JP2002322529A - Aluminum alloy plate for printing plate and production method therefor - Google Patents
Aluminum alloy plate for printing plate and production method thereforInfo
- Publication number
- JP2002322529A JP2002322529A JP2001128268A JP2001128268A JP2002322529A JP 2002322529 A JP2002322529 A JP 2002322529A JP 2001128268 A JP2001128268 A JP 2001128268A JP 2001128268 A JP2001128268 A JP 2001128268A JP 2002322529 A JP2002322529 A JP 2002322529A
- Authority
- JP
- Japan
- Prior art keywords
- aluminum alloy
- mass
- intermetallic compound
- temperature
- less
- 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
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 42
- 238000007639 printing Methods 0.000 title claims abstract description 15
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 12
- 238000000137 annealing Methods 0.000 claims abstract description 15
- 239000012535 impurity Substances 0.000 claims abstract description 13
- 239000000203 mixture Substances 0.000 claims abstract description 11
- 229910052802 copper Inorganic materials 0.000 claims abstract description 4
- 229910000765 intermetallic Inorganic materials 0.000 claims description 38
- 239000002245 particle Substances 0.000 claims description 21
- 238000005098 hot rolling Methods 0.000 claims description 13
- 238000010438 heat treatment Methods 0.000 claims description 11
- 238000000034 method Methods 0.000 claims description 8
- 230000001105 regulatory effect Effects 0.000 claims description 4
- 238000007788 roughening Methods 0.000 abstract description 12
- 230000009257 reactivity Effects 0.000 abstract description 11
- 230000000630 rising effect Effects 0.000 abstract 2
- 230000000052 comparative effect Effects 0.000 description 12
- 238000000265 homogenisation Methods 0.000 description 7
- VEXZGXHMUGYJMC-UHFFFAOYSA-N Hydrochloric acid Chemical compound Cl VEXZGXHMUGYJMC-UHFFFAOYSA-N 0.000 description 6
- 239000006104 solid solution Substances 0.000 description 6
- 238000005266 casting Methods 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 238000005868 electrolysis reaction Methods 0.000 description 5
- 230000005611 electricity Effects 0.000 description 4
- 238000004090 dissolution Methods 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 3
- 238000005530 etching Methods 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 238000001953 recrystallisation Methods 0.000 description 3
- 239000000243 solution Substances 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 239000011148 porous material Substances 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 102220253765 rs141230910 Human genes 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 229910018084 Al-Fe Inorganic materials 0.000 description 1
- 229910018192 Al—Fe Inorganic materials 0.000 description 1
- 229910018191 Al—Fe—Si Inorganic materials 0.000 description 1
- GRYLNZFGIOXLOG-UHFFFAOYSA-N Nitric acid Chemical compound O[N+]([O-])=O GRYLNZFGIOXLOG-UHFFFAOYSA-N 0.000 description 1
- ISWSIDIOOBJBQZ-UHFFFAOYSA-N Phenol Chemical compound OC1=CC=CC=C1 ISWSIDIOOBJBQZ-UHFFFAOYSA-N 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 238000001479 atomic absorption spectroscopy Methods 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 239000000706 filtrate Substances 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 238000001095 inductively coupled plasma mass spectrometry Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910017604 nitric acid Inorganic materials 0.000 description 1
- 230000001376 precipitating effect Effects 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 238000010998 test method Methods 0.000 description 1
Abstract
Description
【0001】[0001]
【発明の属する技術分野】本発明は平版印刷版用アルミ
ニウム合金板及びその製造方法に関し、より少ない電気
量で均一な電解粗面化面を形成することができる印刷版
用アルミニウム合金板及びその製造方法に関するもので
ある。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an aluminum alloy plate for a lithographic printing plate and a method for producing the same. It is about the method.
【0002】[0002]
【従来の技術】印刷用アルミニウム合金板は、一般的に
塩酸又は硝酸の希釈液中で通電を行うことにより、表面
を粗面化して使用される。このとき、少ない電気量でか
つ均一な粗面を形成するアルミニウム合金が求められ
る。2. Description of the Related Art In general, an aluminum alloy plate for printing is used by roughening the surface by applying a current in a dilute solution of hydrochloric acid or nitric acid. At this time, an aluminum alloy that forms a uniform rough surface with a small amount of electricity is required.
【0003】電解粗面化時に、反応性が高く且つ均一な
粗面が得られるアルミニウム合金板の製造技術として、
2種類の技術が提案されている。先ず、添加元素を調整
することにより電解粗面の均一化を図った方法として、
例えば、特開平11−99760号公報に記載されたも
のが挙げられる。また、アルミニウム合金中の添加元素
の金属間化合物を調整することにより電解粗面の均一化
を図った方法として、例えば、特開平11−11533
3号公報に記載されたものが挙げられる。[0003] As a technique for manufacturing an aluminum alloy plate capable of obtaining a highly reactive and uniform roughened surface during electrolytic surface roughening,
Two types of technology have been proposed. First, as a method of achieving a uniform electrolytic rough surface by adjusting the additive element,
For example, those described in JP-A-11-99760 can be mentioned. As a method for achieving a uniform electrolytic roughened surface by adjusting an intermetallic compound of an additional element in an aluminum alloy, for example, Japanese Patent Application Laid-Open No. H11-11533
No. 3 publication.
