JP2663078B2 - Aluminum alloy for T6 treatment with stable artificial aging - Google Patents
Aluminum alloy for T6 treatment with stable artificial agingInfo
- Publication number
- JP2663078B2 JP2663078B2 JP4101762A JP10176292A JP2663078B2 JP 2663078 B2 JP2663078 B2 JP 2663078B2 JP 4101762 A JP4101762 A JP 4101762A JP 10176292 A JP10176292 A JP 10176292A JP 2663078 B2 JP2663078 B2 JP 2663078B2
- Authority
- JP
- Japan
- Prior art keywords
- treatment
- artificial aging
- alloy
- aging
- quenching
- 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.)
- Expired - Lifetime
Links
- 230000032683 aging Effects 0.000 title claims description 48
- 229910000838 Al alloy Inorganic materials 0.000 title claims description 16
- 239000013078 crystal Substances 0.000 claims description 19
- 229910052804 chromium Inorganic materials 0.000 claims description 6
- 229910052726 zirconium Inorganic materials 0.000 claims description 6
- 229910052720 vanadium Inorganic materials 0.000 claims description 5
- 239000012535 impurity Substances 0.000 claims description 4
- 229910052748 manganese Inorganic materials 0.000 claims description 4
- 229910052742 iron Inorganic materials 0.000 claims description 3
- 229910052719 titanium Inorganic materials 0.000 claims description 3
- 229910052725 zinc Inorganic materials 0.000 claims description 3
- 230000003679 aging effect Effects 0.000 claims description 2
- 229910045601 alloy Inorganic materials 0.000 description 36
- 239000000956 alloy Substances 0.000 description 36
- 239000000243 solution Substances 0.000 description 28
- 238000010791 quenching Methods 0.000 description 25
- 230000000694 effects Effects 0.000 description 14
- 230000000171 quenching effect Effects 0.000 description 14
- 239000000463 material Substances 0.000 description 10
- 238000000034 method Methods 0.000 description 7
- 229910019018 Mg 2 Si Inorganic materials 0.000 description 6
- 238000005275 alloying Methods 0.000 description 6
- 238000000137 annealing Methods 0.000 description 6
- 230000000052 comparative effect Effects 0.000 description 6
- 229910052751 metal Inorganic materials 0.000 description 6
- 239000002184 metal Substances 0.000 description 6
- 229910018464 Al—Mg—Si Inorganic materials 0.000 description 5
- 230000002411 adverse Effects 0.000 description 4
- 238000005266 casting Methods 0.000 description 4
- 238000005097 cold rolling Methods 0.000 description 4
- 238000010438 heat treatment Methods 0.000 description 4
- 238000007796 conventional method Methods 0.000 description 3
- 238000005098 hot rolling Methods 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005520 cutting process Methods 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 238000000265 homogenisation Methods 0.000 description 2
- 238000001192 hot extrusion Methods 0.000 description 2
- 238000009776 industrial production Methods 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 238000004881 precipitation hardening Methods 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- 229910021365 Al-Mg-Si alloy Inorganic materials 0.000 description 1
- 229910000676 Si alloy Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 238000001125 extrusion Methods 0.000 description 1
- 229910052738 indium Inorganic materials 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000011856 silicon-based particle Substances 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
- 238000011105 stabilization Methods 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
Landscapes
- Powder Metallurgy (AREA)
- Materials For Medical Uses (AREA)
Description
【０００１】[0001]
【産業上の利用分野】この発明は主に強度が重視される
船舶、車両、陸上構造材あるいは機械部品等に使用され
るアルミニウム合金に関するものであり、特に人工時効
処理を施すことによって所要の高強度を与えるようにし
た熱処理型Ｔ６処理用アルミニウム合金に関するもので
ある。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an aluminum alloy used mainly for ships, vehicles, onshore structural materials, mechanical parts, etc., where strength is emphasized. strength relates heat treatable T6 treatment a aluminum alloy to give.
【０００２】[0002]
【従来の技術】従来から、強度が重視される船舶、車
両、陸上構造材などには、溶体化処理および焼入れ後、
人工時効処理を施して所要の高強度を得るという、所謂
Ｔ６処理を施して用いる熱処理型合金が広く使用されて
いる。この種の熱処理型合金としてはＡｌ−Ｍｇ−Ｓｉ
系合金、例えば６０６１合金、６０６３合金、６１５１
合金等が代表的である。2. Description of the Related Art Conventionally, for ships, vehicles, land-based structural materials, etc., for which strength is important, after solution treatment and quenching,
A heat-treatable alloy which is subjected to a so-called T6 treatment, in which a required high strength is obtained by performing an artificial aging treatment, is widely used. Al-Mg-Si is a heat-treatable alloy of this type.
Series alloys, for example, 6061 alloy, 6063 alloy, 6151
Alloys and the like are typical.
【０００３】[0003]
【発明が解決しようとする課題】前述のようなＡｌ−Ｍ
ｇ−Ｓｉ系合金について、溶体化処理−焼入れ後、直ち
に人工時効処理を行なわずに、室温に数日から数ケ月間
放置した場合、室温時効（自然時効）が生じて、その結
果としてその後の人工時効処理で充分に強度が上昇しな
いことがある。このような現象は、２段目の時効（人工
時効）に対して１段目の時効（室温時効）が負の効果を
もたらしているところから、負の２段時効と称される。SUMMARY OF THE INVENTION The above-mentioned Al-M
When the g-Si alloy is left at room temperature for several days to several months without being subjected to artificial aging immediately after solution treatment-quenching, room temperature aging (natural aging) occurs, and as a result, The strength may not be sufficiently increased by the artificial aging treatment. Such a phenomenon is called negative two-stage aging because the first-stage aging (room temperature aging) has a negative effect on the second-stage aging (artificial aging).
