JP3487160B2 - Method for producing aluminum alloy plate in which no streak pattern is generated by alkali treatment before anodizing treatment, aluminum alloy plate and molded product of aluminum alloy plate - Google Patents
Method for producing aluminum alloy plate in which no streak pattern is generated by alkali treatment before anodizing treatment, aluminum alloy plate and molded product of aluminum alloy plateInfo
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- JP3487160B2 JP3487160B2 JP05667398A JP5667398A JP3487160B2 JP 3487160 B2 JP3487160 B2 JP 3487160B2 JP 05667398 A JP05667398 A JP 05667398A JP 5667398 A JP5667398 A JP 5667398A JP 3487160 B2 JP3487160 B2 JP 3487160B2
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- aluminum alloy
- alloy plate
- rolling
- hot
- temperature
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Description
【０００１】[0001]
【発明の属する技術分野】本発明は、アルカリ処理によ
り筋状模様の生じない表面の美麗なアルミニウム合金板
を高い生産性で得ることができる、アルカリ処理に適し
たアルミニウム合金板の製造方法およびそれにより製造
されたアルミニウム合金板およびこのアルミニウム合金
板を成形したアルミニウム合金板成形品に関するもので
ある。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing an aluminum alloy sheet suitable for alkali treatment, which can obtain a beautiful aluminum alloy sheet having a streak-free surface by alkali treatment with high productivity. The present invention relates to an aluminum alloy plate manufactured by and an aluminum alloy plate molded product obtained by molding the aluminum alloy plate.
【０００２】[0002]
【従来の技術】アルミニウム合金は、その成形性の良さ
と良好な表面処理性によって、鍋や釜等の器物あるいは
内装、外装のパネル等に使用されている。これらの器物
あるいはパネル等は一般に下記のように製造される。す
なわち、溶湯を鋳造して鋳塊とし、該鋳塊を高温で均質
化処理し、次いで熱間圧延、冷間圧延を施して所望の板
厚のアルミニウム合金板とする。通常、冷間圧延後に巻
き取ってコイルの形とする。得られたアルミニウム合金
板を所定寸法に成形してパネルあるいは器物等の製品形
状にする。得られたパネル、器物等の成形品は一般に、
装飾性や耐蝕性等の特性付与のために陽極酸化処理等の
表面処理を施す。2. Description of the Related Art Aluminum alloys are used for pots, pots and other vessels, interior and exterior panels, etc. due to their good moldability and good surface treatment. These items, panels and the like are generally manufactured as follows. That is, the molten metal is cast into an ingot, the ingot is homogenized at high temperature, and then hot-rolled and cold-rolled to obtain an aluminum alloy plate having a desired plate thickness. Usually, it is coiled after cold rolling. The obtained aluminum alloy plate is formed into a predetermined size to form a product such as a panel or a container. Molded articles such as the obtained panels and articles are generally
Surface treatment such as anodic oxidation treatment is applied to impart characteristics such as decorativeness and corrosion resistance.
【０００３】この表面処理は下記のように行う。先ず、
前処理として合金板もしくは成形品を硫酸等の酸性水溶
液または苛性ソーダ等のアルカリ性水溶液、もしくはこ
れら両方の水溶液で洗浄処理する。この処理により、表
面が僅かにエッチングされ表面の油脂乃至は酸化物等の
汚れが除去される。次いで、硫酸、蓚酸等の電解浴中で
陽極酸化処理して酸化皮膜を形成する。また、この酸化
皮膜を形成された上述の板もしくは成形品は、必要によ
り更に二次電解処理により所望の色に電解着色される。This surface treatment is performed as follows. First,
As a pretreatment, the alloy plate or the molded product is washed with an acidic aqueous solution such as sulfuric acid or an alkaline aqueous solution such as caustic soda, or both of them. By this treatment, the surface is slightly etched to remove oil and fat or oxides and other stains on the surface. Next, an anodic oxidation treatment is performed in an electrolytic bath of sulfuric acid, oxalic acid or the like to form an oxide film. If necessary, the above-mentioned plate or molded article having the oxide film formed thereon is electrolytically colored to a desired color by secondary electrolytic treatment.
【０００４】従来、このように成形およびその後の表面
処理を施される用途のアルミニウム合金板は、前述の如
く鋳塊を４５０〜６００℃の高温で均質化処理を施し、
熱間圧延し、冷間圧延の中間で焼鈍処理を施して製造さ
れている（特開平５−２０２４５３号公報）。Conventionally, the aluminum alloy sheet for the purpose of being subjected to the forming and the subsequent surface treatment is subjected to the homogenization treatment of the ingot at a high temperature of 450 to 600 ° C. as described above,
It is manufactured by hot rolling and annealing in the middle of cold rolling (JP-A-5-202453).
【０００５】[0005]
【発明が解決しようとする課題】しかしながら上記従来
の製造方法は、鋳塊を高温で均質化処理を施すものであ
るため、加熱処理の時間が長く生産性が低いという欠点
があった。そこで、本発明の目的は、アルカリ処理を施
しても被処理面に筋模様の発生しないアルミニウム合金
板を高い生産性で製造する方法およびそれにより製造さ
れたアルミニウム合金板およびアルミニウム合金板成形
品を提供することである。However, the above-described conventional manufacturing method has a drawback that the heat treatment takes a long time and the productivity is low because the ingot is homogenized at a high temperature. Therefore, an object of the present invention is to provide a method for producing an aluminum alloy sheet having no streaks on the surface to be treated with high productivity even when subjected to alkali treatment, and an aluminum alloy sheet and an aluminum alloy sheet molded article produced thereby. Is to provide.
【０００６】[0006]
【課題を解決するための手段】そこで発明者らは、この
生産性が低いという欠点を改善すべく、鋳塊を低温で均
質化処理しかつ低温で熱間圧延してアルミニウム合金板
を製造したところ、得られたアルミニウム合金板から成
形した成形品は、前述のアルカリ処理を施しても被処理
面に筋模様が発生しないとの知見を得て本発明を完成し
たものである。Therefore, in order to improve the disadvantage of low productivity, the inventors produced an aluminum alloy sheet by homogenizing the ingot at low temperature and hot rolling at low temperature. However, the present invention has been completed based on the finding that a streak pattern does not occur on the surface to be treated of a molded article obtained by molding the obtained aluminum alloy plate even if it is subjected to the above-mentioned alkali treatment.
【０００７】即ち本発明は、下記成分、Ｆｅ：０．４０
を超え１．５wt％以下、Ｓｉ：０．０３〜０．３０wt
％、Ｃｕ：０．００４〜０．２０wt％、Ｔｉ：０．０１
〜０．０５wt％、Ｂ：０．０００１〜０．０２wt％、お
よび残部：アルミニウムおよび不可避不純物から成るア
ルミニウム合金鋳塊を準備し、該鋳塊に温度３５０〜４
３０℃の均質化熱処理を施し、引き続き該鋳塊に該均質
化処理の終了温度を超えない３００〜４３０℃の開始温
度で複数パスの熱間圧延を施して板厚２〜１０ｍｍの熱
間圧延板とする際に、該複数パスのパス間時間を１０se
c〜１．５minの範囲内、最終パスの圧延率を５５％以
上、熱間圧延の終了温度を２００〜３８０℃とすること
により、最終パス以前の再結晶を防止すると同時に最終
パス後の放冷中に該熱間圧延板の少なくとも表面層を再
結晶させて圧延方向に直角な方向の平均再結晶粒サイズ
が５０μｍ未満である再結晶組織とし、ただし該表面層
は該熱間圧延板の表面から深さ１ｍｍ以下の領域であ
り、該熱間圧延板に冷間圧延を施す、ことを特徴とする
陽極酸化処理前のアルカリ処理により筋模様の発生しな
いアルミニウム合金板の製造方法である。That is, according to the present invention, the following component, Fe: 0.40
Over 1.5wt%, Si: 0.03-0.30wt
%, Cu: 0.004 to 0.20 wt%, Ti: 0.01
˜0.05 wt%, B: 0.0001 to 0.02 wt%, and the balance: aluminum and inevitable impurities are prepared, and an aluminum alloy ingot is prepared at a temperature of 350 to 4
Subjected to a homogenization heat treatment of 30 ℃, continue the homogeneous quality in the template mass
Temperature of 300 to 430 ℃, which does not exceed the end temperature of chemical treatment
When a hot rolling plate having a plate thickness of 2 to 10 mm is subjected to hot rolling for several passes at a time, the time between passes of the plurality of passes is set to 10 se.