【0004】[0004]
【発明が解決しようとする課題】しかしながら、近時、
高生産性の要求のもとに、特開平11−188973号
公報に記載されているように、電解処理条件が120A
/dm2にて3秒間、85A/dm2にて6秒間のよう
に、高電流密度及び短時間での電解粗面化が提案される
ようになった。However, recently,
Under the demand of high productivity, as described in Japanese Patent Application Laid-Open No.
/ Dm 2 at 3 seconds, as in 85A / dm 2 for 6 seconds, began to high current density and electrolytic roughening in a short time are suggested.
【0005】また、感光膜の技術の向上により、より細
かいピットを形成すること、換言すれば、均一に分散し
たピットを形成することができるアルミニウム合金板が
求められている。Further, with the improvement of the technology of the photosensitive film, there is a demand for an aluminum alloy plate capable of forming finer pits, in other words, forming uniformly dispersed pits.
【0006】しかし、前述の従来の電解粗面の均一化技
術では、高電流密度及び短時間での電解処理において、
反応性、ピットの細かさ、及び粗面の均一性がいずれも
不十分なものであり、近時の印刷版及びその製造方法に
要求される特性を満足するアルミニウム合金板の開発が
要望されている。[0006] However, in the above-mentioned conventional technology for making the electrolytic rough surface uniform, in the electrolytic treatment at a high current density and in a short time,
The reactivity, the fineness of the pits, and the uniformity of the rough surface are all inadequate, and there has been a demand for the development of an aluminum alloy plate that satisfies the characteristics required for recent printing plates and their manufacturing methods. I have.
【0007】本発明はかかる問題点に鑑みてなされたも
のであって、高電流密度及び短時間での電解粗面化処理
において、電解効率が高く、反応性、ピットの細かさ及
び粗面の均一性を向上させることができる印刷版用アル
ミニウム合金板及びその製造方法を提供することを目的
とする。The present invention has been made in view of the above problems, and has high electrolysis efficiency, high reactivity, fineness of pits and rough surface in a high current density and short time electrolytic surface roughening treatment. An object of the present invention is to provide an aluminum alloy plate for a printing plate capable of improving uniformity and a method for producing the same.
【0008】[0008]
【課題を解決するための手段】本発明に係る印刷版用ア
ルミニウム合金板は、Fe:0.25乃至0.45質量
%、Si:0.02乃至0.08質量%、Cu:0.04
質量%以下を含有し、残部がAl及び不可避的不純物か
らなり、不可避的不純物におけるNiを0.005質量
%以下に規制した組成を有し、粒径が1μm以下のFe
金属間化合物が0.02質量%以上であることを特徴と
する。The aluminum alloy plate for a printing plate according to the present invention comprises 0.25 to 0.45% by mass of Fe, 0.02 to 0.08% by mass of Si, and 0.04% of Cu.
% Of Al and unavoidable impurities, and the composition is such that Ni in the unavoidable impurities is regulated to 0.005% by mass or less, and the particle size is 1 μm or less.
The amount of the intermetallic compound is 0.02% by mass or more.
【0009】本発明に係る印刷版用アルミニウム合金板
の製造方法は、Fe:0.25乃至0.45質量%、S
i:0.02乃至0.08質量%、Cu:0.04質量%
以下を含有し、残部がAl及び不可避的不純物からな
り、不可避的不純物におけるNiを0.005質量%以
下に規制した組成を有するアルミニウム合金鋳塊を、5
50℃以上の温度で均質化処理する工程と、開始温度を
400乃至450℃として熱間圧延する工程と、その
後、少なくとも1回、平均昇温速度10乃至60℃/時
で昇温させて450乃至500℃に1乃至20時間保持
する焼鈍処理を行う工程とを有し、粒径が1μm以下の
Fe金属間化合物が0.02質量%以上であるアルミニ
ウム合金板を製造することを特徴とする。The method for producing an aluminum alloy plate for a printing plate according to the present invention is characterized in that Fe: 0.25 to 0.45% by mass,
i: 0.02 to 0.08 mass%, Cu: 0.04 mass%
The aluminum alloy ingot having the following composition, with the balance being Al and inevitable impurities, having a composition in which Ni in the inevitable impurities is regulated to 0.005% by mass or less, is
A step of homogenizing at a temperature of 50 ° C. or higher, a step of hot rolling at a starting temperature of 400 to 450 ° C., and thereafter, heating at least once at an average heating rate of 10 to 60 ° C./hour to 450 Performing an annealing treatment at 1 to 20 hours at a temperature of from 500 to 500 ° C. to produce an aluminum alloy sheet having an Fe intermetallic compound having a particle size of 1 μm or less of 0.02% by mass or more. .