【０００４】このような負の時効によって最終的に充分
な高強度が得られないような事態が生じることを防止す
るためには、溶体化処理−焼入れ後、室温に放置される
時間をできるだけ短縮して、長くても２〜３日のうちに
人工時効処理を行なわなければならない。しかしながら
このように溶体化処理−焼入れから人工時効処理までの
期間が制約されることは、工業生産上の不便を招かざる
を得ない。すなわち、実際の工業的な生産現場において
は、溶体化処理−焼入れを行ってから人工時効処理まで
に長期間保管しておきたい場合があり、また需要家側で
人工時効処理を行なう場合は、溶体化処理−焼入れから
人工時効処理までの期間が長期間とならざるを得ないこ
ともある。そこで上述のような制約を受けることなく、
人工時効処理によって常に所要の高強度を得ることがで
きるＡｌ−Ｍｇ−Ｓｉ系熱処理型アルミニウム合金の開
発が強く望まれている。In order to prevent a situation in which a sufficiently high strength is not finally obtained due to such negative aging, the time for which the alloy is left at room temperature after solution treatment and quenching is shortened as much as possible. Then, the artificial aging treatment must be performed within a few days at most. However, the restriction of the period from the solution treatment-quenching to the artificial aging treatment inevitably leads to inconvenience in industrial production. That is, in an actual industrial production site, there is a case where it is desired to store for a long time after the solution treatment-quenching to the artificial aging treatment, and when performing the artificial aging treatment on the customer side, The period from solution treatment-quenching to artificial aging may have to be long. So, without being restricted by the above,
There is a strong demand for the development of an Al-Mg-Si heat-treated aluminum alloy that can always obtain a required high strength by artificial aging.
【０００５】また一般にアルミニウム合金の結晶粒が粗
大であれば、機械的諸性質や成形性、製品の外観等に悪
影響を及ぼすから、Ａｌ−Ｍｇ−Ｓｉ系合金についても
結晶粒が可及的に微細であることが望まれる。In general, when the crystal grains of an aluminum alloy are coarse, mechanical properties, formability, appearance of a product, and the like are adversely affected. Therefore, the crystal grains of an Al—Mg—Si alloy are as large as possible. Fineness is desired.
【０００６】この発明は以上の事情を背景としてなされ
たもので、溶体化処理−焼入れ後、室温での放置による
自然時効の影響を受けることなく、人工時効処理によっ
て確実かつ安定して所要の高強度を得ることができるよ
うなＡｌ−Ｍｇ−Ｓｉ系熱処理型アルミニウム合金、換
言すれば溶体化処理−焼入れ後の室温での放置期間の長
短に左右されることなく、人工時効処理によって所要の
高強度を達成することができるようなＡｌ−Ｍｇ−Ｓｉ
系熱処理型アルミニウム合金を提供し、併せて結晶粒が
微細なＡｌ−Ｍｇ−Ｓｉ系熱処理型アルミニウム合金を
提供することを目的とするものである。The present invention has been made in view of the above circumstances, and after being subjected to solution treatment and quenching, is not affected by natural aging caused by being left at room temperature, and is reliably and stably performed by artificial aging treatment. Al-Mg-Si heat treatment type aluminum alloy capable of obtaining strength, in other words, solution treatment-required height by artificial aging treatment regardless of the length of the standing period at room temperature after quenching. Al-Mg-Si that can achieve strength
An object of the present invention is to provide a heat treatment type aluminum alloy based on Al-Mg-Si and provide a heat treatment type aluminum alloy having fine crystal grains.
【０００７】[0007]
【課題を解決するための手段】前述のような課題を解決
するための方策について本発明者等が鋭意実験・検討を
重ねた結果、合金元素の含有量を適切に設定するばかり
でなく、特にＳｉ量をＭｇ量との関係で適切な値に設定
することによって、室温時効の影響を受けることなく、
人工時効によって確実かつ安定して高強度を得ることが
できるとともに、結晶粒も微細化し得ることを見出し、
この発明をなすに至った。The inventors of the present invention have conducted intensive experiments and studies on measures for solving the above-mentioned problems, and as a result, not only have the content of alloying elements set appropriately, By setting the Si content to an appropriate value in relation to the Mg content, without being affected by room temperature aging,
We found that high strength can be obtained reliably and stably by artificial aging, and that crystal grains can be refined,
The present invention has been made.
【０００８】 具体的には、請求項１の発明のＴ６処理
用アルミニウム合金は、Ｍｇ０．２〜１．２％（ｗｔ
％、以下同じ）、Ｓｉ１．２〜２．６％を、 ０．８５＜｛Ｓｉ（％）−Ｍｇ（％）／１．７３｝＜２．０ を満たすように含有し、残部がＡｌおよび不可避的不純
物よりなることを特徴とするものである。Specifically, the T6 processing according to the first aspect of the present invention
Use A aluminum alloy, Mg0.2~1.2% (wt
%, The same applies hereinafter), Si 1.2 to 2.6% so as to satisfy 0.85 <{Si (%)-Mg (%) / 1.73} <2.0, and the balance is Al and It is characterized by being made of unavoidable impurities.
