JPH0967659A - Method for heat treating aluminum-magnesium-silicon base aluminum alloy - Google Patents
Method for heat treating aluminum-magnesium-silicon base aluminum alloyInfo
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- JPH0967659A JPH0967659A JP24519595A JP24519595A JPH0967659A JP H0967659 A JPH0967659 A JP H0967659A JP 24519595 A JP24519595 A JP 24519595A JP 24519595 A JP24519595 A JP 24519595A JP H0967659 A JPH0967659 A JP H0967659A
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、Ａｌ−Ｍｇ−Ｓｉ
系アルミニウム合金、例えば建築用アルミサッシなどと
して広く用いられているＡｌ−Ｍｇ−Ｓｉ系合金である
ＪＩＳ６０００系アルミニウム合金の熱処理方法に関す
るものである。TECHNICAL FIELD The present invention relates to Al--Mg--Si.
The present invention relates to a heat treatment method for a system aluminum alloy, for example, a JIS6000 system aluminum alloy which is an Al-Mg-Si system alloy widely used as an aluminum sash for buildings and the like.
【０００２】[0002]
【従来の技術】Ａｌ−Ｍｇ−Ｓｉ系アルミニウム合金の
中でも、建築用アルミサッシに用いられる代表的な６０
００系アルミニウム合金押出材は、高温加工から急冷、
矯正された後、人工時効硬化処理（Ｔ5 ）を施した状態
で使用される。この合金系ではＭｇ2 Ｓｉ系の析出相が
析出することにより強度が上昇することが知られてお
り、熱処理を施すことにより機械的特性が上昇する。2. Description of the Related Art Among Al-Mg-Si based aluminum alloys, a typical 60 used for aluminum sashes for construction.
00 series aluminum alloy extruded material is quenched from high temperature processing,
After being straightened, it is used after being subjected to artificial age hardening treatment (T 5 ). It is known that in this alloy system, the strength is increased by the precipitation of the Mg 2 Si-based precipitation phase, and the mechanical properties are increased by the heat treatment.
【０００３】[0003]
【発明が解決しようとする課題】上記合金を工業生産す
る上で、人工時効硬化処理は各社各様の処理条件で行わ
れているのが実情である。一般的に所定の強度を得るた
めには、低温の場合は長時間熱処理する必要があり、高
温の場合は処理時間が短縮されるものの、Ｍｇ2 Ｓｉの
析出相の不均一析出を起こし、強度のバラツキが大き
く、ピーク強度も低くなる傾向が見られる。またこの場
合、熱処理時間が長くなると過時効状態となり、強度が
さらに低下していくことが知られている（図２参照）。
そこで、効率よく熱処理するためには、最適な熱処理条
件を改善、開発する必要がある。従って、本発明の目的
は、Ａｌ−Ｍｇ−Ｓｉ系アルミニウム合金押出材の強度
を比較的短時間に効率よく高めることができ、従ってエ
ネルギー費削減に伴なうコストダウン及び生産性向上を
図れる熱処理方法を提供することにある。In the industrial production of the above alloy, the artificial age hardening treatment is actually carried out under the treatment conditions of each company. Generally, in order to obtain a predetermined strength, it is necessary to heat-treat for a long time at a low temperature, and the processing time is shortened at a high temperature, but the Mg 2 Si precipitation phase causes non-uniform precipitation and Shows a large variation and the peak intensity tends to be low. Further, in this case, it is known that when the heat treatment time becomes long, the state becomes overaged and the strength further decreases (see FIG. 2).
Therefore, in order to perform heat treatment efficiently, it is necessary to improve and develop optimum heat treatment conditions. Therefore, an object of the present invention is to improve the strength of an Al-Mg-Si-based aluminum alloy extruded material efficiently in a relatively short time, and thus to reduce the cost associated with the reduction of energy cost and improve the productivity. To provide a method.
