028207742A CN100343405C (en) | 2001-10-22 | 2002-10-16 | Fe-Ni based alloy for shadow mask raw material excellent in corrosion resistance and shadow mask material |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2001323145A JP3854121B2 (en) | 2001-10-22 | 2001-10-22 | Fe-Ni alloy for shadow mask material with excellent corrosion resistance and shadow mask material |
Publications (2)
Publication Number | Publication Date |
---|---|
JP2003129185A true JP2003129185A (en) | 2003-05-08 |
JP3854121B2 JP3854121B2 (en) | 2006-12-06 |
Family
ID=19140077
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP2001323145A Expired - Fee Related JP3854121B2 (en) | 2001-10-22 | 2001-10-22 | Fe-Ni alloy for shadow mask material with excellent corrosion resistance and shadow mask material |
Country Status (6)
Country | Link |
---|---|
US (1) | US20040238076A1 (en) |
EP (1) | EP1445341A4 (en) |
JP (1) | JP3854121B2 (en) |
KR (1) | KR100595393B1 (en) |
CN (1) | CN100343405C (en) |
WO (1) | WO2003035920A1 (en) |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
KR20160077514A (en) | 2014-12-23 | 2016-07-04 | 주식회사 포스코 | Encapsulant for packaging an organic electric device for display with low thermal expansion coefficient |
KR20160079968A (en) | 2014-12-26 | 2016-07-07 | 주식회사 포스코 | Encapsulant for packaging an organic electric device for display with low thermal expansion coefficient |
Families Citing this family (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US20220380872A1 (en) * | 2019-12-27 | 2022-12-01 | Nippon Steel Corporation | Alloy |
CN115976395A (en) * | 2022-12-28 | 2023-04-18 | 北冶功能材料(江苏)有限公司 | Preparation method of invar alloy for metal mask |
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JPH05186853A (en) * | 1992-01-09 | 1993-07-27 | Nippon Yakin Kogyo Co Ltd | Invar alloy for shadow mask |
JPH07102345A (en) * | 1993-09-30 | 1995-04-18 | Nippon Yakin Kogyo Co Ltd | Fe-ni alloy with high young's modulus and low thermal expansion |
JPH0987808A (en) * | 1995-09-28 | 1997-03-31 | Nikko Kinzoku Kk | Iron-nickel alloy for electron gun part, and press-blanked electron gun part |
JP2001040454A (en) * | 1999-07-28 | 2001-02-13 | Nippon Yakin Kogyo Co Ltd | Fe-Ni BASED MATERIAL FOR SHADOW MASK |
JP2001181796A (en) * | 1999-12-28 | 2001-07-03 | Hitachi Metals Ltd | Fe-Ni-Co ALLOY EXCELLENT IN ETCHING CHARACTERISTIC AND LOW THERMAL EXPANSION CHARACTERISTIC, AND SHADOW MASK EXCELLENT IN ETCHING PIT SHAPE CHARACTERISTIC |
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JP3151100B2 (en) * | 1994-01-14 | 2001-04-03 | 日鉱金属株式会社 | Fe-Ni alloy shadow mask material |
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JP3450711B2 (en) * | 1998-07-02 | 2003-09-29 | 日本冶金工業株式会社 | Fe-Ni lead frame alloy with excellent punching characteristics |
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JP3802326B2 (en) * | 2000-08-30 | 2006-07-26 | 日鉱金属株式会社 | Manufacturing method for preventing hot rolling crack of Fe-Ni alloy material having resistance to drop impact deformation and low thermal expansion |
JP4240823B2 (en) * | 2000-09-29 | 2009-03-18 | 日本冶金工業株式会社 | Method for producing Fe-Ni permalloy alloy |
JP3927494B2 (en) * | 2000-11-21 | 2007-06-06 | 日本冶金工業株式会社 | Fe-Ni alloy material for shadow mask with excellent etching processability |
CN1200130C (en) * | 2001-07-05 | 2005-05-04 | 杰富意钢铁株式会社 | Thin alloy sheet of low thermal expansion and shadow mask using the same |
-
2001
- 2001-10-22 JP JP2001323145A patent/JP3854121B2/en not_active Expired - Fee Related
-
2002
- 2002-10-16 US US10/488,257 patent/US20040238076A1/en not_active Abandoned
- 2002-10-16 KR KR1020047005785A patent/KR100595393B1/en not_active IP Right Cessation
- 2002-10-16 EP EP02777848A patent/EP1445341A4/en not_active Withdrawn
- 2002-10-16 WO PCT/JP2002/010718 patent/WO2003035920A1/en active Application Filing
- 2002-10-16 CN CNB028207742A patent/CN100343405C/en not_active Expired - Fee Related
Patent Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
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JPH05186853A (en) * | 1992-01-09 | 1993-07-27 | Nippon Yakin Kogyo Co Ltd | Invar alloy for shadow mask |
JPH07102345A (en) * | 1993-09-30 | 1995-04-18 | Nippon Yakin Kogyo Co Ltd | Fe-ni alloy with high young's modulus and low thermal expansion |
JPH0987808A (en) * | 1995-09-28 | 1997-03-31 | Nikko Kinzoku Kk | Iron-nickel alloy for electron gun part, and press-blanked electron gun part |
JP2001040454A (en) * | 1999-07-28 | 2001-02-13 | Nippon Yakin Kogyo Co Ltd | Fe-Ni BASED MATERIAL FOR SHADOW MASK |
JP2001181796A (en) * | 1999-12-28 | 2001-07-03 | Hitachi Metals Ltd | Fe-Ni-Co ALLOY EXCELLENT IN ETCHING CHARACTERISTIC AND LOW THERMAL EXPANSION CHARACTERISTIC, AND SHADOW MASK EXCELLENT IN ETCHING PIT SHAPE CHARACTERISTIC |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
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KR20160077514A (en) | 2014-12-23 | 2016-07-04 | 주식회사 포스코 | Encapsulant for packaging an organic electric device for display with low thermal expansion coefficient |
KR20160079968A (en) | 2014-12-26 | 2016-07-07 | 주식회사 포스코 | Encapsulant for packaging an organic electric device for display with low thermal expansion coefficient |
Also Published As
Publication number | Publication date |
---|---|
US20040238076A1 (en) | 2004-12-02 |
CN100343405C (en) | 2007-10-17 |
KR20040045877A (en) | 2004-06-02 |
JP3854121B2 (en) | 2006-12-06 |
WO2003035920A1 (en) | 2003-05-01 |
KR100595393B1 (en) | 2006-06-30 |
EP1445341A1 (en) | 2004-08-11 |
CN1571857A (en) | 2005-01-26 |
EP1445341A4 (en) | 2004-12-15 |
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