JP2002249841A - Aluminum alloy plate for spinning process, and its manufacturing method - Google Patents
Aluminum alloy plate for spinning process, and its manufacturing methodInfo
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- JP2002249841A JP2002249841A JP2001050442A JP2001050442A JP2002249841A JP 2002249841 A JP2002249841 A JP 2002249841A JP 2001050442 A JP2001050442 A JP 2001050442A JP 2001050442 A JP2001050442 A JP 2001050442A JP 2002249841 A JP2002249841 A JP 2002249841A
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- recrystallized
- aluminum alloy
- spinning
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Abstract
Description
【0001】[0001]
【発明の属する技術分野】本発明は自動車等のホイール
リムやパラボラアンテナ、鏡板、鍋釜等の円筒状、カッ
プ状乃至椀型等の製品を得るためのスピニング加工性に
優れ、加工後の表面が平滑なアルミニウム合金厚板およ
び該合金厚板の好ましい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 is excellent in spinning processability for obtaining cylindrical, cup-shaped or bowl-shaped products such as wheel rims, parabolic antennas, head plates, pot pots and the like for automobiles and the like, and the surface after processing. The present invention relates to a smooth aluminum alloy plate and a preferable method for producing the alloy plate.
【0002】[0002]
【従来の技術】円筒状、カップ状ないし椀型などのスピ
ニング加工は図1に示すように軸を中心として回転する
所定形状の成形型1に被加工材としての圧延板3を板押
え4で押さえ込み、成形型1の軸方向にそって移動する
ロール2を移動させて被加工材たる前記圧延板3を所望
形状に成形させるものである。なおこの場合の成形型1
として代表的なリム形状の例は図2に示す断面図の如く
である。2. Description of the Related Art As shown in FIG. 1, a spinning process such as a cylindrical shape, a cup shape or a bowl shape is performed by pressing a rolled plate 3 as a material to be processed into a forming die 1 having a predetermined shape which rotates around an axis. The roll 2 is pressed down and moved along the axial direction of the forming die 1 to form the rolled plate 3 as a workpiece into a desired shape. The molding die 1 in this case
An example of a typical rim shape is as shown in the sectional view of FIG.
【0003】ところで上記したようなスピニング加工は
図1に示したような成形型1を中心として成立し、別段
大きな設備を準備しなくても加工でき、しかもアルミニ
ウム合金は成形性が良好で圧延板から塑性加工したもの
は靱性が高く、成形体の厚さを薄くできて軽量化が図れ
るところから、上述したような製品の多くはアルミニウ
ム合金圧延板をスピニング加工して製造されている。な
おスピニング加工用の厚板は、加工材という観点から厚
板全体を均一微細組織とするために、冷間圧延後再結晶
させて製造されている。[0003] Incidentally, the above-mentioned spinning process is established mainly on the forming die 1 as shown in FIG. 1, and can be processed without preparing any extra large equipment. Most of the above-mentioned products are manufactured by spinning an aluminum alloy rolled plate because the plastically processed product has high toughness and can reduce the thickness of the molded product to reduce the weight. The thick plate for spinning is manufactured by cold rolling and then recrystallized in order to make the entire thick plate into a uniform fine structure from the viewpoint of a work material.
【0004】[0004]
【発明が解決しようとする課題】スピニング加工品の肌
を平滑にするために厚板の再結晶粒を微細化すると厚板
の耐力が高くなりスピニング加工性が低下する。またス
ピニング加工性を向上させるために再結晶粒を粗大化さ
せて板の耐力を下げると、スピニング加工品の肌が粗く
なる。即ち本発明においては、上記したような従来材の
欠点を解決し、スピニング加工品の表面が平滑で、かつ
耐力の低い特性を合わせ持つスピニング加工性の良い厚
板とその製造方法を提案するものである。If the recrystallized grains of the thick plate are made finer to smooth the skin of the spinned product, the yield strength of the thick plate is increased and the spinning workability is reduced. Further, if the recrystallized grains are coarsened to improve the spinning workability and the proof stress of the plate is reduced, the skin of the spinned product becomes rough. That is, the present invention solves the above-mentioned drawbacks of the conventional materials, and proposes a spinning-processable thick plate having a smooth surface of a spinned product and having characteristics of low proof stress and a method of manufacturing the same. It is.
