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JPH0625808A - Production of aluminum alloy sheet for anodic oxidation treatment - Google Patents

Production of aluminum alloy sheet for anodic oxidation treatment

Info

Publication number
JPH0625808A
JPH0625808A JP4178662A JP17866292A JPH0625808A JP H0625808 A JPH0625808 A JP H0625808A JP 4178662 A JP4178662 A JP 4178662A JP 17866292 A JP17866292 A JP 17866292A JP H0625808 A JPH0625808 A JP H0625808A
Authority
JP
Japan
Prior art keywords
aluminum alloy
temperature
corrosion resistance
heat treatment
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
Application number
JP4178662A
Other languages
Japanese (ja)
Other versions
JP3308305B2 (en
Inventor
Tsutomu Moriyama
勉 森山
Makoto Tsuchida
信 土田
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Sumitomo Light Metal Industries Ltd
Original Assignee
Sumitomo Light Metal Industries Ltd
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Sumitomo Light Metal Industries Ltd filed Critical Sumitomo Light Metal Industries Ltd
Priority to JP17866292A priority Critical patent/JP3308305B2/en
Publication of JPH0625808A publication Critical patent/JPH0625808A/en
Application granted granted Critical
Publication of JP3308305B2 publication Critical patent/JP3308305B2/en
Anticipated expiration legal-status Critical
Expired - Fee Related legal-status Critical Current

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Abstract

PURPOSE:To produce an aluminum alloy sheet capable of forming an anodic oxidation film having uniform color tone and superior corrosion resistance. CONSTITUTION:An aluminum alloy having a composition which consists of, by weight, 0.05-0.5% Si, 0.15-0.9% Fe, 0.05-0.5% Cu, 0.01-0.05% Ti, <=0.05% each of inevitable impurities, and the balance Al (where Al content is regulated to >=199.00%) and in which, 0.30<=Si+Fe<=1.0%, >=<=Fe and 0.3 [si%]<=Mg<=1.0 [si%] are satisfied is heat-treated at 450-600 deg.C for 1-20hr. Hot rolling is started at 400-550 deg.C, and the rolling is finished at 200-300 deg.C. Successively, the resulting plate is subjected to cold rolling, to intermediate heat treatment at <=400 deg.C for >=30min, and to final cold rolling at >=30% reduction in thickness. By this method, the aluminum alloy sheet can be produced.

Description

【発明の詳細な説明】Detailed Description of the Invention

【0001】[0001]

【産業上の利用分野】本発明は陽極酸化皮膜の耐食性、
色調の均一性(安定性)、あるいはエッチングしたとき
の外観の均一性を必要とする各種の用途に使用される純
アルミ系合金板。建築用内外装パネル材、日用品、厨房
用品、平版印刷版支持体、装飾用部材などに関する。
The present invention relates to the corrosion resistance of an anodized film,
Pure aluminum alloy plate used for various applications that require uniformity of color tone (stability) or uniformity of appearance when etched. The present invention relates to interior and exterior panel materials for construction, daily necessities, kitchen articles, lithographic printing plate supports, decorative members and the like.

【0002】[0002]

【従来の技術】純アルミ系合金として工業的に使われる
JIS−A1100、1200ないし1050、106
0、1070および1N00、1N30、1230など
の合金では、その陽極酸化皮膜の耐食性や色調の均一性
は、純アルミ系以外の他の合金系のアルミニウム合金に
比べ優れている。しかし、酸性雨に代表されるように、
最近の地球環境は著しく悪化しており、建築用外装パネ
ルなどに使用した場合、従来の純アルミ系合金よりさら
に高度の耐食性が要求されている。
2. Description of the Related Art JIS-A1100, 1200 to 1050, 106 industrially used as a pure aluminum alloy.
In the alloys such as 0, 1070 and 1N00, 1N30, 1230, the corrosion resistance of the anodized film and the uniformity of the color tone are superior to those of other alloy type aluminum alloys other than pure aluminum type. However, as represented by acid rain,
The global environment has been remarkably deteriorated in recent years, and when it is used for exterior panels for buildings and the like, higher corrosion resistance than conventional pure aluminum alloys is required.

【0003】一方、色調の均一化についても、ビルなど
を単なる建築構造物としてではなく、都市のファッショ
ンの一部としてみられる今日では、従来より一層優れた
均一化が要求されている。これらの品質特性は、合金中
に含まれる不純物としてのFe、Siに支配されるの
で、一般にFe、Si量、すなわち、純アルミ系合金の
純度を規制することで対処している。
On the other hand, with respect to the uniformization of the color tone, nowadays, where a building or the like is seen as a part of fashion in a city, not as a simple building structure, there is a demand for a more uniform uniformity. Since these quality characteristics are controlled by Fe and Si as impurities contained in the alloy, they are generally dealt with by controlling the amounts of Fe and Si, that is, the purity of the pure aluminum alloy.

【0004】しかし、アルミ純度を高めることによって
耐食性や陽極酸化皮膜の色調の均一性を向上させること
は、地金コストが上昇し、また、機械的性質、特に硬
さ、強度の低下を招く。耐食性を向上させるために、陽
極酸化皮膜の膜厚を厚くする方法や、アルミ純度を高め
ることによる強度の低下を補うために板厚を厚くする方
法があるが、いずれもコスト上昇を招き好ましくない。
皮膜の色調の均一化に対しては膜厚で調整することが行
なわれるが、膜厚調整に手間取り、コストアップを招
く。
However, improving the corrosion resistance and the uniformity of the color tone of the anodized film by increasing the purity of aluminum raises the cost of the base metal and lowers the mechanical properties, especially hardness and strength. In order to improve the corrosion resistance, there is a method of increasing the film thickness of the anodized film, and a method of increasing the plate thickness to compensate for the decrease in strength due to the increase in aluminum purity, but both of these are not preferable because they increase costs. .
Although the film thickness is adjusted to make the color tone of the film uniform, it takes time to adjust the film thickness, resulting in an increase in cost.