【０００９】 また請求項２の発明のＴ６処理用アルミ
ニウム合金は、請求項１で規定される合金元素のほか、
さらにＣｕ０．０３〜１．２０％、Ｚｎ０．０３〜１．
５０％、Ｍｎ０．０３〜０．８０％、Ｃｒ０．０３〜
０．３０％、Ｚｒ０．０３〜０．３０％、Ｖ０．０３〜
０．３０％、Ｔｉ０．０５〜０．３０％、Ｆｅ０．０５
〜０．６０％のうちから選ばれた１種または２種以上を
含有するものである。[0009] T6 treatment A Rumi <br/> um alloy of the invention of claim 2, in addition to the alloying elements as defined in claim 1,
Further, Cu 0.03 to 1.20%, Zn 0.03 to 1.
50%, Mn 0.03-0.80%, Cr 0.03-
0.30%, Zr 0.03-0.30%, V0.03-
0.30%, Ti 0.05 to 0.30%, Fe 0.05
One or two or more selected from the range of 0.60% to 0.60%.
【００１０】[0010]
【作用】先ずこの発明における合金成分組成の限定理由
について説明する。First, the reasons for limiting the alloy component composition in the present invention will be described.
【００１１】Ｍｇ：Ｍｇはこの発明の系の合金で基本と
なる合金元素であって、Ｓｉと共同して強度向上に寄与
する。Ｍｇ量が０．２％未満では析出硬化によって強度
向上に寄与するＭｇ２Ｓｉの生成量が少ないため、充分
な強度が得られず、一方１．２％を越えればＭｇ２Ｓｉ
が固溶されなくなって、それ以上は強度向上の効果が得
られなくなるとともに、伸び、成形性が低下するから、
Ｍｇ量は０．２〜１．２％の範囲内とした。Mg: Mg is a basic alloying element in the alloy of the present invention, and contributes to improvement in strength in cooperation with Si. Since Mg amount is small the amount of contributing Mg 2 Si for improving the strength by precipitation hardening is less than 0.2%, no sufficient strength is obtained, whereas if exceeds the 1.2% Mg 2 Si
Is no longer dissolved in solid solution, and beyond that, the effect of improving strength cannot be obtained, and elongation and moldability decrease.
The Mg content was in the range of 0.2 to 1.2%.
【００１２】Ｓｉ：Ｓｉもこの発明の系の合金で基本と
なる合金元素であって、Ｍｇと共同して強度向上に寄与
する。そしてＳｉは析出硬化による強度向上に寄与する
Ｍｇ２Ｓｉの生成に必要な量（Ｍｇに対する当量）より
も過剰に含有させることによって、Ｍｇ２Ｓｉの析出を
促進し、安定な人工時効性を付与するに効果がある。ま
たＳｉが過剰に含有されれば、その過剰なＳｉが鋳造時
に金属Ｓｉの晶出物として生成され、その金属Ｓｉ粒子
の周囲が加工によって変形されて、溶体化処理の際に再
結晶核の生成サイトとなるため、結晶粒の微細化にも寄
与する。したがってＳｉは、Ｍｇ２Ｓｉの生成に必要な
当量すなわち［Ｍｇ（％）／１．７３］（％）よりも過
剰に含有させることとし、かつその過剰量が０．８５％
を越え２．０％未満となるように含有させることとし
た。すなわち、Ｓｉ（％）は、次式 ０．８５＜｛Ｓｉ（％）−Ｍｇ（％）／１．７３｝＜２．０ を満足させることとした。Si: Si is also a basic alloying element in the alloy of the present invention, and contributes to improvement in strength in cooperation with Mg. And Si is added in excess of the amount required for the generation of Mg 2 Si (equivalent to Mg) which contributes to the strength improvement by precipitation hardening, thereby promoting the precipitation of Mg 2 Si and providing stable artificial aging. It is effective for you. If Si is excessively contained, the excess Si is generated as a crystal of metal Si at the time of casting, and the periphery of the metal Si particles is deformed by working, so that recrystallization nuclei are formed during solution treatment. Since it becomes a generation site, it also contributes to refinement of crystal grains. Therefore, Si should be contained in excess of the equivalent required for the generation of Mg 2 Si, that is, [Mg (%) / 1.73] (%), and the excess amount is 0.85%.
And less than 2.0%. That is, Si (%) satisfies the following equation: 0.85 <{Si (%)-Mg (%) / 1.73} <2.0.
