JP2006265582A - Heat treatment method of aluminum alloy - Google Patents
Heat treatment method of aluminum alloy Download PDFInfo
- Publication number
- JP2006265582A JP2006265582A JP2005081595A JP2005081595A JP2006265582A JP 2006265582 A JP2006265582 A JP 2006265582A JP 2005081595 A JP2005081595 A JP 2005081595A JP 2005081595 A JP2005081595 A JP 2005081595A JP 2006265582 A JP2006265582 A JP 2006265582A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- temperature
- heat treatment
- partial melting
- treatment
- 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.)
- Granted
Links
Images
Landscapes
- Manufacture And Refinement Of Metals (AREA)
Abstract
Description
本発明は、アルミニウム合金の溶体化処理や均質化処理等の熱処理の方法に関する。 The present invention relates to a heat treatment method such as solution treatment or homogenization treatment of an aluminum alloy.
アルミニウム合金製の鋳造品は、鋳造後に機械的性質を改善するために熱処理が施される。一般に、この熱処理として、均質化処理や溶体化処理などが施される。
均質化処理は、合金を熱的に平衡状態となるように高温に加熱して、高温で原子の拡散を起こさせる熱処理であり、合金成分や組織の均一化、内部応力の除去等を図るものである。
溶体化処理は、合金を均一固溶体範囲の温度に加熱して、合金元素を固溶化させる熱処理であり、この溶体化処理に続く焼入れ処理にて急冷することで、常温における合金元素の固溶化を図るものである。この溶体化処理、焼入れ処理ののち、飽和固溶体を比較的低温に保持する時効処理を施すことにて、均一な析出物が形成され合金の諸性質が改変される。
A cast product made of aluminum alloy is subjected to heat treatment to improve mechanical properties after casting. In general, a homogenization treatment, a solution treatment, or the like is performed as the heat treatment.
Homogenization treatment is a heat treatment that heats the alloy to a high temperature so that it is in thermal equilibrium and causes diffusion of atoms at a high temperature, and homogenizes the alloy composition and structure, and removes internal stress. It is.
The solution treatment is a heat treatment in which the alloy is heated to a temperature in the range of a uniform solid solution to solidify the alloy element. By quenching in the quenching treatment following this solution treatment, the alloy element is solidified at room temperature. It is intended. After the solution treatment and quenching treatment, an aging treatment is performed to keep the saturated solid solution at a relatively low temperature, whereby uniform precipitates are formed and various properties of the alloy are modified.
例えば、Al−Si−Mg系のアルミニウム合金に熱処理として溶体化処理を施す場合、合金を、溶体化処理にて共晶点より低い５２０℃程度で５〜６時間以上保持したのち、焼入れ処理にて急冷し、次いで、人工時効処理にて２００℃以下で４〜１０時間保持する処理過程が、特許文献１に記載されている。
ところで、合金に部分融解（バーニング）が発生する温度（以降「部分融解発生温度」と記載する）は、アルミニウム合金の溶体化処理や均質化処理等の熱処理中において、合金の温度上昇に伴い徐々に上昇することが知られている。しかし、熱処理中の合金の部分融解発生温度の経時変化を把握することが困難であるため、処理開始段階での合金の部分融解発生温度（以降「初期部分融解発生温度」と記載する）よりも低い温度範囲での熱処理が行われる。 By the way, the temperature at which partial melting (burning) occurs in the alloy (hereinafter referred to as “partial melting generation temperature”) is gradually increased as the temperature of the alloy increases during heat treatment such as solution treatment or homogenization treatment of the aluminum alloy. Is known to rise. However, since it is difficult to grasp the temporal change of the partial melting occurrence temperature of the alloy during the heat treatment, it is more than the partial melting occurrence temperature of the alloy at the start of processing (hereinafter referred to as “initial partial melting occurrence temperature”). Heat treatment is performed in a low temperature range.
例えば、上記特許文献１では、合金の部分融解を防止するため、Al−Si−Mg系合金の溶体化処理温度を部分融解が発生する可能性が十分に低い５５０℃以下とすることが記載されている。また、ＪＩＳ規格では、Al−Si−Mg系合金（ＪＩＳ規格記号ＡＣ４Ｃ）の溶体化処理温度は約５２５℃とされている。この溶体化処理温度は、Al−Si−Mg系合金の共晶点よりも５０℃程度低い温度である。 For example, Patent Document 1 describes that in order to prevent partial melting of the alloy, the solution treatment temperature of the Al—Si—Mg-based alloy is set to 550 ° C. or less where the possibility of partial melting is sufficiently low. ing. According to the JIS standard, the solution treatment temperature of the Al—Si—Mg alloy (JIS standard symbol AC4C) is about 525 ° C. This solution treatment temperature is about 50 ° C. lower than the eutectic point of the Al—Si—Mg alloy.
均質化処理や溶体化処理は長時間を必要とする処理であることから、生産性が低くエネルギー消費量が大きいという問題点がある。この問題の解決のために、処理時間の短縮を図って、処理温度を上げることも考え得るが、初期部分融解発生温度より処理温度を上げれば部分融解が起きる可能性があるため、単純に処理温度を上昇させるだけでは、問題点の解決に至らない。 Since the homogenization treatment and solution treatment are treatments that require a long time, there is a problem that productivity is low and energy consumption is large. In order to solve this problem, it is possible to shorten the processing time and increase the processing temperature. However, if the processing temperature is raised from the initial partial melting generation temperature, partial melting may occur. Just raising the temperature does not solve the problem.