【0005】[0005]

【発明が解決しようとする課題】本発明は酸化皮膜を厚
くしたり、板厚を厚くしなくても、耐食性が優れた陽極
酸化皮膜が生成し、かつ、機械的強度も充分なアルミニ
ウム合金板の製造方法を提供しようとするものである。
DISCLOSURE OF THE INVENTION The present invention provides an aluminum alloy sheet which has an excellent corrosion resistance and has a sufficient mechanical strength without thickening the oxide film or increasing the plate thickness. The present invention is intended to provide a manufacturing method of.

【0006】[0006]

【課題を解決するための手段】陽極酸化皮膜の耐食性を
損う機構について研究した結果、アルミ合金中に含まれ
るSiが、単独のSi粒子として析出した状態で存在す
るとき、このようなアルミ合金板を陽極酸化処理する
と、Si粒子が皮膜中に残存し、これが、周囲の皮膜と
化学的性質が異るために、塩素イオンを含む腐食媒によ
って、選択的に溶解脱落して皮膜欠陥となり腐食が進行
することが明らかになった。
[Means for Solving the Problems] As a result of research on the mechanism of impairing the corrosion resistance of an anodized film, when Si contained in an aluminum alloy exists in the state of being precipitated as individual Si particles, such an aluminum alloy When the plate is anodized, Si particles remain in the film, and because the chemical properties of the particles are different from those of the surrounding film, they are selectively dissolved and dropped by a corrosive medium containing chlorine ions, resulting in film defects and corrosion. Became clear.

【0007】また、皮膜の色調は、皮膜中に分布する1
μm以下の細かいSi粒子の粒度分布と陽極酸化処理の
前処理として表面の傷を除くための苛性エッチングの際
のエッチングむらによる光沢差に影響されることが判明
した。
Further, the color tone of the film is distributed in the film 1.
It was found that the particle size distribution of fine Si particles having a size of μm or less and the difference in gloss due to uneven etching during caustic etching for removing scratches on the surface as a pretreatment for anodizing treatment are affected.

【0008】そこで、このSi粒子の析出を防止する方
法について検討し、適当量のMgを添加してMg2Si
なる化合物として析出させればよいことエッチングむら
を防止する方法としては、適当量のCuを添加すれば均
一に苛性エッチングされ、光沢が均一になることが分っ
た。添加するMg量は、固溶しているSiを化合物Mg
2Siとして形成させるに相当する量で十分である。
Therefore, a method for preventing the precipitation of the Si particles was examined, and an appropriate amount of Mg was added to the Mg 2 Si layer.
It has been found that as a method for preventing uneven etching, it is possible to uniformly caustic-etch and add a uniform gloss to prevent uneven etching. The amount of Mg added is based on the solid solution of Si as a compound Mg.
An amount corresponding to the formation of 2 Si is sufficient.

【0009】上記研究の結果、本発明の構成は特許請求
の範囲に記載のとおりの色調が均一で耐食性が優れた陽
極酸化皮膜が得られるアルミニウム合金板の製造方法で
ある。
As a result of the above research, the constitution of the present invention is a method for producing an aluminum alloy plate capable of obtaining an anodized film having a uniform color tone and excellent corrosion resistance as described in the claims.

【0010】以下、上記構成について説明する。The above structure will be described below.

【0011】機械的性質、化学的性質が一般的に知られ
る純アルミとして取扱える範囲内にとどめる必要がある
ので、添加する成分、不可避不純物を除いたAl純度は
99.00%以上でなければならない。
Since it is necessary to keep the mechanical properties and chemical properties within the range that can be handled as pure aluminum, which is generally known, the Al purity excluding the added components and unavoidable impurities must be 99.00% or more. I won't.

【0012】Feは再結晶粒を微細にするために添加さ
れる。0.15%未満ではその効果が小さくなる。0.
9%をこえるFeの添加は、粗大なAl−Fe系および
Al−Fe−Si系化合物を形成し、これが薄板の成形
性を低下させたり、化学的性質の局所的不均一性をもた
らすなどのために好ましくない。
Fe is added to make the recrystallized grains finer. If it is less than 0.15%, the effect becomes small. 0.
Addition of Fe in excess of 9% forms coarse Al-Fe-based and Al-Fe-Si-based compounds, which lowers the formability of the sheet and causes local non-uniformity of chemical properties. Not preferred because of

【0013】Siはアルミ地金中に必然的に含まれる分
が通常0.05%以上あり、0.05%未満にすること
は地金コスト上昇を招く。0.5%を越えるSiはFe
による再結晶粒微細化効果を損い、耐食性を低下させ
る。
The content of Si inevitably contained in the aluminum ingot is 0.05% or more, and if it is less than 0.05%, the ingot cost is increased. Si over 0.5% is Fe
This impairs the effect of refining recrystallized grains and reduces corrosion resistance.

【0014】{Si+Fe}量は、材料強度をはじめと
する機械的性質、および化学的性質、さらには地金コス
トの観点から調整される。その量を0.30%未満にす
ることは、高純度の地金を使うことになりコスト高にな
り、また材料強度の低下となる。
The amount of {Si + Fe} is adjusted from the viewpoints of mechanical strength such as material strength, chemical properties, and ingot cost. If the amount is less than 0.30%, high-purity metal is used, resulting in higher cost and lower material strength.