【０００４】[0004]
【課題を解決するための手段】本発明は、上記の課題を
解決するため、Ｍｇ2 Ｓｉ析出相を均一に析出させ、Ａ
ｌ−Ｍｇ−Ｓｉ系アルミニウム押出合金における所定の
強度を短時間で得る方法を開発したものである。すなわ
ち、本発明のＡｌ−Ｍｇ−Ｓｉ系アルミニウム合金の熱
処理方法は、押出加工後、急冷・矯正した押出材を人工
時効硬化処理するに当って、温度１６０〜１８０℃の範
囲で第１段予備時効処理を施すことによりＭｇ2 Ｓｉ析
出相を均一に析出させ、次いで温度１９５〜２２０℃の
範囲で１．５〜８．０時間第２段時効処理を施すことに
より第１段予備時効時に析出させたＭｇ2 Ｓｉ析出相を
成長させることを特徴としている。In order to solve the above-mentioned problems, the present invention is to uniformly precipitate the Mg 2 Si precipitation phase,
This is a method for obtaining a predetermined strength in an l-Mg-Si based aluminum extruded alloy in a short time. That is, the heat treatment method of the Al-Mg-Si-based aluminum alloy of the present invention, after the extrusion processing, in the artificial age hardening treatment of the rapidly cooled and straightened extruded material, the first stage preliminary in the temperature range of 160 to 180 ° C. The Mg 2 Si precipitation phase is uniformly precipitated by performing the aging treatment, and then the second stage aging treatment is performed in the temperature range of 195 to 220 ° C. for 1.5 to 8.0 hours to precipitate during the first stage preliminary aging. It is characterized in that the Mg 2 Si precipitation phase thus grown is grown.
【０００５】好適な態様においては、第１段予備時効処
理は１６０〜１８０℃の温度範囲で保持時間が０．５〜
１．５時間、より好ましくは１７０℃±５℃の温度で保
持時間が０．５〜１．５時間、第２段時効処理は１９５
〜２２０℃の温度範囲で保持時間が１．５〜３．０時
間、より好ましくは２０５℃±５℃の温度で保持時間が
１．５〜３．０時間の条件で熱処理を行う。なお、押出
加工直後から第１段予備時効処理前までは長時間放置し
て自然時効させても差支えない。In a preferred embodiment, the first stage pre-aging treatment has a holding time of 0.5 to 160 ° C. in a temperature range of 160 to 180 ° C.
1.5 hours, more preferably at a temperature of 170 ° C. ± 5 ° C., holding time of 0.5 to 1.5 hours, second stage aging treatment is 195
The heat treatment is performed in the temperature range of 220 ° C to 220 ° C for 1.5 to 3.0 hours, and more preferably at 205 ° C ± 5 ° C for 1.5 to 3.0 hours. It should be noted that there is no problem even if it is left for a long time to be naturally aged immediately after the extrusion process and before the first stage preliminary aging treatment.
【０００６】[0006]
【発明の実施の形態】本発明で対象とするＡｌ−Ｍｇ−
Ｓｉ系アルミニウム合金押出材としては、ＪＩＳ６００
０系アルミニウム合金、例えば表１に示すようなＪＩＳ
６０６３合金などが挙げられる。BEST MODE FOR CARRYING OUT THE INVENTION Al-Mg- which is the object of the present invention
JIS600 is an extruded material of Si-based aluminum alloy.
0 series aluminum alloy, for example JIS as shown in Table 1
6063 alloy etc. are mentioned.