そこで、本発明では、熱処理中の部分融解発生温度の経時変化を推定し、初期部分融解発生温度より高い温度でも処理物の熱処理を行うことで、部分融解の発生の防止と、処理時間の短縮を実現する、合金の熱処理方法を提案する。 Therefore, in the present invention, the temporal change of the partial melting occurrence temperature during the heat treatment is estimated, and the heat treatment of the processed material is performed even at a temperature higher than the initial partial melting occurrence temperature, thereby preventing partial melting and shortening the processing time. We propose a heat treatment method for alloys that realizes
本発明の解決しようとする課題は以上の如くであり、次にこの課題を解決するための手段を説明する。 The problems to be solved by the present invention are as described above. Next, means for solving the problems will be described.
即ち、請求項１においては、合金の熱処理において、処理温度を処理開始時の合金の部分融解発生温度よりも低い温度とする前期加熱過程と、処理温度を前期加熱過程よりも高く合金の平均組成の固相線温度よりも低い温度とする後期加熱過程とを含む、合金の熱処理方法である。 That is, in the heat treatment of the alloy, in the heat treatment of the alloy, the preheating process in which the treatment temperature is lower than the partial melting occurrence temperature of the alloy at the start of the treatment, This is a heat treatment method for an alloy, which includes a later heating process in which the temperature is lower than the solidus temperature.
請求項２においては、前記合金の熱処理方法において、前期加熱過程は、少なくとも合金の部分融解発生温度が合金の平均組成の固相線温度と略同一となるまで処理を行うものである。 According to a second aspect of the present invention, in the heat treatment method for an alloy, the preheating process is performed until at least the partial melting temperature of the alloy is substantially the same as the solidus temperature of the average composition of the alloy.
請求項３においては、前記熱処理中の合金の部分融解発生温度が合金の平均組成の固相線温度と略同一となるために要する時間を、熱処理前の合金に含有される化合物の析出物・晶出物の短径のうち最大値を拡散距離とし、前記拡散距離を拡散するための拡散時間を、拡散距離と拡散係数と拡散時間との関係を決定する式を用いて各合金元素について求め、得られた拡散時間のうち最大値と推定するものである。
In
本発明の効果として、以下に示すような効果を奏する。 As effects of the present invention, the following effects can be obtained.
請求項１においては、処理中に上昇する合金の部分融解発生温度に基づいて、処理温度を変化させることができる。従って、処理開始時の処理温度に設定される処理開始段階での部分融解発生温度よりも、高い温度（固相線温度により近い温度）を処理温度とすることができ、処理温度の上昇による処理時間の短縮を図ることができる。
特に、溶体化処理においては、処理温度上昇に基づく合金元素の固溶量の増大によって、合金の機械的性質（硬さ、引張強度、耐力等）の向上を図ることができる。
In the first aspect, the processing temperature can be changed based on the partial melting occurrence temperature of the alloy rising during the processing. Accordingly, the processing temperature can be set to a temperature higher than the partial melting occurrence temperature at the processing start stage set to the processing temperature at the start of processing (a temperature closer to the solidus temperature), and processing due to an increase in processing temperature. Time can be shortened.
In particular, in the solution treatment, the mechanical properties (hardness, tensile strength, proof stress, etc.) of the alloy can be improved by increasing the solid solution amount of the alloy element based on the treatment temperature rise.
請求項２においては、前期加熱過程を終えた時点で、合金の部分融解発生温度が合金の平均組成の固相線温度と略同一となっているので、後期加熱過程では、処理開始段階での部分融解発生温度よりも高い温度を処理温度とすることができるので、処理温度の上昇による処理時間の短縮を図ることができる。
In
請求項３においては、熱処理中の合金の部分融解発生温度が合金の平均組成の固相線温度と略同一となるために要する時間を推定することができ、これに基づいて前期加熱過程を定めることができる。
In
次に、発明の実施の形態を説明する。
図１は本発明の実施例に係る溶体化処理の流れ図、図２は本発明の実施例に係る溶体化処理のプロセスを説明する図、図３は合金における析出物・晶出物の様子を示す図である。
図４は合金に含有される化合物の析出物・晶出物とその短径の測定結果の一例を示す図表、図５はアルミニウム合金のAl中の各合金元素の拡散距離の計算結果の一例を示す図表である。
Next, embodiments of the invention will be described.
FIG. 1 is a flow chart of a solution treatment according to an embodiment of the present invention, FIG. 2 is a diagram for explaining a process of a solution treatment according to an embodiment of the present invention, and FIG. 3 shows a state of precipitates and crystallized materials in an alloy. FIG.
FIG. 4 is a chart showing an example of measurement results of precipitates / crystallized compounds and their minor diameters contained in the alloy, and FIG. 5 is an example of calculation results of diffusion distances of each alloy element in Al of the aluminum alloy. It is a chart shown.
