JPH09249951A - Production of aluminum forged product having fine structure - Google Patents
Production of aluminum forged product having fine structureInfo
- Publication number
- JPH09249951A JPH09249951A JP8083330A JP8333096A JPH09249951A JP H09249951 A JPH09249951 A JP H09249951A JP 8083330 A JP8083330 A JP 8083330A JP 8333096 A JP8333096 A JP 8333096A JP H09249951 A JPH09249951 A JP H09249951A
- Authority
- JP
- Japan
- Prior art keywords
- forging
- weight
- treatment
- forged
- forged product
- 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.)
- Pending
Links
- 238000004519 manufacturing process Methods 0.000 title claims description 14
- 229910052782 aluminium Inorganic materials 0.000 title claims description 10
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 title claims description 10
- 238000005242 forging Methods 0.000 claims abstract description 88
- 238000010438 heat treatment Methods 0.000 claims abstract description 27
- 229910000838 Al alloy Inorganic materials 0.000 claims abstract description 22
- 230000032683 aging Effects 0.000 claims abstract description 15
- 230000001105 regulatory effect Effects 0.000 claims abstract description 4
- 239000000463 material Substances 0.000 claims description 23
- 238000000034 method Methods 0.000 claims description 14
- 238000001816 cooling Methods 0.000 claims description 7
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 6
- 229910052742 iron Inorganic materials 0.000 claims description 4
- 238000005520 cutting process Methods 0.000 claims description 2
- 238000002425 crystallisation Methods 0.000 claims 1
- 230000008025 crystallization Effects 0.000 claims 1
- 238000009987 spinning Methods 0.000 abstract description 8
- 229910052804 chromium Inorganic materials 0.000 abstract description 5
- 229910052748 manganese Inorganic materials 0.000 abstract description 5
- 229910052726 zirconium Inorganic materials 0.000 abstract description 4
- 239000000047 product Substances 0.000 description 42
- 239000000243 solution Substances 0.000 description 18
- 230000000694 effects Effects 0.000 description 11
- 238000005266 casting Methods 0.000 description 7
- 239000000203 mixture Substances 0.000 description 7
- 239000011159 matrix material Substances 0.000 description 6
- 239000002244 precipitate Substances 0.000 description 6
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 5
- 229910019018 Mg 2 Si Inorganic materials 0.000 description 5
- 238000005275 alloying Methods 0.000 description 5
- 239000012467 final product Substances 0.000 description 5
- 239000006104 solid solution Substances 0.000 description 5
- 230000007797 corrosion Effects 0.000 description 4
- 238000005260 corrosion Methods 0.000 description 4
- 229910000765 intermetallic Inorganic materials 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 229910018191 Al—Fe—Si Inorganic materials 0.000 description 3
- 229910018565 CuAl Inorganic materials 0.000 description 3
- 229910017818 Cu—Mg Inorganic materials 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 3
- 239000000956 alloy Substances 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 3
- 150000001875 compounds Chemical class 0.000 description 3
- 230000007547 defect Effects 0.000 description 3
- 238000000265 homogenisation Methods 0.000 description 3
- 238000010791 quenching Methods 0.000 description 3
- 230000000171 quenching effect Effects 0.000 description 3
- 238000007670 refining Methods 0.000 description 3
- 230000002411 adverse Effects 0.000 description 2
- 238000009749 continuous casting Methods 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 230000003247 decreasing effect Effects 0.000 description 2
- 238000003754 machining Methods 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 230000035945 sensitivity Effects 0.000 description 2
- 239000002210 silicon-based material Substances 0.000 description 2
- 238000002791 soaking Methods 0.000 description 2
- 238000005452 bending Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 239000000314 lubricant Substances 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 238000004881 precipitation hardening Methods 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 239000013585 weight reducing agent Substances 0.000 description 1
Landscapes
- Forging (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、機械的強度に優れた車
両用ホイール等のアルミ鍛造製品を製造する方法に関す
る。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for manufacturing a forged aluminum product such as a vehicle wheel having excellent mechanical strength.
【０００２】[0002]
【従来の技術】車両用ホイールを例にとると、車両用の
アルミニウム合金製ホイール（以下、アルミホイールと
いう）は、鉄製ホイールに比較して軽量であり、且つ意
匠性，耐食性等に優れていることから、需要が年々増加
する傾向にある。アルミホイールは、製造方法に応じて
鋳造ホイールと鍛造ホイールに大別される。鋳造ホイー
ルは、一体成形が可能なことから工程数が少なく、また
複雑形状への成形も可能なため、低コストで提供され
る。しかし、鋳造により製造されることから、ポロシテ
ィ等に起因して内部品質が劣り、結果として各部を肉厚
にする必要がある。そのため、アルミニウム合金の軽量
性を活かし切れず、車両用として敬遠される重量増加を
招く原因となる。2. Description of the Related Art Taking a wheel for a vehicle as an example, a wheel made of an aluminum alloy for a vehicle (hereinafter referred to as an aluminum wheel) is lighter in weight than an iron wheel, and is excellent in design and corrosion resistance. Therefore, demand tends to increase year by year. Aluminum wheels are roughly classified into cast wheels and forged wheels according to the manufacturing method. Since the casting wheel can be integrally molded, the number of steps is small, and since it can be molded into a complicated shape, it is provided at low cost. However, since it is manufactured by casting, the internal quality is poor due to porosity and the like, and as a result it is necessary to make each part thick. Therefore, the lightness of the aluminum alloy cannot be fully utilized, which causes an increase in weight that is avoided for vehicles.
【０００３】鍛造ホイールは、ディスク部とリム部とを
一体成形した１ピースホイール，それぞれが独立した部
材からなる２ピースホイール，リム部を更に二分割した
３ピースホイールに分類される。１ピースホイールは、
構造面からすると最も剛性が高く、ビレット又は押出し
棒を所定形状に鍛造することにより製造されている。こ
の鍛造ホイールは、リム部にスピニング等の塑性加工を
施し、場合によってはフランジ部をフレアリング加工し
ている。たとえば、特開平１−２７３６３５号公報で
は、鍛造後のスピニング加工によってリアフランジ部を
形成している。また、特開平６−１９８３８２号公報で
は、鍛造後のフレアリング加工によりリアフランジ部を
形成している。The forged wheels are classified into a one-piece wheel in which a disc portion and a rim portion are integrally formed, a two-piece wheel in which each is an independent member, and a three-piece wheel in which the rim portion is further divided into two. The one-piece wheel is
It has the highest rigidity in terms of structure and is manufactured by forging a billet or extruded rod into a predetermined shape. In this forged wheel, the rim portion is subjected to plastic working such as spinning, and in some cases, the flange portion is flared. For example, in JP-A-1-273635, the rear flange portion is formed by spinning after forging. Further, in Japanese Patent Laid-Open No. 6-198382, the rear flange portion is formed by flaring after forging.
【０００４】[0004]
【発明が解決しようとする課題】鍛造ホイールは、鍛造
によって機械的強度が向上し、鋳造ホイールに比較して
薄肉軽量化できる。そのため、スピニングやフレアリン
グ等の工程が必要なことからコスト高になるにも拘ら
ず、高強度の一体構造であることを重視し、乗用車用ホ
イールの大型化，バス・トラックの軽量化に伴って生産
量が増加している。しかしながら、スピニング加工やフ
レアリング加工を省略し鍛造加工のみで所定のホイール
を製造できるようになると、鍛造製品の長所を活かした
ホイールを安価に提供できる。本発明は、このような要
求に応えるべく案出されたものであり、使用するアルミ
ニウム合金の組成，鍛造及び熱処理を特定された条件下
で組み合わせることにより、スピニング加工やフレアリ
ング加工の必要なく、全面微細な再結晶粒にコントロー
ルされた熱処理後の組織をもち、機械的性質に異方性の
ない鍛造ホイールを提供することを目的とする。また、
本発明の技術思想は、複雑形状の一般の鍛造製品につい
ても同様に適用できる。The forged wheel has improved mechanical strength by forging and can be made thinner and lighter than a cast wheel. Therefore, despite the cost increase due to the need for processes such as spinning and flaring, we attach importance to the high-strength integrated structure, and with the increase in the size of passenger car wheels and the weight reduction of buses and trucks. Production is increasing. However, if it becomes possible to manufacture a predetermined wheel only by forging without omitting the spinning process and the flaring process, it is possible to inexpensively provide a wheel that takes advantage of the advantages of the forged product. The present invention has been devised in order to meet such a requirement, by combining the composition of the aluminum alloy used, forging and heat treatment under specified conditions, without the need for spinning or flaring, It is an object of the present invention to provide a forged wheel having a structure after heat treatment in which fine recrystallized grains are controlled over the entire surface and having no anisotropy in mechanical properties. Also,
The technical idea of the present invention can be similarly applied to a general forged product having a complicated shape.