【００１３】このようにＳｉがＭｇ２Ｓｉ生成のための
当量よりも過剰に含有されれば、室温により生成したク
ラスターが人工時効処理において強度に寄与する針状
Ｇ．Ｐ．ゾーンに移行しやすくなるため、室温時効が人
工時効に対して負の効果をもたらすおそれが少なくな
り、その結果室温時効の影響を受けずに人工時効により
安定に高強度を得ることが可能となる。Ｓｉ過剰量が
０．８５％以下ではその効果が充分に得られないから、
前記式の下限値は０．８５％を越える必要がある。な
お、より確実に上記の効果を得るためには、Ｓｉ過剰量
すなわち前記式の下限値が１．０％を越えるように定め
ることが望ましい。また同じＭｇの量に対し、前記式が
満たされれば、金属Ｓｉの晶出物がより多く生成され、
その結果溶体化処理時における再結晶核の生成サイトが
多くなり、溶体化処理−焼入れ後の材料で、より一層微
細な結晶粒が得られ、材料の機械的性質、成形性がより
一層向上される。[0013] When Si is contained in excess of the equivalent amount for the generation of Mg 2 Si, the clusters formed at room temperature contribute to the strength of needle-like G. i. P. Because it is easy to move to the zone, the possibility that room temperature aging has a negative effect on artificial aging is reduced, and as a result, high strength can be obtained stably by artificial aging without being affected by room temperature aging. . If the excess amount of Si is 0.85% or less, the effect cannot be sufficiently obtained.
The lower limit of the above equation must exceed 0.85%. Note that, in order to more reliably obtain the above effect, it is desirable that the excess amount of Si, that is, the lower limit of the above expression be set to exceed 1.0%. Also, for the same amount of Mg, if the above expression is satisfied, more crystallized metal Si is produced,
As a result, the number of sites for generating recrystallization nuclei during the solution treatment increases, and finer crystal grains are obtained in the material after the solution treatment-quenching, and the mechanical properties and moldability of the material are further improved. You.
【００１４】なおＳｉの絶対量が１．２％未満ではたと
え前記式で規定されるＳｉ過剰量が０．８５％以上であ
っても前述の各効果が充分に得られず、一方Ｓｉの絶対
量が２．６％を越えれば晶出する金属Ｓｉが粗大となっ
て合金の靱性が低下し、また成形性を劣化させるから、
Ｓｉの絶対量は１．２〜２．６％の範囲内とした。また
前記式で規定されるＳｉ過剰量が２．０％以上となって
も、晶出する金属Ｓｉが粗大となって合金の靱性が低下
し、成形性も劣化するから、前記式の上限値は２．０％
未満とした。If the absolute amount of Si is less than 1.2%, even if the excess amount of Si defined by the above formula is 0.85% or more, the above-mentioned effects cannot be sufficiently obtained. If the amount exceeds 2.6%, the crystallized metal Si becomes coarse and the toughness of the alloy decreases, and the formability deteriorates.
The absolute amount of Si was in the range of 1.2 to 2.6%. Further, even if the excess amount of Si specified by the above formula is 2.0% or more, the crystallized metal Si becomes coarse, the toughness of the alloy is reduced, and the formability is also deteriorated. Is 2.0%
Less than.
【００１５】 Ｃｕ，Ｚｎ，Ｍｎ，Ｃｒ，Ｚｒ，Ｖ，Ｔｉ，Ｆｅ： これらは強度向上のために請求項２の発明において１種
または２種以上添加される。これらのうち、Ｃｕは固溶
強化を通じて強度向上に有効な元素であるが、Ｃｕ量が
０．０３％未満ではその効果が充分に得られず、一方
１．２０％を越えれば耐食性が低下するから、Ｃｕを添
加する場合のＣｕ量は０．０３〜１．２０％の範囲内と
した。またＺｎは合金の時効性の向上を通じて強度向上
に寄与する元素であり、その含有量が０．０３％未満で
は上記の効果が不充分であり、一方１．５０％を越えれ
ば成形性および耐食性が低下するから、Ｚｎを添加する
場合のＺｎ量は０．０３〜１．５０％の範囲内とした。
さらにＭｎ，Ｃｒ，Ｚｒ，Ｖはいずれも結晶粒の微細化
を通じて強度向上に有効な元素であり、また組織の安定
化にも効果があり、いずれも含有量が０．０３％未満で
は上記の効果が充分に得られず、一方Ｍｎが０．８０
％、Ｃｒ，Ｚｒ，Ｖがそれぞれ０．３０％を越えれば、
上記の効果が飽和するばかりでなく、巨大金属間化合物
が生成されて成形性に悪影響を及ぼすおそれがあり、し
たがってＭｎは０．０３〜０．８０％、Ｃｒ，Ｚｒ，Ｖ
はいずれも０．０３〜０．３０％の範囲内とした。また
Ｔｉは鋳塊組織の微細化を通じて強度向上に寄与する元
素であり、その含有量が０．００５％未満では充分な効
果が得られず、一方０．３０％を越えればＴｉ添加の効
果が飽和するばかりでなく、巨大晶出物が生じるおそれ
があるから、Ｔｉは０．００５〜０．３０％の範囲内と
した。そしてまたＦｅも結晶粒の微細化を通じて強度向
上に寄与する元素であり、その含有量が０．０５％未満
では充分な効果が得られず、一方０．６０％を越えれば
成形性が低下するおそれがあり、したがってＦｅは０．
０５〜０．６０％の範囲内とした。なお０．０５％未満
のＦｅは、通常のアルミ地金を用いれば不可避的に含有
される。[0015] Cu, Zn, Mn, Cr, Zr, V, Ti, Fe: it is added one or more in the invention of claim 2 for the upper strength improvement. Of these, Cu is a solid solution
Is an effective element to the strength of improved by strengthening, Cu amount, the effect can not be obtained sufficiently less than 0.03%, since the corrosion resistance is reduced whereas if exceeds 1.20% when adding Cu Was in the range of 0.03 to 1.20%. Zn is an element that contributes to the strength improvement through the improvement of the aging property of the alloy. If its content is less than 0.03%, the above effects are insufficient, while if it exceeds 1.50%, the formability and corrosion resistance are increased. Therefore, the amount of Zn when Zn is added is in the range of 0.03 to 1.50%.