Within the range of c to 1.5 min, the rolling rate of the final pass is 55% or less.
First, the end temperature of hot rolling should be 200 to 380 ° C.
Prevents recrystallization before the final pass, and
At least the surface layer of the hot-rolled sheet is re-heated during cooling after passing.
The average recrystallized grain size of the perpendicular direction to the rolling direction by crystals and recrystallization structure is less than 50 [mu] m, provided that the surface layer
Is a region having a depth of 1 mm or less from the surface of the hot rolled plate.
And subjecting the hot rolled plate to cold rolling.
No streaking occurs due to alkali treatment before anodizing treatment.
A have manufacturing method of an aluminum alloy plate.
【０００８】鋳塊を低温で均質化処理し、最終パスによ
ってのみ該熱間圧延板の少なくとも表面層を再結晶させ
た場合は、圧延方向に直角方向の平均再結晶粒サイズが
５０μｍ未満と微細で、冷延後の板状コイルから得られ
た板もしくは加工品にアルカリ処理しても筋模様が目視
されない。また前述の熱間圧延最終パスの圧延率を５５
％以上とすると、容易に前述の圧延方向に直角方向の平
均再結晶粒サイズが５０μｍ未満と微細な再結晶粒とな
り、その後のアルカリ処理で筋模様が生じない。When the ingot is homogenized at low temperature and at least the surface layer of the hot-rolled sheet is recrystallized only by the final pass, the average recrystallized grain size in the direction perpendicular to the rolling direction is less than 50 μm. Therefore, even if the plate or the processed product obtained from the plate coil after cold rolling is treated with alkali, no streak pattern is visually observed. In addition, the rolling rate of the hot rolling final pass is set to 55
%, The average recrystallized grain size in the direction perpendicular to the rolling direction is easily less than 50 μm to form fine recrystallized grains, and a streak pattern does not occur in the subsequent alkali treatment.
【０００９】前記再結晶組織は、圧延方向に直角方向の
再結晶粒サイズが１００μｍ以下であることが望まし
い。また前述の製造方法で得られた板状コイルから成形
した成形体は同様にアルカリ処理で筋模様が生じない。
本発明による方法の特徴の一つは、鋳塊の均質化処理を
従来よりも低温の３５０〜４３０℃で行うことである。
この均質化処理により、鋳造時に過飽和に固溶した合金
元素が微細な金属間化合物となって均一に析出する。均
一に分散した微細析出物は、熱間圧延により導入された
転位を補足するピンニング効果があり、熱間圧延途中の
パス間で起きる回復・再結晶過程の進行を阻止あるいは
遅延させる作用がある。微細析出物の均一分散による転
位のピンニング効果は、熱間圧延最終パス後の表面層に
おける再結晶粒組織の均一微細化をも促進する。The recrystallized structure preferably has a recrystallized grain size of 100 μm or less in the direction perpendicular to the rolling direction. Further, similarly to the molded product molded from the plate-shaped coil obtained by the above-mentioned manufacturing method, no streak pattern is formed by the alkali treatment.
One of the characteristics of the method according to the present invention is that the ingot is homogenized at 350 to 430 ° C., which is lower than the conventional temperature.
By this homogenization treatment, the supersaturated solid solution alloy elements during casting become fine intermetallic compounds and are uniformly precipitated. The finely dispersed fine precipitates have a pinning effect that complements the dislocations introduced by hot rolling, and have the effect of preventing or delaying the progress of the recovery / recrystallization process that occurs between passes during hot rolling. The pinning effect of dislocations due to the uniform dispersion of fine precipitates also promotes uniform refinement of the recrystallized grain structure in the surface layer after the final pass of hot rolling.
【００１０】本発明による方法のもう一つの特徴は、熱
間圧延途中での再結晶を実質的に起こさせず、最終パス
後にのみ再結晶を起こさせることである。一般のアルミ
ニウム合金で通常の熱間圧延工程において発現する再結
晶は、実質的に圧延パス間での静的再結晶である。上述
の均一分散した微細析出物は、パス間での再結晶の発現
を有効に阻止する。これにより、熱間圧延工程全体に渡
って材料中に導入された加工歪みは最終パス後まで蓄積
保持され、この状態で最終パス後に一気に再結晶が発現
し、極めて微細で均一性の高い再結晶粒組織が生成す
る。Another feature of the method according to the invention is that it does not substantially cause recrystallization during hot rolling, but only after the final pass. The recrystallization that occurs in a typical aluminum alloy in a normal hot rolling process is substantially a static recrystallization between rolling passes. The above-mentioned uniformly dispersed fine precipitates effectively prevent the occurrence of recrystallization between passes. As a result, the work strain introduced into the material during the entire hot rolling process is accumulated and retained until after the final pass, and in this state, recrystallization occurs at a stretch after the final pass, resulting in extremely fine and highly uniform recrystallization. A grain structure is generated.
【００１１】従来は、熱間圧延途中での再結晶をむしろ
積極的に発現させ、パス毎に再結晶を繰り返させること
によって、最終的に均一微細な再結晶粒組織を生成させ
ていた。しかし、近年の高品質化の要請を満たす程には
ストリークスあるいは筋模様を解消することができなか
った。その理由は、以下のように考えられる。すなわ
ち、パス毎に再結晶を起こさせるということは、１つの
パスで導入された加工歪みがその都度再結晶によって解
消されることであり、大きな歪みが形成されることがな
い。圧延により材料中に導入される歪みは巨視的には均
一であっても、微視的あるいは個々の結晶粒についてみ
れば不均一であり、結晶粒オーダーの領域毎に歪み量が
異なる。したがって、巨視的にみれば十分再結晶を起こ
させるに足る量の歪みが付与されるはぜであっても、結
晶粒オーダーの微視的領域毎に見れば再結晶に必要な歪
みに到達しない領域が残ることがあり得る。また、鋳造
時のミクロ偏析により、再結晶温度が高い領域すなわち
再結晶の発現に大きい歪みを要する領域や、周囲よりも
強度が高く変形し難い領域すなわち歪みが導入され難い
領域が材料内部に散在している。このような微視的な歪
みの不均一性と材料組織の不均一性とが重なった領域の
存在することによって、熱間圧延最終パス後において粗
大な再結晶粒と微細な再結晶粒が発現し不均一な再結晶
組織を形成し、その後の冷間圧延によって圧延方向に延
びた直角方向の巾の不揃でしかも長大なストリークスあ
るいは筋模様として残存する。Conventionally, recrystallization during hot rolling was rather positively expressed and recrystallization was repeated for each pass to finally generate a uniform fine recrystallized grain structure. However, streaks or streaks could not be eliminated to the extent that the recent demand for higher quality was satisfied. The reason is considered as follows. That is, causing recrystallization for each pass means that the processing strain introduced in one pass is eliminated by recrystallization each time, and a large strain is not formed. Although the strain introduced into the material by rolling is macroscopically uniform, it is not uniform microscopically or in terms of individual crystal grains, and the amount of strain differs depending on the crystal grain order region. Therefore, macroscopically, even if a sufficient amount of strain is given to cause recrystallization, the strain required for recrystallization is not reached when viewed in each microscopic region of the crystal grain order. Areas may remain. In addition, due to microsegregation during casting, there are scattered regions inside the material where the recrystallization temperature is high, that is, a region that requires a large strain for manifestation of recrystallization, and where the strength is higher than the surroundings and is difficult to deform, that is, the strain is difficult to introduce. is doing. Due to the existence of such a region where microscopic strain nonuniformity and material microstructure nonuniformity overlap, coarse recrystallized grains and fine recrystallized grains appear after the final pass of hot rolling. Then, a non-uniform recrystallized structure is formed, and by the subsequent cold rolling, the widths in the right-angle direction extending in the rolling direction are not uniform and remain as long streaks or streaks.
