JPH083675A - Aluminum alloy for forging - Google Patents
Aluminum alloy for forgingInfo
- Publication number
- JPH083675A JPH083675A JP10904594A JP10904594A JPH083675A JP H083675 A JPH083675 A JP H083675A JP 10904594 A JP10904594 A JP 10904594A JP 10904594 A JP10904594 A JP 10904594A JP H083675 A JPH083675 A JP H083675A
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- JP
- Japan
- Prior art keywords
- weight
- forging
- aluminum alloy
- amount
- alloy
- 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.)
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Links
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、自動車部品，家電製品
等に使用され、良好な強度及び大きな伸び率を呈する鍛
造用アルミニウム合金に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an aluminum alloy for forging, which is used for automobile parts, home electric appliances and the like and exhibits good strength and a large elongation.
【０００２】[0002]
【従来の技術】アルミニウム合金の代表的な鍛造用素材
として、６０６１合金が使用されている。しかし、６０
６１合金は、押出工程を経て鍛造用素材にされることか
ら、コスト高になる。また、押出し材を鍛造することか
ら、製品形状がおのずと単純な形状に限定される。その
ため、形状が複雑な製品を得る場合、鍛造用素材を鋳造
で得る必要が生じる。現在、鋳造によって所定の形状が
付与された素材、すなわち予形材で鍛造が可能な材料と
しては、ＡＣ４Ｃ，ＡＣ４ＣＨ等がＪＩＳで掲げられて
いる。しかし、ＡＣ４Ｃ，ＡＣ４ＣＨ等のアルミニウム
合金は、６０６１合金に比較し伸び率等の引張り特性が
劣り、形状特性に優れた鍛造製品を得ることができな
い。2. Description of the Related Art As a typical forging material of aluminum alloy, 6061 alloy is used. But 60
Since the 61 alloy is made into a forging material through an extrusion process, the cost is high. Moreover, since the extruded material is forged, the product shape is naturally limited to a simple shape. Therefore, in order to obtain a product having a complicated shape, it is necessary to obtain a forging material by casting. At present, as materials that have been given a predetermined shape by casting, that is, materials that can be forged by preforming, AC4C, AC4CH, etc. are listed in JIS. However, aluminum alloys such as AC4C and AC4CH are inferior in tensile properties such as elongation to the aluminum alloys such as 6061 alloy, and a forged product excellent in shape properties cannot be obtained.
【０００３】ＡＣ４Ｃ，ＡＣ４ＣＨ等のアルミニウム合
金を鋳造することにより得られた鍛造用素材の伸び率を
大きくするため、Ｓｉ含有量を３重量％程度まで少な
く、更にＮａ、Ｓｒ、Ｓｂ等を添加し、共晶Ｓｉを微細
化することが、特開昭５４−１３４０７号公報で紹介さ
れている。共晶Ｓｉの微細化によって、伸び率がある程
度改善される。しかし、依然として６０６１合金の伸び
率には及ばず、鍛造性に問題が残っている。また、得ら
れた鍛造製品の耐力が十分でないことから、所定の構造
強度をだすために厚肉化することを余儀なくされてい
た。その結果、軽量化部品としてのアルミニウム材料の
長所を活用できない現状である。本発明者等は、このよ
うな問題を解消したアルミニウム合金として、Ｐ含有量
を規制し共晶Ｓｉを十分に微細化することにより、鍛造
性を始めとして機械強度等に優れた鍛造用合金を特開平
５−９６３７号公報で紹介した。In order to increase the elongation of the forging material obtained by casting an aluminum alloy such as AC4C or AC4CH, the Si content is reduced to about 3% by weight, and Na, Sr, Sb, etc. are added. The miniaturization of eutectic Si is introduced in JP-A-54-13407. The degree of elongation is improved to some extent by making the eutectic Si finer. However, the elongation rate of the 6061 alloy is still inferior, and a problem remains in forgeability. Further, since the yield strength of the obtained forged product is not sufficient, it has been unavoidable to increase the wall thickness in order to obtain a predetermined structural strength. As a result, the advantages of aluminum materials as lightweight parts cannot be utilized. The present inventors have found, as an aluminum alloy that solves such a problem, a forging alloy that is excellent in mechanical strength and the like, including forgeability, by regulating the P content and sufficiently refining eutectic Si. It was introduced in JP-A-5-9637.