Further, Mn, Cr, Zr, and V all have crystal grain refinement.
Is an element effective for improving the strength of the steel through the alloy, and also has an effect on the stabilization of the structure. When the content is less than 0.03%, the above-mentioned effects cannot be sufficiently obtained.
%, Cr, Zr, and V each exceed 0.30%,
Not only the above effect is saturated, but also a giant intermetallic compound may be generated to adversely affect the formability. Therefore, Mn is 0.03 to 0.80%, Cr, Zr, and V
Were all within the range of 0.03 to 0.30%. The Ti is an element contributing to improving the strength through refining of the ingot tissue, sufficient effects can not be obtained in the content is less than 0.005%, whereas the effect of Ti addition if exceeds 0.30% In addition to saturation, there is a possibility that a giant crystal may be generated. Therefore, Ti is set in the range of 0.005 to 0.30%. In addition, Fe is also suitable for strength through refinement of crystal grains
Is an element contributing to above, sufficient effects can not be obtained in the content is less than 0.05%, whereas there may be deteriorated moldability if exceeds 0.60% thus Fe 0.
In the range of 0.05 to 0.60%. Note that Fe of less than 0.05% is inevitably contained when ordinary aluminum metal is used.
【００１６】以上の各元素のほかは、基本的にはＡｌお
よび不可避的不純物とすれば良い。但し、一般にＭｇを
含有する系の合金においては溶湯の酸化防止のために微
量のＢｅを添加することがあり、この発明の合金の場合
も０．０００１〜０．０１％程度のＢｅの添加は許容さ
れる。また一般に結晶粒微細化のために前述のＴｉと同
時にＢを添加することもあり、この発明の場合もＴｉと
ともに５００ppm 以下のＢを添加することは許容され
る。In addition to the above elements, Al and unavoidable impurities may be basically used. However, in general, a small amount of Be may be added to a Mg-containing alloy in order to prevent oxidation of the molten metal. In the case of the alloy according to the present invention, addition of about 0.0001 to 0.01% of Be is also required. Permissible. Generally, B may be added simultaneously with the above-mentioned Ti in order to refine the crystal grains. In the case of the present invention, addition of 500 ppm or less of B together with Ti is allowable.
【００１７】この発明のアルミニウム合金の製造方法と
しては、従来からＪＩＳ ６０００番系のＡｌ−Ｍｇ−
Ｓｉ系合金に適用されている方法と同様な方法を適用す
ることができる。代表的には、ＤＣ鋳造法等によって鋳
造した後、均質化処理を行ない、さらに熱間圧延を行な
ってから必要に応じ冷間圧延を行なって所要の板厚と
し、その後溶体化処理−焼入れを行ない、さらにその後
人工時効処理を行なえば良い。また必要に応じて、熱間
圧延と冷間圧延との間、あるいは冷間圧延の中途におい
て中間焼鈍を行なっても良い。As a method for producing the aluminum alloy of the present invention, there has been conventionally used a JIS No. 6000 series Al-Mg-
The same method as the method applied to the Si-based alloy can be applied. Typically, after casting by a DC casting method or the like, homogenization treatment is performed, and further hot rolling is performed, and then cold rolling is performed as necessary to obtain a required sheet thickness, and then solution treatment-quenching is performed. And then an artificial aging process. If necessary, intermediate annealing may be performed between hot rolling and cold rolling or in the middle of cold rolling.
【００１８】また、上述のような圧延板のみならず、押
出材として製品に供することもできる。すなわち、常法
に従ってＤＣ鋳造等によりビレットに鋳造し、均質化処
理後熱間押出しに供し、必要に応じて引抜加工等の冷間
加工を行ない、その後溶体化処理−焼入れを施してから
人工時効処理を施せば良い。なおこの場合、熱間押出し
直後に急冷することによって、溶体化処理−焼入れを兼
ねることができる。In addition to the above-mentioned rolled plate, the product can be provided as an extruded material to the product. That is, it is cast into a billet by DC casting or the like according to a conventional method, subjected to hot extrusion after homogenization treatment, cold work such as drawing if necessary, and then subjected to solution treatment-quenching and then artificial aging. Processing may be performed. In this case, rapid cooling immediately after hot extrusion can serve as both solution treatment and quenching.
【００１９】ここで、この発明のアルミニウム合金で
は、後の実施例でも示すように、溶体化処理−焼入れ後
に室温に放置した場合にも、室温時効の影響を受けるこ
となく、人工時効処理によって所要の高強度を確実かつ
安定して得ることができるから、溶体化処理−焼入れか
ら人工時効処理までの期間は特に制限されることはな
い。Here, in the aluminum alloy according to the present invention, as shown in the later examples, even when the aluminum alloy is left at room temperature after solution treatment and quenching, the aluminum alloy is not affected by room temperature aging and required by artificial aging. Can be obtained reliably and stably, and the period from the solution treatment-quenching to the artificial aging treatment is not particularly limited.