【００１２】本発明の方法においては、熱間圧延途中で
の再結晶を実質的に起こさせず、各パスで導入される加
工歪みを解消させることなく最終パス後まで蓄積保持す
ることにより大きな歪みを形成することができ、上記の
ように微視的な歪みの不均一性や材料組織の不均一性が
あっても、特に熱間圧延板の表面層において、どの領域
にも均一微細な再結晶を発現するのに十分な量の歪みを
付与することができ、均一微細な再結晶粒組織が得ら
れ、ストリークスあるいは筋模様を著しく低減できる。In the method of the present invention, recrystallization during hot rolling is not substantially caused, and the processing strain introduced in each pass is not eliminated, and the strain is accumulated and held until after the final pass. Can be formed, and even if there is non-uniformity of microscopic strain or non-uniformity of material structure as described above, even in the surface layer of the hot-rolled sheet, even in every area, fine and fine re-formation is possible. A sufficient amount of strain for expressing crystals can be imparted, a uniform fine recrystallized grain structure can be obtained, and streaks or streaks can be significantly reduced.
【００１３】本発明によれば、熱間圧延パス間での再結
晶の発現は、上述したとおり微細析出物の均一分散によ
り阻止できるので、熱間圧延工程自体には特別の変更を
加えることなく、従来どおりの熱間圧延工程で良い。パ
ス間時間が余り長くなり過ぎないように管理する必要は
あるが、これも材料温度を確保するために従来から行っ
ている程度の管理で十分であり、実質的に管理事項が増
加することはない。According to the present invention, the occurrence of recrystallization between hot rolling passes can be prevented by the uniform dispersion of fine precipitates as described above, so that the hot rolling process itself does not require any special modification. The conventional hot rolling process is sufficient. It is necessary to control so that the time between passes does not become too long, but this is also the control that has been conventionally performed to secure the material temperature, and there is no substantial increase in control items. Absent.
【００１４】このように本発明は、従来より低温で均質
化処理を行って金属間化合物を均一微細に分散させ、こ
の状態の鋳塊を熱間圧延して、従来はむしろ積極的に利
用されていた熱間圧延途中での再結晶の発現を従来とは
逆に阻止し、最終パス後に一気に再結晶を起こさせるよ
うにした。これにより、特に熱間圧延板表面層におい
て、圧延方向に直角な方向の平均粒径が５０μｍ未満と
いう極めて微細で且つ均一な再結晶粒組織を容易に得る
ことができ、これに通常の冷間圧延を施すことによりア
ルカリ処理を施しても被処理面に筋模様の発生しないア
ルミニウム合金板条コイルを製造することができる。ま
た、低温で均質化処理を施こすので、生産性よく、上述
の板条コイルを製造することができる。As described above, according to the present invention, a homogenizing treatment is performed at a lower temperature than in the prior art to uniformly and finely disperse the intermetallic compound, and the ingot in this state is hot-rolled, which is rather positively utilized in the prior art. Contrary to the conventional method, the occurrence of recrystallization in the middle of hot rolling was prevented, and the recrystallization was made to occur at once after the final pass. This makes it possible to easily obtain an extremely fine and uniform recrystallized grain structure having an average grain size of less than 50 μm in the direction perpendicular to the rolling direction, particularly in the surface layer of the hot-rolled sheet. By rolling, it is possible to manufacture an aluminum alloy strip coil in which a streak pattern does not occur on the surface to be treated even when subjected to alkali treatment. Further, since the homogenization treatment is performed at a low temperature, the above-mentioned strip coil can be manufactured with good productivity.
【００１５】[0015]
【発明の実施の形態】まず、本発明におけるアルミニウ
ム合金の成分の限定理由を説明する。
Ｆｅ：０．４０を超え１．５wt％以下
Ｆｅは、Ａｌ−Ｆｅ系およびＡｌ−Ｆｅ−Ｓｉ系の金属
間化合物を形成させ、強度を付与すると共に、鋳造組織
の結晶粒を微細化するために必要な元素である。Ｆｅ含
有量が１．５wt％を越えると、Ａｌ−Ｆｅ系およびＡｌ
−Ｆｅ−Ｓｉ系の粗大な化合物が形成されアルカリ処理
の局所的不均一が顕著になったり、板の成形性を低下さ
せる。また、Ｆｅ含有量が０．４０wt％以下になると、
パネルおよび器物等の加工品としては、強度および鋳造
組織の結晶微細化効果が得られず、粗大な結晶粒の存在
によりアルカリ処理の均一性が損なわれる。BEST MODE FOR CARRYING OUT THE INVENTION First, the reasons for limiting the components of the aluminum alloy in the present invention will be explained. Fe: more than 0.40 and not more than 1.5 wt% Fe forms an Al-Fe-based and Al-Fe-Si-based intermetallic compound to impart strength and refine the crystal grains of the cast structure. Is an element necessary for. When the Fe content exceeds 1.5 wt%, Al-Fe system and Al
A coarse compound of —Fe—Si system is formed, and local nonuniformity of alkali treatment becomes remarkable, or formability of the plate is deteriorated. When the Fe content is 0.40 wt% or less,
As a processed product such as a panel or a container, the strength and the crystal refining effect of the cast structure cannot be obtained, and the presence of coarse crystal grains impairs the uniformity of alkali treatment.
【００１６】Ｓｉ：０．０３〜０．３０wt％
Ｓｉは、Ａｌ−Ｆｅ−Ｓｉ系の金属間化合物を形成さ
せ、強度を付与するために必要な元素である。Ｓｉ含有
量が０．０３wt％未満ではこの効果が不足する。一方、
Ｓｉ含有量が０．３０wt％を越えると、Ａｌ−Ｆｅ−Ｓ
ｉ系の粗大な金属間化合物が形成され、アルカリ処理の
局所的不均一性が顕著になる。また、Ｓｉは通常アルミ
ニウム合金中に不純物として含有される元素であり、Ｓ
ｉ含有量を０．０３wt％未満にすることはコスト上昇に
なる。Si: 0.03 to 0.30 wt% Si is an element necessary for forming an Al--Fe--Si intermetallic compound and imparting strength. If the Si content is less than 0.03 wt%, this effect will be insufficient. on the other hand,
If the Si content exceeds 0.30 wt%, Al-Fe-S
A coarse i-type intermetallic compound is formed, and the local nonuniformity of alkali treatment becomes remarkable. Si is an element usually contained as an impurity in an aluminum alloy, and S
If the i content is less than 0.03 wt%, the cost will increase.