【０００４】[0004]
【発明が解決しようとする課題】ところで、鍛造後の最
終製品になるべく近い形状をもつ鋳造品を鋳造する際、
Ｓｉ量が少ない６０６１，６０６３等の展伸用材料で
は、鋳造時の熱間割れ，鋳巣等の欠陥が発生し易い。一
方、Ｓｉ量が多いＡＣ４Ｃ，ＡＣ４ＣＨ等の鋳造用合金
では、鋳造時に問題が生じないが、鍛造後の強度や靭性
が劣る傾向を示す。本発明は、このような問題を解消す
べく案出されたものであり、鋳造後のＭｇ2 Ｓｉ量又は
Ｍｇ2 Ｓｉ量以外の過剰Ｓｉ量を調整することにより、
鋳造時に熱間割れが発生せず、且つ鍛造後に強度及び靭
性が向上する鍛造用アルミニウム合金を提供することを
目的とする。By the way, when casting a cast product having a shape as close as possible to the final product after forging,
With wrought materials such as 6061 and 6063 having a small amount of Si, defects such as hot cracking and porosity during casting are likely to occur. On the other hand, casting alloys such as AC4C and AC4CH having a large amount of Si do not cause problems during casting, but tend to have poor strength and toughness after forging. The present invention has been devised to solve such problems, by adjusting the amount of Mg 2 Si after casting or the amount of excess Si other than the amount of Mg 2 Si,
An object of the present invention is to provide an aluminum alloy for forging which is free from hot cracking during casting and has improved strength and toughness after forging.
【０００５】[0005]
【課題を解決するための手段】本発明の鍛造用アルミニ
ウム合金は、その目的を達成するため、Ｓｉ：０．６〜
３．０重量％，Ｍｇ：０．２〜２．０重量％，Ｃｕ：
０．３〜１．０重量％，Ｔｉ：０．０１〜０．１重量
％，Ｂ：０．０００１〜０．０１重量％，Ｍｎ：０．１
〜０．５重量％，Ｃｒ：０．１〜０．５重量％及びＦ
ｅ：０．０５〜０．５重量％を含み、且つ合金設計値か
ら換算したＭｇ2 Ｓｉ量が１．５重量％以上となるよう
に成分設計されていることを特徴とする。或いは、合金
設計値から換算したＭｇ2 Ｓｉ当量以外のＳｉ量が０．
５重量％以上となるように、成分設計する。前掲した組
成をもつアルミニウム合金溶湯は、２００℃／秒以下の
冷却速度で所定形状に鋳造される。得られた鋳造品は、
１０〜５０％の据込み率で鍛造加工され、素形材とな
る。In order to achieve the object, the aluminum alloy for forging of the present invention has a Si: 0.6-
3.0% by weight, Mg: 0.2 to 2.0% by weight, Cu:
0.3-1.0 wt%, Ti: 0.01-0.1 wt%, B: 0.0001-0.01 wt%, Mn: 0.1
~ 0.5 wt%, Cr: 0.1-0.5 wt% and F
e: 0.05 to 0.5% by weight, and the composition is designed so that the amount of Mg 2 Si converted from the alloy design value is 1.5% by weight or more. Alternatively, the amount of Si other than the Mg 2 Si equivalent converted from the alloy design value is 0.
The components are designed so that the content is 5% by weight or more. The molten aluminum alloy having the composition described above is cast into a predetermined shape at a cooling rate of 200 ° C./second or less. The cast product obtained is
It is forged with an upsetting rate of 10 to 50% to become a raw material.
【０００６】鍛造後にＴ6 処理を施すアルミニウム合金
を自動車用部品として使用するとき、引張り強さ３００
Ｎ／ｍｍ2 以上，耐力２５０Ｎ／ｍｍ2 以上及び伸び１
０％以上の機械的性質が要求される。本発明の鍛造用ア
ルミニウム合金は、この要求に十分応える特性を呈す
る。なお、本発明のアルミニウム合金は、押出し後に鍛
造することによっても製造されるが、コスト低減のため
に押出し工程を省略し、鋳造後に直接鍛造することによ
って所定の機械的性質を付与することができる。そのた
め、製造コスト自体も低減される。When an aluminum alloy subjected to T 6 treatment after forging is used as an automobile part, a tensile strength of 300 is obtained.
N / mm 2 or more, proof stress 250 N / mm 2 or more and elongation 1
A mechanical property of 0% or more is required. The aluminum alloy for forging according to the present invention exhibits characteristics that sufficiently meet this demand. The aluminum alloy of the present invention is also produced by forging after extrusion, but the extrusion step is omitted for cost reduction, and predetermined mechanical properties can be imparted by directly forging after casting. . Therefore, the manufacturing cost itself is also reduced.