【0015】{Si+Fe}量が1.0%以上になる
と、Alが99.00%未満となり、純アルミとしての
特性が損なわれる。実際には次に記すCu、Ti、Mg
と不可避不純物との総和が1.0%未満でなければなら
ない。
When the amount of {Si + Fe} is 1.0% or more, Al is less than 99.00%, and the characteristics as pure aluminum are impaired. Actually, the following Cu, Ti, Mg
And the unavoidable impurities must be less than 1.0%.

【0016】Si量がFe量よりも多くなると、Feに
よる再結晶粒の微細化効果が損なわれ、耐食性も低下す
るので、{Fe%}≧{Si%}が必要である。
When the amount of Si exceeds the amount of Fe, the effect of refining the recrystallized grains by Fe is impaired and the corrosion resistance is also lowered, so that {Fe%} ≧ {Si%} is required.

【0017】Cuは陽極酸化処理の前処理として一般に
行われる苛性エッチングに影響を与える元素である。苛
性エッチングが不均一になると光沢むらとなり、陽極酸
化処理後の色調のばらつきの原因となる。Cuが0.0
5%以上0.5%以下の量で添加されると、苛性エッチ
ングが均一に行われ、光沢むらがなくなる。0.05%
未満ではその効果が得られない。0.5%を越える場
合、陽極酸化処理前の元板の耐食性が劣化するため好ま
しくない。
Cu is an element that affects caustic etching generally performed as a pretreatment for anodizing treatment. If the caustic etching becomes non-uniform, the gloss becomes uneven, which causes variations in color tone after anodizing. Cu is 0.0
When it is added in an amount of 5% or more and 0.5% or less, caustic etching is uniformly performed, and uneven gloss is eliminated. 0.05%
If less than, the effect cannot be obtained. If it exceeds 0.5%, the corrosion resistance of the base plate before anodizing is deteriorated, which is not preferable.

【0018】Tiは、主として鋳塊の結晶粒微細化のた
めに添加される。0.01%未満では効果小さく、0.
05%を超えると、粗大なAl−Ti化合物を形成し、
圧延板に筋状に分布して陽極酸化皮膜の欠陥となること
がある。
Ti is added mainly for refining the crystal grains of the ingot. If it is less than 0.01%, the effect is small.
If it exceeds 05%, a coarse Al-Ti compound is formed,
It may be distributed in a streaky pattern on the rolled plate and may cause defects in the anodized film.

【0019】Tiはまた圧延した板の再結晶粒を微細化
する効果もある。
Ti also has the effect of refining the recrystallized grains of the rolled plate.

【0020】結晶粒微細化のためには、Ti単独ではな
く、TiとBの複合添加による方法もある。この場合で
もTi量は0.01〜0.05%の範囲に調整するのが
好ましい。B量は不純物として計上するが、その添加量
は通常では30ppm以下である。
There is also a method of adding Ti and B in combination, instead of Ti alone, for refining the crystal grains. Even in this case, it is preferable to adjust the Ti amount in the range of 0.01 to 0.05%. Although the amount of B is included as an impurity, the amount added is usually 30 ppm or less.

【0021】Mgは本発明の主要点に係る添加成分であ
る。陽極酸化皮膜の耐食性を損うSi粒子はAl−Fe
−Si化合物とならずにAl(マトリックス)中に固溶
するSiが、単独で析出したものである。Si粒子は陽
極酸化処理で溶解しないで皮膜中に残存する。Mgを添
加してMg2Siなる化合物にすれば、陽極酸化処理で
アルミニウムとともに溶解してしまうので皮膜欠陥にな
らなくなる。本合金に含まれる0.05〜0.5%のS
iのうち、一部はFe、Alと結合してAl−Fe−S
i系化合物となっており、この結合したSiは、Si粒
子として析出しない。
Mg is an additive component relating to the main points of the present invention. Si particles that impair the corrosion resistance of the anodized film are Al-Fe.
-Si that is not a Si compound but is solid-solved in Al (matrix) is precipitated alone. The Si particles remain in the film without being dissolved by the anodizing treatment. When Mg is added to form a compound of Mg 2 Si, it dissolves together with aluminum in the anodizing process, and thus does not become a film defect. 0.05-0.5% S contained in this alloy
Part of i is combined with Fe and Al to form Al-Fe-S.
It is an i-based compound, and this bonded Si does not precipitate as Si particles.

【0022】すなわち、Mg2SiとするべきSiは、
Al−Fe−Si化合物とならずにAlマトリックス中
に固溶している分であって、X線マイクロアナライザー
による分析結果から推定すると、その量はSiの添加
量、同時に含まれるFe量、加工熱処理の条件などで変
化するが、Siの全添加量のおよそ20〜60%とみな
される。
That is, Si to be Mg 2 Si is
It is the amount that does not become an Al-Fe-Si compound but is solid-solved in the Al matrix, and it is estimated from the analysis result by the X-ray microanalyzer, that amount is the amount of Si added, the amount of Fe contained at the same time, Although it varies depending on the heat treatment conditions and the like, it is considered to be about 20 to 60% of the total amount of Si added.

【0023】以上の事項を考慮し、本発明の目的を達成
するに必要なMg添加量につき種々検討した結果、0.
3×{Si%}≦Mg≦1.0×{Si%}の範囲にM
g量を制御することが必要であることが判った。
In consideration of the above matters, various examinations have been made on the amount of added Mg required to achieve the object of the present invention, and as a result,
M in the range of 3 × {Si%} ≦ Mg ≦ 1.0 × {Si%}
It has been found necessary to control the amount of g.