【００１７】Ｃｕ：０．００４〜０．２０wt％
Ｃｕは耐食性に大きく影響する元素である。Ｃｕ含有量
が０．０４wt％未満であると、糸状腐食が発生し易くな
る。一方、Ｃｕ含有量が０．２０wt％を超えると、孔食
等が発生して耐食性が低下する。
Ｔｉ：０．０１０〜０．０５０wt％
Ｔｉは鋳造組織の結晶粒微細化に有効である。そのた
め、鋳造に際して割れ発生の防止に有用であり、また鋳
造組織の結晶粒粗大化に起因するアルカリ処理の均一性
に有効である。Ｔｉ含有量が０．０１０wt％未満である
と、鋳造組織の結晶粒微細化効果が少ない。一方、Ｔｉ
含有量が０．０５０wt％を超えると、鋳造組織の結晶粒
微細化効果が飽和してしまうばかりでなく、逆にＡｌ−
Ｔｉ系の粗大な化合物が形成され、鋳造組織の結晶粒が
不均一になる。Cu: 0.004 to 0.20 wt% Cu is an element that greatly affects the corrosion resistance. If the Cu content is less than 0.04 wt%, filiform corrosion is likely to occur. On the other hand, when the Cu content exceeds 0.20 wt%, pitting corrosion and the like occur and the corrosion resistance decreases. Ti: 0.010 to 0.050 wt% Ti is effective for refining the crystal grains of the cast structure. Therefore, it is useful for preventing the occurrence of cracks during casting, and is also effective for the uniformity of alkali treatment due to the coarsening of crystal grains in the cast structure. When the Ti content is less than 0.010 wt%, the effect of refining the crystal grains of the cast structure is small. On the other hand, Ti
When the content exceeds 0.050 wt%, not only the effect of refining the crystal grains of the cast structure is saturated, but conversely Al-
A coarse Ti-based compound is formed, and the crystal grains of the cast structure become non-uniform.
【００１８】Ｂ：０．０００１〜０．０２０wt％
Ｂは、Ｔｉと共に添加され、鋳造組織の結晶粒微細化に
有効である。その結果はＴｉのみを添加した場合よりも
高い。Ｂ含有量が０．００１０wt％未満であると、この
効果が少ない。一方、Ｂ含有量が０．０２０wt％を超え
ると、鋳造組織の結晶粒微細化効果が飽和してしまうば
かりでなく、逆にＴｉ−Ｂ系の粗大な化合物が形成され
鋳造組織の結晶粒が不均一になる。B: 0.0001 to 0.020 wt% B is added together with Ti and is effective for refining the crystal grains of the cast structure. The results are higher than when only Ti is added. If the B content is less than 0.0010 wt%, this effect is small. On the other hand, when the B content exceeds 0.020 wt%, not only the effect of refining the crystal grains of the cast structure is saturated, but also a coarse Ti—B-based compound is formed and the crystal grains of the cast structure are It becomes uneven.
【００１９】不純物または有意元素としては、Ｍｇ，Ｍ
ｎ，Ｃｒ，Ｚｒ，Ｖ，Ｚｎ，Ｎｉ，Ｇａ，Ｌｉ，Ｂｅ等
の元素を含有してもよい。が含有されることがあるが、
好ましくは含有量が各々の０．１wt％以下程度の微量で
あれば本発明による効果に大きな悪影響は及ぼさない。
本発明においては、熱間圧延板の表面層の再結晶粒組織
を以下のようにして制御する。As impurities or significant elements, Mg, M
Elements such as n, Cr, Zr, V, Zn, Ni, Ga, Li and Be may be contained. May be included,
Preferably, if the content is a trace amount of about 0.1 wt% or less, the effect of the present invention is not significantly adversely affected.
In the present invention, the recrystallized grain structure of the surface layer of the hot rolled plate is controlled as follows.
【００２０】除滓処理等を施して溶製した前記組成のア
ルミニウム合金を常法により鋳造して鋳塊とする。鋳造
法は特に限定しないが、半連続鋳造法が望ましい。鋳塊
の厚さも特に限定はしないが、通常は５００〜６００mm
程度である。鋳塊の表面を面削した後に、３５０〜４３
０℃の温度に加熱保持することにより均質化処理を行
う。均質化処理の保持時間は３０分〜１２時間程度が適
当である。前述のように、均質化処理が従来よりも低温
である点が本発明の一つの特徴である。この低温均質化
処理中に、鋳造中に過飽和固溶していた合金元素が金属
間化合物として均一微細に析出し、後の熱間圧延工程に
おいて加工により導入された転位を補足するピンニング
効果により熱間圧延途中での再結晶の発現を阻止する。
鋳造中に過飽和固溶している合金元素が金属間化合物と
して均一微細に析出するには３５０〜４３０℃の温度が
最も好ましい温度である。一方転位補足に有効な微細な
金属間化合物が減少し、熱間圧延途中での再結晶の発現
を確実に阻止できないため、最終パスでのみ再結晶を起
こさせて熱間圧延板表面層に微細な再結晶粒組織を生成
させることができない。均質化処理の保持時間は、３０
分未満であると析出が十分でなく、一方、保持時間が１
２時間を超えると、本発明の温度範囲内でも高温側では
析出粒子が再固溶する危険がある上、コストも増加す
る。本発明はこのように従来より低温で均質化処理を行
うので、省エネルギーの上でも有利である。The aluminum alloy having the above composition which has been subjected to slag removal treatment and the like and melted is cast by an ordinary method to obtain an ingot. The casting method is not particularly limited, but a semi-continuous casting method is desirable. The thickness of the ingot is not particularly limited, but usually 500 to 600 mm
It is a degree. 350-43 after chamfering the surface of the ingot
A homogenization treatment is performed by heating and holding at a temperature of 0 ° C. The holding time of the homogenization treatment is appropriately about 30 minutes to 12 hours. As described above, one of the features of the present invention is that the homogenization treatment is performed at a lower temperature than before. During this low-temperature homogenization treatment, the supersaturated solid solution alloy elements during casting are uniformly and finely precipitated as intermetallic compounds, and the pinning effect that complements the dislocations introduced by working in the subsequent hot rolling step causes Prevents recrystallization from occurring during hot rolling.
The temperature of 350 to 430 ° C. is the most preferable temperature for the alloy element which is in a supersaturated solid solution during casting to be uniformly and finely precipitated as an intermetallic compound. On the other hand, the amount of fine intermetallic compounds that are effective for trapping dislocations decreases, and it is impossible to reliably prevent the occurrence of recrystallization during hot rolling.Therefore, recrystallization is caused only in the final pass to form fine grains on the surface layer of the hot rolled plate. Recrystallized grain structure cannot be generated. Hold time for homogenization treatment is 30
If it is less than minutes, the precipitation is not sufficient, while the holding time is 1
If it exceeds 2 hours, the precipitated particles may be re-dissolved on the high temperature side even within the temperature range of the present invention, and the cost also increases. In the present invention, the homogenization treatment is performed at a lower temperature than in the conventional case, and thus it is advantageous in terms of energy saving.
【００２１】均質化処理後、熱間圧延を一般に数回以上
の圧延パスにより行う。本発明においては、熱間圧延途
中で再結晶を発現させないことが必須である。そのため
に、均質化処理により生成した微細析出物の存在が重要
である。この微細析出物が再結晶の発現を遅延させる。
それは、熱間圧延の加工歪みとして導入された転位を微
細析出物が補足あるいはピンニングし、回復・再結晶過
程の開始・進行を阻止するためである。このように熱間
圧延途中での再結晶の発現を阻止して加工歪みを最終パ
ス後にまで蓄積保存し、最終パス後に一気に再結晶を発
現させることにより熱間圧延板表面層に均一微細な再結
晶粒組織を生成させる。After the homogenization treatment, hot rolling is generally performed by several or more rolling passes. In the present invention, it is essential not to cause recrystallization during hot rolling. Therefore, the presence of fine precipitates generated by the homogenization treatment is important. This fine precipitate delays the onset of recrystallization.