【0010】[0010]
【発明の実施の形態】以下、本発明について更に詳細に
説明する。本願発明者等は、アルミニウム合金板中のF
e金属間化合物の影響について鋭意研究した。即ち、従
来技術では、Fe含有量の殆どが、主に鋳造工程で発生
する粒径1μm超の晶出物となり、僅かの残部Feがア
ルミニウム合金中に固溶しており、粒径1μm以下の析
出物(Fe金属間化合物)の存在量は極めて少ない状態
であった。上述した粒径1μm超の晶出物である金属間
化合物だけでは適度の存在密度(面密度)とならない。
そこで、本発明では粒径1μm以下のFe金属間化合物
に注目し、均質化処理及び焼鈍処理で粒径1μm以下の
金属間化合物を析出させることにより、その分布を調整
して、反応性と粗面の均一性について試験を行った。BEST MODE FOR CARRYING OUT THE INVENTION Hereinafter, the present invention will be described in more detail. The inventors of the present application have proposed that F
e) The effect of intermetallic compounds was studied diligently. That is, in the prior art, most of the Fe content is crystallized with a particle diameter of more than 1 μm mainly generated in the casting process, and a small amount of the remaining Fe is dissolved in the aluminum alloy, and the particle diameter is 1 μm or less. The amount of the precipitate (Fe intermetallic compound) was extremely small. The above-mentioned intermetallic compound, which is a crystallized substance having a particle size of more than 1 μm alone, does not have an appropriate existence density (area density).
Therefore, in the present invention, attention is paid to Fe intermetallic compounds having a particle size of 1 μm or less, and by precipitating an intermetallic compound having a particle size of 1 μm or less by a homogenization treatment and an annealing treatment, the distribution thereof is adjusted, and the reactivity and the coarseness are adjusted. A test was performed for surface uniformity.
【0011】その結果、粒径1μm以下のFe金属間化
合物がピット形成核となり、ピットが多数発生すること
によって、少ない電気量でかつ均一な粗面を形成できる
ことを見出した。本発明はこの知見に基づき完成された
ものである。As a result, it has been found that an Fe intermetallic compound having a particle size of 1 μm or less serves as a pit forming nucleus, and a large number of pits can be formed, so that a uniform surface with a small amount of electricity can be formed. The present invention has been completed based on this finding.
【0012】即ち、アルミニウム合金板中の粒径が1μ
m以下の微細なFe金属間化合物のアルミニウム合金中
の含有量を0.02質量%以上に調整することにより、
ピット発生のための起点が多数となり、少ない電気量で
均一に分散した細かいピットを形成することができる。That is, the particle size in the aluminum alloy plate is 1 μm.
m by adjusting the content of the fine Fe intermetallic compound in the aluminum alloy to 0.02 mass% or more,
There are many starting points for pit generation, and fine pits uniformly dispersed with a small amount of electricity can be formed.
【0013】この場合に、このような微細なFe金属間
化合物を所定量以上生成するためには、Feの固溶度が
可能な限り高い値を示す条件で鋳造を行うことが望まし
い。また、鋳造工程で生成した粒径が1μmを超えるF
e金属間化合物は、均質化処理により、アルミニウム合
金中に一旦固溶させた後、中間焼鈍で粒径が1μm以下
のFe金属間化合物として析出させることが可能であ
る。即ち、均質化処理では、アルミニウム合金板をFe
金属間化合物が固溶する550℃以上の温度に加熱し
て、Fe系晶出物を微細化させ、アルミニウム合金中の
Fe固溶量を増加させる。そして、熱間圧延終了後に、
焼鈍を行うことにより、固溶しているFeを析出させ、
粒径が1μm以下のFe金属間化合物に変化させる。In this case, in order to produce such a fine Fe intermetallic compound in a predetermined amount or more, it is desirable to perform casting under the condition that the solid solubility of Fe is as high as possible. Further, the particle size generated in the casting process exceeds 1 μm.
The e intermetallic compound can be once dissolved in an aluminum alloy by a homogenization treatment, and then precipitated as a Fe intermetallic compound having a particle size of 1 μm or less by intermediate annealing. That is, in the homogenization process, the aluminum alloy plate is
Heating to a temperature of 550 ° C. or higher at which the intermetallic compound forms a solid solution makes the Fe-based crystallization finer and increases the amount of Fe solid solution in the aluminum alloy. And, after the end of hot rolling,
By performing annealing, Fe in solid solution is precipitated,
The particle size is changed to an Fe intermetallic compound having a particle size of 1 μm or less.
【0014】熱間圧延を行い、その後、少なくとも1
回、焼鈍処理する。この焼鈍処理条件は、平均昇温速度
が10乃至60℃/時で昇温させ、450乃至500℃
に1乃至20時間保持して加熱するものである。これに
より、粒径が1μm以下のFe金属間化合物のアルミニ
ウム合金中の含有量を0.02質量%以上とすることが
できる。[0014] Hot rolling is performed and then at least one
Annealing times. The annealing treatment conditions are as follows: the temperature is raised at an average rate of 10 to 60 ° C./hour;
And heating for 1 to 20 hours. Thereby, the content of the Fe intermetallic compound having a particle size of 1 μm or less in the aluminum alloy can be 0.02% by mass or more.
