JPH02101116A - Production of fe-ni alloy having significant streaking inhibiting effect at the time of etching - Google Patents
Production of fe-ni alloy having significant streaking inhibiting effect at the time of etchingInfo
- Publication number
- JPH02101116A JPH02101116A JP63251881A JP25188188A JPH02101116A JP H02101116 A JPH02101116 A JP H02101116A JP 63251881 A JP63251881 A JP 63251881A JP 25188188 A JP25188188 A JP 25188188A JP H02101116 A JPH02101116 A JP H02101116A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- etching
- forging
- time
- streaking
- 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.)
- Granted
Links
- 238000005530 etching Methods 0.000 title claims abstract description 21
- 238000004519 manufacturing process Methods 0.000 title claims description 7
- 229910000990 Ni alloy Inorganic materials 0.000 title description 5
- 230000002401 inhibitory effect Effects 0.000 title 1
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 27
- 239000000956 alloy Substances 0.000 claims abstract description 27
- 238000005242 forging Methods 0.000 claims abstract description 22
- 229910001030 Iron–nickel alloy Inorganic materials 0.000 claims abstract description 17
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 8
- 230000000694 effects Effects 0.000 claims description 6
- 239000010865 sewage Substances 0.000 claims description 2
- 238000010438 heat treatment Methods 0.000 abstract description 13
- 238000005204 segregation Methods 0.000 abstract description 12
- 239000000463 material Substances 0.000 abstract description 11
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 16
- 239000013078 crystal Substances 0.000 description 15
- 238000000034 method Methods 0.000 description 8
- 238000001259 photo etching Methods 0.000 description 6
- 238000005516 engineering process Methods 0.000 description 5
- 229910052804 chromium Inorganic materials 0.000 description 4
- 229910052799 carbon Inorganic materials 0.000 description 3
- 239000012535 impurity Substances 0.000 description 3
- 238000012545 processing Methods 0.000 description 3
- 238000005096 rolling process Methods 0.000 description 3
- 238000005266 casting Methods 0.000 description 2
- 238000007796 conventional method Methods 0.000 description 2
- 238000009792 diffusion process Methods 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 229910052710 silicon Inorganic materials 0.000 description 2
- 238000012549 training Methods 0.000 description 2
- 238000011282 treatment Methods 0.000 description 2
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 239000000853 adhesive Substances 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 229960002089 ferrous chloride Drugs 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 230000005484 gravity Effects 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- NMCUIPGRVMDVDB-UHFFFAOYSA-L iron dichloride Chemical compound Cl[Fe]Cl NMCUIPGRVMDVDB-UHFFFAOYSA-L 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 229910000889 permalloy Inorganic materials 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 230000002195 synergetic effect Effects 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
- H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
- H01F1/147—Alloys characterised by their composition
- H01F1/14708—Fe-Ni based alloys
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Physics & Mathematics (AREA)
- Mechanical Engineering (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Dispersion Chemistry (AREA)
- Power Engineering (AREA)
- Electromagnetism (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明は、エツチング時のスジむら抑制効果に優れるF
e−Ni系合金の製造方法に関し、特にカラーテレビブ
ラウン管のシャドウマスクや蛍光表示管等の電子機器用
材料として好適に用いられるFe−Ni系合金に関する
ものである。[Detailed Description of the Invention] [Industrial Application Field] The present invention provides F
The present invention relates to a method for producing an e-Ni alloy, and in particular to an Fe-Ni alloy that is suitably used as a material for electronic devices such as shadow masks for color TV cathode ray tubes and fluorescent display tubes.
なお、本発明のかかるFe−Ni系合金は、シャドウマ
スク用36N iアンバー合金、リードフレーム用42
Ni合金、低熱膨張特性や磁気的特性に着目して使用さ
れる電子、電磁用Fe−Ni系合金、および電磁用材料
として用いられるパーマロイ合金などを対象としている
。The Fe-Ni alloy of the present invention is 36Ni amber alloy for shadow masks and 42Ni amber alloy for lead frames.
Targets include Ni alloys, Fe-Ni alloys for electronic and electromagnetic applications that are used with a focus on low thermal expansion and magnetic properties, and permalloy alloys that are used as electromagnetic materials.