This is because the fine precipitates complement or pin the dislocations introduced as the processing strain of hot rolling, and prevent the initiation / progress of the recovery / recrystallization process. In this way, by preventing the occurrence of recrystallization during hot rolling and accumulating and storing the processing strain until after the final pass, and by expressing recrystallization at once after the final pass, uniform and fine recrystallization is performed on the surface layer of the hot rolled plate. Generate a grain structure.
【００２２】熱間圧延は、均質化処理後直ちに開始して
もよいし、均質化処理後に鋳塊の表面を面削し、所定温
度に再加熱してから開始してもよい。本発明において
は、熱間圧延パス間の組織および熱間圧延終了後の組織
を制御するために、前記均質化処理条件の制御が必須で
ある。また、熱間圧延の開始温度および終了温度を制御
すると、本発明の素板を容易に製造することができる。The hot rolling may be started immediately after the homogenization treatment, or may be started after the surface of the ingot is chamfered after the homogenization treatment and reheated to a predetermined temperature. In the present invention, in order to control the structure between hot rolling passes and the structure after completion of hot rolling, it is essential to control the homogenization treatment conditions. Further, by controlling the starting temperature and the ending temperature of the hot rolling, the raw sheet of the present invention can be easily manufactured.
【００２３】熱間圧延の開始温度は、均質化処理終了温
度を超えない温度で行う。すなわち３００〜４３０℃が
望ましい。３００℃未満では、圧延抵抗が高いため安定
した熱間圧延が困難である。一方、熱間圧延開始温度が
高くなると、通常の熱間圧延速度ではパス間で再結晶が
発現し易く、また再結晶粒の成長もし易く、加工歪みが
開放され易くその結果、最終パス後まで加工歪みを蓄積
保持して一気に再結晶を発現させることが困難になり、
特に熱間圧延板表面層に均一微細な再結晶粒組織を生成
させることが困難になり、粗大な再結晶粒が生じ易いの
で上述の範囲とした。The hot rolling start temperature is set so as not to exceed the homogenization treatment end temperature. That is, 300 to 430 ° C. is desirable. If it is less than 300 ° C, it is difficult to perform stable hot rolling because of high rolling resistance. On the other hand, when the hot rolling start temperature is high, recrystallization is likely to occur between passes at a normal hot rolling speed, and recrystallized grains are also easily grown, resulting in easy release of processing strain, and as a result, after the final pass. It becomes difficult to express the recrystallization at once by accumulating and holding the processing strain,
In particular, it is difficult to generate a uniform and fine recrystallized grain structure in the surface layer of the hot-rolled sheet, and coarse recrystallized grains are easily generated, so the above range is set.
【００２４】熱間圧延の終了温度は、２００〜３８０℃
が望ましい。また、熱間圧延の終了時板厚は２〜１０mm
が望ましい。この範囲の終了温度および終了時板厚とす
ることにより、熱間圧延最終パス後に特別な加熱や保温
等を必要とせずに単純に放冷するだけで、材料自身の持
つ余熱により容易に再結晶を起こさせることができる
し、後工程における冷間圧延にも好都合な板厚が得られ
る。熱間圧延終了時板厚は、３．５〜７mmとすると更に
望ましい。The end temperature of hot rolling is 200 to 380 ° C.
Is desirable. The plate thickness at the end of hot rolling is 2 to 10 mm.
Is desirable. By setting the end temperature and the plate thickness at the end of this range, it is possible to easily recrystallize by the residual heat of the material itself, simply by allowing it to cool after the final pass of hot rolling without requiring special heating or heat retention. Can be caused, and a plate thickness suitable for cold rolling in the subsequent process can be obtained. It is more desirable that the plate thickness at the end of hot rolling is 3.5 to 7 mm.
【００２５】熱間圧延の最終パスにおける圧延率（＝圧
下率、リダクション）は５５％以上とすることが望まし
い。本発明においては、再結晶を最終パス後に発現させ
るので、最終パスによる加工歪みが再結晶に最も大きい
影響を及ぼす。したがって、最終パスで上記圧延率によ
り大きな加工歪み付与すると、最終的に熱間圧延板表面
層に均一微細な再結晶粒組織を生成させる上で非常に有
利になる。すなわち、最終パスを５５％以上の圧延率で
行うことにより、熱間圧延板の少なくとも表面層におい
て圧延方向に直角の方向の平均再結晶粒サイズ５０μｍ
未満、同じく最大結晶粒サイズ１００μｍ未満が容易に
得られる。The rolling ratio (= rolling reduction, reduction) in the final pass of hot rolling is preferably 55% or more. In the present invention, since recrystallization is developed after the final pass, the processing strain due to the final pass has the greatest effect on the recrystallization. Therefore, when a large processing strain is applied to the rolling rate in the final pass, it becomes very advantageous in finally producing a uniform fine recrystallized grain structure in the surface layer of the hot-rolled sheet. That is, by performing the final pass at a rolling rate of 55% or more, the average recrystallized grain size in the direction perpendicular to the rolling direction is 50 μm in at least the surface layer of the hot-rolled sheet.
, Similarly, the maximum crystal grain size of less than 100 μm can be easily obtained.
【００２６】本発明において、熱間圧延板の表面層と
は、厚さ１０mm以下の熱間圧延板の場合には板表面から
深さ１mm程度までの領域である。最終的に厚さ１〜２mm
程度の合金板に対して、アルカリ処理により表面最大
０．１mm程度がエッチング除去される。典型的な例とし
て、熱間圧延板が厚さ３．５〜７mmの場合には、表面層
は深さ３５０μｍから深さ７００μｍまでの間の領域を
指す。In the present invention, the surface layer of the hot rolled plate is a region from the plate surface to a depth of about 1 mm in the case of a hot rolled plate having a thickness of 10 mm or less. Finally thickness 1-2 mm
A maximum of about 0.1 mm of the surface of the alloy plate of about 0.1 mm is etched and removed by alkali treatment. As a typical example, when the hot-rolled sheet has a thickness of 3.5 to 7 mm, the surface layer indicates a region between a depth of 350 μm and a depth of 700 μm.
【００２７】ここで、熱間圧延板の厚さが１０mm以下の
場合には、上記のような表面層内にある再結晶粒のサイ
ズは板厚方向で実質的に変化しないから、熱間圧延板表
面層の再結晶粒サイズの評価は、熱間圧延板表面の再結
晶粒サイズの測定により求めることができる。本発明に
おいては、熱間圧延板の少なくとも表面層が均一微細な
再結晶粒組織であれば良い。すなわち、熱間圧延板の芯
部については、均一微細な再結晶組織であるか否かは問
わず、いずれでも良い。パネルもしくは器物のストリー
クスあるいは筋模様はアルカリ処理によって顕在化する
ものであり、板の芯部はストリークスあるいは筋模様の
生成に直接関与しないからである。When the thickness of the hot-rolled sheet is 10 mm or less, the size of the recrystallized grains in the surface layer as described above does not substantially change in the sheet thickness direction. The recrystallized grain size of the plate surface layer can be evaluated by measuring the recrystallized grain size of the hot-rolled plate surface. In the present invention, at least the surface layer of the hot-rolled sheet should have a uniform fine recrystallized grain structure. That is, the core of the hot-rolled sheet may have any uniform fine recrystallized structure. This is because the streak or streak pattern of the panel or the container is revealed by the alkali treatment, and the core of the plate is not directly involved in the generation of the streak or streak pattern.