【０００５】[0005]
【課題を解決するための手段】本発明の製造方法は、そ
の目的を達成するため、Ｓｉ：０．４〜１．５重量％，
Ｃｕ：０．１５〜０．９重量％，Ｍｇ：０．８〜１．５
重量％及びＣｒ：０．０４〜０．９重量％を含み、Ｆ
ｅ：０．０５〜０．３５重量％，Ｚｎ：０．２５重量％
以下に規制したアルミニウム合金の鋳塊を均質化処理し
た後、切断し、鍛造直後の素材温度が４４０〜５００℃
となるように鍛造し、次いで５１０〜５４５℃×２〜６
時間の溶体化処理を施し、水冷後、１６０〜１９０℃×
４〜１２時間の時効処理を施すことを特徴とする。ま
た、アルミ鍛造ホイール等の鍛造製品は、前述の組成を
もつアルミニウム合金の鋳塊を均質化処理した後、切断
し、一次鍛造直後の素材温度が４４０〜５００℃となる
よう該切断鋳塊を４５０〜５００℃に加熱し、４００〜
４６０℃に保持した金型を使用して一次鍛造し、再度一
次鍛造品を５００〜５４０℃に加熱し、二次鍛造直後の
素材温度が４４０〜５００℃となるように４００〜４６
０℃に保持した金型を使用して形状の複雑な製品に二次
鍛造し、５１０〜５４５℃×２〜６時間の溶体化処理，
水冷後に１６０〜１９０℃×４〜１２時間の時効処理を
施す熱処理を行い、製品形状に機械加工することにより
製造される。使用するアルミニウム合金は、Ｔｉ：０．
００５〜０．１５重量％，Ｂ：０．０００１〜０．０１
重量％及びＭｎ：０．２〜０．６重量％含むことができ
る。更にＺｒ：０．０５〜０．２重量％を含むアルミニ
ウム合金も使用可能である。In order to achieve the object, the manufacturing method of the present invention is: Si: 0.4 to 1.5% by weight,
Cu: 0.15-0.9 wt%, Mg: 0.8-1.5
% By weight and Cr: 0.04 to 0.9% by weight, F
e: 0.05 to 0.35% by weight, Zn: 0.25% by weight
The aluminum alloy ingot regulated below is homogenized, then cut, and the material temperature immediately after forging is 440 to 500 ° C.
Forged, and then 510-545 ° C x 2-6
After solution heat treatment for a period of time and cooling with water, 160-190 ℃ ×
The aging treatment is performed for 4 to 12 hours. Further, forged products such as aluminum forged wheels are obtained by homogenizing an ingot of an aluminum alloy having the above-mentioned composition and then cutting the ingot so that the material temperature immediately after primary forging is 440 to 500 ° C. Heat to 450-500 ℃, 400-
Primary forging is performed using a die held at 460 ° C, the primary forged product is again heated to 500 to 540 ° C, and 400 to 46 so that the material temperature immediately after the secondary forging is 440 to 500 ° C.
Secondary forging into a product with a complicated shape using a mold held at 0 ° C, and solution treatment at 510 to 545 ° C for 2 to 6 hours,
It is manufactured by performing a heat treatment of aging treatment at 160 to 190 ° C. for 4 to 12 hours after water cooling, and machining into a product shape. The aluminum alloy used is Ti: 0.
005 to 0.15% by weight, B: 0.0001 to 0.01
% By weight and Mn: 0.2-0.6% by weight. Further, an aluminum alloy containing Zr: 0.05 to 0.2% by weight can also be used.
【０００６】本発明で使用するアルミニウム合金に含ま
れる合金元素及びその含有量は、次の通りである。 Ｓｉ：０．４〜１．５重量％ 析出効果によってアルミニウム合金の強度を向上させる
元素である。Ｍｇと併用添加しているので、Ｔ６処理時
の時効処理によってＭｇ2 Ｓｉ系化合物が析出し、強度
向上作用が得られる。このようなＳｉ添加の作用は、Ｓ
ｉ含有量が０．４重量％以上で顕著となる。しかし、
１．５重量％を超える多量のＳｉ含有は、Ｓｉの粒界析
出に伴う粒界脆化が生じやすく、押出し及び鍛造加工性
等を低下させる。 Ｃｕ：０．１５〜０．９重量％ マトリックスを固溶強化し、且つＴ６処理時の時効処理
によってＣｕＡｌ2及びＡｌ−Ｃｕ−Ｍｇ系金属間化合
物も析出し、Ｍｇ2 Ｓｉ析出による強度改善作用を促進
させる上で有効な合金元素であり、０．１５重量％以上
の含有量が必要とされる。しかし、０．９重量％を超え
る多量のＣｕを含有させると、焼入れ感受性が高くな
り、耐食性が劣化する。The alloying elements contained in the aluminum alloy used in the present invention and their contents are as follows. Si: 0.4 to 1.5% by weight It is an element that improves the strength of the aluminum alloy by the precipitation effect. Since it is added together with Mg, the Mg 2 Si-based compound is precipitated by the aging treatment during the T6 treatment, and the strength improving action is obtained. The action of such Si addition is S
It becomes remarkable when the i content is 0.4% by weight or more. But,
When a large amount of Si is contained in excess of 1.5% by weight, grain boundary embrittlement easily occurs due to grain boundary precipitation of Si, and extrudability and forgeability are deteriorated. Cu: 0.15 to 0.9 wt% Matrix solid solution strengthening, and CuAl 2 and Al-Cu-Mg based intermetallic compound are also precipitated by the aging treatment at the time of T6 treatment, and strength improving action by Mg 2 Si precipitation It is an alloying element effective in promoting the above-mentioned phenomenon, and a content of 0.15% by weight or more is required. However, when a large amount of Cu exceeding 0.9% by weight is contained, the quenching sensitivity becomes high and the corrosion resistance deteriorates.
【０００７】Ｍｇ：０．８〜１．５重量％ Ｔ６処理時の時効処理によりＳｉと反応しＭｇ2 Ｓｉ系
化合物となってマトリックスに析出し、アルミニウム合
金の強度を向上させる。この析出効果を得るため、０．
８重量％以上のＭｇ含有量が必要である。しかし、１．
５重量％を超えるＭｇを含有させると、析出硬化作用が
飽和するばかりでなく、焼入れ感受性が高くなる。 Ｃｒ：０．０４〜０．９重量％ Ｍｎと共同して再結晶粒の粗大化を抑制する上で重要な
合金元素であり、０．０４重量％以上の含有量が必要で
ある。Ｃｒが再結晶粒の成長を抑制する作用は、特に二
次鍛造及びその後のＴ６処理での溶体化処理時に発揮さ
れ、Ｔ６処理後の組織を全面微細な組織にする。しか
し、０．９重量％を超えてＣｒを含有させるとき、加工
性が低下する。Mg: 0.8-1.5 wt% By aging treatment during T6 treatment, it reacts with Si to form a Mg 2 Si-based compound which precipitates in the matrix and improves the strength of the aluminum alloy. In order to obtain this precipitation effect, 0.
A Mg content of 8% by weight or more is required. However, 1.
When Mg is contained in an amount of more than 5% by weight, not only the precipitation hardening effect is saturated, but also the quenching sensitivity becomes high. Cr: 0.04 to 0.9% by weight It is an important alloying element for suppressing the coarsening of recrystallized grains in cooperation with Mn, and a content of 0.04% by weight or more is necessary. The effect of Cr suppressing the growth of recrystallized grains is exerted particularly during the secondary forging and the solution treatment in the subsequent T6 treatment, and makes the structure after T6 treatment a fine structure on the whole surface. However, when Cr is contained in an amount exceeding 0.9% by weight, workability is reduced.