カラーテレビブラウン管のシャドウマスク素材用鉄−ニ
ソケル合金@ (Fe−Ni系合金)は、これをフォト
エツチング穿孔してシャドウマスクを製造する際に、白
すじ模様すなわち“スジむら”が発生する欠点のあるこ
とが指摘されていた。Iron-Nisokel alloy @ (Fe-Ni alloy) for use as a material for shadow masks for color TV cathode ray tubes has the drawback of producing white streaks or "uneven streaks" when producing shadow masks by photo-etching holes. One thing was pointed out.
従来、このエツチング時のスジむらの発生を抑制するた
めのいくつかの技術が提案されており、例えば特開昭6
0−128253号公報に開示の技術では、普通造塊イ
ンゴットを850℃以上に加熱後、各ヒートでのトータ
ル断面減少率40%以上の鍛造を施すことにより、ニッ
ケルの成分偏析部を軽減することを通じ、該スジむらの
発生を抑制している。In the past, several techniques have been proposed to suppress the occurrence of uneven streaks during etching.
The technology disclosed in Publication No. 0-128253 reduces the segregation of nickel components by heating an ordinary ingot to 850°C or higher and then forging it with a total area reduction rate of 40% or more in each heat. This suppresses the occurrence of uneven streaks.
また、特開昭61−223188号公報に開示の技術は
、インゴット製造時の偏析防止あるいは条材製造工程中
での熱処理によるニッケルの拡散処理を施すことにより
、ニッケルの偏析率、偏析帯を管理して、エツチングの
スジむらを抑制している。In addition, the technology disclosed in JP-A No. 61-223188 manages the segregation rate and segregation band of nickel by preventing segregation during ingot production or performing nickel diffusion treatment by heat treatment during the strip manufacturing process. This suppresses uneven etching lines.
しかしながら、特開昭60−128253号公報に開示
された上記従来技術は、トータル断面減少率が40%を
超えるような鍛造をすることが特徴であるが、一般にこ
の程度の作業は普通に行われる負荷であり、かような方
法では各種元素の偏析かなかなか消滅せず、したがって
、エツチング時のスジむらの発生を防止するのには不十
分であった。However, the above-mentioned conventional technology disclosed in JP-A No. 60-128253 is characterized by forging such that the total area reduction rate exceeds 40%, but this level of work is generally performed. However, such a method does not easily eliminate the segregation of various elements, and is therefore insufficient to prevent the occurrence of uneven streaks during etching.
一方、特開昭61−223188号公報に開示された上
記従来技術は、高温熱処理によるNiの拡散を通じてそ
の成分偏析を軽減することを特徴としているが、スラブ
段階での加熱に比べ板厚が薄いため酸化ロスが相対的に
大きくなり、歩留り低下が著し゛くなる点で問題点があ
った。On the other hand, the above-mentioned conventional technology disclosed in JP-A No. 61-223188 is characterized by reducing component segregation through diffusion of Ni through high-temperature heat treatment, but the plate thickness is thin compared to heating at the slab stage. Therefore, there was a problem in that the oxidation loss became relatively large, resulting in a significant decrease in yield.
特に高精度のものが要求される各種デイスプレィ用シャ
ドウマスクにおいては、穿孔される孔は民生用テレビシ
ャドウマスク孔の172程度の径でかつその数も2倍以
上であり、素材の良否がそのままエツチング時の孔の均
一性を左右するためスジむらの発生を完全に回避するの
は難しく、したがって、エツチング時のスジむらを完全
に抑制できないのが実情であった。In shadow masks for various displays that require particularly high precision, the holes to be drilled have a diameter of about 172 and more than twice the number of holes in consumer TV shadow masks, and the quality of the material is directly affected by etching. It is difficult to completely avoid the occurrence of streak unevenness because it affects the uniformity of the holes during etching, and therefore, the reality is that it is not possible to completely suppress the streak unevenness during etching.
本発明の目的は、かかる斯界の実情に鑑み、エツチング
時にスジむらが発生することのない合金材料、すなわち
Niを30〜80%含有′し、Bを0.001〜0.0
3%を含有するFe−Ni系合金を有利に製造する方法
を提案するところにある。In view of the actual situation in the industry, the object of the present invention is to create an alloy material that does not cause uneven streaks during etching, that is, contains 30 to 80% Ni and 0.001 to 0.0% B.