【００２８】熱間圧延の途中で再結晶したか否かの判定
は、熱間圧延最終パス直前の材料の組織観察により容易
に行うことができる。熱間圧延途中で再結晶していない
場合は、鋳造組織の結晶粒が圧延方向に長く伸びた繊維
状の加工組織となる。これに対して、熱間圧延途中で再
結晶した場合には、その再結晶以前に形成されていた繊
維状加工組織は消失するため、熱間圧延途中で再結晶し
なかった場合に比べて加工組織の伸び率が小さいか、あ
るいは加工組織が消失している。Whether or not recrystallization was performed during hot rolling can be easily determined by observing the microstructure of the material immediately before the final pass of hot rolling. When recrystallization is not performed during hot rolling, the crystal grains of the cast structure have a fibrous worked structure elongated in the rolling direction. On the other hand, when recrystallized during hot rolling, the fibrous work structure that was formed before the recrystallization disappears. The elongation of the structure is small or the processed structure has disappeared.
【００２９】本発明は、以上説明したように鋳造−面削
−均質化処理−熱間圧延−冷間圧延を経て平版印刷版用
アルミニウム合金素板を製造するが、必要に応じて冷間
圧延途中の中間焼鈍および／または冷間圧延終了後の最
終焼鈍を行ってもよい。また、冷間圧延終了後に、平坦
度を向上させるためのレベラー矯正を行うこともでき
る。In the present invention, as described above, an aluminum alloy base plate for a lithographic printing plate is manufactured through the following steps of casting-face cutting-homogenizing treatment-hot rolling-cold rolling. Intermediate annealing on the way and / or final annealing after completion of cold rolling may be performed. Further, after the cold rolling is completed, leveler straightening for improving flatness can be performed.
【００３０】冷間圧延途中の中間焼鈍あるいは最終焼鈍
は、必要に応じて行ってもよい。その場合の焼鈍方法は
バッチ焼鈍あるいは連続焼鈍のいずれでもよい。バッチ
焼鈍は、典型的には、温度２００〜６００℃、保持時間
１〜２４時間で行う。温度が２００℃未満では、冷間圧
延による加工硬化を除去する焼鈍硬化が不十分である。
温度が６００℃を超えると再結晶粒が粗大化し、電気化
学的方法により外観均一性の高い粗面化面が得られない
し、機械的性質も劣化して良好な耐刷性が得られない。
保持時間が１時間未満では、加工効果を除去する焼鈍効
果が不十分である。保持時間が２４時間を超えると、焼
鈍効果が飽和してしまい、単に不経済なだけである。Intermediate annealing or final annealing during the cold rolling may be carried out as necessary. In that case, the annealing method may be either batch annealing or continuous annealing. Batch annealing is typically performed at a temperature of 200 to 600 ° C. and a holding time of 1 to 24 hours. If the temperature is less than 200 ° C, the annealing hardening for removing the work hardening by cold rolling is insufficient.
When the temperature exceeds 600 ° C., the recrystallized grains become coarse, a roughened surface having a high appearance uniformity cannot be obtained by an electrochemical method, and the mechanical properties are deteriorated, so that good printing durability cannot be obtained.
If the holding time is less than 1 hour, the annealing effect for removing the working effect is insufficient. If the holding time exceeds 24 hours, the annealing effect is saturated, which is simply uneconomical.
【００３１】連続焼鈍は、典型的には、連続焼鈍装置を
用い、昇温速度１℃／sec 以上で加熱温度３５０〜６０
０℃に加熱し、所定温度に到達した後、昇温速度１℃／
sec以上で、望ましくは降温速度５００℃／sec 以上の
水冷により、１００℃以下にまで冷却することにより行
う。連続焼鈍装置は特に限定しないが、加熱方法がアル
ミニウム合金自体の発熱を利用する磁気誘導加熱（Tran
sverse Flux Induction Heating)方式は、アルミニウム
合金板表面の酸化皮膜生成量が少なく、板表面への悪影
響が少ないので望ましい。The continuous annealing is typically carried out using a continuous annealing device at a heating rate of 1 ° C./sec or more and a heating temperature of 350 to 60.
After heating to 0 ° C and reaching the predetermined temperature, the temperature rising rate is 1 ° C /
It is performed by cooling to 100 ° C. or lower with water cooling at a temperature lowering rate of 500 ° C./sec or more for more than sec. The continuous annealing apparatus is not particularly limited, but the heating method uses magnetic induction heating (Tran
The sverse Flux Induction Heating method is desirable because it produces less oxide film on the surface of the aluminum alloy plate and has less adverse effect on the plate surface.
【００３２】[0032]
【実施例】表１に示した本発明例の組成のアルミニウム
合金の溶湯を調整した。各アルミニウム合金溶湯を半連
続鋳造して厚さ５６０mmの鋳塊とし、鋳塊の表面を両面
を１５mmずつ面削を行い５３０mmとした。つぎに、均質
化処理を施した後に、可逆式圧延機を用いて熱間圧延を
行って厚さ６mmの熱間圧延板を得た。熱間圧延は、パス
回数１７回で行い、パス間時間はすべて１０sec 〜１．
５min の範囲内であった。Example A molten aluminum alloy having the composition of the present invention shown in Table 1 was prepared. Each aluminum alloy melt was semi-continuously cast to form an ingot having a thickness of 560 mm, and the surface of the ingot was 530 mm by chamfering both surfaces by 15 mm. Next, after performing homogenization treatment, hot rolling was performed using a reversible rolling mill to obtain a hot-rolled sheet having a thickness of 6 mm. The hot rolling is performed with 17 passes, and the time between passes is 10 seconds to 1.
It was within the range of 5 min.
【００３３】表２に均質化処理温度と時間、熱間圧延の
開始温度、終了温度および最終圧延パス圧下率を示す。
試料Ｎｏ．１，２，３は少なくともいずれかの条件が本
発明の範囲外であり、試料Ｎｏ．４，５は各条件が本発
明の範囲内である。ついで、試料Ｎｏ．１，３，４は、
冷間圧延において厚さ２．５mmまで冷間圧延を行った
後、バッチ式中間焼鈍を１００℃／sec の昇温で１時間
保持して行い、そして最終冷間圧延を行って、厚さ１mm
の冷間圧延板とした。Table 2 shows the homogenization treatment temperature and time, the hot rolling start temperature, the end temperature, and the final rolling pass reduction rate.
Sample No. At least one of the conditions of Nos. 1, 2, and 3 is outside the scope of the present invention, and the sample No. Each of conditions 4 and 5 is within the scope of the present invention. Then, the sample No. 1, 3, 4 are
After cold rolling to a thickness of 2.5 mm in cold rolling, batch type intermediate annealing was performed at a temperature rise of 100 ° C / sec for 1 hour, and finally cold rolling was performed to obtain a thickness of 1 mm.
It was a cold rolled plate.
【００３４】一方Ｎｏ．２，５は冷間圧延を行って、厚
さ２mmの冷間圧延板とした。表２の製板工程により得ら
れた合金板について、以下の評価・測定法に従って、熱
間圧延仕上げ板表層部の圧延方向に直角方向の結晶粒の
幅の測定および、アルカリ処理後の表面の筋評価を行っ
た。その結果を表３に示した。
（１）熱間仕上げ板表層部の再結晶粒サイズの測定
バーカー氏液（１１ml／ｌホウフッ酸溶液）による陽極
酸化処理後、偏光顕微鏡によって、結晶粒観察を行い、
直線法を用い結晶粒サイズを測定した。これにより平均
再結晶粒サイズおよび最大結晶粒サイズを求めた。
（２）アルカリ処理後の表面筋の評価
得られた合金板を切断し、１０％ＮａＯＨ，５０℃，２
min エッチングした後、ＨＮＯ３でデスマット処理を施
した。On the other hand, No. Cold rolling was performed on Nos. 2 and 5 to obtain cold rolled plates having a thickness of 2 mm. For the alloy plates obtained by the plate-making process in Table 2, the width of crystal grains in the direction perpendicular to the rolling direction of the surface layer of the hot-rolled finished plate was measured according to the following evaluation and measurement methods, and the surface of the surface after alkali treatment was measured. Muscle evaluation was performed. The results are shown in Table 3. (1) Measurement of recrystallized grain size in the surface layer of hot-finished plate After anodic oxidation treatment with Barker's solution (11 ml / l borohydrofluoric acid solution), crystal grains were observed with a polarizing microscope.