【００２０】[0020]
実施例１：表１のＡ１〜Ａ６，Ｂ１〜Ｂ３に示す各合金
を常法に従ってＤＣ鋳造し、得られた鋳塊を５３０℃×
１０時間均質化処理した後、熱間圧延および冷間圧延を
行なって板厚１mmの圧延板とした。次いで溶体化処理−
焼入れを行なった。この溶体化処理焼入れは、バッチ焼
鈍炉もしくは連続焼鈍炉を用いて行ない、バッチ焼鈍炉
による場合は５３０℃×１時間溶体化処理を施して水焼
入れし、連続焼鈍炉による場合は５４０℃×１０秒の加
熱後強制冷却した。焼入れ後の各圧延板について、それ
ぞれ半分に切分けて、一方は次の（イ）の処理を、他方
は（ロ）の処理を施した。 （イ）焼入れ後、直ちに１７５℃×８時間の時効処理を
施した。 （ロ）焼入れ後、室温（２０℃）に２０日間放置した
後、１７５℃×８時間の時効処理を施した。Example 1: Each alloy shown in Tables A1 to A6 and B1 to B3 was DC-cast according to a conventional method.
After homogenizing for 10 hours, hot rolling and cold rolling were performed to obtain a rolled plate having a thickness of 1 mm. Then solution treatment-
Quenching was performed. This solution treatment quenching is performed using a batch annealing furnace or a continuous annealing furnace. In the case of a batch annealing furnace, a solution treatment is performed at 530 ° C. × 1 hour, and water quenching is performed. In the case of a continuous annealing furnace, 540 ° C. × 10 5 After heating for 2 seconds, it was forcibly cooled. Each quenched rolled plate was cut in half, and one was subjected to the following process (a) and the other was subjected to the process (b). (A) Immediately after quenching, aging treatment was performed at 175 ° C for 8 hours. (Ii) After quenching, the resultant was left at room temperature (20 ° C.) for 20 days, and then subjected to aging treatment at 175 ° C. × 8 hours.
【００２１】上記（イ）もしくは（ロ）の処理後の各板
について、引張り強さを調べた結果を表２に示す。また
溶体化処理−焼入れ直後の結晶粒径を切断法によって調
べた結果を表２中に併せて示す。なおＡ１〜Ａ６の合金
はいずれも合金元素含有量がこの発明で規定する範囲を
満たすと同時にＳｉ量とＭｇ量との関係もこの発明で規
定する関係式を満足している発明合金、Ｂ１〜Ｂ３はＳ
ｉ量が不足し、前記関係式を満たしていない比較合金で
あって、特にＢ３は従来の６０６１合金に相当する合金
である。Table 2 shows the results of examining the tensile strength of each plate after the above-mentioned treatment (a) or (b). Table 2 also shows the results obtained by examining the crystal grain size immediately after solution treatment and quenching by a cutting method. The alloys A1 to A6 each have an alloy element content satisfying the range defined in the present invention, and at the same time, the relationship between the Si amount and the Mg amount also satisfies the relational expression defined in the present invention. B3 is S
A comparative alloy having a shortage of i and not satisfying the above relational expression. In particular, B3 is an alloy corresponding to the conventional 6061 alloy.
【００２２】[0022]
【表１】 [Table 1]
【００２３】[0023]
【表２】 [Table 2]
【００２４】この実施例１は圧延材に適用したものであ
るが、表２から明らかなように、各合金元素の含有量が
この発明で規定する範囲内でしかもＳｉ量がＭｇ量との
関連において前記関係式を満たしている発明合金Ａ１〜
Ａ６は、いずれも溶体化処理−焼入れ後に室温に２０日
間放置してから人工時効処理を施した場合（ロ）におい
ても、溶体化処理−焼入れ直後に人工時効処理施した場
合（イ）と同等の高強度が得られ、室温時効の影響を受
けていないことが判る。またこれらの発明合金は、結晶
粒も最大で６９μｍと、微細化されていることが判る。Example 1 was applied to a rolled material. As is clear from Table 2, the content of each alloying element was within the range specified in the present invention, and the relationship between the Si content and the Mg content. Inventive alloys A1 to
A6 is the same as (a) when the artificial aging treatment is carried out immediately after the solution treatment-quenching after being left at room temperature for 20 days after the solution treatment-quenching (b). It can be seen that a high strength was obtained, and the sample was not affected by aging at room temperature. In addition, it can be seen that these invention alloys have a finer crystal grain of 69 μm at the maximum.
【００２５】これに対し比較合金Ｂ１〜Ｂ３は、いずれ
もＳｉ量がＭｇ量との関連において前記式で規定する下
限値よりも少ないものであるが、これらの比較合金で
は、溶体化処理−焼入れ後に室温に２０日間放置した場
合に人工時効処理によって充分な高強度が得られず、室
温時効の悪影響を受けていることが判る。またこれらの
比較合金は、結晶粒もさほど微細とはならなかった。On the other hand, in the comparative alloys B1 to B3, the amount of Si is smaller than the lower limit specified by the above formula in relation to the amount of Mg. When left at room temperature for 20 days later, it was found that a sufficiently high strength could not be obtained by the artificial aging treatment, which was adversely affected by room temperature aging. Also, these comparative alloys did not have very fine crystal grains.