【0015】次に、本発明の製造方法における数値限定
理由について説明する。Next, the reasons for limiting the numerical values in the manufacturing method of the present invention will be described.
【0016】[均質化処理温度:550℃以上]均質化
処理温度が550℃未満であると、鋳造工程で発生した
晶出物を充分に微細化することができず、Fe固溶量を
増加させることができない。従って、粒径が1μm未満
のFe金属間化合物が少なくなる。[Homogenization treatment temperature: 550 ° C. or higher] If the homogenization treatment temperature is lower than 550 ° C., the crystallized substances generated in the casting process cannot be sufficiently refined, and the amount of Fe solid solution increases. I can't let it. Therefore, Fe intermetallic compounds having a particle size of less than 1 μm are reduced.
【0017】[熱間圧延開始温度:400乃至550
℃]熱間圧延の開始温度が550℃を超えると、結晶粒
が過剰に成長する。これにより、粗面が不均一となるの
で、熱間圧延の開始温度は550℃以下とする。また、
熱間圧延の開始温度が400℃未満では、圧延中の動的
再結晶が不十分であり、同様に粗面の均一性が損なわれ
る。このため、熱間圧延開始温度は400乃至550℃
とする。[Hot rolling start temperature: 400 to 550]
[° C] When the starting temperature of hot rolling exceeds 550 ° C, crystal grains grow excessively. As a result, the roughened surface becomes non-uniform, so the hot rolling start temperature is set to 550 ° C. or less. Also,
When the starting temperature of hot rolling is lower than 400 ° C., dynamic recrystallization during rolling is insufficient, and the uniformity of the rough surface is similarly impaired. Therefore, the hot rolling start temperature is 400 to 550 ° C.
And
【0018】[昇温速度:1乃至60℃/時]昇温速度
が1℃/時未満であると、スループットが長くなりす
ぎ、製造コストが上昇する。一方、昇温速度が60℃/
時を超えると、昇温速度が速すぎて充分に析出が進行せ
ず、所望の微細なFe金属間化合物を生成できない。[Temperature increase rate: 1 to 60 ° C./hour] If the temperature increase rate is less than 1 ° C./hour, the throughput becomes too long and the production cost increases. On the other hand, the heating rate is 60 ° C. /
If the time is exceeded, the rate of temperature rise is too high, so that the precipitation does not proceed sufficiently and a desired fine Fe intermetallic compound cannot be produced.
【0019】[加熱保持温度:450乃至500℃]加
熱保持温度が450℃未満であると、析出の進行速度が
遅く、析出が不十分である。また、加熱保持温度が50
0℃を超えると、逆に固溶が進行して析出物が減少す
る。[Heat-holding temperature: 450 to 500 ° C.] When the heat-holding temperature is lower than 450 ° C., the proceeding speed of the precipitation is slow and the precipitation is insufficient. In addition, the heating holding temperature is 50
If the temperature exceeds 0 ° C., on the contrary, solid solution proceeds and precipitates decrease.
【0020】次に、本発明の印刷版用アルミニウム合金
板の成分添加理由及び組成限定理由について説明する。Next, the reasons for adding the components and the reasons for limiting the composition of the aluminum alloy plate for a printing plate of the present invention will be described.
【0021】[Fe:0.25乃至0.45質量%]F
eはAl−Fe系金属間化合物を形成し、再結晶粒の微
細化及び組織の均一化による機械的強度維持に効果を有
する。このFe系金属間化合物は、電解粗面化時のイニ
シャルピットの開始点として作用する。しかし、Fe含
有量が0.25質量%未満では、アルミニウム合金中に
含有される全てのFeを金属間化合物として析出させて
も、電解処理における反応性が不十分であり、均一なピ
ットを形成することができず、また、強度が低いため、
印刷版としての用途に適さない。一方、Fe含有量が
0.45質量%を超えると、均質化処理の条件に拘わら
ず、粒径が1μmを超える金属間化合物、即ち晶出物が
十分に減少しない。このため、このような粗大晶出物
が、粗大なピットを発生させる起点となる。従って、F
e含有量は、0.25乃至0.45質量%とする。[Fe: 0.25 to 0.45% by mass] F
e forms an Al-Fe intermetallic compound and has an effect on maintaining mechanical strength by refining recrystallized grains and making the structure uniform. This Fe-based intermetallic compound acts as a starting point of initial pits during electrolytic surface roughening. However, when the Fe content is less than 0.25% by mass, even when all the Fe contained in the aluminum alloy is precipitated as an intermetallic compound, the reactivity in the electrolytic treatment is insufficient and uniform pits are formed. And the strength is low,
Not suitable for use as a printing plate. On the other hand, when the Fe content exceeds 0.45% by mass, the intermetallic compound having a particle size exceeding 1 μm, that is, the crystallized product is not sufficiently reduced regardless of the conditions of the homogenization treatment. For this reason, such coarse crystals serve as starting points for generating coarse pits. Therefore, F
The e content is set to 0.25 to 0.45% by mass.