【0024】但し、{Si%}は含有Si量(%)とす
る。
However, {Si%} is the Si content (%).

【0025】尚、Mgが少ないと、固溶Siが残り、S
i粒子として析出する。
If Mg is small, solid solution Si remains and S
Precipitates as i particles.

【0026】また、過剰なMgはAlマトリックス中に
固溶し、陽極酸化皮膜中には残らないので、耐食性や色
調には影響しない。僅かに材料強度を高め、あるいは化
学的性質を変化させるが、その影響は軽微である。
Further, since excess Mg forms a solid solution in the Al matrix and does not remain in the anodized film, it does not affect the corrosion resistance or the color tone. The material strength is slightly increased or the chemical properties are changed, but the effect is slight.

【0027】次に製造方法について述べる。Next, the manufacturing method will be described.

【0028】所定の組成に配合したアルミニウム合金
を、通常の方法により鋳塊とし、表面偏析層が最終製品
の品質上有害であれば、これを切削除去する。切削除去
するのは、均質化熱処理の後、熱間圧延の前でもよい。
An aluminum alloy blended with a predetermined composition is formed into an ingot by a usual method, and if the surface segregation layer is harmful to the quality of the final product, it is cut and removed. Cutting and removal may be performed after the homogenizing heat treatment and before the hot rolling.

【0029】つぎに、鋳塊は鋳造組織の均質化と、F
e、SiをAl−Fe−Si系化合物とするために熱処
理される。450℃より低温、あるいは600℃より高
温では、この化合物の形成が起りにくい。熱処理時間は
長い方が好ましいが、生産性(経済性)から20時間以
内とする。実用上3〜10時間で問題はない。
Next, the ingot is homogenized in the casting structure and F
e and Si are heat-treated to form an Al-Fe-Si-based compound. At a temperature lower than 450 ° C or higher than 600 ° C, formation of this compound is unlikely to occur. The heat treatment time is preferably longer, but it is within 20 hours from the viewpoint of productivity (economical efficiency). There is no problem in practical use in 3 to 10 hours.

【0030】この熱処理のあと、室温に冷却して表層切
削除去後再加熱するか、あるいは冷却することなく、4
00℃〜550℃で熱間圧延を開始し、多パスの圧延を
行なって、終了時材料温度が200〜300℃になるよ
うに圧延を終了する。
After this heat treatment, the substrate is cooled to room temperature and reheated after removing the surface layer, or without cooling, 4
Hot rolling is started at 00 ° C. to 550 ° C., multi-pass rolling is performed, and rolling is finished so that the material temperature at the end is 200 to 300 ° C.

【0031】開始温度が400℃より低温だと圧延が困
難で、550℃より高温では、Al−Fe−Si化合物
が分解する可能性があり、圧延板面の酸化が進むなど好
ましくない。
If the starting temperature is lower than 400 ° C., rolling is difficult, and if the starting temperature is higher than 550 ° C., the Al—Fe—Si compound may decompose, which is not preferable because the rolling plate surface is oxidized.

【0032】終了温度は結晶組織の微細化のために規制
する。200℃より低温では、圧延油が蒸発しきれずに
板面に残留して表面汚れや腐食を招く。300℃より高
温では、再結晶粒が粗大に成長し、最終板で帯状の組織
による色調(光沢)のムラになる。これらの温度範囲内
で、最適温度は、最終板の結晶組織、機械的性質の異方
性などを最適化するように決定される。
The end temperature is regulated for the refinement of the crystal structure. If the temperature is lower than 200 ° C., the rolling oil cannot be completely evaporated and remains on the plate surface, causing surface contamination and corrosion. When the temperature is higher than 300 ° C., the recrystallized grains grow coarsely and the final plate has uneven band tone (gloss) due to the band-like structure. Within these temperature ranges, the optimum temperature is determined so as to optimize the crystal structure of the final plate, the anisotropy of mechanical properties, and the like.

【0033】熱間圧延をこのような温度範囲で行なうこ
とは、圧延中および圧延後の冷却中にMg2Siを形成
させるためにも重要である。
Performing hot rolling in such a temperature range is also important for forming Mg 2 Si during rolling and during cooling after rolling.

【0034】熱間圧延のあと、冷間圧延と中間熱処理を
行なう。中間熱処理の前に冷間圧延を加えることで、中
間熱処理での再結晶粒が微細になり最終板をエッチング
したときの結晶粒に起因する筋状の色調(光沢)ムラが
防止される。熱間圧延終了温度が250℃より低いと冷
間圧延と同様の効果がある。中間熱処理を400℃以下
でかつ30分以上で行なうのは、固溶しているSiとM
gをMg2Siの化合物にするためである。400℃よ
り高温または30分未満では、この化合物が生成されに
くい。通常は、この中間熱処理で冷間圧延による加工組
織を再結晶させるので、300℃以上に加熱するが、再
結晶させる必要のない場合は300℃より低温でもよ
い。
After hot rolling, cold rolling and intermediate heat treatment are performed. By performing cold rolling before the intermediate heat treatment, the recrystallized grains in the intermediate heat treatment become fine, and streaky color tone (gloss) unevenness due to the crystal grains when the final plate is etched can be prevented. When the hot rolling finish temperature is lower than 250 ° C, the same effect as cold rolling is obtained. Performing the intermediate heat treatment at 400 ° C. or lower and for 30 minutes or longer is due to solid solution of Si and M.
This is because g is a compound of Mg 2 Si. At a temperature higher than 400 ° C. or less than 30 minutes, this compound is hard to be produced. Usually, this intermediate heat treatment recrystallizes the work structure by cold rolling, so it is heated to 300 ° C. or higher, but if recrystallization is not necessary, it may be lower than 300 ° C.