【００２６】実施例２：表３のＣ１〜Ｃ４，Ｄ１，Ｄ２
に示す合金を常法にしたがって２００mmφのビレットに
ＤＣ鋳造し、得られたビレットを５３０℃で８時間均質
化処理後、４２０℃で熱間押出しを行なった。このとき
の押出比は１０：１である。得られた押出材について、
バッチ焼鈍炉で５４０℃×１時間の溶体化処理を施し、
水焼入れした。焼入れ後の各材料についてそれぞれ２分
し、実施例１と同様に一方を前記（イ）の条件で、他方
を前記（ロ）の条件で処理した。Example 2: C1 to C4, D1 and D2 in Table 3
Was cast into a 200 mmφ billet by a conventional method, and the obtained billet was homogenized at 530 ° C. for 8 hours and then hot-extruded at 420 ° C. The extrusion ratio at this time is 10: 1. About the obtained extruded material,
Solution treatment at 540 ° C x 1 hour in a batch annealing furnace,
Water quenched. Each of the quenched materials was divided into two, and one was treated under the condition (a) and the other was treated under the condition (b) as in Example 1.
【００２７】（イ）もしくは（ロ）の処理後の各材料に
ついて引張り強さを調べた結果を表４に示す。また溶体
化処理−焼入れ直後の結晶粒径を切断法により調べた結
果を表４中に併せて示す。なおここでＣ１〜Ｃ４の各合
金はいずれも合金元素含有量がこの発明で規定する範囲
内であると同時にＳｉ量とＭｇ量との関係もこの発明で
規定する関係式を満たしている発明合金であり、一方Ｄ
１，Ｄ２の合金はＳｉ量が不足し、前記関係式を満たし
ていない比較合金である。Table 4 shows the results of examining the tensile strength of each material after the treatment (a) or (b). The results obtained by examining the crystal grain size immediately after solution treatment and quenching by a cutting method are also shown in Table 4. Here, each of the alloys C1 to C4 has an alloy element content within the range specified in the present invention, and at the same time, the relationship between the Si amount and the Mg amount also satisfies the relational expression specified in the present invention. While D
The alloys 1 and D2 are comparative alloys that do not satisfy the above-mentioned relational expression due to insufficient amount of Si.
【００２８】[0028]
【表３】 [Table 3]
【００２９】[0029]
【表４】 [Table 4]
【００３０】この実施例２は押出材に適用したものであ
るが、表４から明らかなように、各合金元素の含有量が
この発明で規定する範囲内でしかもＳｉ量がＭｇ量との
関連において前記関係式を満たしている発明合金Ｃ１〜
Ｃ４は、いずれも溶体化処理−焼入れ後に室温に２０日
間放置してから人工時効処理を施した場合（ロ）におい
ても、溶体化処理−焼入れ直後に人工時効処理施した場
合（イ）と同等の高強度が得られ、室温時効の影響を受
けていないことが判る。またこれらの発明合金は、結晶
粒も最大で８８μｍと、微細化されていることが判る。Example 2 was applied to an extruded material. As is clear from Table 4, the content of each alloying element is within the range specified in the present invention, and the relationship between the Si content and the Mg content. In the invention alloy C1 satisfying the above relational expression
C4 is the same as (a) when the solution aging treatment is carried out and then left at room temperature for 20 days and then subjected to the artificial aging treatment (b). It can be seen that a high strength was obtained, and the sample was not affected by aging at room temperature. In addition, it can be seen that these invention alloys have a fine crystal grain of at most 88 μm.
【００３１】これに対し比較合金Ｄ１，Ｄ２はいずれも
Ｓｉ量がＭｇ量との関連において前記式で規定する下限
値よりも少ないものであるが、これらの比較合金では、
溶体化処理−焼入れ後に室温に２０日間放置した場合に
人工時効処理によって充分な高強度が得られず、室温時
効の悪影響を受けていることが判る。またこれらの比較
合金は、結晶粒もさほど微細とはならなかった。On the other hand, in each of the comparative alloys D1 and D2, the amount of Si is smaller than the lower limit specified by the above equation in relation to the amount of Mg.
Solution treatment-When left at room temperature for 20 days after quenching, a sufficiently high strength was not obtained due to the artificial aging treatment, indicating that the room temperature aging was adversely affected. Also, these comparative alloys did not have very fine crystal grains.