【０００８】Ｆｅ：０．０５〜０．３５重量％ Ｆｅは、Ａｌ−Ｆｅ−Ｓｉ系化合物となってマトリック
スに分散される。粗大なＡｌ−Ｆｅ−Ｓｉ系化合物は、
伸び及び耐食性に悪影響を与える。したがって、Ｆｅ含
有量の上限は０．３５重量％にした。一方、０．０５重
量％未満の場合は、鋳造割れが発生するので、下限を
０．０５重量％にした。０．０５〜０．３５重量％の範
囲においては、Ａｌ−Ｆｅ−Ｓｉ系化合物が鍛造品の溶
体化時に再結晶粒の粗大化を抑制する。 Ｚｎ：０．２５重量％以下 Ｚｎは、アルミスクラップ等から混入してくる不可避的
な不純物であり、少ない方が望ましい。０．２５重量％
を超えるＺｎは、応力腐食割れの原因となりやすいの
で、Ｚｎ含有量の上限を０．２５重量％に規定した。Fe: 0.05 to 0.35 wt% Fe becomes an Al-Fe-Si compound and is dispersed in the matrix. The coarse Al-Fe-Si compound is
It adversely affects elongation and corrosion resistance. Therefore, the upper limit of the Fe content is set to 0.35% by weight. On the other hand, if the content is less than 0.05% by weight, cracking in casting occurs, so the lower limit was made 0.05% by weight. In the range of 0.05 to 0.35% by weight, the Al-Fe-Si compound suppresses the coarsening of recrystallized grains during solution treatment of the forged product. Zn: 0.25 wt% or less Zn is an unavoidable impurity that is mixed in from aluminum scrap or the like, and it is desirable that the amount is small. 0.25% by weight
Zn exceeding 5 is likely to cause stress corrosion cracking, so the upper limit of the Zn content is defined as 0.25% by weight.
【０００９】Ｔｉ：０．００５〜０．１５重量％ 鋳造組織の微細化を図る上で、有効な合金元素である。
鋳造組織微細化作用は、Ｔｉ含有量が０．００５重量％
を超えると顕著になる。また、Ｔｉ添加によって組織が
微細化されたアルミニウム合金は、ビレットに鋳造割れ
等の欠陥が発生するのを抑制している。しかし、多量の
Ｔｉ含有は、アルミニウム合金の靭性を劣化させるの
で、上限を０．１５重量％に設定した。 Ｂ：０．０００１〜０．０１重量％ Ｔｉと同様に、鋳造組織の微細化に有効な合金元素であ
り、０．０００１重量％以上の含有量でその効果がみら
れる。また、Ｂ含有量の上限は、Ｔｉ含有量と同様な理
由から０．０１重量％に設定した。Ti: 0.005 to 0.15% by weight It is an effective alloying element for refining the cast structure.
Ti content is 0.005% by weight for refining the cast structure.
It becomes remarkable when it exceeds. In addition, the aluminum alloy whose structure is refined by the addition of Ti suppresses the occurrence of defects such as casting cracks in the billet. However, the inclusion of a large amount of Ti deteriorates the toughness of the aluminum alloy, so the upper limit was set to 0.15% by weight. B: 0.0001 to 0.01 wt% Like Ti, it is an alloying element effective for refining the cast structure, and its effect is observed at a content of 0.0001 wt% or more. The upper limit of the B content was set to 0.01% by weight for the same reason as the Ti content.
【００１０】Ｍｎ：０．２〜０．６重量％ Ｃｒと同様に再結晶粒の成長を抑制し、Ｔ６処理での溶
体化処理時に再結晶粒の粗大化を抑制する上で有効な合
金元素であり、０．２重量％以上含有させることが要求
される。Ｍｎが再結晶粒の成長を抑制する作用は、Ｃｒ
と併存するとき顕著な効果となって現れ、二次鍛造及び
Ｔ６処理の組織を全面微細な組織にする。しかし、０．
６重量％を超える多量のＭｎを含有させるとき、鍛造時
の加工性が悪くなる。 Ｚｒ：０．０５〜０．２重量％ Ｍｎ及びＣｒと共同して、再結晶粒の粗大化を抑制する
上で有効な合金元素であり、Ｔ６処理での溶体化処理時
に効果を発揮する。このようなＺｒ添加の作用は、０．
０５重量％以上のＺｒ含有量で顕著になる。しかし、多
量のＺｒ含有は加工性に悪影響を与えるので、Ｚｒを添
加するときは、その上限を０．２重量％とした。Mn: 0.2 to 0.6% by weight An alloy element effective in suppressing the growth of recrystallized grains similarly to Cr and suppressing coarsening of recrystallized grains during solution treatment in T6 treatment. Therefore, it is required to contain 0.2% by weight or more. The action of Mn to suppress the growth of recrystallized grains is
When it coexists, it appears as a remarkable effect, and the structure of secondary forging and T6 treatment becomes a fine structure throughout the surface. However, 0.
When a large amount of Mn exceeding 6% by weight is contained, the workability during forging becomes poor. Zr: 0.05 to 0.2% by weight It is an alloy element that is effective in suppressing coarsening of recrystallized grains in cooperation with Mn and Cr, and exerts an effect during solution treatment in T6 treatment. The effect of such Zr addition is 0.
It becomes remarkable at a Zr content of 05% by weight or more. However, if a large amount of Zr is contained, the workability is adversely affected. Therefore, when Zr is added, the upper limit is set to 0.2% by weight.
【００１１】以上のように成分調整されたアルミニウム
合金は、通常の半連続鋳造法で円柱状断面をもつビレッ
ト等の鋳塊に鋳造される。鋳塊としては、最終製品に近
い形状が好ましい。たとえば、円形状のホイールでは、
円柱状ビレットが好ましい。次に、ビレットを５２０〜
５６０℃×５〜１０時間の均質化処理を施した後、所定
の長さに切断する。 一次鍛造 一次鍛造工程に供する前に、切断された鋳造素材を加熱
炉に装入し、４５０〜５００℃に加熱する。このときの
加熱温度は、最終製品であるホイールのＴ６処理後の組
織を微細にする上で重要である。加熱温度が、４５０〜
５００℃の範囲にないと、Ｔ６処理後の再結晶組織が粗
粒化し、均一で微細な再結晶粒が得られない。加熱保持
は、温度の均一化を図るため、１時間程度行われる。The aluminum alloy whose composition has been adjusted as described above is cast into an ingot such as a billet having a cylindrical cross section by a normal semi-continuous casting method. The ingot preferably has a shape close to that of the final product. For example, with a circular wheel,
Cylindrical billets are preferred. Next, billet 520-
After subjected to homogenization treatment at 560 ° C. for 5 to 10 hours, it is cut into a predetermined length. Primary Forging Before being subjected to the primary forging step, the cut casting material is charged into a heating furnace and heated to 450 to 500 ° C. The heating temperature at this time is important for making the structure of the final product wheel after the T6 treatment fine. Heating temperature is 450 ~
If it is not in the range of 500 ° C., the recrystallized structure after T6 treatment becomes coarse and uniform and fine recrystallized grains cannot be obtained. The heating and holding is performed for about 1 hour in order to make the temperature uniform.
【００１２】一次鍛造では、金型を４００〜４６０℃に
加熱している。この金型温度は、一次鍛造中の素材が過
度に冷却することを防止する上で重要である。一次鍛造
中の素材は、金型を４００〜４６０℃に保持することに
よって、４４０〜５００℃（好ましくは、４５０〜４９
０℃）の温度範囲に維持される。４４０〜５００℃（好
ましくは、４５０〜４９０℃）の温度範囲は、Ｔ６処理
後の再結晶粒の成長を抑制する上で重要である。このと
きの加熱温度が４４０℃よりも低いと変形抵抗が増し、
鍛造が困難になるばかりでなく、後述する熱処理時に結
晶粒の粗大化が発生し易い。逆に５００℃以上の加熱温
度では、素材にバーニングが発生し易くなる。一次鍛造
では、４５０〜５００℃に加熱された素材を自由鍛造法
によって上下方向に潰し、図１に示すような形状をもつ
一次鍛造品を製造する。このとき、上下方向の変形率
［（初期のビレット長さ−鍛造後のビレット長さ）×
（初期のビレット長さ）-1×１００％］は、５０〜７０
％が好ましい。一次鍛造は、次のホイール形状に近い形
を成形するための工程であり、変形率が小さいと二次鍛
造が難しくなる。しかし、過度に大きな変形率では、鍛
造割れが生じるばかりでなく、二次鍛造による成形が困
難になる。この点、５０〜７０％の変形率でビレットを
鍛造すると、ビレットの鋳造組織が破壊され、またポロ
シティ等の鋳造欠陥が圧着されるため、高強度の最終製
品に有効な素材となる。In the primary forging, the die is heated to 400 to 460 ° C. This mold temperature is important for preventing the material during primary forging from being excessively cooled. The material during the primary forging is 440 to 500 ° C. (preferably 450 to 49 ° C.) by holding the mold at 400 to 460 ° C.