【表１】 [Table 1]
【０００７】上記のＡｌ−Ｍｇ−Ｓｉ系アルミニウム合
金はＭｇ2 Ｓｉ析出相による時効硬化を示すが、６０６
３合金の他にも６０６１、６Ｎ０１合金など他の６００
０系アルミニウム合金についても同様の析出相による時
効硬化過程を示すことが知られている。すなわち、この
合金系の時効析出過程は次に示すとおりである。 過飽和固溶体→クラスター→ＧＰゾーン〔（Ｉ）→（I
I）〕→中間相（β’）→安定相（β） この中でも機械的性質に大きく影響を与えるのはＧＰゾ
ーンと中間相である。すなわち、その前段階である析出
核を均一に析出させて、その後の析出相の変態、成長を
いかに効率良く促進させるかがポイントとなる。本発明
の熱処理方法は、第１段予備時効処理においてクラスタ
ー等の均一な析出核を生成させ、第２段の時効処理にお
いて、その析出核からＧＰゾーン、中間相などの析出物
への変態及び成長を促進させる方法と言える。したがっ
て、本発明による熱処理方法は、この時効析出過程をと
るＡｌ−Ｍｇ−Ｓｉ系アルミニウム合金の全てに対し有
効である。The Al--Mg--Si system aluminum alloy described above shows age hardening due to the Mg 2 Si precipitation phase.
In addition to 3 alloys, 6001, such as 6061 and 6N01 alloys
It is known that 0 series aluminum alloys also show a similar age hardening process due to a precipitation phase. That is, the aging precipitation process of this alloy system is as follows. Supersaturated solid solution → cluster → GP zone [(I) → (I
I)] → Intermediate phase (β ′) → Stable phase (β) Among these, the GP zone and the intermediate phase have a great influence on the mechanical properties. That is, the point is to uniformly precipitate the precipitation nuclei, which is the previous stage, and efficiently promote the subsequent transformation and growth of the precipitation phase. The heat treatment method of the present invention produces uniform precipitation nuclei such as clusters in the first stage preliminary aging treatment, and transforms the precipitation nuclei into precipitates such as GP zone and intermediate phase in the second stage aging treatment and It can be said to be a method of promoting growth. Therefore, the heat treatment method according to the present invention is effective for all Al-Mg-Si-based aluminum alloys that undergo this aging precipitation process.
【０００８】本発明の熱処理方法において、第１段予備
時効処理温度を１６０〜１８０℃の温度範囲に設定する
のは、１６０℃未満では機械的性質に有効な析出相とし
て成長するだけの析出核が生成せず、一方、１８０℃を
超えると、析出核は生成するものの均一ではなく、第２
段時効処理を施しても効率の良い析出相とはならないた
めである。また、第２段時効処理温度を１９５〜２２０
℃の温度範囲に設定するのは、１９５℃未満では析出相
は期待した成長速度が得られず、逆に２２０℃を超える
と析出相が成長しすぎ、いわゆる過時効状態となるため
である。In the heat treatment method of the present invention, the first stage pre-aging treatment temperature is set to a temperature range of 160 to 180 ° C. The precipitation nuclei are simply grown as a precipitation phase effective for mechanical properties at temperatures lower than 160 ° C. On the other hand, when the temperature exceeds 180 ° C., precipitation nuclei are formed but are not uniform,
This is because even if the step aging treatment is applied, an efficient precipitation phase cannot be obtained. Further, the second stage aging treatment temperature is 195 to 220.
The reason why the temperature range is set to ℃ is that the precipitation phase does not achieve the expected growth rate below 195 ° C, and conversely, if it exceeds 220 ° C, the precipitation phase grows too much and becomes a so-called overaged state.
【０００９】上記熱処理温度条件では、第１段予備時効
処理温度と第２段時効処理温度の差△Ｔが△Ｔ≧１５℃
を満たしているが、さらに好ましくは△Ｔ≧２５℃を満
たしていると効果的である。△Ｔ＜１５℃の場合、析出
相の生成と成長が同時に起こり、結果的に不均一な組織
となり、従来法の熱処理と何ら変わらなくなり、期待し
た効果が得られない。また、△Ｔ≧２５℃の場合、析出
核の生成及び成長の各段階の役割を分割し、析出を効率
よく促すため、より効果的である。Under the above heat treatment temperature conditions, the difference ΔT between the first stage preliminary aging temperature and the second stage aging temperature is ΔT ≧ 15 ° C.