【0005】[0005]
【課題を解決するための手段】発明者らは、スピニング
加工用厚板の表層は微細な再結晶粒で、内部は粗な再結
晶粒とすれば、スピニング加工品の表面が平滑でかつス
ピニング加工性の良好な厚板が得られるものとして本発
明を完成したものである。Means for Solving the Problems The inventors have found that if the surface layer of a spinning thick plate is made of fine recrystallized grains and the inside is made of coarse recrystallized grains, the surface of the spinned product will be smooth and spinning-free. The present invention has been completed on the assumption that a thick plate having good workability can be obtained.
【0006】即ち本発明における第1の発明は、アルミ
ニウム合金板の厚さが5〜10mmであって、該合金板の
表面から0.5mmの深さ位置における再結晶粒サイズが円
相当径平均値で50μm 以下、中心部の再結晶粒サイズ
が円相当径平均値で70μm以上であることを特徴とす
るスピニング加工用アルミニウム合金厚板である。この
ような組織の厚板とすることによって、スピニング加工
品の表面が平滑で、かつ耐力の低い性質が併存し、スピ
ニング加工性の良い効果を有している。さらに好ましく
は、前記アルミニウム合金厚板の組成を、第2発明のよ
うにMgが2.0〜3.4重量%、Cuが0.05〜0.10重量
%、SiとFeの合計量が0.05〜0.09重量%、鋳造組織
微細化剤が0.005〜0.2重量%であり、残部Alおよび
不可避的不純物であって、該不可避的不純物のうち、M
n、CrおよびZrがそれぞれ0.01重量%以下とすること
で、上記効果に加え、実製品に則した厚板とすることが
できる。That is, in the first invention of the present invention, the aluminum alloy plate has a thickness of 5 to 10 mm, and the recrystallized grain size at a depth of 0.5 mm from the surface of the aluminum alloy plate has an average circle equivalent diameter. An aluminum alloy thick plate for spinning, characterized in that the thickness is not more than 50 μm, and the recrystallized grain size at the center is not less than 70 μm in terms of the average equivalent circle diameter. By using a thick plate having such a structure, the surface of the spinned product has a smooth surface and a property of low proof stress coexists, and has an effect of good spinning processability. More preferably, the composition of the aluminum alloy plate is 2.0 to 3.4% by weight of Mg, 0.05 to 0.10% by weight of Cu, and the total amount of Si and Fe as in the second invention. 0.05 to 0.09% by weight, the cast structure refining agent is 0.005 to 0.2% by weight, and the balance is Al and inevitable impurities.
By setting each of n, Cr and Zr to 0.01% by weight or less, in addition to the above effects, a thick plate conforming to an actual product can be obtained.
【0007】また、本発明における第3の発明は、上記
組成のアルミニウム合金鋳塊を均質化処理し、次いで該
鋳塊を複数パスで熱間圧延するにあたって、熱間圧延の
最終パスの圧下率を43%以上、ワークロール出側板厚
さを5〜10mmとし、該熱間圧延板を板の自熱で再結晶
させることを特徴とするスピニング加工用アルミニウム
合金厚板の製造方法である。Si、Fe等の再結晶核を形成
する元素が少ないから、このような製造方法とすること
によって、上記の再結晶粒サイズを熱間圧延後の板の自
熱で行わせることができ、厚板の表層部は再結晶粒サイ
ズが平均値で50μm 以下、中心部の再結晶粒サイズが
平均値で70μm 以上の厚板を容易に得ることができ
る。ここで熱間圧延の最終パスの圧下率の上限は55%
程度である。これ以上となると板中心部の再結晶粒サイ
ズが小さくなる。また第4発明のように自熱で再結晶し
た熱間圧延後の合金厚板を再度再結晶温度に加熱する
と、板のコイルの巻き始め等の再結晶不完全部分を再結
晶化できて板全体の機械的特性を均一化できる。In a third aspect of the present invention, an aluminum alloy ingot having the above composition is homogenized, and then the ingot is hot-rolled in a plurality of passes. And a work roll exit side plate thickness of 5 to 10 mm, and re-crystallizing the hot-rolled plate by the self-heating of the plate. Since there are few elements that form recrystallization nuclei such as Si and Fe, by adopting such a manufacturing method, the above-described recrystallized grain size can be performed by the self-heating of the sheet after hot rolling, and the thickness can be increased. A thick plate having a recrystallized grain size of 50 μm or less on average in the surface layer portion of the plate and an average recrystallized grain size of 70 μm or more on the center can be easily obtained. Here, the upper limit of the rolling reduction in the final pass of hot rolling is 55%.