0 ° C) temperature range is maintained. The temperature range of 440 to 500 ° C (preferably 450 to 490 ° C) is important for suppressing the growth of recrystallized grains after T6 treatment. If the heating temperature at this time is lower than 440 ° C, the deformation resistance increases,
Not only is forging difficult, but coarsening of crystal grains easily occurs during the heat treatment described later. On the contrary, if the heating temperature is 500 ° C. or higher, burning easily occurs in the material. In the primary forging, a raw material heated to 450 to 500 ° C. is crushed in the vertical direction by a free forging method to manufacture a primary forged product having a shape as shown in FIG. At this time, the vertical deformation rate [(initial billet length-billet length after forging) x
(Initial billet length) -1 x 100%] is 50 to 70
% Is preferred. Primary forging is a process for forming a shape close to the next wheel shape, and if the deformation rate is small, secondary forging becomes difficult. However, if the deformation ratio is excessively large, not only forging cracks will occur, but also forming by secondary forging becomes difficult. In this respect, when the billet is forged with a deformation rate of 50 to 70%, the casting structure of the billet is destroyed and casting defects such as porosity are pressure-bonded, so that it becomes an effective material for a high-strength final product.
【００１３】二次鍛造 一次鍛造された素材は、二次鍛造に先立って５００〜５
４０℃に加熱される。加熱温度５００〜５４０℃は、通
常の熱間鍛造温度と比較すると高い設定値であるが、フ
ランジ部をもつ複雑な形状の製品を鍛造によって作製す
るのに適している。このときの加熱温度が５４０℃を超
えると、二次鍛造品に割れが発生し易くなる。逆に、５
００℃に達しない加熱温度では、Ｔ６処理した後で最終
製品の再結晶粒が粗粒化する。二次鍛造では、一次鍛造
と同様に鍛造中の鍛造品が４４０〜５００℃（好ましく
は、４８０〜４９０℃）になるように、金型温度を４０
０〜４６０℃の範囲に維持する。金型温度は高い方が望
ましいが、金型温度が４６０℃を超えると、金型の寿命
が短くなることは勿論、潤滑剤のつきも悪くなり、結果
として鍛造割れ等の欠陥が生じやすくなる。逆に、４５
０℃未満の金型温度では、二次鍛造品のＴ６処理後の再
結晶粒が粗大化する。Secondary Forging The material that has been forged for primary is 500 to 5 prior to secondary forging.
Heat to 40 ° C. The heating temperature of 500 to 540 ° C. is a high set value as compared with the normal hot forging temperature, but it is suitable for producing a product having a complicated shape having a flange portion by forging. If the heating temperature at this time exceeds 540 ° C, the secondary forged product is likely to crack. Conversely, 5
At a heating temperature that does not reach 00 ° C, the recrystallized grains of the final product become coarse after T6 treatment. In the secondary forging, the die temperature is set to 40 so that the forged product under forging is 440 to 500 ° C. (preferably 480 to 490 ° C.) as in the primary forging.
Maintain in the range of 0-460 ° C. It is desirable that the mold temperature is high, but if the mold temperature exceeds 460 ° C., the life of the mold is shortened and the lubricant is also deteriorated, resulting in defects such as forging cracks. . Conversely, 45
At a mold temperature of less than 0 ° C., the recrystallized grains of the secondary forged product after the T6 treatment become coarse.
【００１４】一次鍛造品は、５０〜７０％程度の変形率
で二次鍛造品に鍛造される。二次鍛造では、複雑な変形
をさせるため鍛造中の温度が高いほど変形抵抗が少なく
なる。具体的には、鍛造前の加熱温度を５００〜５４０
℃と高く設定するとき、変形抵抗熱の発生と併せて金型
温度が４００〜４６０℃と低くても、鍛造中の材料温度
が４８０〜４９０℃の範囲に維持される。二次鍛造工程
では、二次鍛造品を完成品に近いホイールに極力近付け
るため、図１に示すように左右に分割できる雌型を使用
する。組み立てた雌型の内部に一次鍛造品を収容し、雄
型を押し込むことにより鍛造する。これにより、複雑な
形状をもつ成形品であっても、１回の鍛造によって成形
することが可能となり、しかも成形品の型抜きも容易に
なる。そのため、リム部をスピニング加工で成形した
り、フランジ部をフレアリング加工等の曲げ加工で成形
することが不要になり、結果として製造コストの低減が
図られる。また、本発明では鍛造温度を比較的高く設定
しているので、これによっても複雑形状の成形が容易に
行われる。更に、この技術思想は、他の複雑形状な一般
の鍛造品についても同様に適用することが可能である。The primary forged product is forged into a secondary forged product with a deformation rate of about 50 to 70%. In the secondary forging, since the deformation is complicated, the higher the temperature during forging, the less the deformation resistance. Specifically, the heating temperature before forging is set to 500 to 540.
When the temperature is set to be as high as 0 ° C, the material temperature during forging is maintained in the range of 480 to 490 ° C even if the die temperature is as low as 400 to 460 ° C together with the generation of deformation resistance heat. In the secondary forging step, in order to bring the secondary forged product as close as possible to the wheel close to the finished product, a female die that can be divided into left and right as shown in FIG. 1 is used. The primary forged product is housed inside the assembled female die and the male die is pushed in for forging. As a result, even a molded product having a complicated shape can be molded by a single forging, and the molded product can be easily demolded. Therefore, there is no need to form the rim portion by spinning or the flange portion by bending such as flaring, and as a result, the manufacturing cost can be reduced. Further, in the present invention, since the forging temperature is set to be relatively high, molding of a complicated shape can be easily performed also by this. Further, this technical idea can be similarly applied to other general forged products having complicated shapes.
【００１５】熱処理 完成品に近い二次鍛造品は、５１０〜５４５℃×２〜６
時間加熱し、水冷した後で１６０〜１９０℃×４〜１２
時間加熱する時効処理、いわゆるＴ６処理が施される。
５１０〜５４５℃×２〜６時間の加熱は、Ｍｇ，Ｓｉ，
Ｃｕ等を固溶させる溶体化処理である。固溶したＭｇ，
Ｓｉは、後の時効工程でＭｇ2 Ｓｉとなって析出し、強
度を確保する。Ｃｕは、固溶によってマトリックスを強
化すると共に、一部がＣｕＡｌ2 及びＡｌ−Ｃｕ−Ｍｇ
系の金属間化合物として時効処理時に析出し、強度を更
に向上させる。他方、Ｃｒ，Ｍｎ，Ｚｒ等の合金成分
は、ビレットの均質化処理によってすでに微細な金属間
化合物となって析出しており、溶体化処理によってもマ
トリックスに固溶せず、鍛造後の再結晶粒粗大化を防止
する働きを呈するものと考えられる。これら析出物の作
用は、鍛造温度や加工度により析出物の形態が異なって
おり、ある種の特定形態や特定分布の析出物が再結晶粒
の粗大化を阻止しているものと推察される。鍛造中の素
材温度が４４０〜５００℃付近のとき、熱間加工中に導
入された歪みが冷却の途上で解放され、溶体化処理前
（鍛造製品）中に蓄積される歪みエネルギーが小さくな
る。このため、溶体化処理時に結晶成長に利用できるエ
ネルギーが小さく、Ｍｎ，Ｃｒ，Ｚｒ系粒子により再結
晶粒の粗大化を阻止できる。一方、４４０℃よりも低い
温度で鍛造を行うと、冷却終了後にも鍛造時に導入され
た歪が多く残存し、これが溶体化処理時の再結晶粒の成
長のエネルギーとなり、Ｍｎ，Ｃｒ，Ｚｒ系粒子が存在
しても、その粗大化を抑制することが不可能となる。逆
に５００℃よりも高い温度で鍛造すると、バーニングの
発生により健全な製品ができない。溶体化処理された製
品は、水焼入れされ、１６０〜１９０℃で４〜１２時間
加熱する時効処理が施される。この時効処理によりＭｇ
2 Ｓｉ，ＣｕＡｌ2 ，Ａｌ−Ｃｕ−Ｍｇ系金属間化合物
等が析出し、マトリックスの強度が確保される。 機械加工 熱処理された製品は、各部の板厚調整やネジ孔加工等の
ために機械加工される。機械加工された最終製品は、ホ
イール等に仕上げられる。Heat treatment A secondary forged product close to the finished product is 510 to 545 ° C. × 2 to 6
After heating for an hour and cooling with water, 160-190 ° C x 4-12
An aging treatment of heating for a time, so-called T6 treatment is performed.
Heating at 510 to 545 ° C. for 2 to 6 hours is performed with Mg, Si,
This is a solution heat treatment for solid solution of Cu and the like. Solid solution Mg,
Si precipitates as Mg 2 Si in the subsequent aging step and secures the strength. Cu strengthens the matrix by solid solution, and partly CuAl 2 and Al-Cu-Mg.