However, it is more effective if ΔT ≧ 25 ° C. is satisfied. When ΔT <15 ° C., the precipitation phase is generated and grown at the same time, resulting in a non-uniform structure, which is no different from the heat treatment of the conventional method, and the expected effect cannot be obtained. Further, when ΔT ≧ 25 ° C., the role of each stage of generation and growth of precipitation nuclei is divided and the precipitation is efficiently promoted, which is more effective.
【００１０】同様に、第１段予備時効時間についても保
持時間を０．５〜１．５時間に設定するのは、０．５時
間より少ないと有効な析出核が得られず、強度発現が不
安定になるためである。また保持時間が１．５時間を超
えると、第２段時効時間と合わせて一般的な時効処理時
間を超え、経済的ではなくなる。さらに、第２段時効時
間が１．５〜８．０時間で好ましくは１．５〜３．０時
間の保持時間で処理するのは、１．５時間未満では析出
相の成長が期待できないためである。逆に、８時間を超
えると過時効状態になり、強度の低下を招くため、上限
を８時間とする必要がある。さらに、８時間を超えた場
合、経済的にも効果がない。Similarly, with respect to the first stage preliminary aging time, the holding time is set to 0.5 to 1.5 hours. If the holding time is less than 0.5 hours, effective precipitation nuclei cannot be obtained and strength development is not achieved. This is because it becomes unstable. Further, if the holding time exceeds 1.5 hours, it exceeds the general aging treatment time together with the second stage aging time, which is not economical. Further, the second stage aging time is 1.5 to 8.0 hours, preferably 1.5 to 3.0 hours, so that the growth of the precipitation phase cannot be expected in less than 1.5 hours. Is. On the other hand, if it exceeds 8 hours, the steel will be overaged and the strength will be lowered. Therefore, it is necessary to set the upper limit to 8 hours. Further, if it exceeds 8 hours, it is economically ineffective.
【００１１】[0011]
【実施例】以下、実施例を示して本発明の効果について
具体的に説明するが、本発明が下記実施例に限定される
ものでないことはもとよりである。EXAMPLES The effects of the present invention will be specifically described below by showing Examples, but it goes without saying that the present invention is not limited to the following Examples.
【００１２】実施例１〜３及び比較例１〜１２ 表２に示す合金組成のアルミニウム合金を通常の方法で
溶解鋳造を行い、６インチビレットとし、このビレット
に５７０℃×４ｈｒの均質化処理を施し、押出された３
ｍｍ厚の平板状の形材を用いた。これらのサンプルに表
３に示す各種熱処理を施し、硬度測定を中心に機械的性
質を調べた。その結果を以下に示す。Examples 1 to 3 and Comparative Examples 1 to 12 Aluminum alloys having the alloy compositions shown in Table 2 were melt-cast by a usual method to form a 6-inch billet, and this billet was homogenized at 570 ° C. for 4 hours. Delivered and extruded 3
A plate-shaped material having a thickness of mm was used. Various heat treatments shown in Table 3 were applied to these samples, and the mechanical properties were examined centering on hardness measurement. The results are shown below.
【表２】 [Table 2]
【００１３】[0013]
【表３】 [Table 3]
【００１４】表３中、実施例１〜３は、本発明の条件に
よる二段階熱処理を、比較例１〜７は従来法による一段
階熱処理を、比較例８〜１２は本発明の範囲外の条件に
よる二段階熱処理を行った例である。なお、熱処理は、
実ラインの昇温過程に即して一段階目の所定の熱処理温
度に達するまでの時間を０．５ｈｒとした。In Table 3, Examples 1 to 3 are two-step heat treatments under the conditions of the present invention, Comparative Examples 1 to 7 are conventional one-step heat treatments, and Comparative Examples 8 to 12 are outside the scope of the present invention. This is an example of performing the two-step heat treatment under the conditions. The heat treatment is
The time required to reach the predetermined heat treatment temperature in the first step was set to 0.5 hr in accordance with the temperature rising process of the actual line.