【０００７】[0007]
【作用】本発明の鍛造用アルミニウム合金においては、
鋳造後のＭｇ2 Ｓｉ量又はＭｇ2 Ｓｉ量以外の過剰Ｓｉ
量を調整することにより、鋳造時の熱間割れが防止され
る。鋳造時に発生したミクロポロシティは、据込み率１
０〜５０％の鍛造によって押し潰される。その結果、鍛
造加工性に優れ機械的性質が向上したアルミニウム合金
が得られる。In the aluminum alloy for forging of the present invention,
The amount of Mg 2 Si after casting or excess Si other than the amount of Mg 2 Si
By adjusting the amount, hot cracking during casting is prevented. The microporosity generated during casting has an upset rate of 1
Crushed by 0-50% forging. As a result, an aluminum alloy having excellent forgeability and improved mechanical properties can be obtained.
【０００８】以下、合金成分及びその含有量等について
説明する。 Ｓｉ：０．６〜３．０重量％ 本発明の鍛造用アルミニウム合金は、鋳造で得られた予
形材を鍛造することにより、所定形状をもつ製品とされ
る。この予形材を得るために、溶湯の流動性，引け性等
が良く、鋳造割れ等の欠陥が発生しないことが要求され
る。この鋳造性を確保する上から、Ｓｉを含有させるこ
とが必要である。Ｓｉ含有量が０．６重量％未満では、
Ｍｇ2 Ｓｉ化合物以外の過剰Ｓｉが０．５重量％未満と
なるため、鋳造時に割れが発生し易くなる。しかし、多
量のＳｉ含有は、アルミニウム合金の伸びや機械的強度
を低下させる。０．６〜３．０重量％の範囲のＳｉ含有
量で、必要とする伸びや機械的強度が得られると共に、
鋳造性も良好になる。Ｓｉ含有量が３．０重量％を超え
ると、ミクロ組織でも検出されるように粒界に比較的多
量の共晶Ｓｉが晶出し、伸び，機械的強度等を劣化させ
る。逆に、Ｓｉ含有量が０．６重量％未満のときには、
鋳造性が悪化し、鋳造時に割れが発生し易くなる。The alloy components and their contents will be described below. Si: 0.6 to 3.0 wt% The aluminum alloy for forging of the present invention is made into a product having a predetermined shape by forging a preformed material obtained by casting. In order to obtain this preformed material, it is required that the melt has good fluidity, shrinkability, etc., and that defects such as casting cracks do not occur. In order to secure this castability, it is necessary to contain Si. When the Si content is less than 0.6% by weight,
Since excess Si other than the Mg 2 Si compound is less than 0.5% by weight, cracking is likely to occur during casting. However, the inclusion of a large amount of Si reduces the elongation and mechanical strength of the aluminum alloy. With the Si content in the range of 0.6 to 3.0% by weight, the required elongation and mechanical strength can be obtained, and
Castability is also improved. If the Si content exceeds 3.0% by weight, a relatively large amount of eutectic Si crystallizes at the grain boundaries as detected in the microstructure, deteriorating elongation and mechanical strength. Conversely, when the Si content is less than 0.6% by weight,
Castability deteriorates and cracks are likely to occur during casting.
【０００９】Ｍｇ：０．２〜２．０重量％ Ｓｉと共存して熱処理によりＭｇ2 Ｓｉとして析出し、
引張強さ，耐力等の機械的強度を向上させる。しかし、
Ｍｇ含有量が２．０重量％を越えると，Ｍｇによる強度
改善効果が飽和する。また、０．２重量％未満のＭｇ含
有量では、強度の向上に有効なＭｇ2 Ｓｉとして働くＭ
ｇ分が不足する。 Ｃｕ：０．３〜１．０重量％ 時効処理後にＡｌ−Ｃｕ系，Ａｌ−Ｃｕ−Ｍｇ系等の析
出物となって、アルミニウム合金の強度を上昇させる。
このような効果を得るためには、０．３重量％以上のＣ
ｕ含有量が必要である。また、Ｍｇとの併用添加によっ
て、十分な伸びが確保される。しかし、１．０重量％を
超える多量のＣｕが含まれると、耐糸錆性が劣化する。Mg: 0.2-2.0% by weight Coexisting with Si to precipitate as Mg 2 Si by heat treatment,
Improves mechanical strength such as tensile strength and proof stress. But,
When the Mg content exceeds 2.0% by weight, the strength improving effect of Mg is saturated. Further, when the Mg content is less than 0.2% by weight, M acting as Mg 2 Si effective for improving strength is increased.
There is not enough g. Cu: 0.3-1.0 wt% After aging treatment, it becomes a precipitate of Al-Cu type, Al-Cu-Mg type, etc., and increases the strength of the aluminum alloy.
In order to obtain such effects, 0.3% by weight or more of C
u content is required. Moreover, sufficient elongation is secured by the combined addition with Mg. However, if a large amount of Cu exceeding 1.0% by weight is contained, the yarn rust resistance deteriorates.