It is about. Above this, the recrystallized grain size at the center of the plate becomes smaller. Further, when the hot-rolled alloy thick plate recrystallized by self-heating as in the fourth invention is heated again to the recrystallization temperature, an incomplete recrystallization portion such as the beginning of winding of a coil of the plate can be recrystallized. The entire mechanical properties can be made uniform.
【0008】なお上述したスピニング加工は上記した如
く、厚板と型が共に回転している状態で、ロール治具を
使用して厚板を型面形状にならしていく加工方法である
ために、厚板表層部の結晶粒は延ばされた状態で加工品
の外観となる。厚板表層部の結晶粒サイズが小さければ
延ばされても小さく、平滑感は損なわれない。平滑感を
損なわない加工前の厚板表層部の結晶粒サイズは円相当
径平均値で約50μm以下である。さらに小サイズであ
れば良好となる。しかしながら厚板全体が小結晶粒サイ
ズとなると、ホールペッチの法則で知られているように
耐力が高くなり、スピニング加工の速度が低下し生産性
を下げる。従って本発明の如く、厚板表層部は小再結晶
粒サイズ、中心部は粗な再結晶粒サイズとする。The spinning process described above is a processing method in which the thick plate is shaped into a mold surface using a roll jig in a state where the thick plate and the mold are rotating together, as described above. On the other hand, the crystal grains in the surface layer of the thick plate have the appearance of a processed product in a stretched state. If the grain size of the surface layer portion of the thick plate is small, it is small even if it is elongated, and the smoothness is not impaired. The crystal grain size of the surface layer portion of the thick plate before processing that does not impair the smoothness is about 50 μm or less in terms of the equivalent circle diameter. Further, if the size is small, it is good. However, when the entire thick plate has a small crystal grain size, the yield strength increases as known by the Hall-Petch law, and the spinning speed is reduced, thereby lowering productivity. Therefore, as in the present invention, the surface layer of the thick plate has a small recrystallized grain size, and the central portion has a coarse recrystallized grain size.
【0009】上述したようなスピニング加工で加工品の
表面性状に影響を与えるのは概略0.5mm程度であるか
ら、表層部の厚さは0.5mmの範囲で小結晶粒サイズであ
ればよい。一方中心部は逆に粗な再結晶粒サイズとし、
その部分の耐力を低下させ全体として加工性を良好なも
のとさせる。中心部の結晶粒サイズが円相当径平均値で
約70μm 以上であると全体的な耐力も低下し、スピニ
ング加工性が良くなる。結晶粒サイズは、表層部から中
心部へ徐々に大きくなっていく。中心部の厚さは2mmの
範囲で粗な結晶粒サイズであればよい。なおここで結晶
粒サイズが円相当径平均値とは、単位視野内における再
結晶数から計算される平均1再結晶粒当りの円相当径を
いう。[0009] Since the above-mentioned spinning process affects the surface properties of the processed product by about 0.5 mm, the thickness of the surface layer may be in the range of 0.5 mm as long as the crystal grain size is small. . On the other hand, the center part has a coarse recrystallized grain size,
The proof stress of that part is reduced, and the workability as a whole is improved. When the crystal grain size at the center is not less than about 70 μm in terms of the equivalent circle diameter, the overall proof stress is reduced and spinning workability is improved. The crystal grain size gradually increases from the surface layer to the center. The thickness of the central portion may be in the range of 2 mm as long as it has a coarse crystal grain size. Here, the average value of the crystal grain size of the circle-equivalent diameter refers to the average circle-equivalent diameter per recrystallized grain calculated from the number of recrystallizations in a unit visual field.