【0035】中間熱処理のあとに行なう30%以上の最
終冷間圧延は、最終板の機械的性質を調整するためで、
その加工度が大きければ強度、硬さが増す。最適値は最
終板の用途にもとづいて選定される。
The final cold rolling of 30% or more performed after the intermediate heat treatment is to adjust the mechanical properties of the final plate.
If the degree of processing is large, strength and hardness increase. The optimum value is selected based on the end plate application.

【0036】用途によっては、伸びの大きい焼なまし材
の方がよいことがある。このためには、最終冷間圧延の
あと、200〜400℃で熱処理を加えればよい。20
0℃より低温では、機械的性質の変化が遅い。400℃
より高温では、再結晶粒が粗大化する。また、形成され
ていたMg2Siの分解が起こり、MgとSiが再溶解
するので好ましくない。
Depending on the application, it may be preferable to use an annealed material having a large elongation. For this purpose, heat treatment may be applied at 200 to 400 ° C. after the final cold rolling. 20
At temperatures lower than 0 ° C, changes in mechanical properties are slow. 400 ° C
At higher temperatures, the recrystallized grains become coarse. In addition, the formed Mg 2 Si is decomposed and Mg and Si are redissolved, which is not preferable.

【0037】中間熱処理を平均昇温速度10℃/秒の急
速加熱によって行なえば、再結晶粒が微細になり、成形
加工性やエッチングしたときの外観などが改善される。
再結晶させるには400℃以上に5秒間以上加熱するこ
とが必要である。この熱処理温度が500℃より高温で
あったり、保持時間が長すぎると、熱間圧延の後半およ
び終了後の冷却中に形成されたMg2Siの分解、再固
溶が起こる。規定した条件内であれば、実用上無害であ
る。
If the intermediate heat treatment is performed by rapid heating at an average temperature rising rate of 10 ° C./sec, the recrystallized grains become finer, and the moldability and appearance when etched are improved.
To recrystallize, it is necessary to heat to 400 ° C. or higher for 5 seconds or longer. If this heat treatment temperature is higher than 500 ° C. or if the holding time is too long, the decomposition and re-solid solution of Mg 2 Si formed during the latter half of hot rolling and during cooling after the end of hot rolling will occur. It is practically harmless if it is within the specified conditions.

【0038】こうして得られた最終板は、例えば苛性ソ
ーダ水溶液によりエッチングし、中和処理してから硫酸
水溶液中で陽極酸化処理して、美観および耐食性を附与
して使用される。
The final plate thus obtained is used by, for example, etching it with an aqueous solution of caustic soda, neutralizing it, and then anodizing it in an aqueous solution of sulfuric acid to impart aesthetics and corrosion resistance.

【0039】[0039]

【実施例】以下、実施例によって本発明を具体的に説明
する。
EXAMPLES The present invention will be specifically described below with reference to examples.

【0040】実施例1 表1に示す化学成分をもつアルミニウム合金を溶解鋳造
し、鋳塊とした。表面偏析層を切削除去した後、500
℃×8時間熱処理したのち、そのまま熱間圧延に供し、
終了温度が245±15℃になるように圧延した。熱間
圧延板厚6mmから冷間圧延で3.5mmとしたのち、
360±10℃×2時間の中間熱処理を施してから、冷
間圧延して2.0mm厚みの板とした。最終冷間圧延の
板厚減少率は43%である。これをH14材とする。
Example 1 An aluminum alloy having the chemical composition shown in Table 1 was melt cast to obtain an ingot. After cutting and removing the surface segregation layer, 500
After heat treatment at ℃ × 8 hours, directly subjected to hot rolling,
Rolling was performed so that the end temperature was 245 ± 15 ° C. After making the hot rolled plate thickness 6 mm to 3.5 mm by cold rolling,
An intermediate heat treatment of 360 ± 10 ° C. × 2 hours was performed, and then cold rolling was performed to obtain a plate having a thickness of 2.0 mm. The plate thickness reduction rate of the final cold rolling is 43%. This is designated as H14 material.

【0041】さらに冷間圧延して0.70mm厚み(板
厚減少率80%)にした板をH18材とする。
Further, a cold-rolled sheet having a thickness of 0.70 mm (sheet thickness reduction rate of 80%) is designated as H18 material.

【0042】さらにこのH18材を250℃×2時間加
熱して半なまし状態にした。(H24材) また、360℃×2時間加熱して完全焼きなまししたも
のを製作した。(O材) これら、各材料の陽極酸化皮膜の耐食性を次のようにし
て評価した。
Further, this H18 material was heated at 250 ° C. for 2 hours to be semi-annealed. (H24 material) Further, a product that was completely annealed by heating at 360 ° C. for 2 hours was manufactured. (O material) The corrosion resistance of the anodic oxide film of each of these materials was evaluated as follows.

【0043】まず、10%苛性ソーダ水溶液(40℃)
中で2分間エッチングした。水洗および中和処理のあ
と、15%硫酸浴(25℃)中で1A/dm2の電流密
度で10分間陽極酸化処理を施す。生成する皮膜の厚さ
はおよそ2.5μmである。つぎに、3%食塩水(25
℃)を用いて浸漬10分間、乾燥50分間の交互浸漬を
10サイクル行ない皮膜を腐食させる。次に、飽和硫酸
銅液(25℃)中で、2V×3分間の通電を行なう。こ
れによって、陽極酸化皮膜に微小孔など欠陥があると、
通電によってそこに銅が還元されて析出する。
First, a 10% aqueous sodium hydroxide solution (40 ° C.)
Etched in 2 minutes. After washing with water and neutralization, anodization is performed for 10 minutes at a current density of 1 A / dm 2 in a 15% sulfuric acid bath (25 ° C.). The thickness of the film formed is approximately 2.5 μm. Next, 3% saline solution (25
(10 ° C.), the coating is corroded by performing alternate dipping for 10 minutes for dipping and 50 minutes for drying for 10 cycles. Next, electricity is applied for 2 V × 3 minutes in a saturated copper sulfate solution (25 ° C.). As a result, if the anodic oxide film has defects such as micropores,
Copper is reduced and deposited there by energization.