【００１０】Ｔｉ：０．０１〜０．１重量％及びＢ：
０．０００１〜０．０１重量％ アルミニウム合金の鋳造組織は、Ｔｉ及びＢの併用添加
によって微細化される。鋳造組織の微細化に伴い、粒界
に析出する不純物やシュリンケージ等が細かく分散さ
れ、機械的特性が向上する。このような効果を得るため
には、０．０１重量％以上のＴｉ及び０．０００１重量
％以上のＢを含有させることが必要である。しかし、Ｔ
ｉ含有量及びＢ含有量がそれぞれ０．１重量％及び０．
０１重量％を超えると、析出する介在物が多くなり、却
って靭性，強度，伸び等が劣化する。Ti: 0.01 to 0.1% by weight and B:
The cast structure of 0.0001 to 0.01 wt% aluminum alloy is refined by the combined addition of Ti and B. As the cast structure becomes finer, impurities and shrinkages precipitated at the grain boundaries are finely dispersed, and the mechanical properties are improved. In order to obtain such effects, it is necessary to contain 0.01% by weight or more of Ti and 0.0001% by weight or more of B. But T
i content and B content are 0.1% by weight and 0.
If it exceeds 01% by weight, the amount of inclusions to be precipitated increases, and rather the toughness, strength, elongation, etc. deteriorate.
【００１１】Ｍｎ及びＣｒ：０．１〜０．５重量％ 加工時にアルミニウム合金が再結晶することを防止する
ために、添加される元素である。再結晶防止を図るため
には、０．１重量％以上のＭｎ及び０．１重量％以上の
Ｃｒを複合して含有させることが必要である。０．１重
量％以上のＭｎ及びＣｒを含有させるとき、熱間加工中
及びその後のＴ6 処理（５２０℃×４時間加熱→水冷→
１６０℃×６時間加熱→放冷）における再結晶が防止さ
れる。しかし、これら元素を多量に添加すると、粗大な
金属間化合物が生成し、材料特性を低下させる。また、
Ｍｎ又はＣｒを単独添加した場合では、鍛造繊維組織の
方向に幅１〜２ｍｍ及び長さ５ｍｍ程度の再結晶粒が発
達する。この再結晶粒は、Ｍｎ及びＣｒを併用添加する
ことにより、幅及び長さ共に１ｍｍ以下に抑えられる。
更に、Ｍｎ及びＣｒの過剰添加は、マトリックスの硬度
が上昇し、却って加工性が低下する。そこで、Ｍｎ含有
量及びＣｒ含有量の上限は、共に０．５重量％に規定し
た。Mn and Cr: 0.1 to 0.5% by weight These are elements added in order to prevent recrystallization of the aluminum alloy during processing. In order to prevent recrystallization, it is necessary to contain 0.1% by weight or more of Mn and 0.1% by weight or more of Cr in combination. When 0.1% by weight or more of Mn and Cr are contained, T 6 treatment (520 ° C. × 4 hours heating → water cooling →
Recrystallization at 160 ° C. × 6 hours heating → cooling) is prevented. However, if these elements are added in a large amount, a coarse intermetallic compound is generated and the material properties are deteriorated. Also,
When Mn or Cr is added alone, recrystallized grains having a width of 1 to 2 mm and a length of 5 mm develop in the direction of the forged fiber structure. The width and length of the recrystallized grains can be suppressed to 1 mm or less by adding Mn and Cr together.
Further, the excessive addition of Mn and Cr increases the hardness of the matrix and rather reduces the workability. Therefore, the upper limits of the Mn content and the Cr content are both defined to be 0.5% by weight.
【００１２】Ｆｅ：０．０５〜０．５重量％ 鋳造時にβ−ＡｌＦｅＳｉ系の晶出物を粒界に発生さ
せ、すでに発生している初晶のＡｌ結晶粒を結合させる
作用を呈する。その結果、鋳造割れが防止される。この
ような効果は、０．０５重量％以上のＦｅ含有量で顕著
になる。しかし、０．５重量％を超える多量のＦｅが含
まれると、巨大な晶出物が生成し、機械的性質に悪影響
を与える。 Ｍｇ2 Ｓｉ量：１．５重量％以上 Ｍｇ2 Ｓｉ量は、合金設計の段階で含まれるＭｇ量（分
析値）に（１＋１／１．７３）を乗じる設計値で算出さ
れる。この設計値が１．５重量％以上になると鋳造時に
割れの発生が抑えられるので、設計値１．５重量％以上
を満足するようにＳｉ含有量及びＭｇ含有量が決定され
る。Ｍｇ2 Ｓｉ量が割れ抑制に与える関係は、表１に示
すように本発明者等による多数の実験結果から求められ
たものである。Fe: 0.05 to 0.5% by weight It has a function of producing a β-AlFeSi type crystallized substance at the grain boundary during casting and binding the already-generated primary Al crystal grains. As a result, casting cracking is prevented. Such an effect becomes remarkable when the Fe content is 0.05% by weight or more. However, when a large amount of Fe exceeding 0.5% by weight is contained, huge crystallized substances are formed, which adversely affects the mechanical properties. Mg 2 Si content: 1.5 wt% or more The Mg 2 Si content is calculated by a design value obtained by multiplying the Mg content (analytical value) included in the alloy design stage by (1 + 1 / 1.73). If this design value is 1.5 wt% or more, cracking is suppressed during casting, so the Si content and the Mg content are determined so as to satisfy the design value of 1.5 wt% or more. The relationship that the amount of Mg 2 Si gives to the crack suppression is obtained from a large number of experimental results by the present inventors as shown in Table 1.