The present invention proposes a method for advantageously producing a Fe-Ni alloy containing 3% Fe--Ni.
そこで、本発明者らは、上述の目的を実現すべ(JFe
−Ni系合金のスジむらについて種々研究を行った。そ
の結果、探り得たスジむらの原因として、■CやSi、
Mn、 Crなどの不純物元素の成分偏析、■結晶組
織の相違、が主たるものであることを突きとめた。Therefore, the present inventors aimed to realize the above-mentioned purpose (JFe
- Various studies were conducted on streak unevenness in Ni-based alloys. As a result, we found that the causes of uneven streaks include ■C, Si,
It was found that the main factors were component segregation of impurity elements such as Mn and Cr, and (1) differences in crystal structure.
たとえば、CやSt、 Mn、 Crなどの不純物元素
の成分偏析部分は、他の部分に比べると、工・ノチング
の速度が変わるため、フォトエツチング穿孔時に孔形状
の差異を発生してスジむらの原因となるのである。For example, in areas where impurity elements such as C, St, Mn, and Cr are segregated, the etching/notching speed is different compared to other areas, resulting in differences in hole shape during photoetching and uneven streaks. It is the cause.
一方、結晶組織の相違については、たとえば、(100
)面が多く配向している個所は、他の部分に比べると、
エツチングの速度が速くなって、フォトエツチング穿孔
時に孔形状の差異を生じる。これは、鋳造時の凝固組織
、すなわち特定方位を有する柱状組織の存在に起因して
おり、この柱状組織は以後の加工、熱処理段階でも消滅
することなく、形を変えながら圧延方向tこ伸ばされ、
最終的にスジむらの原因をつくることになるのである。On the other hand, regarding the difference in crystal structure, for example, (100
) In areas where many planes are oriented, compared to other areas,
The etching speed increases, resulting in differences in hole shape during photoetching. This is due to the presence of a solidified structure during casting, that is, a columnar structure with a specific orientation, and this columnar structure does not disappear even in the subsequent processing and heat treatment stages, and is elongated in the rolling direction while changing its shape. ,
This ultimately causes uneven streaks.
また、本発明者らが知見したところによれば、Fe−N
i系合金に添加成分としてBを使用すると、スラブ加熱
時に上記柱状晶を分断し、ランダム化を加速させる効果
のあることが判明した。Furthermore, according to the findings of the present inventors, Fe-N
It has been found that the use of B as an additive component in the i-based alloy has the effect of disrupting the columnar crystals during slab heating and accelerating randomization.
このことから、本発明では、成分偏析の抑制のみならず
、Bの添加という相乗効果による結晶組織の調整をも狙
って、上述の課題の克服を試みた。Therefore, in the present invention, an attempt was made to overcome the above-mentioned problems by aiming not only at suppressing component segregation but also at adjusting the crystal structure through the synergistic effect of the addition of B.
すなわち、その課題克服の手段として本発明は、Niを
30〜80wt%およびBを0 、002〜0.03w
t%含み、残部が主としてFeである、Fe−Ni系合
金のインゴットを、900℃以上の温度に加熱した後、
鍛錬成形比゛l/1.2U以上のスエ込鍛錬を施し、つ
いでトータル断面減少率30%以上の熱間鍛錬を施すこ
とを特徴とするエツチング時のスジむら抑制効果に優れ
るFe−Ni系合金の製造方法、を提案する。That is, as a means to overcome this problem, the present invention provides Ni in an amount of 30 to 80 wt% and B in an amount of 0.002 to 0.03 wt%.
After heating an ingot of an Fe-Ni alloy containing t% and the remainder being mainly Fe to a temperature of 900 ° C. or higher,
An Fe-Ni alloy that has an excellent effect of suppressing streak unevenness during etching, which is characterized by performing sewage forging with a forging forming ratio of 1/1.2U or more, and then hot forging with a total cross-section reduction rate of 30% or more. We propose a manufacturing method for
さて、本発明において、素材についてのNi含有量の下
限を3h+t%(以下は単に「%」で略記する)とした
のは、Fe−Ni系合金を上記機能材として使用する場
合にこのNi含有量が30%未満では十分な電磁気特性
が発揮されず実用に耐えないためであり、逆にNiが8
0%を超える場合、電子、電磁用材料としての品質が劣
化するためである。Now, in the present invention, the lower limit of the Ni content of the material is set to 3h+t% (hereinafter simply abbreviated as "%") because this Ni-containing This is because if the Ni content is less than 30%, sufficient electromagnetic properties will not be exhibited and it will not be practical.