図１に示す如く、合金の熱処理方法は、その加熱処理工程において、前期加熱過程（Ｓ１１ａ）と、後期加熱過程（Ｓ１１ｂ）とを少なくとも実行し、図２（ｂ）に示す如く、前期加熱過程（Ｓ１１ａ）と後期加熱過程（Ｓ１１ｂ）とで異なる温度環境を処理物に与えることを特徴としている。
なお、本発明に係る合金の熱処理方法は、合金の均質化処理や溶体化処理等の熱処理の方法に適用させることができる。
As shown in FIG. 1, in the heat treatment process of the alloy, in the heat treatment process, at least the first heating process (S11a) and the second heating process (S11b) are executed, and as shown in FIG. A different temperature environment is given to a processed material in (S11a) and a late heating process (S11b), It is characterized by the above-mentioned.
The alloy heat treatment method according to the present invention can be applied to heat treatment methods such as alloy homogenization treatment and solution treatment.
以下に示す本実施例では、本発明に係る合金の熱処理方法を採用した熱処理の例として、溶体化処理について説明する。
なお、溶体化処理の処理物は、溶体化処理前のアルミニウム合金であり、以下「合金」と記載する。
In the present embodiment described below, solution treatment will be described as an example of heat treatment employing the alloy heat treatment method according to the present invention.
In addition, the processed material of the solution treatment is an aluminum alloy before the solution treatment, and is hereinafter referred to as “alloy”.
図１に示す如く、溶体化処理（Ｓ１１）と、焼入れ処理（Ｓ１２）と、時効処理（Ｓ１３）との、アルミニウム合金の一連の熱処理を行う場合に、このうち溶体化処理（Ｓ１１）において、前期加熱過程（Ｓ１１ａ）と、後期加熱過程（Ｓ１１ｂ）とを行う。 As shown in FIG. 1, in the case of performing a series of heat treatments of an aluminum alloy including solution treatment (S11), quenching treatment (S12), and aging treatment (S13), of these, in solution treatment (S11), The first heating process (S11a) and the second heating process (S11b) are performed.
前期溶体化処理（Ｓ１１）の第一段階である前期加熱過程（Ｓ１１ａ）において、合金を、前期加熱処理温度で、前期加熱処理時間だけ保持させる。
図２（ａ）に示す如く、前期加熱過程（Ｓ１１ａ）での処理温度である前期加熱処理温度は、溶体化処理前の合金に部分融解（バーニング）が発生する温度（以下「初期部分融解発生温度」と記載する）よりも低い温度とする。初期部分融解発生温度は、合金に基づいて決定され、前期加熱処理温度は、合金に部分融解が発生しないために十分な程度に初期部分融解発生温度よりも低い温度が採用される。
In the first heating step (S11a), which is the first stage of the first solution treatment (S11), the alloy is held at the first heating temperature for the first heating time.
As shown in FIG. 2 (a), the pre-heating temperature, which is the processing temperature in the pre-heating process (S11a), is the temperature at which partial melting (burning) occurs in the alloy before solution treatment (hereinafter referred to as "initial partial melting occurrence"). The temperature is lower than that described in “Temperature”. The initial partial melting occurrence temperature is determined on the basis of the alloy, and a temperature lower than the initial partial melting occurrence temperature is adopted as the initial heat treatment temperature sufficiently to prevent partial melting in the alloy.
また、前期加熱過程（Ｓ１１ａ）での処理時間である前期加熱処理時間は、処理温度を前期加熱処理温度まで昇温してから、溶体化処理中の部分融解発生温度が、合金の平均組成の固相線温度（以下「固相線温度」と記載する）と略同一となるまでの時間以上の時間とする。なお、固相線温度は、合金の平均組成において、固相と液相との境界を形成する温度であり、加熱により固相の一部が溶け始める温度である。 The pre-heating time, which is the processing time in the pre-heating process (S11a), is that the partial melting occurrence temperature during the solution treatment is equal to the average composition of the alloy after the processing temperature is raised to the pre-heating temperature. The time is equal to or longer than the time until it becomes substantially the same as the solidus temperature (hereinafter referred to as “solidus temperature”). The solidus temperature is a temperature that forms a boundary between the solid phase and the liquid phase in the average composition of the alloy, and is a temperature at which a part of the solid phase starts to melt by heating.
溶体化処理前の合金は、組成が均一でないため、平均組成の合金に部分融解が発生するとされる温度よりも、低い温度でも部分融解を発生することがある。また、合金の加熱により合金元素の固溶化が進行すれば、組成のばらつきが低減し、合金に部分融解が発生する温度は、平均組成の合金が融解する温度（平均組成の固相線温度）となる。すなわち、合金の部分融解発生温度は、溶体化処理の進行に伴い上昇することとなる。
従って、溶体化処理の進行に伴って、初期部分融解発生温度であった部分融解発生温度は、上昇して、固相線温度と略同一となる状態が発生することとなる。前期加熱処理時間の求め方については後述する。
Since an alloy before solution treatment is not uniform in composition, partial melting may occur even at a temperature lower than the temperature at which partial melting occurs in an alloy having an average composition. Moreover, if the alloy element is solidified by heating the alloy, the variation in composition is reduced, and the temperature at which partial melting occurs in the alloy is the temperature at which the alloy with the average composition melts (the solidus temperature of the average composition). It becomes. That is, the partial melting occurrence temperature of the alloy increases as the solution treatment progresses.
Therefore, as the solution treatment progresses, the partial melting generation temperature, which was the initial partial melting generation temperature, increases, and a state that is substantially the same as the solidus temperature occurs. The method for obtaining the first heat treatment time will be described later.