【0022】[Si:0.02乃至0.08質量%]S
iはAl−Fe−Si系金属間化合物を形成し、熱間圧
延時における各パス間での再結晶の核として作用するの
で、熱間圧延時の再結晶を微細化する効果を有する。更
に、イニシャルピットの形成を促進し、ピットの均一性
を向上させる効果を奏する。しかし、Si含有量が0.
02質量%未満では電解処理における反応性が低く、逆
にSi含有量が0.08質量%を超えると電解処理にお
ける反応性が過剰となり、不均一なピットが形成され
る。[Si: 0.02 to 0.08% by mass] S
i forms an Al-Fe-Si-based intermetallic compound and acts as a nucleus for recrystallization between passes during hot rolling, and thus has an effect of miniaturizing recrystallization during hot rolling. Further, the effect of promoting the formation of initial pits and improving the uniformity of pits is achieved. However, when the Si content is 0.1.
When the Si content is less than 02% by mass, the reactivity in the electrolytic treatment is low, and when the Si content exceeds 0.08% by mass, the reactivity in the electrolytic treatment becomes excessive and non-uniform pits are formed.
【0023】[Cu:0.04質量%以下]Cuは電解
粗面化の均一性に影響するが、Cu含有量が0.04質
量%を超えると、均一に分散したピットを形成できな
い。このため、Cu含有量は0.04質量%以下とす
る。[Cu: 0.04% by mass or less] Cu affects the uniformity of electrolytic surface roughening, but if the Cu content exceeds 0.04% by mass, uniformly dispersed pits cannot be formed. Therefore, the Cu content is set to 0.04% by mass or less.
【0024】積極添加元素については上述のとおりであ
るが、不可避的不純物であるNiの含有量を規制する理
由は、以下のとおりである。The positively added element is as described above. The reason for restricting the content of Ni, which is an unavoidable impurity, is as follows.
【0025】[Ni:0.005質量%以下]Niは電
解粗面化のエッチング性を向上させるものの、Ni含有
量が0.005質量%を超えると、電解粗面化時のエッ
チング性が過剰となり、腐食されやすくなって印刷汚れ
を生じる。このため、Ni含有量は0.005質量%以
下に規制する。[Ni: 0.005% by mass or less] Although Ni improves the etching property of electrolytic surface roughening, if the Ni content exceeds 0.005% by mass, the etching property during electrolytic surface roughening becomes excessive. And it is easily corroded, resulting in printing stains. For this reason, the Ni content is restricted to 0.005% by mass or less.
【0026】なお、不可避的不純物であるMnはアルミ
ニウム合金のエッチング性を低下させて印刷汚れの原因
となりうるので、その含有量は0.05質量%以下に規
制することが好ましい。Since Mn, which is an unavoidable impurity, lowers the etching property of the aluminum alloy and may cause printing stains, its content is preferably limited to 0.05% by mass or less.
【0027】[0027]
【実施例】以下、本発明の実施例について、本発明の範
囲から外れる比較例と比較して本発明の効果について説
明する。下記表1は使用したアルミニウム合金板の組成
と、その製造条件を示す。先ず、この表1に示す組成の
アルミニウム合金の溶湯を400mm厚さの鋳塊に鋳造
した。次に、表1に記載の温度で6時間加熱することに
よりこのアルミニウム合金板を均質化処理し、開始温度
を450℃として熱間圧延を開始した。また、アルミニ
ウム合金板の厚さが3mmになったときに熱間圧延を終
了した。その後、厚さが1.5mmになるまで冷間圧延
し、その後、表1に記載の条件で中間焼鈍した。中間焼
鈍後に、アルミニウム合金板を厚さが0.24mmにな
るまで冷間圧延した。なお、表1におけるFe金属間化
合物の量は粒径1μm以下のFe系金属間化合物がアル
ミニウム合金全体に占める質量割合である。EXAMPLES The effects of the present invention will be described below with reference to examples of the present invention, as compared with comparative examples that are out of the scope of the present invention. Table 1 below shows the composition of the aluminum alloy plate used and the manufacturing conditions. First, a molten aluminum alloy having the composition shown in Table 1 was cast into an ingot having a thickness of 400 mm. Next, the aluminum alloy sheet was homogenized by heating at a temperature shown in Table 1 for 6 hours, and the starting temperature was set to 450 ° C. to start hot rolling. Hot rolling was completed when the thickness of the aluminum alloy plate reached 3 mm. Then, it cold-rolled until thickness became 1.5 mm, and then performed intermediate annealing under the conditions described in Table 1. After the intermediate annealing, the aluminum alloy sheet was cold-rolled until the thickness became 0.24 mm. The amount of the Fe intermetallic compound in Table 1 is the mass ratio of the Fe-based intermetallic compound having a particle size of 1 μm or less to the entire aluminum alloy.