This is because if it exceeds 0%, the quality as an electronic or electromagnetic material will deteriorate.
なお、フォトエツチングにより穿孔される材料としては
、Ni50%以下のFe−Ni系合金を用いるのがより
好適である。As the material to be perforated by photoetching, it is more preferable to use a Fe--Ni alloy containing 50% or less Ni.
またBは、この発明のFe−Ni系合金の特性をきわだ
たせる重要な元素であり、CやSi、 Mn、 Crな
ど不純物元素の結晶粒界への偏析を阻止すると共に、み
ずから結晶粒界や他の欠陥部に優先的に凝集して再結晶
の核となり、結晶粒を微細化して等軸晶化を向−ヒさせ
る。しかし、このような作用は0.0OI%未満の含有
量では不十分であり、含有量が増加するにしたがって顕
著な効果を示すが、0.03%を超えて添加すると、M
2B(Ni、 Cr、 Fe)の金属間化合物の外に、
C,O,Nを含む種々のホウ化物が生成し高温で凝固割
れを起こす危険性が高くなるので、上限は0.03%に
限定する必要がある。In addition, B is an important element that emphasizes the characteristics of the Fe-Ni alloy of the present invention, and it prevents impurity elements such as C, Si, Mn, and Cr from segregating at the grain boundaries, and also acts as a self-adhesive element at the grain boundaries. It preferentially agglomerates in other defects and becomes nuclei for recrystallization, making crystal grains finer and promoting equiaxed crystallization. However, such an effect is insufficient at a content of less than 0.0OI%, and as the content increases, it shows a remarkable effect, but when added in an amount exceeding 0.03%, M
In addition to intermetallic compounds of 2B (Ni, Cr, Fe),
The upper limit needs to be limited to 0.03% because various borides containing C, O, and N are generated, increasing the risk of solidification cracking at high temperatures.
次に、鍛造に先立つインゴットの加熱温度を900°C
以−ヒとした理由は、加熱温度が900℃未満では鍛造
性が劣化し、また成分偏析を軽減することができないた
めである。なお、加熱温度の上限は融点を超えない温度
にすることは勿論である。Next, the heating temperature of the ingot prior to forging was set to 900°C.
The reason for this is that if the heating temperature is less than 900°C, forgeability deteriorates and component segregation cannot be reduced. It goes without saying that the upper limit of the heating temperature should not exceed the melting point.
またスエ込鍛錬における鍛錬成形比(以下スエ込鍛錬比
という)を1/1.2 U以上とした理由は、スエ込鍛
錬比が1/1.2 U未満では結晶の均一化を十分には
かることができずにスジむらが発生するためである。以
下このことをさらに詳しく述べる。In addition, the reason why the forging forming ratio in the suede forging (hereinafter referred to as the suede forging ratio) was set to 1/1.2 U or more is that if the suede forging ratio is less than 1/1.2 U, the crystals cannot be made sufficiently uniform. This is because uneven streaks occur. This will be explained in more detail below.
すなわち、かかるスジむらは、鋳造時の特定方位をもつ
巨大結晶粒が、その後の加工、熱処理で消滅することな
く、形を変化させながら圧延加工により圧延方向に伸ば
されたものが起因していることが判った。しかも、本発
明者らの研究によれば、最終板厚にまで加工された際に
特定方位をもつ結晶粒の長さの短いものは、その幅、長
さも相対的に小さ(なり、エツチング穿孔時に発生する
部分的なエツチング速度の差は見られず、したがって、
連続したスジむらとしては観察されなかった。ところが
、この柱状晶(結晶粒)の長さが長いものは、加工を経
てもその幅および長さに相当するものがそのまま、すな
わち大きいまま残存し、これがエツチング時のスジむら
となったのである。In other words, such uneven streaks are caused by giant crystal grains with a specific orientation during casting that are elongated in the rolling direction during rolling while changing their shape without disappearing during subsequent processing and heat treatment. It turned out that. Moreover, according to the research of the present inventors, when crystal grains with a specific orientation are short when processed to the final plate thickness, their width and length are also relatively small (and the etching perforation becomes difficult). The differences in local etching rates that sometimes occur are not observed, and therefore,
Continuous uneven streaks were not observed. However, when these columnar crystals (crystal grains) have a long length, even after processing, the width and length of the columnar crystals (crystal grains) remain as they are, that is, they remain large, and this causes uneven streaks during etching. .