Precipitates as an intermetallic compound of the system during aging treatment and further improves the strength. On the other hand, alloy components such as Cr, Mn, and Zr have already been precipitated as fine intermetallic compounds by the homogenization treatment of the billet, do not form a solid solution in the matrix even by solution treatment, and recrystallize after forging. It is considered to have a function of preventing grain coarsening. The effect of these precipitates is that the morphology of the precipitates differs depending on the forging temperature and the degree of processing, and it is speculated that certain specific morphologies and specific distributions of precipitates prevent coarsening of recrystallized grains. . When the material temperature during forging is around 440 to 500 ° C., the strain introduced during hot working is released during cooling, and the strain energy accumulated before the solution treatment (forged product) becomes small. Therefore, the energy that can be used for crystal growth during solution treatment is small, and coarsening of recrystallized grains can be prevented by Mn, Cr, and Zr-based grains. On the other hand, when forging is performed at a temperature lower than 440 ° C., a large amount of strain introduced during forging remains after cooling, and this serves as energy for the growth of recrystallized grains during solution treatment, and the Mn, Cr, Zr-based Even if particles exist, it becomes impossible to suppress the coarsening. On the contrary, if forged at a temperature higher than 500 ° C, a sound product cannot be produced due to the occurrence of burning. The solution-treated product is water-quenched and subjected to an aging treatment of heating at 160 to 190 ° C. for 4 to 12 hours. By this aging treatment, Mg
2 Si, CuAl 2, Al- Cu-Mg intermetallic compounds are precipitated, the strength of the matrix is ensured. Machining The heat-treated product is machined to adjust the plate thickness of each part and to process screw holes. The final machined product is finished into wheels and the like.
【００１６】[0016]
実施例１：表１に示す成分・組成をもつアルミニウム合
金を半連続鋳造し、直径２４０ｍｍのビレットを鋳造し
た。このビレットを５４０℃×８時間の均質化処理を施
した後、直径３５ｍｍ，長さ９０ｍｍのテスト用鍛造素
材を切り出した。Example 1: An aluminum alloy having the components and compositions shown in Table 1 was semi-continuously cast into a billet having a diameter of 240 mm. After subjecting this billet to homogenization treatment at 540 ° C. for 8 hours, a test forging material having a diameter of 35 mm and a length of 90 mm was cut out.
【００１７】 [0017]
【００１８】得られた鍛造素材に４８０℃×１時間の均
熱処理を施した後、直ちに金型温度４３０℃，素材各部
の変形率として平均変形率５０％で長さ方向に対して垂
直な方向から鍛造し、図２の二次成形品に近い形状にま
ず成形した。この一次鍛造品を４００℃及び５２０℃に
１時間加熱した後、金型温度４３０℃，平均変形率７０
％で長さ方向に対して垂直な方向から二次鍛造し、図２
に示す二次鍛造品の形状に鍛造した。二次鍛造直後の素
材温度は、４００℃加熱のときは３８０℃，５２０℃加
熱のときは４９０℃であった。二次鍛造素材の上下方向
断面のマクロ組織を観察すると、二次鍛造温度に関係な
く、図３，図４に示すように何れの鍛造素材も全面均一
で微細な組織をもっていた。各二次鍛造品に５３０℃×
３時間→水焼入れの処理を施した後、上下方向の断面マ
クロ組織を観察した。マクロ組織は、二次鍛造温度が４
００℃のとき、図５に示すように上下方向中央部を中心
にして再結晶粒が成長した組織となっていた。これに対
し、二次鍛造温度が５２０℃のものでは、図６に示すよ
うに全面が微細な再結晶組織となっており、再結晶粒の
成長が検出されなかった。図５から明らかなように、二
次鍛造温度が４００℃の場合、中心部の再結晶粒は粗大
化している。これは、中心部の変形率が高いことにも原
因があり、変形率が高いと、鍛造温度が低い場合に蓄積
される歪みエネルギーが大きく、再結晶粒が粗大化する
ことを示している。他方、試料Ｎo.２，３は、試料Ｎo.
１に比較して中心部で再結晶粒の粗大化が進行していな
い。これは、Ｃｒの効果を狙った試料番号１に比べ、試
料Ｎo.２ではＣｒ＋Ｍｎを、試料Ｎo.３ではＣｒ＋Ｍｎ
＋Ｚｒを複合添加した効果が顕著に発現されていること
を示している。なお、一次鍛造温度が４００℃で二次鍛
造温度が５２０℃の場合、及び一次鍛造温度が４００℃
で二次鍛造温度が４００℃の場合には、何れも溶体化処
理後の再結晶組織は、中心部が粗大化していた。これに
より、鍛造中の温度が低い工程が入ると、溶体化処理に
より再結晶が粗大化することが判る。なお、時効処理で
は、再結晶粒が粗大化していなかった。The obtained forged material was subjected to a soaking treatment at 480 ° C. for 1 hour, and immediately thereafter, at a mold temperature of 430 ° C., the deformation ratio of each part of the material was 50%, and the average deformation ratio was 50%. Then, it was first forged into a shape close to the secondary molded product of FIG. After heating this primary forged product at 400 ° C. and 520 ° C. for 1 hour, the mold temperature was 430 ° C. and the average deformation rate was 70.
Secondary forging from the direction perpendicular to the length direction in%, Fig. 2
Forged into the shape of the secondary forged product shown in. The material temperature immediately after the secondary forging was 380 ° C. when heating at 400 ° C. and 490 ° C. when heating at 520 ° C. When the macrostructure of the vertical cross section of the secondary forging material was observed, all the forging materials had a uniform and fine structure as shown in FIGS. 3 and 4, regardless of the secondary forging temperature. 530 ℃ for each secondary forging
After the water quenching treatment for 3 hours, the vertical cross-section macrostructure was observed. The macrostructure has a secondary forging temperature of 4
At 00 ° C., as shown in FIG. 5, the recrystallized grains were grown around the center in the vertical direction. On the other hand, when the secondary forging temperature was 520 ° C., the entire surface had a fine recrystallized structure as shown in FIG. 6, and the growth of recrystallized grains was not detected. As is clear from FIG. 5, when the secondary forging temperature is 400 ° C., the recrystallized grains in the central portion are coarse. This is also due to the high deformation rate of the central portion, and when the deformation rate is high, the strain energy accumulated when the forging temperature is low is large and the recrystallized grains become coarse. On the other hand, sample Nos. 2 and 3 are sample No.
Compared with No. 1, coarsening of recrystallized grains did not proceed in the central portion. Compared with the sample No. 1 aiming at the effect of Cr, the sample No. 2 contained Cr + Mn and the sample No. 3 contained Cr + Mn.
It is shown that the effect of the combined addition of + Zr is remarkably exhibited. In addition, when the primary forging temperature is 400 ° C. and the secondary forging temperature is 520 ° C., and the primary forging temperature is 400 ° C.
When the secondary forging temperature was 400 ° C., the recrystallized structure after the solution treatment was coarse in the central portion in all cases. From this, it is understood that when a process in which the temperature during forging is low is included, recrystallization is coarsened by the solution treatment. In the aging treatment, the recrystallized grains were not coarsened.
【００１９】実施例２：表１に示した各組成のアルミニ
ウム合金から直径２４０ｍｍのビレットを半連続鋳造法
で製造し、５４０℃×８時間の均質化処理を施した後、
直径２４０ｍｍ，長さ４８０ｍｍのホイール用鍛造素材
をビレットから切り出した。鍛造用素材に４８０℃×１
時間の均熱処理を施し、上下方向に一次鍛造して、直径
４２０ｍｍ，厚さ１７０ｍｍの一次鍛造品を製造した。
このときの変形率は６５％，金型の予熱温度は４１０℃
であった。一次鍛造品を５２０℃に加熱し、割り型の中
にセットした後、変形率８０％で二次鍛造した。二次鍛
造時の金型温度は、雄型を４５２℃，雌型を４３３℃に
設定した。鍛造前に５２０℃の高温に加熱されているこ
とから、塑性変形が円滑に行われ、リム部の湾曲した形
状も容易に成形することができた。Example 2 A billet having a diameter of 240 mm was produced from the aluminum alloys having the respective compositions shown in Table 1 by a semi-continuous casting method, and after homogenizing treatment at 540 ° C. for 8 hours,
A forging material for wheels having a diameter of 240 mm and a length of 480 mm was cut out from the billet. 480 ℃ × 1 for forging material
After soaking for an hour, primary forging was performed in the vertical direction to produce a primary forged product having a diameter of 420 mm and a thickness of 170 mm.