【0044】[0044]

【表1】 [Table 1]

【0045】このように処理した板を、光学顕微鏡で拡
大観察すると、点状に析出した銅を認めることができ
る。皮膜の耐食性の評価は、表1に示すNo.4,8,1
2,16(比較材)の皮膜に発生した銅の析出点(皮膜
欠陥)の密度をランク5とし、全く欠陥のない状態をラ
ンク0として、その間をランク4,3,2,1に分類し
た。
When the plate thus treated is magnified and observed under an optical microscope, spotted copper can be observed. Evaluation of the corrosion resistance of the coating is shown in Table 1, No. 4, 8, 1
The density of copper precipitation points (film defects) generated in the films of Nos. 2 and 16 (comparative material) was ranked as rank 5, the state without any defects was ranked as rank 0, and the spaces between them were classified into ranks 4, 3, 2, 1. .

【0046】従って、評価は相対評価である。また、陽
極酸化前の元板の耐食性の評価は、JIS Z 237
1塩水噴霧試験法に基づき、35℃の5%食塩水を10
0時間噴霧し、その結果を相対的に比較して次のように
3段階評価により表した。
Therefore, the evaluation is a relative evaluation. In addition, the evaluation of the corrosion resistance of the original plate before anodizing is performed according to JIS Z237.
1 Based on the salt spray test method, 10% of 5% saline at 35 ° C was used.
It was sprayed for 0 hour, and the results were compared relatively and expressed by the following three-stage evaluation.

【0047】JIS A 1050と同等:○ JIS A 1050より若干劣る:△ JIS A 1050より劣る:× なお、H14、H18、H24、O材の調質による元板
の耐食性には大差がなかったため、H14材の結果につ
いて表した。
Equivalent to JIS A 1050: ○ Slightly inferior to JIS A 1050: △ Inferior to JIS A 1050: × In addition, there was no great difference in the corrosion resistance of the base plate due to the tempering of the H14, H18, H24 and O materials. The results of H14 material are shown.

【0048】評価結果を表2に示す。Mg含有量の少な
い比較材に比べて、Mgを加えた発明材では皮膜の耐食
性が改良されており、Cuが本発明の成分範囲を越える
と、元板の耐食性が悪いことが分る。
The evaluation results are shown in Table 2. As compared with the comparative material having a low Mg content, the corrosion resistance of the film was improved in the invention material containing Mg, and it can be seen that when the content of Cu exceeds the composition range of the present invention, the corrosion resistance of the base plate is poor.

【0049】[0049]

【表2】 [Table 2]

【0050】さらに、陽極酸化皮膜の色調安定性を次の
ようにして評価した。
Further, the color tone stability of the anodized film was evaluated as follows.

【0051】表1に示した合金のうち、No.13,1
7,18,19のH18材について、150〜450℃
で各8時間焼なまし処理を施し、6%苛性ソーダ水溶液
(70℃)中で3分間エッチングし、中和したあと、1
5%硫酸浴(20℃)中で1.5A/dm2×40mi
nの陽極酸化処理を行なって(皮膜厚み15μm),常
圧沸騰水中で封孔処理し、皮膜の色調を測定した。
Among the alloys shown in Table 1, No. 13, 1
About H18 material of 7, 18, 19 150-450 ℃
After annealing for 8 hours each, etching in 6% caustic soda aqueous solution (70 ° C) for 3 minutes to neutralize
1.5 A / dm 2 × 40 mi in a 5% sulfuric acid bath (20 ° C.)
Anodizing treatment of n (coating thickness 15 μm) was performed, and sealing treatment was performed in normal pressure boiling water, and the color tone of the coating was measured.

【0052】その結果を表3に示す。MgとCuを添加
した合金(No.13,17)では、200〜400℃の
範囲では焼なまし温度によって陽極酸化皮膜の色調が殆
ど変化しないことが分る。このことは、圧延板の製造工
程で熱間圧延温度や熱処理などの条件が変動した場合で
も、最終板の皮膜色調が殆ど変化せず、安定した色調が
複数のロット間あるいは1コイル内で得られることを示
している。
The results are shown in Table 3. In the alloy containing Mg and Cu (No. 13, 17), it can be seen that the color tone of the anodized film hardly changes depending on the annealing temperature in the range of 200 to 400 ° C. This means that even if conditions such as hot rolling temperature and heat treatment change in the manufacturing process of the rolled plate, the film color tone of the final plate hardly changes, and stable color tone is obtained between multiple lots or within one coil. Is shown.

【0053】[0053]

【表3】 [Table 3]

【0054】 (注)皮膜色調表示はJISZ8729−1980に準
拠。
(Note) The film color tone display conforms to JIS Z8729-1980.

【0055】L*は 明るい(大)←→暗い(小) a*は 赤(+)←→緑(−) b*は 黄(+)←→青(−)を表わす。L * is bright (large) ← → dark (small) a * is red (+) ← → green (-) b * is yellow (+) ← → blue (-).