上記前期加熱過程（Ｓ１１ａ）に続いて行われる後期加熱過程（Ｓ１１ｂ）では、合金を、後期加熱処理温度で、後期加熱処理時間だけ保持させる。 In the late heating process (S11b) performed subsequent to the early heating process (S11a), the alloy is held at the late heating temperature for the late heating time.
後期加熱過程（Ｓ１１ｂ）での処理温度である後期加熱処理温度は、固相線温度よりも低い温度とする。後期加熱過程（Ｓ１１ｂ）では、部分融解発生温度は固相線温度よりも高くなるため、固相線温度以下であれば合金に部分融解は発生しない。なお、後期加熱処理温度は、処理時間の短縮のために、初期部分融解発生温度と固相線温度の間の温度であって、固相線温度により近い温度とすることが好ましい。 The late heat treatment temperature, which is the treatment temperature in the late heating step (S11b), is set to a temperature lower than the solidus temperature. In the latter heating process (S11b), the partial melting occurrence temperature becomes higher than the solidus temperature, and therefore, the partial melting does not occur in the alloy as long as it is equal to or lower than the solidus temperature. The late heat treatment temperature is preferably a temperature between the initial partial melting occurrence temperature and the solidus temperature, and is closer to the solidus temperature in order to shorten the treatment time.
後期加熱過程（Ｓ１１ｂ）での処理時間である後期加熱処理時間は、前期加熱過程ののち、処理温度を後期加熱処理温度まで昇温してから、合金元素（合金を構成する元素）が適当に固溶化した状態に拡散するまでの時間である。後期加熱処理時間の求め方については後述する。
なお、上記前期加熱処理時間・後期加熱処理時間は、合金をそれぞれ前期加熱処理温度・後期加熱処理温度で保持する時間とする。すなわち、合金の昇温時間は処理時間に含まれない。
The late heat treatment time, which is the treatment time in the late heating process (S11b), is set so that the alloying elements (elements constituting the alloy) are appropriately set after raising the treatment temperature to the late heating temperature after the early heating process. This is the time until diffusion into a solid solution state. The method for obtaining the late heat treatment time will be described later.
The above-mentioned first heat treatment time and late heat treatment time are the times for holding the alloy at the first heat treatment temperature and the latter heat treatment temperature, respectively. That is, the temperature raising time of the alloy is not included in the processing time.
上記後期加熱過程（Ｓ１１ｂ）に続いて、焼入れ処理（Ｓ１２）では、溶体化処理（Ｓ１１）を終えた合金を強制的に冷却する。これにより、合金は常温において合金元素が固溶化した過飽和固溶体となる。
さらに、焼入れ処理（Ｓ１２）に続いて、時効処理（Ｓ１３）にて、過飽和固溶体を比較的低温に保持し、均一な析出物を形成させ、合金の機械的性質を向上させる。
Subsequent to the latter heating step (S11b), in the quenching process (S12), the alloy after the solution treatment (S11) is forcibly cooled. As a result, the alloy becomes a supersaturated solid solution in which the alloy elements are solid solution at room temperature.
Further, in the aging treatment (S13) following the quenching treatment (S12), the supersaturated solid solution is maintained at a relatively low temperature to form uniform precipitates and improve the mechanical properties of the alloy.
図２（ａ）に示す如く、従来の一般的な溶体化処理では、合金は、合金の初期部分融解発生温度よりも低い略一定の温度環境で、所定の処理時間保持されたのち、冷却される。
これに対して、本発明の実施例に係る溶体化処理では、合金に二段階の温度環境を与えている。つまり、一段階目の環境では、部分融解発生温度が固相線温度と略同一と推定される状態となるまでは初期部分融解発生温度よりも低い処理温度を与え、二段階目の環境となるそれ以降は、一段階目よりも高い処理温度で、かつ固相線温度により近い処理温度を与えている。
これにより、合金に部分融解を発生させずに高温で処理することが可能となり、処理時間の大幅な短縮が図られ、生産性の向上とエネルギー消費量の低減に寄与することができる。
As shown in FIG. 2 (a), in the conventional general solution treatment, the alloy is cooled after being maintained for a predetermined treatment time in a substantially constant temperature environment lower than the initial partial melting occurrence temperature of the alloy. The
On the other hand, in the solution treatment according to the embodiment of the present invention, a two-stage temperature environment is given to the alloy. In other words, in the first stage environment, a process temperature lower than the initial partial melting generation temperature is given until the partial melting generation temperature is estimated to be substantially the same as the solidus temperature, and the second stage environment is obtained. Thereafter, a processing temperature higher than that of the first stage and a processing temperature closer to the solidus temperature is given.
As a result, the alloy can be processed at a high temperature without causing partial melting, the processing time can be greatly shortened, and the productivity can be improved and the energy consumption can be reduced.
また、溶体化処理の処理温度を従来と比較して高く設定できるので、処理温度上昇に基づく合金元素の固溶量の増大によって、合金の機械的性質（硬さ、引張強度、耐力等）を向上させることが期待される。 In addition, since the treatment temperature of the solution treatment can be set higher than in the past, the mechanical properties (hardness, tensile strength, proof stress, etc.) of the alloy can be increased by increasing the solid solution amount of the alloy element based on the treatment temperature rise. It is expected to improve.