【００１３】表１では、リングテスト試料における表面
の割れのトータル長さが１．５ｃｍ以下を合格とした。
リングテスト法では、所定組成の溶湯を７１０℃の保持
し、柄杓で約１００ｇを金型温度１５０℃の金型に注
ぎ、凝固後のリング表面全体に表れる割れの長さを測定
した。金型としては、外径５８ｍｍ及び内径３８ｍｍの
リング状金型を使用し、断面の形状は高さ２０ｍｍ及び
横１０ｍｍの四角形でコーナー部が丸くなっている。こ
のときの溶湯冷却速度は、約１５℃／秒であった。ま
た、表面割れの総長で１．５ｃｍ以下を合格とした。表
１の試料Ｎo.１〜４にみられるように、Ｍｇ2 Ｓｉ量が
設計値１．５重量％以上で割れの発生がなくなってい
る。Ｍｇ2 Ｓｉ量の調整による割れが抑制されること
は、Ａｌ−Ｍｇ2 Ｓｉ系においてＭｇ2 Ｓｉが共晶とし
て存在していると、Ａｌ−Ｍｇ2 Ｓｉの共晶溶湯が結晶
粒界に補給されることに起因するものと推察される。In Table 1, the total length of cracks on the surface of the ring test sample was 1.5 cm or less, which was regarded as acceptable.
In the ring test method, a molten metal having a predetermined composition was held at 710 ° C., about 100 g was poured into a mold having a mold temperature of 150 ° C. with a ladle, and the length of cracks appearing on the entire ring surface after solidification was measured. As the mold, a ring-shaped mold having an outer diameter of 58 mm and an inner diameter of 38 mm is used, and the cross-sectional shape is a quadrangle having a height of 20 mm and a width of 10 mm, and the corner portion is round. The molten metal cooling rate at this time was about 15 ° C./sec. The total length of surface cracks was 1.5 cm or less. As can be seen from Sample Nos. 1 to 4 in Table 1, the occurrence of cracks disappeared when the amount of Mg 2 Si was the designed value of 1.5% by weight or more. The suppression of cracking by adjusting the amount of Mg 2 Si means that when Mg 2 Si is present as a eutectic in the Al-Mg 2 Si system, the eutectic melt of Al-Mg 2 Si replenishes the crystal grain boundaries. It is presumed that this is due to
【００１４】[0014]
【表１】 [Table 1]
【００１５】過剰Ｓｉ量：０．５重量％以上 過剰Ｓｉ量が設計計算値で０．５重量％以上になると、
表１のＮo.５，６にみられるように割れが防止される。
過剰Ｓｉによる割れ抑制作用は、Ａｌ−Ｍｇ2 Ｓｉ−Ｓ
ｉ系において、ＳｉがＡｌ−Ｓｉ系の共晶となり、結晶
粒界にＡｌ−Ｓｉ系共晶溶湯が補給されることに由来す
るものと推察される。すなわち、Ｍｇが全てＭｇ2 Ｓｉ
になっていると推定し、残りの過剰Ｓｉが共晶Ｓｉにな
るものと考えられる。そこで、設計計算値で０．５重量
％以上の過剰Ｓｉ量となるように、Ｓｉ含有量及びＭｇ
含有量を決定する。 鋳造時の溶湯冷却速度：２００℃／秒以下 鋳造割れが生じないためには、共晶Ｍｇ2 Ｓｉ又はＳｉ
の存在が重要である。共晶Ｍｇ2 Ｓｉ又はＳｉは溶湯の
冷却速度に依存し、冷却速度が遅いほど発生量が多くな
ることから、必要量の共晶Ｍｇ2 Ｓｉ又はＳｉを確保す
るため溶湯の冷却速度を２００℃／秒以下にする。Excess Si amount: 0.5% by weight or more When the excess Si amount is 0.5% by weight or more in design calculation value,
As shown in Nos. 5 and 6 of Table 1, cracking is prevented.