【0028】[0028]
【表1】 [Table 1]
【0029】次に、上述の条件で製造されたアルミニウ
ム合金板の試験方法について説明する。Next, a description will be given of a test method of the aluminum alloy plate manufactured under the above-described conditions.
【0030】[Fe金属間化合物の析出量の測定方法]
約2gのアルミニウム合金板を180℃に加熱したフェ
ノールに溶解させた。そして、残渣を1μm孔のミクロ
フィルターで濾過した。この濾液をさらに0.1μm孔
のミクロフィルターで濾過した。得られた残渣はAl−
Fe系化合物と単体金属Siである。更に、この残渣を
塩酸で溶解し、浴中のFe量をICP−MS(原子吸光
分析法)により測定し、この測定値から1μm以下のF
e金属間化合物量を算出した。[Method for measuring the amount of Fe intermetallic compound deposited]
About 2 g of an aluminum alloy plate was dissolved in phenol heated to 180 ° C. Then, the residue was filtered with a micro filter having a pore size of 1 μm. The filtrate was further filtered through a 0.1 μm pore microfilter. The residue obtained is Al-
Fe-based compound and simple metal Si. The residue was dissolved in hydrochloric acid, and the amount of Fe in the bath was measured by ICP-MS (atomic absorption spectrometry).
e The amount of the intermetallic compound was calculated.
【0031】[電解効率の測定方法]アルミニウム合金
板を2質量%−HCl水溶液中に浸漬し、このHCl水
溶液の温度を25℃に調整し、電流密度が80A/dm
2、通電時間が11秒間の条件で通電し、電解粗面化を
行った。アルミニウム合金板の通電前後の質量を測定
し、これらの差を溶解減量とした。この場合に、通電さ
れた電気量は880C/dm2であるから、ファラデー
の法則から理論溶解量は0.0821g/dm2と算出
される。従って、電解効率は下記数式1により算出でき
る。[Method of Measuring Electrolytic Efficiency] An aluminum alloy plate was immersed in a 2% by mass aqueous HCl solution, the temperature of the aqueous HCl solution was adjusted to 25 ° C., and the current density was 80 A / dm.
2. Energization was performed under the condition that the energization time was 11 seconds to perform electrolytic surface roughening. The mass of the aluminum alloy plate before and after energization was measured, and the difference between them was defined as the dissolution loss. In this case, since the amount of electricity passed is 880 C / dm 2 , the theoretical dissolution amount is calculated to be 0.0821 g / dm 2 from Faraday's law. Therefore, the electrolysis efficiency can be calculated by the following equation 1.
【0032】[0032]
【数1】電解効率[%]=溶解減量[g/dm2]/
0.0821[g/dm2]×100[%]## EQU1 ## Electrolysis efficiency [%] = dissolution loss [g / dm 2 ] /
0.0821 [g / dm 2 ] × 100 [%]
【0033】[粗面の観察]上述の電解効率の測定で電
解粗面化を行ったアルミニウム合金板の表面を走査型電
子顕微鏡で観察した。そして、粗面を走査型電子顕微鏡
で1000倍にて観察し、約7乃至10μmのピットが
ほぼ全面に均一に分散して存在する場合を○、3μm以
下の小さなピット又は15μm以上の粗大なピットが混
在する場合を×とした。[Observation of Rough Surface] The surface of the aluminum alloy plate subjected to electrolytic surface roughening in the above-described measurement of electrolytic efficiency was observed with a scanning electron microscope. Then, the rough surface is observed at a magnification of 1000 with a scanning electron microscope, and when pits of about 7 to 10 μm are uniformly dispersed almost over the entire surface, ○ small pits of 3 μm or less or coarse pits of 15 μm or more Are mixed when X is mixed.
【0034】表1に、粒径1μm未満のFe金属間化合
物の割合、電解効率及び粗面の均一性を記載した。その
結果、実施例1乃至7は組成及びFe金属間化合物の割
合が本発明の請求項1を満足するものであり、電解効率
及び粗面の均一性のいずれも優れたものであった。ま
た、実施例1乃至7は本発明の請求項2に記載の製造条
件を満足するものであり、Fe金属間化合物の量が充分
に多いものであった。Table 1 shows the ratio of Fe intermetallic compound having a particle size of less than 1 μm, the electrolytic efficiency and the uniformity of the rough surface. As a result, in Examples 1 to 7, the composition and the ratio of the Fe intermetallic compound satisfied the first aspect of the present invention, and both the electrolytic efficiency and the uniformity of the rough surface were excellent. Examples 1 to 7 satisfied the production conditions described in claim 2 of the present invention, and the amount of the Fe intermetallic compound was sufficiently large.
