JPH08951B2 - Method for manufacturing aluminum alloy member - Google Patents
Method for manufacturing aluminum alloy memberInfo
- Publication number
- JPH08951B2 JPH08951B2 JP60086084A JP8608485A JPH08951B2 JP H08951 B2 JPH08951 B2 JP H08951B2 JP 60086084 A JP60086084 A JP 60086084A JP 8608485 A JP8608485 A JP 8608485A JP H08951 B2 JPH08951 B2 JP H08951B2
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- aluminum alloy
- treatment
- alloy member
- remelted
- alloy material
- Prior art date
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Description
【発明の詳細な説明】 〔産業上の利用分野〕 本発明は、表面改質処理を施したアルミニウム合金部
材の製造方法に関するものである。The present invention relates to a method for producing a surface-modified aluminum alloy member.
アルミニウム合金の金属組織を微細化すると、硬度、
引張り強度、靭性が増して、耐摩耗性、耐熱疲労特性を
向上させ得ることは周知の技術である。このような金属
組織の微細化は、鋳造後、溶湯を急速冷却すれば得られ
るものの、この方法は急冷の困難な大型部品には適用不
可能であると共に、例えば内燃機関用ピストンのホット
スポット部やエッジ部などを局部的に改質強化するとい
った要請には応えることが出来ない。When the metal structure of aluminum alloy is refined, hardness,
It is a well-known technique that tensile strength and toughness can be increased to improve wear resistance and heat fatigue resistance. Such a fine metal structure can be obtained by rapidly cooling the molten metal after casting, but this method is not applicable to large parts that are difficult to quench rapidly, and, for example, hot spots of pistons for internal combustion engines. We cannot meet the demand for locally modifying and strengthening the edges and edges.
そこで近年、このような技術的要請に応えるために、
金属素材の表面組織を局部的に微細化処理する表面改質
方法が開発されている。その１つの方法は、アルミニウ
ム合金からなる内燃機関用ピストンのピストンヘッドの
ホットスポット部やエッジ部をレーザービームなどの高
密度エネルギ熱線で溶融・急冷してその部分の金属組織
を微細化した後、全体にT7処理を施すもの（特開昭59-1
08849号公報）である。Therefore, in order to meet such technical demands in recent years,
A surface modification method has been developed in which the surface structure of a metal material is locally miniaturized. One of the methods is to melt and rapidly cool the hot spot portion or the edge portion of the piston head of the piston for an internal combustion engine made of an aluminum alloy with a high-density energy heat ray such as a laser beam to refine the metal structure of the portion, The whole is subjected to T 7 treatment (Japanese Patent Laid-Open No. 59-1
No. 08849).
上記T7処理は、溶体化処理の後、通常の焼戻し温度よ
り高い温度で加熱する安定化処理を施すものであり、こ
の安定化処理により焼入れひずみや鋳造ひずみを除いた
り、高温で使用する場合に析出の進行によって生じる変
形を防止するようにしている。The T 7 treatment is a solution treatment followed by a stabilization treatment of heating at a temperature higher than the normal tempering temperature, and the quenching strain and casting strain are removed by this stabilization treatment, or when used at high temperature. Moreover, the deformation caused by the progress of precipitation is prevented.
ところで、上記高密度エネルギ熱線の照射により溶融
・急冷された再溶融部の周りには溶融時の熱の影響（30
0〜450℃まで昇温して過時効となる）で軟化域が生成さ
れるが、前記方法では溶融・急冷処理の後に行われるT7
処理の焼戻し温度が高いので、上記軟化域が消失せずそ
のまま残存することになる。そのため、この軟化域の部
分からクラックが発生するおそれがあり、かえって耐熱
疲労特性を悪くしてしまうという問題を有する。By the way, the influence of heat at the time of melting (30
A softening zone is generated by increasing the temperature from 0 to 450 ° C. and overaging), but in the above method, T 7 which is performed after the melting / quenching treatment is performed.
Since the tempering temperature of the treatment is high, the softened region does not disappear and remains as it is. Therefore, there is a possibility that cracks may occur from the softened region, which rather deteriorates the thermal fatigue resistance.