The deformation rate at this time is 65%, and the die preheating temperature is 410 ° C.
Met. The primary forged product was heated to 520 ° C., set in a split mold, and then secondary forged with a deformation rate of 80%. The mold temperature during the secondary forging was set to 452 ° C for the male mold and 433 ° C for the female mold. Since it was heated to a high temperature of 520 ° C. before forging, plastic deformation was smoothly performed, and the curved shape of the rim portion could be easily formed.
【００２０】二次鍛造品に５４０℃×２時間の溶体化処
理を施した後、水焼入れし、１８０℃×６時間の時効処
理を施し、放冷した。Ｔ６処理終了後の二次鍛造品を機
械加工し、ネジ部，飾り穴部，断面厚さ等を調整加工
し、最終製品である図７のホイールに仕上げた。このホ
イールからディスク部及びリム部を切り出し、Ｔ６処理
後のマクロ組織及び機械的性質を調査した。調査結果を
表２に示す。なお、表２では、組成が試料Ｎo.１のアル
ミニウム合金について一次鍛造温度及び二次鍛造温度を
変化させ、Ｔ６処理を本発明に従った条件下で行ったも
のを比較例として示した。The secondary forged product was subjected to solution treatment at 540 ° C. for 2 hours, then water-quenched, subjected to aging treatment at 180 ° C. for 6 hours, and allowed to cool. The secondary forged product after the T6 treatment was machined to adjust the screw portion, the decorative hole portion, the cross-sectional thickness, etc., and finished into the final product wheel of FIG. 7. The disc portion and the rim portion were cut out from this wheel, and the macrostructure and mechanical properties after T6 treatment were investigated. Table 2 shows the survey results. In Table 2, as a comparative example, the aluminum alloy having the composition No. 1 was subjected to T6 treatment under the conditions according to the present invention while changing the primary forging temperature and the secondary forging temperature.
【００２１】 [0021]
【００２２】表２に示されているように、本発明に従っ
たものでは、ディスク部及びリム部共に引張強さが比較
例に比べて大幅に上昇しており、耐力も向上していた。
また、伸びは減少していた。これに対し、比較例では、
再結晶粒が成長していることから引張強さが減少してお
り、伸びが大きくなっていた。引張試験に供した試料
は、製品の長手方向に採取しているので、引張方向と再
結晶粒の成長方向が一致している。そのため、伸びが大
きくでたものと考えられるが、材料に異方性があること
から好ましいことではない。この点、本発明に従った試
験片では、全面が均一で微細な再結晶組織となっている
ので、機械的性質に異方性がなく、信頼性の高いホイー
ルとなる。また、再結晶粒が粗大化した位置は、比較的
変形率の高い部分であった。このような機械的性質の相
違は、マクロ組織の如何によるものである。たとえばホ
イールＮo.１のリム部は、マクロ組織を図８に示すよう
に、全面が均一で微細な再結晶組織をもっていた。これ
に対し、ホイールＮo.４は、図９に示すようにディスク
部及びリム部共に再結晶粒が粗大化した組織になってい
た。また、ホイールＮo.５も、図１０に示すように一部
に粗大化した再結晶粒が検出された。As shown in Table 2, according to the present invention, the tensile strengths of both the disc portion and the rim portion were significantly higher than those of the comparative examples, and the yield strength was also improved.
Also, the growth was decreasing. In contrast, in the comparative example,
Since the recrystallized grains grew, the tensile strength decreased and the elongation increased. Since the sample used for the tensile test is taken in the longitudinal direction of the product, the tensile direction and the recrystallized grain growth direction are the same. Therefore, it is considered that the elongation was large, but it is not preferable because the material has anisotropy. In this respect, since the test piece according to the present invention has a uniform and fine recrystallized structure on the entire surface, the wheel has high anisotropy in mechanical properties and high reliability. Further, the position where the recrystallized grains became coarse was a portion having a relatively high deformation rate. This difference in mechanical properties is due to the macrostructure. For example, as shown in FIG. 8, the rim portion of the wheel No. 1 has a macro structure as shown in FIG. On the other hand, the wheel No. 4 had a structure in which recrystallized grains were coarsened in both the disc portion and the rim portion as shown in FIG. Further, in the wheel No. 5 as well, as shown in FIG. 10, partially recrystallized grains were detected.
【００２３】[0023]
【発明の効果】以上に説明したように、本発明において
は、成分・組成及び鍛造を特定条件下で組み合わせるこ
とにより、溶体化処理後に再結晶粒の粗大化を抑制し、
全面が均一で微細な再結晶組織としている。そのため、
機械的性質に異方性がなく、信頼性の高い高強度鍛造ホ
イールが得られる。また、この方法は、スピニング加工
やフレアリング加工を必要とせず、鍛造のみで必要形状
に成形できるため、製造コストの低減も図られる。As described above, in the present invention, by combining the components / compositions and forging under specific conditions, coarsening of recrystallized grains after solution treatment is suppressed,
The entire surface is uniform and has a fine recrystallized structure. for that reason,
Highly reliable high-strength forged wheels with no anisotropy in mechanical properties can be obtained. In addition, this method does not require spinning or flaring and can be formed into a required shape only by forging, so that the manufacturing cost can be reduced.
【図１】 本発明に従った製造工程を示すフローFIG. 1 is a flow chart showing a manufacturing process according to the present invention.
【図２】 実施例１で製造したテスト用二次鍛造品FIG. 2 Secondary forging for test manufactured in Example 1
【図３】 二次鍛造温度４００℃の二次鍛造を終了した
テスト用二次鍛造品のマクロ組織を示す写真FIG. 3 is a photograph showing a macrostructure of a test forged product that has undergone secondary forging at a secondary forging temperature of 400 ° C.
【図４】 二次鍛造温度５２０℃の二次鍛造を終了した
テスト用二次鍛造品のマクロ組織を示す写真FIG. 4 is a photograph showing the macrostructure of a test forged product that has undergone secondary forging at a secondary forging temperature of 520 ° C.
【図５】 二次鍛造温度４００℃で二次鍛造した製品を
溶体化処理したテスト用二次鍛造品のマクロ組織を示す
写真FIG. 5 is a photograph showing a macrostructure of a test secondary forged product obtained by subjecting a product secondary forged at a secondary forging temperature of 400 ° C. to a solution treatment.
【図６】 二次鍛造温度５２０℃で二次鍛造した製品を
溶体化処理したテスト用二次鍛造品のマクロ組織を示す
写真FIG. 6 is a photograph showing a macrostructure of a test secondary forged product obtained by subjecting a product secondary forged at a secondary forging temperature of 520 ° C. to a solution treatment.
【図７】 実施例２で製造したホイールの断面図FIG. 7 is a cross-sectional view of the wheel manufactured in Example 2.
【図８】 ホイールＮo.１のホイール断面のマクロ組織
を示す写真FIG. 8 is a photograph showing a macro structure of a wheel cross section of wheel No. 1.
【図９】 ホイールＮo.４のホイール断面のマクロ組織
を示す写真FIG. 9 is a photograph showing a macro structure of a wheel cross section of wheel No. 4.
【図１０】 ホイールＮo.５のホイール断面のマクロ組
織を示す写真FIG. 10 is a photograph showing a macro structure of a wheel cross section of wheel No. 5.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 小林 重幸 静岡県庵原郡蒲原町蒲原１丁目34番１号 日本軽金属株式会社グループ技術センター 内 (72)発明者 山田 達 静岡県庵原郡蒲原町蒲原１丁目34番１号 日本軽金属株式会社グループ技術センター 内 (72)発明者 柚木 裕嗣 静岡県庵原郡蒲原町蒲原１丁目34番１号 日本軽金属株式会社グループ技術センター 内 ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Shigeyuki Kobayashi 1-34-1, Kambara, Kambara-cho, Anbara-gun, Shizuoka Prefecture, Japan Group Technology Center, Japan Light Metal Co., Ltd. 34-1-1, Nippon Light Metal Co., Ltd. Group Technical Center (72) Inventor Yuuji Yuki, 1-34-1 Kambara, Kambara-cho, Anbara-gun, Shizuoka Prefecture
Claims (4)
０．１５〜０．９重量％，Ｍｇ：０．８〜１．５重量％
及びＣｒ：０．０４〜０．９重量％を含み、Ｆｅ：０．
０５〜０．３５重量％，Ｚｎ：０．２５重量％以下に規
制したアルミニウム合金の鋳塊を均質化処理した後、切
断し、鍛造直後の素材温度が４４０〜５００℃となるよ
うに鍛造し、次いで５１０〜５４５℃×２〜６時間の溶
体化処理を施し、水冷後、１６０〜１９０℃×４〜１２
時間の時効処理を施すことにより溶体化処理時の再結晶
粒の粗大成長を抑制したアルミ鍛造製品の製造方法。1. Si: 0.4 to 1.5% by weight, Cu:
0.15-0.9 wt%, Mg: 0.8-1.5 wt%
And Cr: 0.04 to 0.9 wt%, Fe: 0.