【００１５】試験例１（硬度測定） 実施例１〜３、比較例１〜７及び比較例８〜１２につい
て、その硬度測定結果をそれぞれ図１〜３に示す。な
お、所定の硬度の目安は、これまでの実績から硬度値６
８とする。また、図１〜３は０．５ｈｒの昇温時間を含
んでいる（以下、図４〜８についても同様である）。Test Example 1 (Hardness Measurement) The hardness measurement results of Examples 1 to 3, Comparative Examples 1 to 7 and Comparative Examples 8 to 12 are shown in FIGS. In addition, the standard of the predetermined hardness is the hardness value 6 from the actual results so far.
8 is assumed. Further, FIGS. 1 to 3 include a temperature rising time of 0.5 hr (hereinafter, the same applies to FIGS. 4 to 8).
【００１６】図２は従来法による一段階熱処理を行った
場合で、所定の硬度を得るためには、低温の場合は長時
間熱処理する必要があり、高温の場合は処理時間が短縮
されるものの、強度のバラツキが大きく、ピーク強度も
低くなる傾向が見られる。またこの場合、熱処理時間が
長くなると過時効状態となり、強度がさらに低下してい
くことがわかる。これに対し、図１に示す本発明の方法
では、所定の硬度に達する時間が短く、最高硬度に達し
た後も直ちに過時効状態とはならない。図３は、二段階
熱処理法における本発明の範囲外の例であるが、図１と
比較すると第１段熱処理の時間が短い場合（比較例
８）、第２段熱処理の温度が低い場合（比較例９）、第
２段熱処理の時間が短い場合（比較例１０）、第１段熱
処理の時間が長い場合（比較例１１）、第１段熱処理の
温度が高い場合（比較例１２）、いずれも所定の硬度に
達する時間がかかることがわかる。このように、本発明
の熱処理方法では、短時間で所定の硬度に達することが
わかる。FIG. 2 shows the case where the conventional one-step heat treatment is carried out. In order to obtain a predetermined hardness, it is necessary to perform the heat treatment for a long time at a low temperature, and the treatment time is shortened at a high temperature. There is a tendency for the strength to vary greatly and the peak strength to decrease. Further, in this case, it can be seen that when the heat treatment time becomes long, the state becomes overaged and the strength further decreases. On the other hand, in the method of the present invention shown in FIG. 1, it takes a short time to reach a predetermined hardness, and the overaging state does not occur immediately after the maximum hardness is reached. FIG. 3 shows an example of the two-step heat treatment method outside the scope of the present invention, but when the time of the first-step heat treatment is shorter than that of FIG. 1 (Comparative Example 8), and when the temperature of the second-step heat treatment is low ( Comparative Example 9), when the second stage heat treatment time is short (Comparative Example 10), when the first stage heat treatment time is long (Comparative Example 11), when the first stage heat treatment temperature is high (Comparative Example 12), It can be seen that it takes time to reach a predetermined hardness. Thus, it can be seen that the heat treatment method of the present invention reaches a predetermined hardness in a short time.
【００１７】試験例２（機械的性質の測定） 次に、上記実施例１、比較例３及び４について、機械的
性質（引張強度及び耐力）を調べた結果を図４及び図５
に示す。図４及び図５から明らかなように、本発明の実
施例１では比較例に比べて引張強度、耐力共に短時間で
所定の強度に達したことがわかる。Test Example 2 (Measurement of Mechanical Properties) Next, the results of examining the mechanical properties (tensile strength and proof stress) of Example 1 and Comparative Examples 3 and 4 are shown in FIGS. 4 and 5.
Shown in As is clear from FIGS. 4 and 5, it can be seen that in Example 1 of the present invention, both the tensile strength and the proof stress reached predetermined strengths in a short time as compared with the comparative example.