次に、前記前期加熱処理時間の求め方について説明する。
まず、熱処理される合金に含有される析出物・晶出物の化合物相の同定を行い、析出物・晶出物を構成する化合物を特定する。
そして、合金に含有される化合物について、最も大きな短径ｄを有する析出物・晶出物の短径ｄの大きさを測定する。なお、析出物・晶出物は様々な形状であるが、図３に示す如く、略楕円体と捉えてこの短径ｄを測定する。なお、析出物・晶出物がネットワーク状に現れている場合は、ネットワークの幅を短径ｄとする。
Next, the method for obtaining the previous heat treatment time will be described.
First, the compound phase of the precipitate / crystallized substance contained in the alloy to be heat-treated is identified, and the compound constituting the precipitate / crystallized substance is specified.
And about the compound contained in an alloy, the magnitude | size of the minor axis d of the precipitate and crystallization thing which has the largest minor axis d is measured. Although the precipitates and crystallized substances have various shapes, as shown in FIG. In the case where precipitates / crystallized substances appear in a network shape, the width of the network is defined as the minor axis d.
続いて、合金元素の拡散距離ｘが、上記短径ｄの値と略同一となる拡散時間ｔを、下記［数１］に基づいて算出する。そして、全ての合金元素の中で、最も大きな値の拡散時間ｔを、熱処理中の部分融解発生温度が固相線温度と略同一となるために要する時間と推定し、これを前期加熱処理時間とする。
なお、［数１］において、ｘは拡散距離、Ｄは拡散係数、ｔは拡散時間である。
Subsequently, a diffusion time t at which the diffusion distance x of the alloy element is substantially the same as the value of the minor axis d is calculated based on the following [Equation 1]. Of all the alloy elements, the diffusion time t having the largest value is estimated as the time required for the partial melting occurrence temperature during the heat treatment to be substantially the same as the solidus temperature, and this is the previous heat treatment time. And
In [Expression 1], x is a diffusion distance, D is a diffusion coefficient, and t is a diffusion time.
［数１］
Ｘ=（Ｄｔ）0.5
[Equation 1]
X = (Dt) 0.5
次に、前記後期加熱処理時間の求め方について説明する。
合金に含有されるそれぞれの化合物について、合金元素の目標拡散距離を決定する。目標拡散距離は実験的に得られた値に基づいて任意に定められる値である。例えば、従来の溶体化処理方法にて溶体化処理されたあとの合金より実験的に得られた値に基づいて目標拡散距離を決定することができる。
目標拡散距離は、前期加熱過程と後期加熱過程とにおける合金元素の拡散距離を合わせたものであり、後期加熱過程での合金元素の拡散距離は、目標拡散距離から前期加熱過程での拡散距離を除いたものとなる。
上記の如く決定した後期加熱過程での合金元素の拡散距離の値を用いて、前記前期加熱処理時間を求めるときと同様に、［数１］を用いて、後期加熱処理時間を算出する。
Next, how to determine the latter heat treatment time will be described.
For each compound contained in the alloy, a target diffusion distance of the alloy element is determined. The target diffusion distance is an arbitrarily determined value based on an experimentally obtained value. For example, the target diffusion distance can be determined based on a value experimentally obtained from an alloy after solution treatment by a conventional solution treatment method.
The target diffusion distance is the sum of the diffusion distances of the alloy elements in the early heating process and the late heating process. The diffusion distance of the alloy elements in the late heating process is the diffusion distance in the early heating process from the target diffusion distance. Excluded.
Using the value of the diffusion distance of the alloy element in the late heating process determined as described above, the late heat treatment time is calculated using [Equation 1] in the same manner as when obtaining the previous heat treatment time.
なお、本実施例においては、前期加熱処理時及び後期加熱処理時間は、熱処理される合金に含有される析出物・晶出物の大きさと、合金元素の目標拡散処理とに基づいて決定しているが、前期加熱処理時及び後期加熱処理時間ともに、実験により得た値に基づいて定めることもできる。 In this example, the first heat treatment time and the second heat treatment time are determined based on the size of the precipitate / crystallized material contained in the heat-treated alloy and the target diffusion treatment of the alloy element. However, both the first heat treatment time and the second heat treatment time can be determined based on values obtained by experiments.
続いて、上記溶体化処理の実施例について説明する。
本実施例では、主な析出物・晶出物がAl2CuとMg2Siであるアルミニウム合金を処理物として溶体化処理を行った。この溶体化処理では、従来の溶体化処理の手法にて、４８０℃で２４０分加熱保持したものと略同様の合金元素の拡散距離を得ることを目標とした。
なお、図５に示す図表は、［数１］に基づいて各処理温度におけるAl中の各合金元素の拡散距離を示すものであり、この図５に示す図表に基づいて各合金元素の目標とするAl中の拡散距離（４８０℃で２４０分加熱保持した場合のAl中の拡散距離）を推定すると、Mgの目標拡散距離は約３９μｍであり、Siの目標拡散距離は約３７μｍであり、Cuの目標拡散距離は約２０μｍである。
Next, examples of the solution treatment will be described.
In this example, the solution treatment was performed using an aluminum alloy whose main precipitates / crystallized materials are Al 2 Cu and Mg 2 Si as a processed material. In this solution treatment, the aim was to obtain a diffusion distance of alloy elements substantially the same as that obtained by heating and holding at 480 ° C. for 240 minutes by a conventional solution treatment method.