【0035】一方、比較例1は、平均昇温速度が速す
ぎ、また中間焼鈍の保持時間が短すぎて、微細なFe金
属間化合物の生成が不十分であった。比較例2は、中間
焼鈍の保持温度が高すぎて、微細なFe金属間化合物の
量が少なかった。比較例3は、中間焼鈍の保持温度が低
すぎて、微細なFe金属間化合物の量が少なかった。比
較例4は、中間焼鈍の保持温度が高すぎ、保持時間が長
すぎたため、微細なFe金属間化合物の量が不十分であ
った。比較例8は均質化温度が低すぎたため、鋳造時に
発生した粒径1μm以上のFe金属間化合物が充分に固
溶せず、このため、後工程で微細なFe金属間化合物が
充分に析出しなかった。更に、比較例5はFe含有量が
少ないと共に、平均昇温速度が速すぎ、また中間焼鈍時
間が短すぎたため、Fe金属間化合物の割合が少なかっ
た。このため、比較例1乃至5、8はいずれも電解効率
が低く、粗面の均一性も劣るものであった。On the other hand, in Comparative Example 1, the average heating rate was too high, and the holding time of the intermediate annealing was too short, so that the formation of fine Fe intermetallic compounds was insufficient. In Comparative Example 2, the holding temperature of the intermediate annealing was too high, and the amount of the fine Fe intermetallic compound was small. In Comparative Example 3, the holding temperature of the intermediate annealing was too low, and the amount of the fine Fe intermetallic compound was small. In Comparative Example 4, since the holding temperature of the intermediate annealing was too high and the holding time was too long, the amount of the fine Fe intermetallic compound was insufficient. In Comparative Example 8, since the homogenization temperature was too low, the Fe intermetallic compound having a particle size of 1 μm or more generated at the time of casting did not sufficiently form a solid solution. Did not. Further, in Comparative Example 5, the Fe content was small, the average heating rate was too high, and the intermediate annealing time was too short, so that the proportion of the Fe intermetallic compound was small. Therefore, Comparative Examples 1 to 5 and 8 all had low electrolytic efficiency and poor uniformity of the rough surface.
【0036】比較例6はFe含有量が少ないため、電解
効率が低く、反応性が不十分で、粗面の均一性が悪いも
のであった。比較例7はFe含有量が過剰であるため、
反応性が過大であり、粗面が不均一であった。比較例9
はCu含有量が多すぎたため、均一なピットが形成され
ず、粗面の均一性が劣るものであった。比較例10は不
可避的不純物のNi含有量が多すぎるため、反応性が過
剰となり、粗面の均一性が劣るものであった。In Comparative Example 6, since the Fe content was small, the electrolysis efficiency was low, the reactivity was insufficient, and the uniformity of the rough surface was poor. In Comparative Example 7, since the Fe content was excessive,
The reactivity was excessive and the rough surface was uneven. Comparative Example 9
Since the Cu content was too large, uniform pits were not formed and the uniformity of the rough surface was poor. In Comparative Example 10, the Ni content of the inevitable impurities was too large, so that the reactivity became excessive and the uniformity of the rough surface was poor.
【0037】[0037]
【発明の効果】以上説明したように、本発明によれば、
高電流密度及び短時間での電解粗面化処理において、電
解効率が高く、反応性が優れており、ピットが細かく均
一に分散されており、粗面の均一性が優れた印刷版用ア
ルミニウム合金板を得ることができる。As described above, according to the present invention,
Aluminum alloy for printing plates with high electrolysis efficiency, excellent reactivity, fine and uniform pits distribution, and excellent uniformity of rough surface in electrolytic roughening treatment with high current density and short time You can get a board.
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.7 識別記号 FI テーマコート゛(参考) // C22F 1/00 623 C22F 1/00 623 674 674 684 684C 691 691B 694 694B Fターム(参考) 2H025 AA14 AB03 DA20 DA36 2H096 AA06 CA03 CA20 2H114 AA04 AA16 DA04 DA73 EA01 EA02 GA02 ──────────────────────────────────────────────────続 き Continued on the front page (51) Int.Cl. 7 Identification symbol FI Theme coat ゛ (reference) // C22F 1/00 623 C22F 1/00 623 674 674 684 684C 691 691B 694 694B F term (reference) 2H025 AA14 AB03 DA20 DA36 2H096 AA06 CA03 CA20 2H114 AA04 AA16 DA04 DA73 EA01 EA02 GA02
Claims (2)
i:0.02乃至0.08質量%、Cu:0.04質量%
以下を含有し、残部がAl及び不可避的不純物からな
り、不可避的不純物におけるNiを0.005質量%以
下に規制した組成を有し、粒径が1μm以下のFe金属
間化合物が0.02質量%以上であることを特徴とする
印刷版用アルミニウム合金板。1. Fe: 0.25 to 0.45 mass%, S
i: 0.02 to 0.08 mass%, Cu: 0.04 mass%
And the balance consists of Al and unavoidable impurities, and has a composition in which Ni in the unavoidable impurities is regulated to 0.005% by mass or less, and the Fe intermetallic compound having a particle size of 1 μm or less is 0.02% by mass. % Of an aluminum alloy plate for a printing plate.