このスジむらが出るか否かの限界となる結晶粒の長さは
、スエ込鍛錬によって決定し、すなわち、スエ込鍛錬比
が1/1.2 U未満では結晶粒の長さが長くなってス
ジむらの発生を招いてしまう。The length of the crystal grains, which is the limit for whether or not this streak unevenness will appear, is determined by the forging process.In other words, if the forging ratio is less than 1/1.2U, the length of the crystal grains becomes longer. This results in the occurrence of uneven streaks.
次に、上記スエ込鍛錬に続く鍛錬(実体鍛錬や展伸鍛錬
を含めて言う)におけるトータル断面減少率を30%以
上としたのは、30%未満では鍛造による成分偏析の軽
減が十分に達成されないためである。Next, the reason why we set the total cross-section reduction rate in the forging that follows the above-mentioned suede forging (including physical training and extension training) to 30% or more is because if it is less than 30%, the reduction of component segregation due to forging is sufficiently achieved. This is so that it will not happen.
以上のようにBを添加したFe −Ni系合金のインゴ
ットを特定の鍛造条件で鍛錬することにより、結晶粒の
均質化および成分偏析の軽減をはかってエツチング時の
スジむらが抑制でき、したがって、極めて優れたエツチ
ング性を確保することが可能である。As described above, by forging the Fe-Ni alloy ingot added with B under specific forging conditions, it is possible to homogenize the crystal grains and reduce component segregation, thereby suppressing uneven streaks during etching. It is possible to ensure extremely excellent etching properties.
第1表に、この実施例で用いたFe −Ni系合金の化
学組成および実施の条件と得られた製品の評価結果を示
す。Table 1 shows the chemical composition of the Fe--Ni alloy used in this example, the conditions of implementation, and the evaluation results of the obtained product.
この第1表に示した特に本発明の対象とする合金は、電
気炉で溶解した溶融金属を、引き続いてAOD法または
VOD法により精錬した後インゴットに造塊し、次いで
、第1表に示す条件に従って熱間鍛練を施してスラブと
した後、熱間圧延を施して5.51厚のコイルとした。The alloys shown in Table 1, which are particularly targeted by the present invention, are obtained by refining molten metal in an electric furnace by the AOD method or VOD method, and then forming ingots as shown in Table 1. After hot forging according to the conditions to form a slab, hot rolling was performed to form a coil with a thickness of 5.51 mm.
その熱間圧延以降は常法に従い冷間圧延と熱処理を適宜
組合わせた常法に従う処理を行って最終製品を得た。After the hot rolling, a final product was obtained by performing treatments according to a conventional method by appropriately combining cold rolling and heat treatment.
このようにして製造した供試材料を、塩化第一鉄溶液(
比重1.45.50℃)で実際のフォトエツチング開孔
を行い、スジむら発生の有無を調査した。The test material produced in this way was mixed with a ferrous chloride solution (
Actual photoetching was performed at a temperature of 1.45.50°C (specific gravity: 1.45.50°C), and the presence or absence of uneven streaks was investigated.
その結果は第1表に示すとおりであった。The results were as shown in Table 1.
この第1表に示すところから判るように、本発明法に従
って製造したFe−Ni系合金は、同一組成の従来法に
よって製造した、Fe−Ni系合金(比較例)に比べる
と、エツチング時のスジむらの発生はほとんど見られず
、エツチング用素材として優れた合金であることが明ら
かとなった。As can be seen from Table 1, the Fe-Ni alloy manufactured according to the method of the present invention has a higher etching rate than the Fe-Ni alloy (comparative example) manufactured according to the conventional method with the same composition. Almost no streaks were observed, making it clear that the alloy is an excellent material for etching.
以上説明したように、本発明方法によって製造したBを
適量添加したFe−Ni系合金は、フォトエツチング穿
孔後のスジむらが全く無いため、電子。As explained above, the Fe-Ni alloy to which an appropriate amount of B is added, which is produced by the method of the present invention, has no uneven streaks after photo-etching, and therefore is highly resistant to electrons.