【００１８】試験例３（室温時効の影響） 室温時効の影響を調べるため、実施例１の試料につい
て、室温で２週間放置し、その後本発明の方法による熱
処理（実施例１の方法）を行い、その機械的性質（硬
度、引張強度、耐力）を調べた。その硬度測定の結果を
図６に示し、図７及び図８には引張り強度及び耐力の結
果をそれぞれ示す。図６〜８から明らかなように、硬
度、引張強度及び耐力のいずれの特性も室温放置しない
ものと同等であることがわかる。従って、本発明の方法
に従って室温放置したものを二段階時効しても構わない
ことがわかる。Test Example 3 (Effect of Room Temperature Aging) In order to investigate the effect of room temperature aging, the sample of Example 1 was left at room temperature for 2 weeks, and then heat treated by the method of the present invention (method of Example 1). , Its mechanical properties (hardness, tensile strength, proof stress) were examined. The result of the hardness measurement is shown in FIG. 6, and the results of tensile strength and proof stress are shown in FIGS. 7 and 8, respectively. As is clear from FIGS. 6 to 8, it can be seen that all of the properties of hardness, tensile strength and proof stress are equivalent to those not left at room temperature. Therefore, it is understood that the one left at room temperature according to the method of the present invention may be aged in two steps.
【００１９】[0019]
【発明の効果】以上のように、本発明のＡｌ−Ｍｇ−Ｓ
ｉ系アルミニウム合金の熱処理方法は、従来の熱処理方
法に比べ、上記合金の強度を短時間に高めることがで
き、従ってエネルギー費削減によるコストダウン及び生
産性向上を図ることができ、経済的に大きな効果が望め
る有利な熱処理方法である。As described above, the Al-Mg-S of the present invention is used.
Compared with conventional heat treatment methods, the heat treatment method for i-type aluminum alloys can increase the strength of the above alloys in a short time, and therefore can reduce the cost and improve the productivity by reducing the energy cost, which is economically large. This is an advantageous heat treatment method that can be expected to be effective.
【図１】本発明による二段階時効硬化処理により処理し
たＡｌ−Ｍｇ−Ｓｉ系アルミニウム合金の硬度と熱処理
時間との関係を示すグラフである。FIG. 1 is a graph showing a relationship between hardness and heat treatment time of an Al—Mg—Si based aluminum alloy treated by a two-step age hardening treatment according to the present invention.
【図２】従来の一段階時効硬化処理により処理したＡｌ
−Ｍｇ−Ｓｉ系アルミニウム合金の硬度と熱処理時間と
の関係を示すグラフである。FIG. 2 Al treated by a conventional one-step age hardening treatment
4 is a graph showing the relationship between hardness of Mg—Si based aluminum alloy and heat treatment time.
【図３】本発明の範囲外の二段階時効硬化処理により処
理したＡｌ−Ｍｇ−Ｓｉ系アルミニウム合金の硬度と熱
処理時間との関係を示すグラフである。FIG. 3 is a graph showing a relationship between hardness and heat treatment time of an Al—Mg—Si based aluminum alloy treated by a two-step age hardening treatment outside the scope of the present invention.
【図４】本発明による二段階時効硬化処理又は従来の一
段階時効硬化処理により処理したＡｌ−Ｍｇ−Ｓｉ系ア
ルミニウム合金の引張強度と熱処理時間との関係を示す
グラフである。FIG. 4 is a graph showing the relationship between tensile strength and heat treatment time of an Al—Mg—Si based aluminum alloy treated by the two-step age hardening treatment according to the present invention or the conventional one-step age hardening treatment.
【図５】本発明による二段階時効硬化処理又は従来の一
段階時効硬化処理により処理したＡｌ−Ｍｇ−Ｓｉ系ア
ルミニウム合金の耐力と熱処理時間との関係を示すグラ
フである。FIG. 5 is a graph showing a relationship between proof stress and heat treatment time of an Al—Mg—Si based aluminum alloy treated by the two-step age hardening treatment according to the present invention or the conventional one-step age hardening treatment.