【００３２】[0032]
【発明の効果】実施例からも明らかなように、この発明
のＴ６処理用アルミニウム合金は、Ｓｉ量をＭｇ量に応
じて適切な範囲内に定めることによって、溶体化処理一
焼入れ後の室温時効の影響を受けることなく、人工時効
処理により所要の高強度を得ることができ、そのため溶
体化処理−焼入れから人工時効処理までの期間が特に短
く制約されることがないため、工業的な規模での製造上
極めて有利であり、また結晶粒が微細であるため機械的
性質、成形性、外観が優れる等の長所も有する。As is clear from the embodiments, the present invention
'S T6 treatment for A aluminum alloy, by determining the amount of Si within a suitable range according to the Mg content, without being affected by the room temperature aging after solution treatment one hardening, high strength required by the artificial aging Since the period from solution treatment-quenching to artificial aging treatment is not particularly short and is not restricted, it is extremely advantageous for production on an industrial scale, and the crystal grains are fine. Therefore, it also has advantages such as excellent mechanical properties, moldability, and appearance.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 小松原 俊雄 東京都中央区日本橋室町４丁目３番18号 スカイアルミニウム株式会社内 (56)参考文献 特開 昭63−103046（ＪＰ，Ａ) 特開 昭64−65243（ＪＰ，Ａ) 特開 平３−180453（ＪＰ，Ａ) 特開 平４−231434（ＪＰ，Ａ) ──────────────────────────────────────────────────続 き Continuation of front page (72) Inventor Toshio Komatsubara 4-3-1-18 Nihonbashi Muromachi, Chuo-ku, Tokyo Inside Sky Aluminum Co., Ltd. (56) References JP-A-63-103046 (JP, A) JP-A Sho 64-65243 (JP, A) JP-A-3-180453 (JP, A) JP-A-4-231434 (JP, A)
Claims (2)
じ）、Ｓｉ１．２〜２．６％を、 ０．８５＜｛Ｓｉ（％）−Ｍｇ（％）／１．７３｝＜２．０ を満たすように含有し、残部がＡｌおよび不可避的不純
物よりなり、結晶粒が微細でかつ安定な人工時効性を有
するＴ６処理用アルミニウム合金。1. Mg 0.2-1.2% (wt%, the same applies hereinafter), Si 1.2-2.6%, 0.85 <{Si (%)-Mg (%) / 1.73} <contained so as to satisfy 2.0, the balance being of Al and unavoidable impurities, the crystal grains are fine and have a stable artificial aging resistance <br /> be that T6 treatment a aluminum alloy.
２．６％を、 ０．８５＜｛Ｓｉ（％）−Ｍｇ（％）／１．７３｝＜２．０ を満たすように含有し、かつＣｕ０．０３〜１．２０
％、Ｚｎ０．０３〜１．５０％、Ｍｎ０．０３〜０．８
０％、Ｃｒ０．０３〜０．３０％、Ｚｒ０．０３〜０．
３０％、Ｖ０．０３〜０．３０％、Ｔｉ０．０５〜０．
３０％、Ｆｅ０．０５〜０．６０％のうちから選ばれた
１種または２種以上を含有し、残部がＡｌおよび不可避
的不純物よりなり、結晶粒が微細でかつ安定な人工時効
性を有するＴ６処理用アルミニウム合金。2. Mg 0.2-1.2%, Si 1.2-
2.6% is contained so as to satisfy 0.85 <{Si (%)-Mg (%) / 1.73} <2.0, and Cu is 0.03 to 1.20.
%, Zn 0.03 to 1.50%, Mn 0.03 to 0.8
0%, Cr 0.03 to 0.30%, Zr 0.03 to 0.
30%, V 0.03-0.30%, Ti 0.05-0.
30%, one or two or more selected from 0.05 to 0.60% Fe, with the balance being Al and unavoidable impurities, having fine and stable artificial aging properties. T6 treatment for a aluminum alloy you.
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|---|---|---|---|
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP4101762A JP2663078B2 (en) | 1992-03-27 | 1992-03-27 | Aluminum alloy for T6 treatment with stable artificial aging |
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|---|---|
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| JP2663078B2 true JP2663078B2 (en) | 1997-10-15 |
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| WO1999023266A1 (en) | 1997-10-31 | 1999-05-14 | The Furukawa Electric Co., Ltd. | Extruded material of aluminum alloy for structural members of automobile body and method of manufactruing the same |
| JP3398085B2 (en) * | 1999-04-28 | 2003-04-21 | 古河電気工業株式会社 | Aluminum alloy materials for welded structures and their welded joints |
| JP2001181768A (en) | 1999-12-17 | 2001-07-03 | Furukawa Electric Co Ltd:The | Aluminum alloy extruded material for automotive structural member and producing method therefor |
| JP5159196B2 (en) * | 2007-07-20 | 2013-03-06 | 古河スカイ株式会社 | Aluminum alloy for high pressure hydrogen gas storage container |
| JP2011252212A (en) * | 2010-06-03 | 2011-12-15 | Sumitomo Light Metal Ind Ltd | Method for forming processing of 6000 series aluminum alloy material, and forming processed product |
| DE102015013540A1 (en) * | 2015-10-19 | 2017-04-20 | Trimet Aluminium Se | aluminum alloy |
| CN112813316B (en) * | 2020-12-30 | 2022-06-28 | 安徽鑫铂铝业股份有限公司 | Preparation method of high-strength corrosion-resistant aluminum alloy |
| CN112845649A (en) * | 2020-12-30 | 2021-05-28 | 安徽鑫铂铝业股份有限公司 | Preparation method of high-toughness large-sized vehicle aluminum profile |
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| JPS63103046A (en) * | 1986-10-20 | 1988-05-07 | Furukawa Alum Co Ltd | Aluminum alloy for cold forging |
| JPH0674480B2 (en) * | 1987-09-03 | 1994-09-21 | 本田技研工業株式会社 | Forming and welding alloy sheet excellent in weldability, rust resistance, formability and bake hardenability, and method for producing the same |
| JPH03180453A (en) * | 1989-12-07 | 1991-08-06 | Kobe Steel Ltd | Production of aluminum alloy stock for cold forging |
| JPH04231434A (en) * | 1990-12-27 | 1992-08-20 | Furukawa Alum Co Ltd | Aluminum alloy for forming excellent in baking hardenability |
-
1992
- 1992-03-27 JP JP4101762A patent/JP2663078B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPH05271834A (en) | 1993-10-19 |
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