電磁材料として望ましい性質を有するFe−Ni系合金
を安価に提供することができる。A Fe-Ni alloy having properties desirable as an electromagnetic material can be provided at low cost.
特許出願人 日本冶金工業株式会社 代理人 弁理士 小 川 順 玉 量 弁理士 中 村 盛 夫Patent applicant Nippon Yakin Kogyo Co., Ltd. Agent Patent Attorney Jun Tama Kogawa Quantity Patent attorney Morio Nakamura
Claims (1)
.03wt%含み、残部が主としてFeであるFe−N
i系合金のインゴットを、900℃以上の温度に加熱し
た後、鍛錬成形比1/1.2U以上のスエ込鍛錬を施し
、ついでトータル断面減少率30%以上の熱間鍛錬を施
すことを特徴とするエッチング時のスジむら抑制効果に
優れるFe−Ni系合金の製造方法。1. 30 to 80 wt% Ni and 0.001 to 0 B
.. Fe-N containing 03 wt% and the remainder being mainly Fe
The ingot of the i-series alloy is heated to a temperature of 900°C or higher, then subjected to sewage forging at a forging forming ratio of 1/1.2U or higher, and then hot forged at a total cross-section reduction rate of 30% or higher. A method for producing a Fe-Ni alloy that has an excellent effect of suppressing streak unevenness during etching.
Priority Applications (6)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP25188188A JPH0711033B2 (en) | 1988-10-07 | 1988-10-07 | Method for producing Fe-Ni based alloy excellent in streak unevenness suppressing effect during etching |
CA000613799A CA1331127C (en) | 1988-10-07 | 1989-09-27 | Method of producing fe-ni series alloys having improved effect for restraining streaks during etching |
US07/414,539 US5002619A (en) | 1988-10-07 | 1989-09-29 | Method of producing Fe-Ni series alloys having improved effect for restraining streaks during etching |
DE3933297A DE3933297C2 (en) | 1988-10-07 | 1989-10-05 | Process for producing Fe-Ni alloy plates suitable for shadow masks of cathode ray tubes with improved resistance to the occurrence of etching strips |
KR1019890014369A KR920004707B1 (en) | 1988-10-07 | 1989-10-06 | METHOD OF PRODUCING Fe-Ni SERIES ALLOYS HAVING IMPROVED EFFECT FOR RESTRAINING STREAKS DURING ETCHING |
FR898913114A FR2637614B1 (en) | 1988-10-07 | 1989-10-06 | PROCESS FOR PRODUCING FE-NI SERIES ALLOYS HAVING IMPROVED EFFECT TO LIMIT SCRATCHES DURING ENGRAVING |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP25188188A JPH0711033B2 (en) | 1988-10-07 | 1988-10-07 | Method for producing Fe-Ni based alloy excellent in streak unevenness suppressing effect during etching |
Publications (2)
Publication Number | Publication Date |
---|---|
JPH02101116A true JPH02101116A (en) | 1990-04-12 |
JPH0711033B2 JPH0711033B2 (en) | 1995-02-08 |
Family
ID=17229329
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP25188188A Expired - Lifetime JPH0711033B2 (en) | 1988-10-07 | 1988-10-07 | Method for producing Fe-Ni based alloy excellent in streak unevenness suppressing effect during etching |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPH0711033B2 (en) |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0515954B1 (en) * | 1991-05-30 | 1996-01-10 | Hitachi Metals, Ltd. | High-fineness shadow mask material and process for producing the same |
US5532088A (en) * | 1993-03-12 | 1996-07-02 | Kabushiki Kaisha Toshiba | Shadow mask plate material and shadow mask |
-
1988
- 1988-10-07 JP JP25188188A patent/JPH0711033B2/en not_active Expired - Lifetime
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0515954B1 (en) * | 1991-05-30 | 1996-01-10 | Hitachi Metals, Ltd. | High-fineness shadow mask material and process for producing the same |
US5532088A (en) * | 1993-03-12 | 1996-07-02 | Kabushiki Kaisha Toshiba | Shadow mask plate material and shadow mask |
Also Published As
Publication number | Publication date |
---|---|
JPH0711033B2 (en) | 1995-02-08 |
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