Cracking inhibiting effect of excess Si is, Al-Mg 2 Si-S
It is presumed that this is derived from the fact that in the i-system, Si becomes an Al-Si-based eutectic, and the Al-Si-based eutectic melt is replenished to the crystal grain boundaries. That is, all Mg is Mg 2 Si
It is considered that the remaining excess Si becomes eutectic Si. Therefore, the Si content and the Mg content should be adjusted so that the excess Si content is 0.5% by weight or more as calculated by design.
Determine the content. Melt cooling rate during casting: 200 ° C / sec or less In order to prevent casting cracks, eutectic Mg 2 Si or Si
The existence of is important. Eutectic Mg 2 Si or Si depends on the cooling rate of the molten metal, and the generation amount increases as the cooling rate slows. Therefore, in order to secure the necessary amount of eutectic Mg 2 Si or Si, the cooling rate of the molten metal is 200 ° C. / Sec or less.
【００１６】鍛造時の据込み率：１０〜５０％ 鋳造品に生じているポロシティが据込み率１０％以上の
鍛造によって押し潰され、アルミニウム合金の機械的特
性を改善する。据込み率がポロシティに与える影響を図
１に示す。しかし、５０％を超える据込み率は、ポロシ
ティ圧潰作用を飽和させ、且つ図２に示すように引張り
強さ及び耐力の値が低下する傾向を示し、却って鍛造加
工に要する費用を上昇させる。Upsetting ratio during forging: 10 to 50% Porosity generated in the cast product is crushed by forging with an upsetting ratio of 10% or more, improving the mechanical properties of the aluminum alloy. Figure 1 shows the effect of upsetting on porosity. However, an upsetting rate of more than 50% saturates the porosity crushing action, and tends to decrease the values of tensile strength and proof stress as shown in FIG. 2, and rather increases the cost required for forging.
【００１７】[0017]
【実施例】表２に示した合金成分の素材をＪＩＳＤ４号
の舟形鋳型を使用して鋳造した。金型を２００℃に予熱
しておいた。このとき、溶湯の冷却速度は約１０℃／秒
であった。得られた素材を４５０℃に加熱し、型温度２
００℃で据込み率４０％の熱間鍛造を施し、Ｔ6 処理
（５２０℃×４時間加熱→水焼入れ→１６０℃×６時間
加熱→空冷）した後、機械的性質を調査した。Ｍｇ2 Ｓ
ｉ量及び過剰Ｓｉ量の計算値及び鋳造割れの結果を表３
に、鋳造材をＴ6 処理した後の機械的性質を表４に示
す。Example Materials of the alloy components shown in Table 2 were cast using a JIS D4 boat-shaped mold. The mold was preheated to 200 ° C. At this time, the cooling rate of the molten metal was about 10 ° C./sec. The resulting material is heated to 450 ° C and the mold temperature is 2
After hot forging with an upsetting rate of 40% at 00 ° C. and T 6 treatment (520 ° C. × 4 hours heating → water quenching → 160 ° C. × 6 hours heating → air cooling), mechanical properties were investigated. Mg 2 S
Table 3 shows calculated values of i amount and excess Si amount and results of casting cracking.
Table 4 shows the mechanical properties of the cast material after T 6 treatment.
【００１８】[0018]
【表２】 [Table 2]
【００１９】[0019]
【表３】 [Table 3]
【００２０】[0020]
【表４】 [Table 4]
【００２１】表３にみられるように、Ｍｇ2 Ｓｉ量及び
過剰Ｓｉ量が鋳造割れの抑制に効果的であり、それぞれ
１．５重量％以上及び０．５重量％以上になっているの
で、Ｓｉ及びＭｇ以外の元素の添加にも拘らず割れの発
生が見られなかった。鋳造材をＴ6 処理した後の機械的
性質は、表４に示すように、試料Ｎo.１０，１１では何
れも据込み率４０％のときの目標値である引張り強さ３
００Ｎ／ｍｍ2 ，耐力２５０Ｎ／ｍｍ2 以上及び伸び１
０％以上を満足している。試料Ｎo.１０について、据込
み率とポロシティとの関係を調査した。ポロシティ量
は、試験片の比重を測定し、据込み率６０％のときの比
重に対する差で表した。図１から明らかなように、据込
み率１０％でポロシティがほぼつぶれていることが判
る。また、試料Ｎo.１０について据込み率と機械的性質
との関係をしめした図２から、引張り強さ及び耐力は、
据込み率４０〜５０％で飽和していることが判る。As can be seen from Table 3, the amounts of Mg 2 Si and excess Si are effective in suppressing casting cracks, and are 1.5% by weight and 0.5% by weight, respectively. No generation of cracks was observed despite the addition of elements other than Si and Mg. As shown in Table 4, the mechanical properties of the cast material after T 6 treatment were tensile strength 3 which is a target value when the upsetting rate is 40% in each of the samples No. 10 and 11.