【図６】室温で２週間放置し又はしないＡｌ−Ｍｇ−Ｓ
ｉ系アルミニウム合金に対して本発明の二段階時効硬化
処理を施した後の硬度と熱処理時間との関係を示すグラ
フである。FIG. 6 Al-Mg-S left or not left at room temperature for 2 weeks
3 is a graph showing the relationship between the hardness and the heat treatment time after the i-type aluminum alloy is subjected to the two-step age hardening treatment of the present invention.
【図７】室温で２週間放置し又はしないＡｌ−Ｍｇ−Ｓ
ｉ系アルミニウム合金に対して本発明の二段階時効硬化
処理を施した後の引張強度と熱処理時間との関係を示す
グラフである。FIG. 7: Al-Mg-S left or not left at room temperature for 2 weeks
3 is a graph showing the relationship between tensile strength and heat treatment time after the i-type aluminum alloy is subjected to the two-step age hardening treatment of the present invention.
【図８】室温で２週間放置し又はしないＡｌ−Ｍｇ−Ｓ
ｉ系アルミニウム合金に対して本発明の二段階時効硬化
処理を施した後の耐力と熱処理時間との関係を示すグラ
フである。FIG. 8: Al-Mg-S left or not left at room temperature for 2 weeks
It is a graph which shows the relationship between the yield strength and the heat treatment time after carrying out the two-step age hardening treatment of the present invention on an i-based aluminum alloy.
Claims (5)
出材を人工時効硬化処理するに当って、温度１６０〜１
８０℃で第１段予備時効処理を施すことによりＭｇ2 Ｓ
ｉ析出相を均一に析出させ、次いで温度１９５〜２２０
℃の範囲で１．５〜８．０時間の第２段時効処理を施す
ことにより第１段予備時効時に析出させたＭｇ2 Ｓｉ析
出相を成長させることを特徴とするＡｌ−Ｍｇ−Ｓｉ系
アルミニウム合金の熱処理方法。1. A temperature of 160 to 1 for artificial age hardening treatment of an Al-Mg-Si-based aluminum alloy extruded material.
Mg 2 S by performing the first stage preliminary aging treatment at 80 ° C
i precipitate the precipitation phase uniformly and then the temperature is 195-220
Al-Mg-Si system characterized by growing the Mg 2 Si precipitation phase precipitated during the first stage preliminary aging by performing the second stage aging treatment for 1.5 to 8.0 hours in the range of ° C. Aluminum alloy heat treatment method.
０．５〜１．５時間、第２段時効処理の際の保持時間を
１．５〜３．０時間として処理することを特徴とする請
求項１記載の熱処理方法。2. The treatment is performed by setting the holding time in the first stage preliminary aging treatment to 0.5 to 1.5 hours and the holding time in the second stage aging treatment to 1.5 to 3.0 hours. The heat treatment method according to claim 1, which is characterized in that.
理温度の差△Ｔが△Ｔ≧２５℃を満たしている請求項１
又は２に記載の熱処理方法。3. The difference ΔT between the first stage preliminary aging treatment temperature and the second stage aging treatment temperature satisfies ΔT ≧ 25 ° C.
Or the heat treatment method according to 2.
℃±５℃、保持時間が０．５〜１．５時間、第２段時効
処理の処理温度が２０５℃±５℃、保持時間が１．５〜
３．０時間である請求項１記載の熱処理方法。4. The treatment temperature of the first stage preliminary aging treatment is 170.
℃ ± 5 ℃, holding time 0.5 ~ 1.5 hours, the second stage aging treatment temperature is 205 ℃ ± 5 ℃, holding time 1.5 ~
The heat treatment method according to claim 1, which is for 3.0 hours.