【0010】[0010]
【発明の実施の形態】上述したような本発明によるもの
の具体的な実施形態について説明すると、先ず本発明に
おける厚板の好ましい組成について述べるならば以下の
如くである。Mg:2.0〜3.4重量%、およびCu:0.05
〜0.10重量%とする。MgおよびCuは非熱処理タイプの
加工品に強度を付与するためのもので、下限値未満では
実製品としての強度不足となり、また上限値を超えると
加工硬化が大きくスピニング加工速度が低下する。また
これらの元素は固溶タイプの元素でこの程度の含有量で
あれば他の元素含有量の規制と相まって金属間化合物を
形成し難く、再結晶の核と成り難い。BEST MODE FOR CARRYING OUT THE INVENTION A specific embodiment of the present invention as described above will be described. First, a preferred composition of a thick plate according to the present invention will be described as follows. Mg: 2.0 to 3.4% by weight, and Cu: 0.05
To 0.10% by weight. Mg and Cu are for imparting strength to a non-heat-treated type processed product. If the value is less than the lower limit, the strength of the actual product is insufficient, and if the value exceeds the upper limit, work hardening is large and the spinning speed is reduced. In addition, these elements are solid-solution type elements, and if the content is at this level, it is difficult to form an intermetallic compound in combination with the regulation of the content of other elements, and it is difficult to form a nucleus for recrystallization.
【0011】SiとFeの合計量を0.05〜0.09重量%と
する。SiとFeはAl−Fe系化合物およびAl−Si−Fe系化合
物の1種または2種を形成させ、再結晶の核となるもの
である。下限値未満では再結晶の核の数が少なく、厚板
表層部の再結晶粒の微細化が困難になる。上限値を超え
ると厚板中心部の再結晶粒も微細化してしまう。SiとFe
は添加してもいいし、返り材の調整で含有させることも
できる。The total amount of Si and Fe is 0.05 to 0.09% by weight. Si and Fe form one or two of Al-Fe-based compounds and Al-Si-Fe-based compounds, and serve as nuclei for recrystallization. Below the lower limit, the number of recrystallization nuclei is small, making it difficult to refine recrystallized grains in the surface layer of the thick plate. If the upper limit is exceeded, the recrystallized grains at the center of the thick plate will also be refined. Si and Fe
May be added, or may be contained by adjusting the return material.
【0012】鋳造組織微細化剤を0.005〜0.2重量%
使用する。鋳造組織微細化剤は鋳造割れ防止のために添
加するものである。下限値未満では効果が少なく、上限
値を超えても効果が飽和し経済的でない。鋳造組織微細
化剤としては、例えばTi単独、TiとBの併用等がある。
Ti単独の場合は、Ti:0.005〜0.2重量%、TiとBの
併用の場合は、Ti:0.005〜0.2重量%およびB:0.
005〜0.2重量%をアルミニウム合金溶湯に含有させ
ればよい。[0012] 0.005 to 0.2% by weight of a casting structure refining agent
use. The cast structure refining agent is added to prevent casting cracks. If the amount is less than the lower limit, the effect is small, and if the amount exceeds the upper limit, the effect is saturated and it is not economical. Examples of the cast structure refining agent include Ti alone and a combination of Ti and B.
In the case of Ti alone, Ti: 0.005 to 0.2% by weight, and in the case of combined use of Ti and B, Ti: 0.005 to 0.2% by weight and B: 0.00%.
What is necessary is just to make 005-0.2 weight% contain in an aluminum alloy molten metal.
【0013】Mn、CrおよびZrをそれぞれ0.01重量%以
下とする。アルミニウムには製錬および返り材から入っ
て来る元素が多数あるが、そのなかでも含有量が多くか
つそれらの化合物が再結晶粒の核となり易い元素は原料
を選別し、品位の高い地金および返り材を使用する。即
ちMn、CrおよびZrのそれぞれの元素が上限値を超える
と、金属間化合物を形成して厚板の中心部も微細再結晶
粒となり好ましくない。他の不可避的不純物は各0.05
重量%以下であることが好ましい。Mn, Cr and Zr are each made 0.01% by weight or less. Aluminum contains a large number of elements coming from smelting and return materials, and among them, the elements that are high in content and whose compounds tend to be nuclei of recrystallized grains are selected from raw materials, and high-grade ingots and Use return material. That is, when the respective elements of Mn, Cr and Zr exceed the upper limit values, an intermetallic compound is formed, and the center of the thick plate is also undesirably formed as fine recrystallized grains. Other unavoidable impurities are 0.05 each
It is preferable that the content be not more than weight%.
【0014】次に好ましい本発明の製造方法について説
明すると、以下の如くである。上記組成のアルミニウム
合金鋳塊を均質化処理する。均質化処理は特に限定する
ものではないが、例えば鋳塊の加熱昇温速度を150℃
/時間以下、加熱温度範囲を440〜540℃、保持時
間を1〜24時間とし、あるいは鋳塊の上記加熱温度範
囲を含有合金元素の固溶条件に適した温度、例えば44
0〜490℃の低温部と、490〜540℃の高温部の
2段に分け、それぞれの温度領域に加熱保持してもよ
い。Next, a preferred production method of the present invention will be described as follows. The aluminum alloy ingot having the above composition is homogenized. Although the homogenization treatment is not particularly limited, for example, the heating rate of the ingot is set to 150 ° C.