The grain size was measured using the linear method. Thus, the average recrystallized grain size and the maximum crystal grain size were obtained. (2) Evaluation of surface streaks after alkali treatment The obtained alloy plate was cut and 10% NaOH, 50 ° C, 2
After etching for min, desmut treatment was performed with HNO3.
【００３５】表面の目視観察により表面の筋模様の評価
を行った。評価は、外観が非常に均一なものは「非常に
良好（◎）」、外観が均一で筋模様の認められないもの
は「良好（○）」、外観が均一でなく筋模様等が観察さ
れたものは「不良（×）」とした。なお、熱間圧延途中
での再結晶の発現の有無を判定するために、表２中の各
試料について熱間圧延最終パス直前の熱間圧延板の組織
を観察した。その結果本発明例使用Ｎｏ．４，５は、結
晶粒が圧延方向に長く伸びた繊維状の加工組織が観察さ
れ、熱間圧延途中で再結晶が起きていないことが確認さ
れた。これらに比べて、試料Ｎｏ．１，２，３は、結晶
粒の伸び率が小さく、熱間圧延途中で再結晶が起きたこ
とが確認された。The streak pattern on the surface was evaluated by visual observation of the surface. The evaluation was “very good (⊚)” when the appearance was very uniform, “good (∘)” when the appearance was uniform and no streak was observed, and streak pattern etc. were not observed. Those that were marked as "poor (x)". In order to determine whether or not recrystallization occurred during hot rolling, the structure of the hot rolled sheet immediately before the final hot rolling pass was observed for each sample in Table 2. As a result, the invention sample No. In Nos. 4 and 5, a fibrous processed structure in which crystal grains were elongated in the rolling direction was observed, and it was confirmed that recrystallization did not occur during hot rolling. Compared with these, the sample No. In Nos. 1, 2 and 3, the elongation of crystal grains was small, and it was confirmed that recrystallization occurred during hot rolling.
【００３６】表３からも明らかなように、本発明例であ
る試料Ｎｏ．４は、上述したように熱間圧延途中で再結
晶していないため熱間仕上げ圧延板表層部の平均再結晶
粒サイズが２５μｍであり、最大再結晶粒サイズも７０
μｍと、微細で均一な再結晶粒組織が得られた。そのた
め、アルカリ処理後の表面に筋模様がみられず、非常に
均一で良好な外観を呈していた。均質化処理温度が低い
ために、均質化処理にかかる時間が短く、生産性の良い
ことが判る。As is clear from Table 3, the sample No. which is an example of the present invention. No. 4 has an average recrystallized grain size of 25 μm and a maximum recrystallized grain size of 70 μm in the surface layer portion of the hot finish rolled plate because it was not recrystallized during hot rolling as described above.
A fine and uniform recrystallized grain structure of μm was obtained. Therefore, no streak pattern was observed on the surface after the alkali treatment, and the surface was very uniform and had a good appearance. It can be seen that since the homogenization treatment temperature is low, the time required for the homogenization treatment is short and the productivity is good.
【００３７】また、本発明例である試料Ｎｏ．５は、上
述したように熱間圧延途中で再結晶していないため熱間
仕上げ圧延板表層部の平均再結晶粒サイズが１５μｍで
あり、最大再結晶粒サイズも４０μｍと、微細で均一な
再結晶粒組織が得られた。それにより、アルカリ処理後
の表面に筋模様がみられず、均一な外観をしていた。均
質化処理温度が低いために、均質化処理にかかる時間が
短く、中間焼鈍も省略できることより、生産性が非常に
良いことが判る。Further, the sample No. which is an example of the present invention. Since No. 5 did not recrystallize during hot rolling as described above, the average recrystallized grain size of the surface layer portion of the hot finish rolled plate was 15 μm, and the maximum recrystallized grain size was 40 μm. A grain structure was obtained. As a result, no streak pattern was observed on the surface after the alkali treatment, and the surface had a uniform appearance. Since the homogenization treatment temperature is low, the time required for the homogenization treatment is short and the intermediate annealing can be omitted. Therefore, it is understood that the productivity is very good.
【００３８】これに対し、従来例の試料Ｎｏ．１は、熱
間圧延途中において再結晶が起きており、熱間圧延板表
層の平均再結晶サイズが１２０μｍ、また最大再結晶サ
イズが１５０μｍと大きい。しかし、中間焼鈍処理を行
うことにより、アルカリ処理後の表面に筋模様がみられ
ず、均一な外観をしていた。しかし、均質化処理温度が
高く、また、熱間圧延開始温度が低いために、均質化処
理および熱間圧延開始温度までの冷却の時間が非常に長
く、さらに、中間焼鈍も行っているため、生産性は良く
ないことが判る。On the other hand, the sample No. of the conventional example. In No. 1, recrystallization occurred during hot rolling, and the average recrystallized size of the surface layer of the hot rolled plate was 120 μm and the maximum recrystallized size was as large as 150 μm. However, by performing the intermediate annealing treatment, no streak pattern was observed on the surface after the alkali treatment, and the surface had a uniform appearance. However, since the homogenization treatment temperature is high and the hot rolling start temperature is low, the cooling time to the homogenization treatment and the hot rolling start temperature is very long, and further, since the intermediate annealing is performed, It turns out that productivity is not good.
【００３９】また、比較例の試料Ｎｏ．２は、熱間圧延
途中において再結晶が起きており、熱間圧延板表層の平
均再結晶サイズが２５０μｍよりも大きく、また最大再
結晶サイズが３５０μｍと大きいため、アルカリ処理後
の表面外観の筋模様が顕著であった。さらに、均質化処
理温度が高く、昇温に時間を要し、生産性は良くないこ
とが判る。In addition, the sample No. of the comparative example. In No. 2, recrystallization occurred during hot rolling, the average recrystallized size of the surface layer of the hot rolled plate was larger than 250 μm, and the maximum recrystallized size was as large as 350 μm. The pattern was remarkable. Further, it can be seen that the homogenization treatment temperature is high, it takes time to raise the temperature, and the productivity is not good.
【００４０】また、比較例の試料Ｎｏ．３は、熱間圧延
途中において再結晶が起きており、熱間圧延板表層の平
均再結晶サイズが１８０μｍ、また最大再結晶サイズが
２５０μｍと大きい。従って、中間焼鈍処理を行って
も、アルカリ処理後の表面外観の筋模様が顕著である。
さらに、均質化処理温度は低いが、熱間圧延開始温度が
高いということは、更に加熱処理が必要であり、また中
間焼鈍も行っているため、生産性は良くないことが判
る。In addition, the sample No. of the comparative example. In No. 3, recrystallization occurred during hot rolling, and the average recrystallized size of the surface layer of the hot rolled plate was 180 μm and the maximum recrystallized size was as large as 250 μm. Therefore, even if the intermediate annealing treatment is performed, the streak pattern of the surface appearance after the alkali treatment is remarkable.
Furthermore, the fact that the homogenization treatment temperature is low, but the hot rolling start temperature is high, shows that productivity is not good because further heat treatment is necessary and intermediate annealing is also performed.