【0056】実施例2 表4に示す合金、No.20及び21を造塊し、表面偏析
層を除去してから、540℃×4時間加熱して、480
℃に冷却し熱間圧延を開始。終了温度が275±15
℃、厚み5mmになるように熱間圧延し、引きつづいて
厚み2mmに冷間圧延した。ここで中間熱処理条件を種
々変えて処理したあと、板厚減少率50%の冷間圧延を
施して厚み1mmの板(H14材)とした。なお、中間
熱処理での昇温速度を30℃/秒とした。さらに360
℃×2時間の最終熱処理を施した板(0材)を用意し
て、それらの陽極酸化処理後の耐食性を実施例1と同様
にして評価した。また、陽極酸化処理した板面を目視で
外観検査し、結晶粒に起因する筋状の色調(光沢)むら
の程度を外観品質として評価した。評価値は同一合金材
の中での相対評価である。結果を表5に示す。中間熱処
理温度が低く短時間であると十分な再結晶が起らず、熱
間圧延で生成した粗大な結晶粒がそのまま圧延されるた
めに、最終板をエッチング、陽極酸化皮膜処理すると筋
状のむらが目立つようになる。中間熱処理温度を500
℃より高くすれば、再結晶が十分起るが、やや粗大化し
て筋状むらを呈し、また皮膜の耐食性が低下する。
Example 2 Alloys Nos. 20 and 21 shown in Table 4 were agglomerated, and after removing the surface segregation layer, they were heated at 540 ° C. for 4 hours and then 480
Cool to ℃ and start hot rolling. End temperature is 275 ± 15
It was hot-rolled to a temperature of 5 mm and a thickness of 5 mm, and then cold-rolled to a thickness of 2 mm. Here, after the intermediate heat treatment conditions were variously changed, the plate was cold-rolled at a plate thickness reduction rate of 50% to obtain a plate (H14 material) having a thickness of 1 mm. The temperature rising rate in the intermediate heat treatment was 30 ° C / sec. Further 360
A plate (0 material) that had been subjected to a final heat treatment of ° C x 2 hours was prepared, and the corrosion resistance thereof after the anodizing treatment was evaluated in the same manner as in Example 1. In addition, the appearance of the anodized plate surface was visually inspected, and the degree of streaky color tone (gloss) unevenness caused by crystal grains was evaluated as the appearance quality. The evaluation value is a relative evaluation within the same alloy material. The results are shown in Table 5. When the temperature of the intermediate heat treatment is low and the time is short, sufficient recrystallization does not occur, and the coarse crystal grains generated by hot rolling are rolled as they are. Will be noticeable. Intermediate heat treatment temperature 500
If the temperature is higher than 0 ° C, recrystallization will occur sufficiently, but it will become a little coarser and present streaky unevenness, and the corrosion resistance of the film will decrease.

【0057】陽極酸化皮膜の耐食性は中間熱処理温度が
低い方が良好であった。
The lower the intermediate heat treatment temperature was, the better the corrosion resistance of the anodized film was.

【0058】最終0材では、十分に冷間圧延された板が
再結晶して、筋状むらはH14材より軽微になったが、
中間熱処理の不適当なものではまだその影響が認められ
た。
In the final 0 material, the sufficiently cold-rolled sheet was recrystallized and the streak unevenness was smaller than that of the H14 material.
The effect was still recognized in the unsuitable intermediate heat treatment.

【0059】[0059]

【表4】 [Table 4]

【0060】[0060]

【表5】 [Table 5]

【0061】注)外観品質の説明 ○:良好、△:筋状の光沢むらが認められるが軽微、
×:筋状の光沢むらが部分的に認められる、××:筋状
の光沢むらが全面に認められる。
Note) Description of appearance quality ◯: good, Δ: streak-like gloss unevenness is recognized but slight,
X: Partial uneven streaks are observed, XX: Uneven streaks are observed on the entire surface.

【0062】実施例3 表6に示す合金No.22を造塊して、小さく切断し、均
質化熱処理、熱間圧延、冷間圧延、中間熱処理および冷
間圧延してH14担当材を作製し、その陽極酸化皮膜の
耐食性と皮膜の色調を実施例1と同様にして評価した。
Example 3 Alloy No. 22 shown in Table 6 was ingoted, cut into small pieces, and subjected to homogenizing heat treatment, hot rolling, cold rolling, intermediate heat treatment and cold rolling to prepare a material for H14. The corrosion resistance of the anodized film and the color tone of the film were evaluated in the same manner as in Example 1.

【0063】結果を表7に示す。400℃を越える高温
での長時間の中間熱処理、あるいは450℃未満の低温
での均質化処理では、陽極酸化皮膜の耐食性がよくなか
った。
The results are shown in Table 7. The corrosion resistance of the anodized film was not good in the intermediate heat treatment for a long time at a high temperature of over 400 ° C. or the homogenization treatment at a low temperature of less than 450 ° C.

【0064】[0064]

【表6】 [Table 6]

【0065】[0065]

【表7】 [Table 7]

【0066】[0066]

【表8】 [Table 8]

【0067】[0067]

【発明の効果】以上、説明したように、従来は、地金純
度を高めて対処した陽極酸化皮膜の耐食性と色調安定性
の改良に対し、少量のMgとCuの添加により純度の良
い合金と同様の効果が得られるので、地金コストの上昇
が避けられ、経済的効果が大きい。同一純度(Si,F
e量)の地金を使う場合は耐食性が向上し、製品寿命が
長くなる。
As described above, in the past, in order to improve the corrosion resistance and color stability of the anodic oxide film, which was dealt with by increasing the purity of the base metal, the alloy with a high purity was obtained by adding a small amount of Mg and Cu. Since the same effect can be obtained, it is possible to avoid an increase in the cost of bullion, and the economic effect is large. Same purity (Si, F
When the amount e of metal is used, the corrosion resistance is improved and the product life is extended.