/ Hour or less, the heating temperature range is 440 to 540 ° C., the holding time is 1 to 24 hours, or the heating temperature range of the ingot is a temperature suitable for the solid solution condition of the contained alloy element, for example, 44
It may be divided into two stages of a low temperature part of 0 to 490 ° C. and a high temperature part of 490 to 540 ° C., and may be heated and held in each temperature region.
【0015】上述したような条件で均質化処理した上記
鋳塊を、複数パスで熱間圧延する。熱間圧延するにあた
って熱間圧延の最終パスの圧下率を43%以上、ロール
出側板厚さを5〜10mmとし、該熱間圧延板をコイルに
し自熱で再結晶させる。熱間圧延の最終パスの圧下率を
43%以上とするのは、厚板表層部に大きな加工歪を付
与し、厚板中心部はその歪が減衰し軽度の加工歪となる
ことにより、このようにして加工された厚板を圧延ロー
ル出側の厚板自体の熱で再結晶化し、あるいは再度再加
熱して再結晶化させる。このようにすることにより、厚
板表層部の再結晶粒は微細化し、Si、Fe、Mn、Crおよび
Zrのように再結晶の核となる化合物を形成する元素が少
ないことと中心部の軽度の加工歪とが相まって、厚板中
心部の再結晶粒は粗大化する。ロール出側板厚さを5〜
10mmとするのは板の厚さが薄ければ中心部まで大きな
加工歪が伝搬し、厚板の表層部と同様に再結晶粒が微細
化してしまうからである。板厚さの上限値は実際のスピ
ニング加工用板としての値である。熱延上がりの厚板温
度は320℃以上であれば等軸晶の再結晶を得ることが
できる。上限は380℃程度でこの温度を超えると再結
晶粒の成長が発生し易い。The ingot homogenized under the above conditions is hot-rolled in a plurality of passes. In the hot rolling, the rolling reduction of the final pass of the hot rolling is 43% or more, the thickness of the roll exit side plate is 5 to 10 mm, and the hot rolled plate is coiled and recrystallized by self-heating. The reason why the rolling reduction in the final pass of hot rolling is set to 43% or more is that a large work strain is imparted to the surface layer of the thick plate, and the strain is attenuated at the center of the thick plate, resulting in a slight work strain. The thick plate processed in this manner is recrystallized by the heat of the thick plate itself on the roll-roll exit side, or is re-heated again to be recrystallized. By doing so, the recrystallized grains in the surface layer of the thick plate are refined, and Si, Fe, Mn, Cr and
Recrystallization grains in the center of the thick plate are coarsened due to the fact that a small number of elements forming a compound serving as a nucleus for recrystallization such as Zr are combined with a slight processing strain at the center. Roll exit side plate thickness is 5
The reason why the thickness is set to 10 mm is that if the thickness of the plate is small, a large processing strain propagates to the center, and the recrystallized grains become finer as in the surface layer of the thick plate. The upper limit of the thickness is a value as an actual spinning plate. If the temperature of the hot-rolled thick plate is 320 ° C. or higher, recrystallization of equiaxed crystals can be obtained. The upper limit is about 380 ° C. If the temperature is exceeded, the growth of recrystallized grains tends to occur.
【0016】[0016]
【実施例】上記したような本発明によるものの具体的な
実施例について説明すると以下の如くである。DESCRIPTION OF THE PREFERRED EMBODIMENTS Specific embodiments of the present invention as described above will be described as follows.
【実施例1】本発明者等が具体的に採用した合金の組成
は次の表1に示す如くである。EXAMPLE 1 The composition of the alloy specifically adopted by the present inventors is as shown in Table 1 below.