00N / mm 2 , yield strength 250N / mm 2 or more and elongation 1
We are satisfied with 0% or more. The relationship between the upsetting rate and the porosity of the sample No. 10 was investigated. The porosity amount was measured by measuring the specific gravity of the test piece, and expressed as a difference from the specific gravity when the upsetting rate was 60%. As is clear from FIG. 1, it is understood that the porosity is almost collapsed at the upsetting rate of 10%. Further, from FIG. 2 showing the relationship between the upsetting rate and the mechanical properties of Sample No. 10, the tensile strength and proof stress are
It can be seen that the upset ratio is saturated at 40 to 50%.
【００２２】[0022]
【発明の効果】以上に説明したように、本発明の鍛造用
アルミニウム合金は、Ｍｇ2 Ｓｉ量及び過剰Ｓｉ量を調
整することにより、鋳造時に発生し易い熱間割れを防止
し、鍛造後優れたに強度及び靭性を呈する。また、鋳造
材に含まれているポロシティは、鍛造によって押し潰さ
れ、良好な機械的特性を持った製品が得られる。As described above, the aluminum alloy for forging according to the present invention prevents the hot cracking that tends to occur during casting by adjusting the amount of Mg 2 Si and the amount of excess Si, and is excellent after forging. It also exhibits strength and toughness. Moreover, the porosity contained in the cast material is crushed by forging, and a product having good mechanical properties can be obtained.
【図１】 本発明鍛造用アルミニウム合金の据込み率と
ポロシティとの関係を示したグラフFIG. 1 is a graph showing the relationship between upsetting ratio and porosity of the aluminum alloy for forging according to the present invention.
【図２】 同じく据込み率がアルミニウム合金の機械的
特性に与える影響を示したグラフFIG. 2 is a graph showing the effect of upsetting on the mechanical properties of an aluminum alloy.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 大野 昭自 静岡県庵原郡蒲原町蒲原161番地 株式会 社日軽技研内 ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Akio Ohno 161 Kambara, Kambara-cho, Anbara-gun, Shizuoka Stock Company Nikkei Giken
Claims (4)
０．２〜２．０重量％，Ｃｕ：０．３〜１．０重量％，
Ｔｉ：０．０１〜０．１重量％，Ｂ：０．０００１〜
０．０１重量％，Ｍｎ：０．１〜０．５重量％，Ｃｒ：
０．１〜０．５重量％及びＦｅ：０．０５〜０．５重量
％を含み、且つ合金設計値から換算したＭｇ2 Ｓｉ量が
１．５重量％以上となるように成分設計されている鍛造
用アルミニウム合金。1. Si: 0.6 to 3.0% by weight, Mg:
0.2 to 2.0% by weight, Cu: 0.3 to 1.0% by weight,
Ti: 0.01 to 0.1% by weight, B: 0.0001 to
0.01% by weight, Mn: 0.1 to 0.5% by weight, Cr:
0.1 to 0.5 wt% and Fe: 0.05 to 0.5 wt% are included, and the composition is designed so that the amount of Mg 2 Si converted from the alloy design value is 1.5 wt% or more. Aluminum alloy for forging.
０．２〜２．０重量％，Ｃｕ：０．３〜１．０重量％，
Ｔｉ：０．０１〜０．１重量％，Ｂ：０．０００１〜
０．０１重量％，Ｍｎ：０．１〜０．５重量％，Ｃｒ：
０．１〜０．５重量％及びＦｅ：０．０５〜０．５重量
％を含み、且つ合金設計値から換算したＭｇ2 Ｓｉ当量
以外のＳｉ量が０．５重量％以上となるように成分設計
されている鍛造用アルミニウム合金。2. Si: 0.6 to 3.0% by weight, Mg:
0.2 to 2.0% by weight, Cu: 0.3 to 1.0% by weight,
Ti: 0.01 to 0.1% by weight, B: 0.0001 to
0.01% by weight, Mn: 0.1 to 0.5% by weight, Cr:
0.1 to 0.5% by weight and Fe: 0.05 to 0.5% by weight, and the amount of Si other than the Mg 2 Si equivalent calculated from the alloy design value should be 0.5% by weight or more. Aluminum alloy for forging that has been designed as a component.
求項１又は２記載の組成をもつアルミニウム合金溶湯を
鋳造することを特徴とする鍛造用アルミニウム合金の鋳
造方法。3. A method for casting an aluminum alloy for forging, which comprises casting a molten aluminum alloy having the composition according to claim 1 or 2 with a cooling rate set to 200 ° C./second or less.