【００４１】[0041]
【表１】 [Table 1]
【００４２】[0042]
【表２】 [Table 2]
【００４３】[0043]
【表３】 [Table 3]
【００４４】[0044]
【発明の効果】以上説明したように、本発明によれば、
鋳塊を低温で均質化処理し、且つ低温で熱間圧延するこ
とにより、アルカリ処理を施しても被処理面に筋模様の
発生しないアルミニウム合金板を高い生産性で製造する
ことができる。As described above, according to the present invention,
By homogenizing the ingot at a low temperature and hot rolling at a low temperature, it is possible to manufacture with high productivity an aluminum alloy plate that does not have a streak pattern on the surface to be treated even when subjected to an alkali treatment.
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.7 識別記号 ＦＩ Ｃ２２Ｆ 1/00 ６８２ Ｃ２２Ｆ 1/00 ６８２ ６８３ ６８３ ６８５ ６８５Ｚ ６９１ ６９１Ｂ ６９４ ６９４Ａ ６９４Ｂ (72)発明者 山岸 智秀 愛知県稲沢市小池１丁目11番１号 日本 軽金属株式会社 名古屋工場内 (72)発明者 水嶋 一光 愛知県稲沢市小池１丁目11番１号 日本 軽金属株式会社 名古屋工場内 (56)参考文献 特開 平５−9674（ＪＰ，Ａ) 特開 平３−100144（ＪＰ，Ａ) 特開 平１−215946（ＪＰ，Ａ) 特開 平６−346176（ＪＰ，Ａ) 特開 平11−256293（ＪＰ，Ａ) 特開 平５−9675（ＪＰ，Ａ) 特開 昭61−110741（ＪＰ，Ａ) (58)調査した分野(Int.Cl.7，ＤＢ名) C22F 1/04 - 1/057 B41N 1/08 C22C 21/00 - 21/18 ─────────────────────────────────────────────────── ─── Continuation of front page (51) Int.Cl. 7 Identification code FI C22F 1/00 682 C22F 1/00 682 683 683 685 685Z 691 691B 694 694A 694B (72) Inventor Tomohide Yamagishi 1 Koike, Inazawa, Aichi Prefecture 11-11-1 Nippon Light Metal Co., Ltd., Nagoya Plant (72) Inventor Ikko Mizushima 1-11-1 Koike, Inazawa City, Aichi Prefecture Japan Light Metal Co., Ltd., Nagoya Plant (56) Reference JP-A-5-9674 ( JP, A) JP 3-100144 (JP, A) JP 1-215946 (JP, A) JP 6-346176 (JP, A) JP 11-256293 (JP, A) JP 5-9675 (JP, A) JP-A-61-110741 (JP, A) (58) Fields investigated (Int.Cl. 7 , DB name) C22F 1/04-1/057 B41N 1/08 C22C 21 / 00-21/18
Claims (4)
００〜４３０℃の開始温度で複数パスの熱間圧延を施し
て板厚２〜１０ｍｍの熱間圧延板とする際に、該複数パ
スのパス間時間を１０sec〜１．５minの範囲内、最終パ
スの圧延率を５５％以上、熱間圧延の終了温度を２００
〜３８０℃とすることにより、最終パス以前の再結晶を
防止すると同時に最終パス後の放冷中に該熱間圧延板の
少なくとも表面層を再結晶させて圧延方向に直角な方向
の平均再結晶粒サイズが５０μｍ未満である再結晶組織
とし、ただし該表面層は該熱間圧延板の表面から深さ１
ｍｍ以下の領域であり、 該熱間圧延板に冷間圧延を施す、 ことを特徴とする陽極酸化処理前のアルカリ処理により
筋模様の発生しないアルミニウム合金板の製造方法。1. The following components: Fe: more than 0.40 and not more than 1.5 wt%, Si: 0.03 to 0.30 wt%, Cu: 0.004 to 0.20 wt%, Ti: 0.01 to 0 0.05 wt%, B: 0.0001 to 0.02 wt%, and the balance: an aluminum alloy ingot composed of aluminum and unavoidable impurities was prepared, and the ingot was subjected to homogenizing heat treatment at a temperature of 350 to 430 ° C. Do not exceed the end temperature of the homogenization treatment in the ingot 3
When a hot-rolled sheet having a thickness 2~10mm subjected to hot rolling of a plurality paths starting temperature of from 00 to 430 ° C., said plurality of path
Set the time between passes to within 10 seconds to 1.5 min.
Rolling rate of 55% or more, end temperature of hot rolling 200
By setting the temperature to ~ 380 ° C, recrystallization before the final pass
At the same time, prevent the hot rolled sheet from
The average recrystallized grain size of the perpendicular direction to the rolling direction is recrystallized at least the surface layer is a recrystallized structure is less than 50 [mu] m, provided that the surface layer is a depth from the surface of the heat-rolled plate of 1
mm region or less , cold rolling is performed on the hot-rolled sheet, by an alkali treatment before anodizing treatment.
A method for manufacturing an aluminum alloy plate having no streak pattern .
の最大再結晶粒サイズが１００μｍ未満であることを特
徴とする請求項１記載の方法。2. A method according to claim 1, wherein said recrystallized structure, wherein a maximum recrystallized grain size of the perpendicular direction to the rolling direction is less than 100 [mu] m.
たことを特徴とする陽極酸化処理前のアルカリ処理によ
り筋模様の発生しないアルミニウム合金板。3. to claim 1 or anodized before the alkali treatment, characterized in that it is manufactured in two described methods
An aluminum alloy plate that does not have streaks .
たアルミニウム合金板を成形して得られたことを特徴と
する陽極酸化処理前のアルカリ処理により筋模様の発生
しないアルミニウム合金板成形品。Wherein the occurrence of streaks by claim 1 or 2 anodization before the alkali treatment, characterized in that obtained by molding the aluminum alloy plate which is produced in a way described
Not an aluminum alloy plate molded product.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP05667398A JP3487160B2 (en) | 1998-03-09 | 1998-03-09 | Method for producing aluminum alloy plate in which no streak pattern is generated by alkali treatment before anodizing treatment, aluminum alloy plate and molded product of aluminum alloy plate |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP05667398A JP3487160B2 (en) | 1998-03-09 | 1998-03-09 | Method for producing aluminum alloy plate in which no streak pattern is generated by alkali treatment before anodizing treatment, aluminum alloy plate and molded product of aluminum alloy plate |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH11256294A JPH11256294A (en) | 1999-09-21 |
| JP3487160B2 true JP3487160B2 (en) | 2004-01-13 |
Family
ID=13033951
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|---|---|---|---|
| JP05667398A Expired - Fee Related JP3487160B2 (en) | 1998-03-09 | 1998-03-09 | Method for producing aluminum alloy plate in which no streak pattern is generated by alkali treatment before anodizing treatment, aluminum alloy plate and molded product of aluminum alloy plate |
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| JP (1) | JP3487160B2 (en) |
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|---|---|---|---|---|
| JP5004007B2 (en) * | 2007-04-12 | 2012-08-22 | 日本軽金属株式会社 | Aluminum alloy plate for battery lid and manufacturing method thereof |
| CN104805336B (en) * | 2015-05-13 | 2017-11-07 | 江苏亨通电力特种导线有限公司 | Shielding aluminium alloy rod |
| CN106148740A (en) * | 2015-05-13 | 2016-11-23 | 江苏亨通电力特种导线有限公司 | The manufacture method of high strength heat resistant type aluminium alloy rod |
| ES2653729B1 (en) | 2016-08-05 | 2018-11-16 | Acr Ii Aluminium Group Cooperatief U.A. | ALUMINUM LAMINATION PROCESS FOR FINE GRAIN APPLICATIONS |
-
1998
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107254607A (en) * | 2015-05-13 | 2017-10-17 | 江苏亨通电力特种导线有限公司 | Alloy with High Conductivity wire rod |
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| JPH0387329A (en) | Aluminum alloy material for baking finish and its manufacture |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| LAPS | Cancellation because of no payment of annual fees |