Aluminum alloy ingot regulated to 05 to 0.35 wt% and Zn: 0.25 wt% or less is homogenized, cut, and forged so that the material temperature immediately after forging is 440 to 500 ° C. Then, solution treatment is performed at 510 to 545 ° C. for 2 to 6 hours, and after water cooling, 160 to 190 ° C. for 4 to 12
A method for manufacturing an aluminum forged product in which coarse crystallization of recrystallized grains during solution treatment is suppressed by performing time aging treatment.
０．１５〜０．９重量％，Ｍｇ：０．８〜１．５重量％
及びＣｒ：０．０４〜０．９重量％を含み、Ｆｅ：０．
０５〜０．３５重量％，Ｚｎ：０．２５重量％以下に規
制したアルミニウム合金の鋳塊を均質化処理した後、切
断し、一次鍛造直後の素材温度が４４０〜５００℃とな
るよう該切断鋳塊を４５０〜５００℃に加熱し、４００
〜４６０℃に保持した金型を使用して一次鍛造し、再度
一次鍛造品を５００〜５４０℃に加熱し、二次鍛造直後
の素材温度が４４０〜５００℃となるように４００〜４
６０℃に保持した金型を使用して形状の複雑な製品に二
次鍛造し、５１０〜５４５℃×２〜６時間の溶体化処
理、水冷後に１６０〜１９０℃×４〜１２時間の時効処
理を施す熱処理を行うアルミ鍛造製品の製造方法。2. Si: 0.4 to 1.5% by weight, Cu:
0.15-0.9 wt%, Mg: 0.8-1.5 wt%
And Cr: 0.04 to 0.9 wt%, Fe: 0.
Aluminum alloy ingot regulated to 05 to 0.35 wt% and Zn: 0.25 wt% or less is homogenized and then cut, and the cutting is performed so that the material temperature immediately after primary forging is 440 to 500 ° C. The ingot is heated to 450 to 500 ° C., and 400
Primary forging is performed using a mold held at 460 ° C., the primary forged product is heated again to 500 to 540 ° C., and 400 to 4 so that the material temperature immediately after the secondary forging is 440 to 500 ° C.
Secondary forging into a product with a complicated shape using a mold held at 60 ° C, solution treatment at 510 to 545 ° C for 2 to 6 hours, and aging treatment at 160 to 190 ° C for 4 to 12 hours after water cooling. A method for manufacturing an aluminum forged product, in which heat treatment is performed.
％，Ｂ：０．０００１〜０．０１重量％及びＭｎ：０．
２〜０．６重量％を含むアルミニウム合金を使用する請
求項１又は２記載のアルミ鍛造製品の製造方法。3. Further, Ti: 0.005 to 0.15% by weight, B: 0.0001 to 0.01% by weight, and Mn: 0.
The method for manufacturing an aluminum forged product according to claim 1, wherein an aluminum alloy containing 2 to 0.6% by weight is used.
むアルミニウム合金を使用する請求項１〜３の何れかに
記載のアルミ鍛造製品の製造方法。4. The method for manufacturing an aluminum forged product according to claim 1, wherein an aluminum alloy further containing Zr: 0.05 to 0.2% by weight is used.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP8083330A JPH09249951A (en) | 1996-03-12 | 1996-03-12 | Production of aluminum forged product having fine structure |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP8083330A JPH09249951A (en) | 1996-03-12 | 1996-03-12 | Production of aluminum forged product having fine structure |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH09249951A true JPH09249951A (en) | 1997-09-22 |
Family
ID=13799429
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP8083330A Pending JPH09249951A (en) | 1996-03-12 | 1996-03-12 | Production of aluminum forged product having fine structure |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH09249951A (en) |
Cited By (24)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2002195759A (en) * | 2000-12-27 | 2002-07-10 | Asahi Tec Corp | Multi-layer heat treatment furnace, heat treatment apparatus, and heat treatment method |
| JP2002348630A (en) * | 2001-05-18 | 2002-12-04 | Nissan Motor Co Ltd | Aluminum forged component and manufacturing method therefor |
| JP2003001357A (en) * | 2001-06-20 | 2003-01-07 | Asahi Tec Corp | Manufacturing method of aluminum cast and forged product |
| JP2007210017A (en) * | 2006-02-10 | 2007-08-23 | Nissan Motor Co Ltd | Forged road wheel made of aluminum alloy, and manufacturing method therefor |
| EP2003219A2 (en) * | 2006-03-31 | 2008-12-17 | Kabushiki Kaisha Kobe Seiko Sho | Aluminum alloy forging member and process for producing the same |
| JP2009079299A (en) * | 2008-10-31 | 2009-04-16 | Showa Denko Kk | Automotive parts |
| JP2009274135A (en) * | 2008-04-16 | 2009-11-26 | Washi Kosan Co Ltd | Forged wheel made of light alloy and method for producing the same |
| WO2010026779A1 (en) * | 2008-09-05 | 2010-03-11 | ワシ興産株式会社 | Method for producing wheel and wheel |
| WO2010067626A1 (en) * | 2008-12-11 | 2010-06-17 | ワシマイヤー株式会社 | Wheel and method of manufaturing thereof |
| WO2010067465A1 (en) * | 2008-12-11 | 2010-06-17 | ワシマイヤー株式会社 | Forged billet and wheel |
| JP2011068994A (en) * | 2010-11-05 | 2011-04-07 | Showa Denko Kk | Aluminum alloy ingot for plastic working |
| KR101044899B1 (en) * | 2009-09-11 | 2011-06-28 | 주식회사 센트랄 | Forging method for aluminum |
| WO2011096212A1 (en) * | 2010-02-02 | 2011-08-11 | ワシ興産株式会社 | Forged billet, process for production of forged billet, and process for production of wheel |
| WO2011096178A1 (en) * | 2010-02-02 | 2011-08-11 | ワシ興産株式会社 | Forged billet, wheel made from light metal, and processes for production of those products |
| JP2012036504A (en) * | 2011-09-29 | 2012-02-23 | Showa Denko Kk | Method for manufacturing aluminum alloy ingot for plastic working, method for manufacturing aluminum alloy plastic worked article, and aluminum alloy plastic worked article |
| JP2014025149A (en) * | 2013-09-10 | 2014-02-06 | Showa Denko Kk | Aluminum alloy plastic worked product |
| CN103658475A (en) * | 2013-11-28 | 2014-03-26 | 江西洪都航空工业集团有限责任公司 | Airplane two-seater canopy framework integral-forging method |
| EP2811042A4 (en) * | 2012-02-02 | 2016-06-08 | Kobe Steel Ltd | Forged aluminum alloy material and method for producing same |
| CN106623743A (en) * | 2016-12-01 | 2017-05-10 | 西北工业大学 | GH4738 alloy die forging and preparation method thereof |
| CN108555223A (en) * | 2017-12-13 | 2018-09-21 | 陕西宏远航空锻造有限责任公司 | A kind of GH901 alloys diskware manufacturing method |
| CN109622844A (en) * | 2018-12-25 | 2019-04-16 | 昆山惠众机电有限公司 | A kind of forging technology of the pump housing for vent gas treatment |
| CN110180981A (en) * | 2019-06-25 | 2019-08-30 | 航桥新材料科技（滨州）有限公司 | A kind of method of aluminium alloy spring hydraulic operating mechanism working cylinder forging molding |
| US10646914B2 (en) | 2018-01-12 | 2020-05-12 | Accuride Corporation | Aluminum alloys for applications such as wheels and methods of manufacture |
| CN111218591A (en) * | 2020-02-28 | 2020-06-02 | 福建祥鑫股份有限公司 | Preparation method of high-strength and high-toughness 7XXX aluminum alloy section for new energy automobile power system |
-
1996
- 1996-03-12 JP JP8083330A patent/JPH09249951A/en active Pending
Cited By (39)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2002195759A (en) * | 2000-12-27 | 2002-07-10 | Asahi Tec Corp | Multi-layer heat treatment furnace, heat treatment apparatus, and heat treatment method |
| JP4699605B2 (en) * | 2000-12-27 | 2011-06-15 | 旭テック株式会社 | Multi-layer heat treatment furnace, heat treatment apparatus, and heat treatment method |
| JP2002348630A (en) * | 2001-05-18 | 2002-12-04 | Nissan Motor Co Ltd | Aluminum forged component and manufacturing method therefor |
| JP2003001357A (en) * | 2001-06-20 | 2003-01-07 | Asahi Tec Corp | Manufacturing method of aluminum cast and forged product |
| JP2007210017A (en) * | 2006-02-10 | 2007-08-23 | Nissan Motor Co Ltd | Forged road wheel made of aluminum alloy, and manufacturing method therefor |