i:0.02乃至0.08質量%、Cu:0.04質量%
以下を含有し、残部がAl及び不可避的不純物からな
り、不可避的不純物におけるNiを0.005質量%以
下に規制した組成を有するアルミニウム合金鋳塊を、5
50℃以上の温度で均質化処理する工程と、開始温度を
400乃至450℃として熱間圧延する工程と、その
後、少なくとも1回、平均昇温速度10乃至60℃/時
で昇温させて450乃至500℃に1乃至20時間保持
する焼鈍処理を行う工程とを有し、粒径が1μm以下の
Fe金属間化合物が0.02質量%以上であるアルミニ
ウム合金板を製造することを特徴とする印刷版用アルミ
ニウム合金板の製造方法。2. Fe: 0.25 to 0.45 mass%, S
i: 0.02 to 0.08 mass%, Cu: 0.04 mass%
The aluminum alloy ingot having the following composition, with the balance being Al and inevitable impurities, having a composition in which Ni in the inevitable impurities is regulated to 0.005% by mass or less, is
A step of homogenizing at a temperature of 50 ° C. or higher, a step of hot rolling at a starting temperature of 400 to 450 ° C., and thereafter, heating at least once at an average heating rate of 10 to 60 ° C./hour to 450 Performing an annealing treatment at 1 to 20 hours at a temperature of from 500 to 500 ° C. to produce an aluminum alloy plate having an Fe intermetallic compound having a particle size of 1 μm or less of 0.02% by mass or more. A method for manufacturing an aluminum alloy plate for a printing plate.
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Cited By (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2007026574A1 (en) * | 2005-08-30 | 2007-03-08 | Fuji Photo Film Co., Ltd. | Aluminum alloy plate for surface printing plate and method for production thereof |
JP2007063586A (en) * | 2005-08-30 | 2007-03-15 | Fujifilm Holdings Corp | Aluminum alloy plate for lithographic printing plate, and method for producing the same |
JP2007063587A (en) * | 2005-08-30 | 2007-03-15 | Fujifilm Holdings Corp | Aluminum alloy plate for lithographic printing plate, and method for producing the same |
JP2007063588A (en) * | 2005-08-30 | 2007-03-15 | Fujifilm Holdings Corp | Aluminum alloy plate for lithographic printing plate, and method for producing the same |
JP2007070674A (en) * | 2005-09-06 | 2007-03-22 | Fujifilm Holdings Corp | Aluminum alloy sheet for planographic printing plate, and manufacturing method therefor |
JP2007092170A (en) * | 2005-08-30 | 2007-04-12 | Fujifilm Corp | Aluminum alloy plate for lithographic printing plate and method for production thereof |
JP2009255434A (en) * | 2008-04-18 | 2009-11-05 | Fujifilm Corp | Aluminum alloy plate for planographic printing plate, support body for planographic printing, original plate for planographic printing plate, and manufacturing process of aluminum alloy plate for planographic printing plate |
EP2110261A3 (en) * | 2008-04-18 | 2016-01-20 | FUJIFILM Corporation | Aluminum alloy plate for lithographic printing plate, ligthographic printing plate support, presensitized plate, method of manufacturing aluminum alloy plate for lithographic printing plate and method of manufacturing lithographic printing plate support |
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2001
- 2001-04-25 JP JP2001128268A patent/JP3893031B2/en not_active Expired - Fee Related
Cited By (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2007026574A1 (en) * | 2005-08-30 | 2007-03-08 | Fuji Photo Film Co., Ltd. | Aluminum alloy plate for surface printing plate and method for production thereof |
JP2007063586A (en) * | 2005-08-30 | 2007-03-15 | Fujifilm Holdings Corp | Aluminum alloy plate for lithographic printing plate, and method for producing the same |
JP2007063587A (en) * | 2005-08-30 | 2007-03-15 | Fujifilm Holdings Corp | Aluminum alloy plate for lithographic printing plate, and method for producing the same |
JP2007063588A (en) * | 2005-08-30 | 2007-03-15 | Fujifilm Holdings Corp | Aluminum alloy plate for lithographic printing plate, and method for producing the same |
JP2007092170A (en) * | 2005-08-30 | 2007-04-12 | Fujifilm Corp | Aluminum alloy plate for lithographic printing plate and method for production thereof |
JP2007070674A (en) * | 2005-09-06 | 2007-03-22 | Fujifilm Holdings Corp | Aluminum alloy sheet for planographic printing plate, and manufacturing method therefor |
JP2009255434A (en) * | 2008-04-18 | 2009-11-05 | Fujifilm Corp | Aluminum alloy plate for planographic printing plate, support body for planographic printing, original plate for planographic printing plate, and manufacturing process of aluminum alloy plate for planographic printing plate |
EP2110261A3 (en) * | 2008-04-18 | 2016-01-20 | FUJIFILM Corporation | Aluminum alloy plate for lithographic printing plate, ligthographic printing plate support, presensitized plate, method of manufacturing aluminum alloy plate for lithographic printing plate and method of manufacturing lithographic printing plate support |
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