【0017】[0017]
【表1】 [Table 1]
【0018】前記した表1の合金符号1−Aおよび1−
Bに示す組成のアルミニウム合金を溶製し、半連続鋳造
して厚さ約500mmのスラブ鋳塊を鋳造した。該鋳塊の
表面を厚さ15mm面削除去後昇温速度120℃/時間で
加熱し、500±10℃に12時間保持して均質化処理
をした。熱間圧延は7パスとし、6パス後の板厚を9.4
mm、14.5mmおよび17.5mmの3種とし、7パス目の最
終熱間圧延で8mmに圧延しコイル巻きした。それぞれの
圧下率は15%、45%、54%、ロール出側板温度で
340℃であった。The alloy codes 1-A and 1-
An aluminum alloy having the composition shown in B was melted and semi-continuously cast to cast a slab ingot having a thickness of about 500 mm. The surface of the ingot was heated at a rate of 120 ° C./hour after removing the surface of 15 mm in thickness, and kept at 500 ± 10 ° C. for 12 hours for homogenization. Hot rolling is performed in 7 passes, and the plate thickness after 6 passes is 9.4.
mm, 14.5 mm and 17.5 mm, and were rolled to 8 mm in the final hot rolling in the seventh pass and coiled. The rolling reduction was 15%, 45%, 54%, and the roll exit side plate temperature was 340 ° C.
【0019】自熱による再結晶終了後、室温で機械的性
質および厚板の表面より0.5mm下、および中央の結晶粒
のサイズを測定した。測定面は圧延方向で板厚方向の断
面である。測定方法は画像解析装置を用いて測定視野0.
28mm2 内の再結晶粒数から計算した円相当径平均値で
ある。この測定結果は次の表2に示す如くであった。After completion of the recrystallization by self-heating, the mechanical properties and the size of crystal grains 0.5 mm below and at the center of the surface of the thick plate at room temperature were measured. The measurement surface is a cross section in the thickness direction in the rolling direction. The measurement method is 0 using the image analyzer.
This is the average value of the circle equivalent diameter calculated from the number of recrystallized grains in 28 mm 2 . The measurement results are as shown in Table 2 below.
【0020】[0020]
【表2】 [Table 2]
【0021】なお次の表3には上記したような実施例に
おける圧下率45%板の熱間圧延後自熱で再結晶させた
ものの機械的性質を示した。The following Table 3 shows the mechanical properties of the 45% reduction plate in the above-described embodiment after hot rolling and recrystallization by self-heating.
【0022】[0022]
【表3】 [Table 3]
【0023】前記した表2の結果から、圧下率15%で
は表層部と中心部では再結晶粒のサイズに顕著な差は見
られず、しかも表層部の再結晶サイズが大きい。45
%、54%では顕著な差が見られ、表層部の再結晶サイ
ズが小さい。From the results shown in Table 2 above, at a rolling reduction of 15%, there is no remarkable difference in the size of recrystallized grains between the surface portion and the central portion, and the recrystallized size of the surface portion is large. 45
% And 54%, a remarkable difference is seen, and the recrystallized size of the surface layer is small.
【0024】比較例として、上述と同様にして得られた
厚さ12.3mmの熱間圧延板を冷間圧延で厚さ8mmの冷間
圧延板とした。次いで340℃の温度に加熱し、1時間
保持して再結晶させた。機械的特性および再結晶粒の円
相当径を測定した。測定条件は実施例と同じであるが、
このような結果は次の表4に示す如くである。As a comparative example, a hot-rolled plate having a thickness of 12.3 mm obtained in the same manner as described above was cold-rolled into a cold-rolled plate having a thickness of 8 mm. Then, the mixture was heated to a temperature of 340 ° C. and kept for 1 hour to recrystallize. The mechanical properties and the circle equivalent diameter of the recrystallized grains were measured. The measurement conditions are the same as in the example,
Such results are shown in Table 4 below.
【0025】[0025]
【表4】 [Table 4]
【0026】前記したような表4の結果によるならば、
圧下率35%で冷間圧延し再結晶させた厚板は、表層部
と中心部では再結晶粒のサイズに大きな差は見られず、
しかも表層部の再結晶サイズが大きい。According to the results of Table 4 as described above,
In the thick plate cold rolled and recrystallized at a rolling reduction of 35%, there is no large difference in the size of recrystallized grains between the surface layer portion and the central portion.
Moreover, the recrystallized size of the surface layer is large.