| EP2003219A4 (en) * | 2006-03-31 | 2011-05-18 | Kobe Steel Ltd | Aluminum alloy forging member and process for producing the same |
| EP2003219A2 (en) * | 2006-03-31 | 2008-12-17 | Kabushiki Kaisha Kobe Seiko Sho | Aluminum alloy forging member and process for producing the same |
| US8152940B2 (en) | 2006-03-31 | 2012-04-10 | Kobe Steel, Ltd. | Aluminum alloy forging member and process for producing the same |
| JP2009274135A (en) * | 2008-04-16 | 2009-11-26 | Washi Kosan Co Ltd | Forged wheel made of light alloy and method for producing the same |
| WO2010026778A1 (en) * | 2008-09-05 | 2010-03-11 | ワシ興産株式会社 | Forged billet and wheel |
| WO2010026780A1 (en) * | 2008-09-05 | 2010-03-11 | ワシ興産株式会社 | Method for producing wheel by extrusion and wheel |
| WO2010026779A1 (en) * | 2008-09-05 | 2010-03-11 | ワシ興産株式会社 | Method for producing wheel and wheel |
| JP2009079299A (en) * | 2008-10-31 | 2009-04-16 | Showa Denko Kk | Automotive parts |
| WO2010067626A1 (en) * | 2008-12-11 | 2010-06-17 | ワシマイヤー株式会社 | Wheel and method of manufaturing thereof |
| WO2010067465A1 (en) * | 2008-12-11 | 2010-06-17 | ワシマイヤー株式会社 | Forged billet and wheel |
| JP2010137257A (en) * | 2008-12-11 | 2010-06-24 | Washimaiyaa Kk | Forged billet and wheel |
| JP4562810B2 (en) * | 2008-12-11 | 2010-10-13 | ワシマイヤー株式会社 | Wheel and manufacturing method thereof |
| JPWO2010067626A1 (en) * | 2008-12-11 | 2012-05-17 | ワシマイヤー株式会社 | Wheel and manufacturing method thereof |
| KR101044899B1 (en) * | 2009-09-11 | 2011-06-28 | 주식회사 센트랄 | Forging method for aluminum |
| WO2011096212A1 (en) * | 2010-02-02 | 2011-08-11 | ワシ興産株式会社 | Forged billet, process for production of forged billet, and process for production of wheel |
| WO2011096178A1 (en) * | 2010-02-02 | 2011-08-11 | ワシ興産株式会社 | Forged billet, wheel made from light metal, and processes for production of those products |
| JP2011177785A (en) * | 2010-02-02 | 2011-09-15 | Washi Kosan Co Ltd | Forged billet, wheel made from light metal, and processes for production of those products |
| JP2011068994A (en) * | 2010-11-05 | 2011-04-07 | Showa Denko Kk | Aluminum alloy ingot for plastic working |
| JP2012036504A (en) * | 2011-09-29 | 2012-02-23 | Showa Denko Kk | Method for manufacturing aluminum alloy ingot for plastic working, method for manufacturing aluminum alloy plastic worked article, and aluminum alloy plastic worked article |
| EP2811042A4 (en) * | 2012-02-02 | 2016-06-08 | Kobe Steel Ltd | Forged aluminum alloy material and method for producing same |
| EP2811042B1 (en) | 2012-02-02 | 2017-06-21 | Kabushiki Kaisha Kobe Seiko Sho | ALUMINiUM ALLOY forged MATERIAL AND METHOD FOR manufacturING the SAME |
| JP2014025149A (en) * | 2013-09-10 | 2014-02-06 | Showa Denko Kk | Aluminum alloy plastic worked product |
| CN103658475A (en) * | 2013-11-28 | 2014-03-26 | 江西洪都航空工业集团有限责任公司 | Airplane two-seater canopy framework integral-forging method |
| CN106623743A (en) * | 2016-12-01 | 2017-05-10 | 西北工业大学 | GH4738 alloy die forging and preparation method thereof |
| CN106623743B (en) * | 2016-12-01 | 2018-08-14 | 西北工业大学 | A kind of GH4738 alloy die forgings and preparation method thereof |
| CN108555223A (en) * | 2017-12-13 | 2018-09-21 | 陕西宏远航空锻造有限责任公司 | A kind of GH901 alloys diskware manufacturing method |
| US10646914B2 (en) | 2018-01-12 | 2020-05-12 | Accuride Corporation | Aluminum alloys for applications such as wheels and methods of manufacture |
| CN111770840A (en) * | 2018-01-12 | 2020-10-13 | 阿库莱德公司 | Aluminum wheel and method of manufacture |
| US11420249B2 (en) | 2018-01-12 | 2022-08-23 | Accuride Corporation | Aluminum wheels and methods of manufacture |
| CN111770840B (en) * | 2018-01-12 | 2023-04-07 | 阿库莱德公司 | Aluminum wheel and method of manufacture |
| CN109622844A (en) * | 2018-12-25 | 2019-04-16 | 昆山惠众机电有限公司 | A kind of forging technology of the pump housing for vent gas treatment |
| CN110180981A (en) * | 2019-06-25 | 2019-08-30 | 航桥新材料科技（滨州）有限公司 | A kind of method of aluminium alloy spring hydraulic operating mechanism working cylinder forging molding |
| CN111218591A (en) * | 2020-02-28 | 2020-06-02 | 福建祥鑫股份有限公司 | Preparation method of high-strength and high-toughness 7XXX aluminum alloy section for new energy automobile power system |
| CN111218591B (en) * | 2020-02-28 | 2020-09-15 | 福建祥鑫股份有限公司 | Preparation method of high-strength and high-toughness 7XXX aluminum alloy section for new energy automobile power system |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JPH09249951A (en) | Production of aluminum forged product having fine structure | |
| CA2797446C (en) | Damage tolerant aluminium material having a layered microstructure | |
| JPH06172949A (en) | Member made of magnesium alloy and its production | |
| JP7044863B2 (en) | Al-Mg-Si based aluminum alloy material | |
| JPH0860285A (en) | Bumper reinforcement made of aluminum alloy and its production | |
| JP5233607B2 (en) | Aluminum alloy plate excellent in formability and method for producing the same | |
| JPH111737A (en) | Heat treated type 7000 series aluminum alloy with excellent corrosion resistance and high strength, and its production | |
| TW202031909A (en) | Aluminum alloy forged wheel, method of making the same, and billet for forming forged wheel having light weight, toughness, high rigidity and high thermal resistance | |
| JP4822324B2 (en) | Aluminum alloy forged road wheel and manufacturing method thereof | |
| JP4774630B2 (en) | Manufacturing method of aluminum forged parts | |
| JPH11286758A (en) | Production of forged product using aluminum casting material | |
| JPH09249949A (en) | Production of aluminum extruded material forged product | |
| JPH10110231A (en) | Aluminum alloy material for casting-forging excellent in wear resistance, castability and forgeability and its production | |
| JP2000212673A (en) | Aluminum alloy sheet for aircraft stringer excellent in stress corrosion cracking resistance and its production | |
| JPH11286759A (en) | Production of forged product using aluminum extruded material | |
| JPH04341546A (en) | Production of high strength aluminum alloy-extruded shape material | |
| JPH05112840A (en) | Baking hardenability al-mg-si alloy sheet excellent in press formability and its manufacture | |
| JPH09249953A (en) | Production of aluminum extruded material forged product | |
| JPH08232035A (en) | High strength aluminum alloy material for bumper, excellent in bendability, and its production | |
| JP2848368B2 (en) | Manufacturing method of aluminum alloy for compressor parts with excellent wear resistance and toughness | |
| JPH06330264A (en) | Production of aluminum alloy forged material excellent in strength and toughness | |
| JP3687505B2 (en) | Aluminum alloy for casting forging and method for producing casting forging | |
| JPH07150312A (en) | Manufacture of aluminum alloy forged base stock | |
| JPH05306440A (en) | Manufacture of aluminum alloy sheet for forming excellent baking hardenability | |
| JPH09249952A (en) | Production of aluminum forged product |