The chart shown in FIG. 5 shows the diffusion distance of each alloy element in Al at each processing temperature based on [Equation 1]. Based on the chart shown in FIG. Estimating the diffusion distance in Al (diffusion distance in Al when kept heated at 480 ° C. for 240 minutes), the target diffusion distance of Mg is about 39 μm, the target diffusion distance of Si is about 37 μm, and Cu The target diffusion distance is about 20 μm.
まず、合金に含まれる化合物の相の同定を行ったところ、化合物は主にAl2CuとMg2Siであり、主な合金元素はAl、Mg、Si、Cuであった。そして、これらの化合物において析出物・晶出物の最も大きな短径ｄを計測したところ、Al2Cuではｄ＝０．３μｍ、Mg2Siではｄ＝５μｍであった（図４）。 First, the phases of the compounds contained in the alloy were identified. The compounds were mainly Al 2 Cu and Mg 2 Si, and the main alloy elements were Al, Mg, Si, and Cu. In these compounds, the largest minor axis d of the precipitate / crystallized substance was measured, and d = 0.3 μm for Al 2 Cu and d = 5 μm for Mg 2 Si (FIG. 4).
そこで、初期部分融解発生温度よりも低い温度である４８０℃を前期加熱処理温度と設定し、４８０℃のAlの中において、MgとSiとが拡散距離ｘ＝５μｍだけ拡散する拡散時間、Cuが拡散距離ｘ＝０．３μｍだけ拡散する拡散時間を、［数１］に基づいてそれぞれ算出し、これらのうち最も大きな値となったものを、前期加熱処理時間とした。この結果、前期加熱処理時間を５分と設定した。 Therefore, 480 ° C., which is lower than the initial partial melting occurrence temperature, is set as the initial heat treatment temperature, and in Al at 480 ° C., the diffusion time in which Mg and Si diffuse by the diffusion distance x = 5 μm, Cu is The diffusion time for diffusing by the diffusion distance x = 0.3 μm was calculated based on [Equation 1], and the largest value among them was defined as the previous heat treatment time. As a result, the previous heat treatment time was set to 5 minutes.
また、後期加熱処理温度を固相線温度よりも低い温度である５４０℃と設定した。４８０℃で５分保持した場合の各元素のAl中での拡散距離は、Mgは約６μｍ、Siは約５μｍ、Cuは約３μｍと推定される。従って、後期溶体化処理過程では、５４０℃のAlの中において、Mgを拡散距離ｘ＝約３３μｍ、Siを拡散距離ｘ＝約３２μｍ、Cuを拡散距離ｘ＝約１７μｍだけ拡散する拡散時間ｔを、［数１］に基づいてそれぞれ算出し、これらのうち最も大きな値となったものを、後期加熱処理時間とした。この結果、後期加熱処理時間を４０分と設定した。 The late heat treatment temperature was set to 540 ° C., which is lower than the solidus temperature. The diffusion distance of each element in Al when held at 480 ° C. for 5 minutes is estimated to be about 6 μm for Mg, about 5 μm for Si, and about 3 μm for Cu. Therefore, in the late solution treatment process, in Al at 540 ° C., the diffusion time t for diffusing Mg by the diffusion distance x = about 33 μm, Si by the diffusion distance x = about 32 μm, and Cu by the diffusion distance x = about 17 μm is set. , [Equation 1] was calculated, and the largest value among these was determined as the late heat treatment time. As a result, the late heat treatment time was set to 40 minutes.
上述の如く、従来の溶体化処理の手法にて、４８０℃で２４０分加熱保持したものと略同様の合金元素の拡散距離を得るために、本発明では、前期加熱過程において、前期加熱処理温度を４８０℃、前期加熱処理時間を５分とし、後期加熱過程において、後期加熱処理温度を５４０℃、後期加熱処理時間を４０分とした。溶体化処理において加熱保持する時間は、従来の２４０分から４５分に大幅に短縮されたことになる。 As described above, in the present invention, in order to obtain the diffusion distance of the alloy element substantially the same as that obtained by heating and maintaining at 480 ° C. for 240 minutes by the conventional solution treatment method, Was 480 ° C., the first heat treatment time was 5 minutes, and the second heat treatment temperature was 540 ° C. and the second heat treatment time was 40 minutes in the latter heating process. The time for heating and holding in the solution treatment is greatly reduced from the conventional 240 minutes to 45 minutes.
なお、上記実施例では、アルミニウム合金の熱処理のうち、溶体化処理について述べているが、均質化処理の場合も、上記合金の熱処理方法を適用させることができる。
すなわち、均質化処理において、初期部分融解発生温度以下の温度で、処理中の部分融解発生温度が合金の平均組成の固相線温度となるまで加熱する前期加熱過程と、平均組成の固相線により近い温度で、合金元素が十分に拡散されるまで加熱する後期加熱過程を行うのである。なお、前期熱処理過程の前期加熱処理時間は、上述の溶体化処理の場合と同様に、熱処理前の合金に含有される析出物・晶出物の大きさに基づいて定めることができる。
In the above embodiment, the solution treatment is described as the heat treatment of the aluminum alloy. However, the heat treatment method of the alloy can be applied also in the case of the homogenization treatment.