ニウム合金を鋳造し、１０〜５０％の据込み率で鍛造加
工を施した素形材。4. A cast material produced by casting an aluminum alloy having the composition according to claim 1 or 2 and forging it at an upsetting rate of 10 to 50%.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10904594A JP3471421B2 (en) | 1994-04-25 | 1994-04-25 | Manufacturing method of aluminum alloy forging |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10904594A JP3471421B2 (en) | 1994-04-25 | 1994-04-25 | Manufacturing method of aluminum alloy forging |
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| Publication Number | Publication Date |
|---|---|
| JPH083675A true JPH083675A (en) | 1996-01-09 |
| JP3471421B2 JP3471421B2 (en) | 2003-12-02 |
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ID=14500216
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP10904594A Expired - Fee Related JP3471421B2 (en) | 1994-04-25 | 1994-04-25 | Manufacturing method of aluminum alloy forging |
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| Country | Link |
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Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2000514138A (en) * | 1996-07-04 | 2000-10-24 | コマルコ アルミニウム リミテッド | 6xxx aluminum alloy |
| EP1158068A1 (en) * | 2000-05-24 | 2001-11-28 | Pechiney Rhenalu | Thick products made of heat-treatable aluminum alloy with improved toughness and process for manufacturing these products |
| WO2004031424A1 (en) * | 2002-10-01 | 2004-04-15 | Asahi Tec Corporation | Aluminum alloy for casting-forging, aluminum cast/forged article, and method for manufacture thereof |
| WO2008044564A1 (en) | 2006-10-05 | 2008-04-17 | Gohsyu Co., Ltd. | High-strength process material, method of producing the same and production apparatus therefor |
| JP2008117839A (en) * | 2006-11-01 | 2008-05-22 | Oya Giken:Kk | Magnetic core member and method for manufacturing the same |
| US20100288401A1 (en) * | 2007-11-08 | 2010-11-18 | Ksm Castings Gmbh | Aluminum casting alloy |
| WO2021230080A1 (en) * | 2020-05-13 | 2021-11-18 | 日本軽金属株式会社 | Aluminum alloy forging material and method for manufacturing same |
-
1994
- 1994-04-25 JP JP10904594A patent/JP3471421B2/en not_active Expired - Fee Related
Cited By (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2000514138A (en) * | 1996-07-04 | 2000-10-24 | コマルコ アルミニウム リミテッド | 6xxx aluminum alloy |
| EP1158068A1 (en) * | 2000-05-24 | 2001-11-28 | Pechiney Rhenalu | Thick products made of heat-treatable aluminum alloy with improved toughness and process for manufacturing these products |
| US7135077B2 (en) | 2000-05-24 | 2006-11-14 | Pechiney Rhenalu | Thick products made of heat-treatable aluminum alloy with improved toughness and process for manufacturing these products |
| WO2004031424A1 (en) * | 2002-10-01 | 2004-04-15 | Asahi Tec Corporation | Aluminum alloy for casting-forging, aluminum cast/forged article, and method for manufacture thereof |
| EP1566458A1 (en) * | 2002-10-01 | 2005-08-24 | Asahi Tec Corporation | Aluminum alloy for casting-forging, aluminum cast/forged article, and method formanufacture thereof |
| JPWO2004031424A1 (en) * | 2002-10-01 | 2006-02-02 | 旭テック株式会社 | Aluminum alloy for casting forging, aluminum casting forged product and manufacturing method |
| EP1566458A4 (en) * | 2002-10-01 | 2006-04-26 | Asahi Tec Corp | Aluminum alloy for casting-forging, aluminum cast/forged article, and method formanufacture thereof |
| WO2008044564A1 (en) | 2006-10-05 | 2008-04-17 | Gohsyu Co., Ltd. | High-strength process material, method of producing the same and production apparatus therefor |
| US8250897B2 (en) | 2006-10-05 | 2012-08-28 | Gohsyu Co., Ltd. | High strength workpiece material and method and apparatus for producing the same |
| JP2008117839A (en) * | 2006-11-01 | 2008-05-22 | Oya Giken:Kk | Magnetic core member and method for manufacturing the same |
| US20100288401A1 (en) * | 2007-11-08 | 2010-11-18 | Ksm Castings Gmbh | Aluminum casting alloy |
| WO2021230080A1 (en) * | 2020-05-13 | 2021-11-18 | 日本軽金属株式会社 | Aluminum alloy forging material and method for manufacturing same |
Also Published As
| Publication number | Publication date |
|---|---|
| JP3471421B2 (en) | 2003-12-02 |
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