【0027】[0027]
【実施例2】実施例1の本発明例における45%熱間圧
延後の再結晶板と比較例の25%冷間圧延後の再結晶板
を用いて、下記する条件でスピニング加工性を比較し
た。即ち前述した図1に示す如き装置を用い、上記の板
成形型に板押さえで押さえ加工した。 成形型寸法:250mmφ 板寸法:8mm×350mmφ 成形型回転数:300rpm ロール送り測度:600mm/分 ロールと成形型の間隔:7mm 潤滑油なしEXAMPLE 2 Spinning workability was compared under the following conditions using the recrystallized sheet after hot rolling at 45% in the inventive example of Example 1 and the recrystallized sheet after 25% cold rolling of the comparative example. did. That is, using the apparatus as shown in FIG. 1 described above, the above plate forming die was pressed by a plate press. Mold size: 250mmφ Plate size: 8mm x 350mmφ Mold rotation speed: 300rpm Roll feed rate: 600mm / min Interval between roll and mold: 7mm No lubrication oil
【0028】加工終了後板の表面を目視観察し、割れ発
生の有無および肌荒れの有無を目視で判断した結果を次
の表5に示す。After the completion of the working, the surface of the plate was visually observed, and the result of visually judging the occurrence of cracks and the presence or absence of skin roughness is shown in Table 5 below.
【0029】[0029]
【表5】 [Table 5]
【0030】即ち上述したような本発明のスピニング加
工用厚板は、肌が平滑でかつスピニング加工性が良好で
あるから、優れた加工品を生産性良く生産できる効果を
有しており、また本発明のスピニング加工用厚板の製造
方法は、熱間圧延後の自熱で再結晶させているので、省
エネ効果を有していることも明らかである。That is, the spinning thick plate of the present invention as described above has the effect of producing excellent processed products with good productivity because the skin is smooth and the spinning workability is good. Since the method for producing a thick plate for spinning according to the present invention is recrystallized by self-heating after hot rolling, it is also apparent that it has an energy saving effect.
【0031】[0031]
【発明の効果】以上説明したような本発明によるなら
ば、車輌用ホイールリムやパラボラアンテナ、鏡板、鍋
釜などの円筒状ないしカップ状、椀型などの各種製品を
得るためのスピニング加工性に優れ、加工後の表面性状
の卓越した平滑なアルミニウム合金厚板および該合金厚
板の好ましい製造を得しめることが明らかであり、工業
的にその効果の大きい発明であることが明らかである。According to the present invention as described above, the spinning processability for obtaining various products such as wheel rims for vehicles, parabolic antennas, head plates, pots, and other cylindrical or cup-shaped or bowl-shaped products can be obtained. It is evident that an excellent and smooth aluminum alloy plate having excellent surface properties after processing and a preferable production of the alloy plate can be obtained, and it is clear that the invention is industrially effective.
【図面の簡単な説明】[Brief description of the drawings]
【図1】スピニング加工の状態を示した断面的説明図で
ある。FIG. 1 is an explanatory sectional view showing a state of spinning processing.
【図2】図1に示したものにおける成形型としてホイー
ル成形型の1例についての断面図である。FIG. 2 is a cross-sectional view of an example of a wheel mold as the mold in FIG.
【図3】本発明における再結晶粒測定位置についての説
明図である。FIG. 3 is an explanatory diagram of a recrystallized grain measurement position in the present invention.
1 軸を中心として回転する成形型 2 成形型を横方向に移動させるロール 3 被加工材たる板 4 板押え 5 再結晶粒サイズ測定位置 6 中心部 7 板厚方向 1 Forming die that rotates around an axis 2 Roll that moves the forming die in the lateral direction 3 Plate as work piece 4 Plate holder 5 Recrystallized grain size measurement position 6 Central part 7 Plate thickness direction
─────────────────────────────────────────────────────
────────────────────────────────────────────────── ───
【手続補正書】[Procedure amendment]
【提出日】平成13年3月1日(2001.3.1)[Submission date] March 1, 2001 (2001.3.1)
【手続補正1】[Procedure amendment 1]
【補正対象書類名】図面[Document name to be amended] Drawing
【補正対象項目名】図1[Correction target item name] Fig. 1
【補正方法】変更[Correction method] Change
【補正内容】[Correction contents]
【図1】 FIG.