That is, in the homogenization process, the initial heating process in which heating is performed at a temperature equal to or lower than the initial partial melting generation temperature until the partial melting generation temperature during the process reaches the solidus temperature of the average composition of the alloy, and the solidus line of the average composition The latter heating process is performed at a temperature closer to the temperature until the alloy elements are sufficiently diffused. In addition, the heat treatment time of the first heat treatment process can be determined based on the size of the precipitate / crystallized material contained in the alloy before the heat treatment, as in the case of the solution treatment described above.
Claims (3)
処理温度を処理開始時の合金の部分融解発生温度よりも低い温度とする前期加熱過程と、処理温度を前期加熱過程よりも高く合金の平均組成の固相線温度よりも低い温度とする後期加熱過程とを含むことを
特徴とする合金の熱処理方法。 In heat treatment of aluminum alloy,
Early heating process in which the processing temperature is lower than the partial melting occurrence temperature of the alloy at the start of processing, and late heating in which the processing temperature is higher than the previous heating process and lower than the solidus temperature of the average composition of the alloy And a heat treatment method for the alloy.
前期加熱過程は、少なくとも合金の部分融解発生温度が合金の平均組成の固相線温度と略同一となるまで処理を行う、
請求項１に記載の合金の熱処理方法。 In the heat treatment method of the alloy,
The first heating process is performed until at least the partial melting temperature of the alloy is substantially the same as the solidus temperature of the average composition of the alloy.
The heat processing method of the alloy of Claim 1.
熱処理前の合金に含有される化合物の析出物・晶出物の短径のうち最大値を拡散距離とし、
前記拡散距離を拡散するための拡散時間を、拡散距離と拡散係数と拡散時間との関係を決定する式を用いて各合金元素について求め、
得られた拡散時間のうち最大値と推定する、
請求項２に記載の合金の熱処理方法。
The time required for the partial melting occurrence temperature of the alloy during the heat treatment to be substantially the same as the solidus temperature of the average composition of the alloy,
The maximum value of the short diameters of the precipitates and crystallized compounds contained in the alloy before heat treatment is the diffusion distance,
The diffusion time for diffusing the diffusion distance is determined for each alloy element using an equation that determines the relationship between the diffusion distance, the diffusion coefficient, and the diffusion time,
Estimate the maximum value of the obtained diffusion time.
A method for heat-treating the alloy according to claim 2.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2005081595A JP4635669B2 (en) | 2005-03-22 | 2005-03-22 | Alloy heat treatment method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2005081595A JP4635669B2 (en) | 2005-03-22 | 2005-03-22 | Alloy heat treatment method |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2006265582A true JP2006265582A (en) | 2006-10-05 |
| JP4635669B2 JP4635669B2 (en) | 2011-02-23 |
Family
ID=37201854
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2005081595A Expired - Fee Related JP4635669B2 (en) | 2005-03-22 | 2005-03-22 | Alloy heat treatment method |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP4635669B2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104532172A (en) * | 2014-12-09 | 2015-04-22 | 中国科学院上海技术物理研究所 | Heat treatment method for eliminating tellurium-rich precipitate-phase defect in tellurium-zinc-cadmium material through two-step process |
| JP2018520267A (en) * | 2015-04-28 | 2018-07-26 | コンソリデイテット エンジニアリング カンパニー，インコーポレイテッド | System and method for heat treating aluminum alloy castings |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61163232A (en) * | 1985-01-11 | 1986-07-23 | Kobe Steel Ltd | High strength al-mg-si alloy and its manufacture |
| JPH06220564A (en) * | 1992-12-28 | 1994-08-09 | Nippon Light Metal Co Ltd | Aluminum alloy excellent in corrosion resistance and undercoat coating treatability and its production |
| JPH1171663A (en) * | 1997-06-18 | 1999-03-16 | Tateyama Alum Ind Co Ltd | Artificial aging treatment of aluminum-magnesium-silicon series aluminum alloy |
| JP2001279359A (en) * | 2000-01-25 | 2001-10-10 | Nippon Light Metal Co Ltd | Method for producing pellicle frame and hollow extruded material for pellicle frame |
| JP2002348631A (en) * | 2001-05-22 | 2002-12-04 | Aisin Seiki Co Ltd | Aluminum-zinc-magnesium aluminum alloy for casting and forging, aluminum-zinc-magnesium cast and forged article, and manufacturing method therefor |
| JP2003253367A (en) * | 2002-03-05 | 2003-09-10 | Asahi Tec Corp | PRECIPITATION HARDENED Al ALLOY |
| JP2003286552A (en) * | 2002-03-28 | 2003-10-10 | Kobe Steel Ltd | METHOD FOR MANUFACTURING Al-Mg-Si ALLOY SHEET |
-
2005
- 2005-03-22 JP JP2005081595A patent/JP4635669B2/en not_active Expired - Fee Related
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61163232A (en) * | 1985-01-11 | 1986-07-23 | Kobe Steel Ltd | High strength al-mg-si alloy and its manufacture |
| JPH06220564A (en) * | 1992-12-28 | 1994-08-09 | Nippon Light Metal Co Ltd | Aluminum alloy excellent in corrosion resistance and undercoat coating treatability and its production |
| JPH1171663A (en) * | 1997-06-18 | 1999-03-16 | Tateyama Alum Ind Co Ltd | Artificial aging treatment of aluminum-magnesium-silicon series aluminum alloy |
| JP2001279359A (en) * | 2000-01-25 | 2001-10-10 | Nippon Light Metal Co Ltd | Method for producing pellicle frame and hollow extruded material for pellicle frame |