ム合金である請求項１乃至４のいずれか一項に記載の熱
処理方法。5. The heat treatment method according to claim 1, wherein the target alloy is a JIS 6000 series aluminum alloy.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP24519595A JPH0967659A (en) | 1995-08-31 | 1995-08-31 | Method for heat treating aluminum-magnesium-silicon base aluminum alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP24519595A JPH0967659A (en) | 1995-08-31 | 1995-08-31 | Method for heat treating aluminum-magnesium-silicon base aluminum alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0967659A true JPH0967659A (en) | 1997-03-11 |
Family
ID=17130043
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP24519595A Pending JPH0967659A (en) | 1995-08-31 | 1995-08-31 | Method for heat treating aluminum-magnesium-silicon base aluminum alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0967659A (en) |
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2002536552A (en) * | 1999-02-12 | 2002-10-29 | ノルスク・ヒドロ・アーエスアー | Aluminum alloy containing magnesium and silicon |
| JP2009149991A (en) * | 2009-01-09 | 2009-07-09 | Norsk Hydro Asa | Method for treating aluminum alloy comprising aluminum and silicon |
| US20100201155A1 (en) * | 2003-11-20 | 2010-08-12 | Novelis, Inc. | Automobile Body Part |
| US9193134B2 (en) | 2008-08-13 | 2015-11-24 | Novelis Inc. | Automobile body part |
| CN105112825A (en) * | 2015-09-23 | 2015-12-02 | 辽宁工程技术大学 | Thermal treatment method of liquid-forged Al-Mg-Si alloy |
| JP2016040414A (en) * | 2010-11-01 | 2016-03-24 | 日本碍子株式会社 | Heat treatment method, and heat treatment apparatus |
| CN105838943A (en) * | 2016-05-31 | 2016-08-10 | 广西南南铝加工有限公司 | Al-Mg-Si aluminum alloy and extrusion method for sectional bar of Al-Mg-Si aluminum alloy |
| EP3187604A1 (en) | 2015-12-14 | 2017-07-05 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Forged aluminum alloy for automobiles |
| CN111455197A (en) * | 2020-04-07 | 2020-07-28 | 台山市金桥铝型材厂有限公司 | Preparation method of Al-Zn-Mg alloy |
-
1995
- 1995-08-31 JP JP24519595A patent/JPH0967659A/en active Pending
Cited By (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2002536552A (en) * | 1999-02-12 | 2002-10-29 | ノルスク・ヒドロ・アーエスアー | Aluminum alloy containing magnesium and silicon |
| US9731772B2 (en) | 2003-11-20 | 2017-08-15 | Novelis Inc. | Automobile body part |
| US20100201155A1 (en) * | 2003-11-20 | 2010-08-12 | Novelis, Inc. | Automobile Body Part |
| KR101130656B1 (en) * | 2003-11-20 | 2012-04-02 | 노벨리스 인코퍼레이티드 | Automobile body part |
| US9085328B2 (en) | 2003-11-20 | 2015-07-21 | Novelis Inc. | Automobile body part |
| US9242678B2 (en) | 2003-11-20 | 2016-01-26 | Novelis Inc. | Automobile body part |
| US9193134B2 (en) | 2008-08-13 | 2015-11-24 | Novelis Inc. | Automobile body part |
| JP2009149991A (en) * | 2009-01-09 | 2009-07-09 | Norsk Hydro Asa | Method for treating aluminum alloy comprising aluminum and silicon |
| JP2016040414A (en) * | 2010-11-01 | 2016-03-24 | 日本碍子株式会社 | Heat treatment method, and heat treatment apparatus |
| CN105112825A (en) * | 2015-09-23 | 2015-12-02 | 辽宁工程技术大学 | Thermal treatment method of liquid-forged Al-Mg-Si alloy |
| EP3187604A1 (en) | 2015-12-14 | 2017-07-05 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Forged aluminum alloy for automobiles |
| CN105838943A (en) * | 2016-05-31 | 2016-08-10 | 广西南南铝加工有限公司 | Al-Mg-Si aluminum alloy and extrusion method for sectional bar of Al-Mg-Si aluminum alloy |
| CN111455197A (en) * | 2020-04-07 | 2020-07-28 | 台山市金桥铝型材厂有限公司 | Preparation method of Al-Zn-Mg alloy |
| CN111455197B (en) * | 2020-04-07 | 2021-09-07 | 台山市金桥铝型材厂有限公司 | Preparation method of Al-Zn-Mg alloy |
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