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 1/00 623 630 630K 682 682 683 683 684 684C 694 694Z 694A (72)発明者 田島 靖史 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 玉置 雄一 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 高橋 忍 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Continuation of the front page (51) Int.Cl. 7 Identification symbol FI Theme coat II (reference) C22F 1/00 623 C22F 1/00 623 630 630K 682 682 683 683 684 684C 694 694Z 694A (72) Inventor Yasushi Tajima Aichi 1-11-1 Koike, Inazawa-shi Nippon Light Metal Co., Ltd. Nagoya Plant (72) Inventor Yuichi Tamaki 1-11-1 Koike, Inazawa-shi, Aichi Prefecture Nippon Light Metal Co., Ltd. Nagoya Plant (72) Inventor Shinobu Takahashi 1-1-11 Koike, Inazawa, Aichi Prefecture Nippon Light Metal Co., Ltd. Nagoya Plant
Claims (4)
であって、該合金板の表面から0.5mmの深さ位置におけ
る再結晶粒サイズが円相当径平均値で50μm 以下、中
心部の再結晶粒サイズが円相当径平均値で70μm 以上
であることを特徴とするスピニング加工用アルミニウム
合金厚板。1. A thickness of the aluminum alloy plate 5~10mm
Wherein the recrystallized grain size at a depth of 0.5 mm from the surface of the alloy plate is 50 μm or less in terms of the average equivalent circle diameter, and the recrystallized grain size in the center is 70 μm or more in terms of the average equivalent circle diameter. An aluminum alloy plate for spinning, characterized in that:
0〜3.4重量%、Cuが0.05〜0.10重量%、SiとFeの
合計量が0.05〜0.09重量%、鋳造組織微細化剤が0.
005〜0.2重量%であり、残部Alおよび不可避的不純
物であって、該不可避的不純物のうち、Mn、CrおよびZr
がそれぞれ0.01重量%以下であることを特徴とする請
求項1に記載のスピニング加工用アルミニウム合金厚
板。2. The composition of an aluminum alloy plate having a Mg content of 2.
0 to 3.4% by weight, 0.05 to 0.10% by weight of Cu, 0.05 to 0.09% by weight of the total amount of Si and Fe, and 0.
005 to 0.2% by weight, with the balance being Al and inevitable impurities, of which Mn, Cr and Zr
2 is 0.01% by weight or less, respectively.
10重量%、SiとFeの合計量が0.05〜0.09重量%、
鋳造組織微細化剤が0.005〜0.2重量%、残部Alおよ
び不可避的不純物とし、該不可避的不純物のうち、Mn、
CrおよびZrをそれぞれ0.01重量%以下に規制したアル
ミニウム合金鋳塊を均質化処理し、次いで該鋳塊を複数
パスで熱間圧延するにあたって、熱間圧延の最終パスの
圧下率を43%以上、ワークロール出側板厚さを5〜1
0mmとし、該熱間圧延板を板の自熱で再結晶させること
を特徴とするスピニング加工用アルミニウム合金厚板の
製造方法。3. Mg is 2.0 to 3.4% by weight, and Cu is 0.05 to 0.5% by weight.
10% by weight, the total amount of Si and Fe is 0.05 to 0.09% by weight,
The cast structure refining agent is 0.005 to 0.2% by weight, the balance being Al and inevitable impurities, and among the inevitable impurities, Mn,
When an aluminum alloy ingot in which Cr and Zr are each controlled to 0.01% by weight or less is homogenized, and then the ingot is hot-rolled in a plurality of passes, the rolling reduction in the final pass of hot rolling is 43%. As described above, the work roll exit side plate thickness is 5 to 1
A method for producing an aluminum alloy thick plate for spinning, wherein the thickness is set to 0 mm and the hot-rolled plate is recrystallized by the self-heating of the plate.
再結晶させることを特徴とする請求項3に記載のスピニ
ング加工用アルミニウム合金厚板の製造方法。4. The method for producing an aluminum alloy thick plate for spinning according to claim 3, wherein the hot-rolled sheet recrystallized by self-heating of the sheet is recrystallized again.
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Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2009167533A (en) * | 2009-03-25 | 2009-07-30 | Nippon Light Metal Co Ltd | Aluminum alloy thick plate for spinning |
JP2015224377A (en) * | 2014-05-29 | 2015-12-14 | 株式会社Uacj | Aluminum alloy plate excellent in ridging resistance |
-
2001
- 2001-02-26 JP JP2001050442A patent/JP4479114B2/en not_active Expired - Lifetime
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2009167533A (en) * | 2009-03-25 | 2009-07-30 | Nippon Light Metal Co Ltd | Aluminum alloy thick plate for spinning |
JP2015224377A (en) * | 2014-05-29 | 2015-12-14 | 株式会社Uacj | Aluminum alloy plate excellent in ridging resistance |
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