| JP2002348631A (en) * | 2001-05-22 | 2002-12-04 | Aisin Seiki Co Ltd | Aluminum-zinc-magnesium aluminum alloy for casting and forging, aluminum-zinc-magnesium cast and forged article, and manufacturing method therefor |
| JP2003253367A (en) * | 2002-03-05 | 2003-09-10 | Asahi Tec Corp | PRECIPITATION HARDENED Al ALLOY |
| JP2003286552A (en) * | 2002-03-28 | 2003-10-10 | Kobe Steel Ltd | METHOD FOR MANUFACTURING Al-Mg-Si ALLOY SHEET |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104532172A (en) * | 2014-12-09 | 2015-04-22 | 中国科学院上海技术物理研究所 | Heat treatment method for eliminating tellurium-rich precipitate-phase defect in tellurium-zinc-cadmium material through two-step process |
| JP2018520267A (en) * | 2015-04-28 | 2018-07-26 | コンソリデイテット エンジニアリング カンパニー，インコーポレイテッド | System and method for heat treating aluminum alloy castings |
| US11408062B2 (en) | 2015-04-28 | 2022-08-09 | Consolidated Engineering Company, Inc. | System and method for heat treating aluminum alloy castings |
Also Published As
| Publication number | Publication date |
|---|---|
| JP4635669B2 (en) | 2011-02-23 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| Ma et al. | Microstructural refinement and property enhancement of cast light alloys via friction stir processing | |
| JP5711253B2 (en) | Method of forming a component of complex shape from sheet material | |
| JP5295951B2 (en) | Treatment of Al / Zn based alloy coated products | |
| CA2921895C (en) | Method for the manufacturing of al-mg-si and al-mg-si-cu extrusion alloys | |
| RU2015132953A (en) | CORROSION-RESISTANT ALUMINUM ALLOYS WITH HIGH MAGNESIUM CONTENT AND METHODS FOR PRODUCING THEM | |
| JP2008101264A (en) | Heat-resistant aluminum-alloy extruded material and heat treatment method therefor | |
| JP6064874B2 (en) | Method for producing aluminum alloy material | |
| Pezda | The effect of the T6 heat treatment on hardness and microstructure of the EN AC-AlSi12CuNiMg alloy | |
| JP4635669B2 (en) | Alloy heat treatment method | |
| Kaiser | Effect of Solution Treatment on the Age-Hardening Behavior of Al-12Si-1Mg-1Cu Piston Alloy with Trace-Zr Addition | |
| JP2007070685A (en) | Highly workable magnesium alloy, and method for producing the same | |
| JP2009203516A (en) | Aluminum alloy | |
| CN103119190B (en) | Method for heat-treating a cast component | |
| CN106350756B (en) | A kind of homogenization heat treatment method of magnesium-rare earth casting | |
| JPH07116574B2 (en) | Method for heat treating a cast nickel-base superalloy article | |
| JP5279119B2 (en) | Partially modified aluminum alloy member and manufacturing method thereof | |
| JP6026431B2 (en) | Lead-free rolled aluminum plain bearing | |
| JP2011127163A (en) | Magnesium alloy sheet material having excellent formability, and method for production thereof | |
| JP2008127665A (en) | Method for producing aluminum alloy cylinder block | |
| JP2007239029A (en) | Malleable heat-resistant aluminum alloy | |
| JP4110620B2 (en) | Heat treatment method of aluminum alloy | |
| US20110030855A1 (en) | CORROSION RESISTANCE OF THE CAST Mg ALLOYS BY NOVEL MICROSTRUCTURAL PHASE MODIFICATIONS | |
| TW200303368A (en) | Cu-based alloy and method of manufacturing high strength and high thermal conductive forged article using the same | |
| JP2008002957A (en) | Creep characteristics evaluation and formulation method of aluminum alloy material, estimation method for the creep characteristics of aluminum alloy, and manufacturing method of aluminum alloy casting | |
| JP2010106335A (en) | Magnesium alloy for forging |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A621 | Written request for application examination |
Free format text: JAPANESE INTERMEDIATE CODE: A621 Effective date: 20070829 |
|
| A977 | Report on retrieval |
Free format text: JAPANESE INTERMEDIATE CODE: A971007 Effective date: 20091111 |
|
| A131 | Notification of reasons for refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A131 Effective date: 20091117 |
|
| A521 | Written amendment |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20100115 |
|
| A131 | Notification of reasons for refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A131 Effective date: 20100330 |
|
| A521 | Written amendment |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20100521 |
|
| A02 | Decision of refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A02 Effective date: 20100615 |
|
| A521 | Written amendment |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20100806 |
|
| A911 | Transfer of reconsideration by examiner before appeal (zenchi) |
Free format text: JAPANESE INTERMEDIATE CODE: A911 Effective date: 20100916 |
|
| TRDD | Decision of grant or rejection written | ||
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 Effective date: 20101026 |
|
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 |
|
| A61 | First payment of annual fees (during grant procedure) |
Free format text: JAPANESE INTERMEDIATE CODE: A61 Effective date: 20101108 |
|
| FPAY | Renewal fee payment (prs date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20131203 Year of fee payment: 3 |
|
| FPAY | Renewal fee payment (prs date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20131203 Year of fee payment: 3 |
|
| LAPS | Cancellation because of no payment of annual fees |