【0068】また、従来その量を特に管理していなかっ
た不純物扱いのMgを、積極的に添加し調整したことに
よって使用地金によって変動していた耐食性のばらつき
が解消され、品質安定化が達成される。
Further, by positively adding and adjusting Mg, which has been treated as an impurity, whose amount has not been conventionally controlled, the variation in corrosion resistance, which fluctuates depending on the metal used, is eliminated, and quality stabilization is achieved. To be done.

Claims (3)

【特許請求の範囲】[Claims] 【請求項1】 重量基準でSi;0.05〜0.5%、
Fe;0.15〜0.9%、Si+Fe;0.30%以
上、1.0%未満、Si%≦Fe%であって、更に、C
u;0.05〜0.5%、Ti;0.01〜0.05
%、Mg;{Si%}×{0.3〜1.0}%を含み、
これらの成分と各0.05%以下の不可避不純物との残
部がAl(ただし、99.00%以上)からなるアルミ
ニウム合金を、半連続式鋳造によって造塊した後、必要
に応じて表面偏析層を切削除去し、450℃以上600
℃以下で1〜20時間熱処理して400℃以上550℃
以下で熱間圧延を開始して、材料温度が200℃以上3
00℃以下となるよう圧延を終了し、続いて冷間圧延と
400℃以下で30分以上の中間熱処理を行ない、板厚
減少率30%以上の最終冷間圧延をすることを特徴とす
る。色調が均一で耐食性が優れた陽極酸化皮膜が得られ
るアルミニウム合金板の製造方法。
1. Si based on weight; 0.05-0.5%,
Fe; 0.15-0.9%, Si + Fe; 0.30% or more, less than 1.0%, Si% ≦ Fe%, and further C
u: 0.05 to 0.5%, Ti: 0.01 to 0.05
%, Mg; including {Si%} × {0.3 to 1.0}%,
An aluminum alloy in which the balance between these components and 0.05% or less of each inevitable impurities is Al (however, 99.00% or more) is cast by semi-continuous casting, and then, if necessary, a surface segregation layer. Cutting and removing, 450 ℃ or more 600
Heat treatment at temperatures below 400C for 1 to 20 hours
The hot rolling was started below and the material temperature was 200 ° C or higher 3
It is characterized in that the rolling is finished so that the temperature becomes 00 ° C. or less, then the cold rolling and the intermediate heat treatment at 400 ° C. or less for 30 minutes or more are performed to perform the final cold rolling at a sheet thickness reduction rate of 30% or more. A method for producing an aluminum alloy plate, which can obtain an anodized film having a uniform color tone and excellent corrosion resistance.
【請求項2】 請求項1における中間熱処理を400℃
より高温で行う時の条件を平均昇温温度10℃/秒以上
で温度400℃を超え500℃以下に加熱し、5秒以
上、30秒以内保持するように替えたことを特徴とする
請求項1記載の色調が均一で耐食性が優れた陽極酸化皮
膜が得られるアルミニウム合金板の製造方法。
2. The intermediate heat treatment according to claim 1 is 400 ° C.
The condition when performing at a higher temperature is changed so that the average temperature rising temperature is 10 ° C./sec or more and the temperature is heated to more than 400 ° C. and 500 ° C. or less and held for 5 seconds or more and 30 seconds or less. 1. A method for producing an aluminum alloy plate, which can obtain an anodized film having a uniform color tone according to 1 and excellent corrosion resistance.
【請求項3】 最終冷間圧延の後に、200〜400℃
で最終熱処理をすることを特徴とする請求項1または請
求項2記載の色調が均一で耐食性が優れた陽極酸化皮膜
が得られるアルミニウム合金板の製造方法。
3. After the final cold rolling, 200 to 400 ° C.
The method for producing an aluminum alloy plate according to claim 1 or 2, wherein the anodized film having a uniform color tone and excellent corrosion resistance is obtained.
JP17866292A 1992-07-06 1992-07-06 Manufacturing method of aluminum alloy plate for anodizing treatment Expired - Fee Related JP3308305B2 (en)

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Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US6521046B2 (en) 2000-02-04 2003-02-18 Kabushiki Kaisha Kobe Seiko Sho Chamber material made of Al alloy and heater block
US6640042B2 (en) 1998-09-01 2003-10-28 Fujitsu Limited Optical fiber holder
JP2013237926A (en) * 2012-04-20 2013-11-28 Sumitomo Light Metal Ind Ltd Aluminum alloy sheet excellent in surface quality after anodizing and method for producing the same
CN115584404A (en) * 2022-09-07 2023-01-10 河南明晟新材料科技有限公司 Preparation method of high-strength high-conductivity 1-series aluminum alloy cathode plate substrate

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US6640042B2 (en) 1998-09-01 2003-10-28 Fujitsu Limited Optical fiber holder
US6521046B2 (en) 2000-02-04 2003-02-18 Kabushiki Kaisha Kobe Seiko Sho Chamber material made of Al alloy and heater block
JP2013237926A (en) * 2012-04-20 2013-11-28 Sumitomo Light Metal Ind Ltd Aluminum alloy sheet excellent in surface quality after anodizing and method for producing the same
CN115584404A (en) * 2022-09-07 2023-01-10 河南明晟新材料科技有限公司 Preparation method of high-strength high-conductivity 1-series aluminum alloy cathode plate substrate
CN115584404B (en) * 2022-09-07 2023-10-10 河南明晟新材料科技有限公司 Preparation method of high-strength high-conductivity 1-series aluminum alloy cathode plate base material

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