本発明は、アルミニウム合金部材の表面改質処理にお
ける前記問題点を考慮してなされたものであって、高密
度エネルギ熱線の照射による表面改質処理部の近傍に軟
化域を残すことのない耐熱疲労特性に優れたアルミニウ
ム合金部材の製造方法の提供を目的とするものである。The present invention has been made in consideration of the above problems in the surface modification treatment of an aluminum alloy member, and is a heat-resistant material that does not leave a softened region in the vicinity of the surface modification-treated portion due to irradiation of high-density energy heat rays. It is an object of the present invention to provide a method for manufacturing an aluminum alloy member having excellent fatigue characteristics.
本発明のアルミニウム合金部材の製造方法は、高密度
エネルギ熱線でアルミニウム合金素材を局部的に溶融・
急冷処理することにより、耐熱疲労強度の向上した再溶
融部を形成した後、上記アルミニウム合金素材に対して
T6処理を施すことによって、上記再溶融部の近傍に生成
し、上記アルミニウム合金素材の耐熱疲労強度を低下さ
せる軟化域を消失させることにより、上記軟化域に起因
する耐熱疲労強度の低下を回避して、上記アルミニウム
合金素材の耐熱疲労強度の向上を図るようにしたことを
特徴とするものである。The method for manufacturing an aluminum alloy member of the present invention is a method of locally melting an aluminum alloy material with high-density energy heat rays.
After forming a remelted part with improved thermal fatigue strength by quenching,
By applying T 6 treatment, it is generated in the vicinity of the re-melted part, and by eliminating the softening zone that reduces the thermal fatigue strength of the aluminum alloy material, avoiding the reduction of the thermal fatigue strength due to the softening zone. Then, the heat resistance fatigue strength of the aluminum alloy material is improved.
〔実施例１〕 本発明の第１の実施例を、第１図ないし第20図に基づ
いて以下に詳述する。[Embodiment 1] A first embodiment of the present invention will be described in detail below with reference to FIGS. 1 to 20.
本実施例のアルミニウム合金部材の製造方法は、適用
アルミニウム合金素材としてAC8A、180×80×8tmmの平
板試片を用い、第１図にフロー図で示すようにこのアル
ミニウム合金素材１に対して溶融・急冷→溶体化・焼入
れ→人工時効の順序で熱処理を施すものである。The manufacturing method of the aluminum alloy member of this embodiment uses AC8A, 180 × 80 × 8tmm flat plate specimen as the applicable aluminum alloy material, and melts the aluminum alloy material 1 as shown in the flow chart of FIG.・ The heat treatment is performed in the order of rapid cooling → solution / quenching → artificial aging.
上記溶融・急冷処理は、第２図に示すようにアルミニ
ウム合金素材１の平板試片に対して、高密度エネルギ熱
線としてレーザービーム２を矢符号Ｐで示す走査方向に
移動させながら照射し、アルミニウム合金素材１の表面
を局部的に溶融・急冷させるものである。このときの、
レーザービーム２の照射条件を表１に示している。In the melting / quenching process, as shown in FIG. 2, a flat plate sample of aluminum alloy material 1 is irradiated with a laser beam 2 as a high-density energy heat ray while moving in the scanning direction indicated by arrow P, and The surface of the alloy material 1 is locally melted and rapidly cooled. At this time,
The irradiation conditions of the laser beam 2 are shown in Table 1.
なお、アルミニウム合金素材１の表面には、レーザー
ビーム２の照射に先だちグラファイトをコーティングし
て、レーザービーム２の吸収率を高めている。 The surface of the aluminum alloy material 1 is coated with graphite prior to irradiation with the laser beam 2 to increase the absorption rate of the laser beam 2.
また上記溶体化・焼入れ処理は、加熱温度480〜520℃
×加熱時間４〜10Hrで加熱固溶するのが好適で、水冷に
より焼入れする。この処理において、加熱温度が480℃
以下では溶体化が不十分となり、また520℃以上ではア
ルミニウム合金素材１の母材部分1bが溶融してしまうお
それがある。加熱時間も4Hr以下では溶体化が不十分で
ある一方、10Hr以上になると溶体化効果が飽和になり不
経済である。In addition, the solution temperature / quenching treatment is performed at a heating temperature of 480 to 520 ° C.
× It is preferable that the solution is heated and solid-dissolved for a heating time of 4 to 10 hours, and quenching is performed by cooling with water. In this process, the heating temperature is 480 ℃
At below, solution treatment may be insufficient, and at above 520 ° C, the base material portion 1b of the aluminum alloy material 1 may melt. If the heating time is 4 hours or less, the solution treatment is insufficient, while if it is 10 hours or more, the solution treatment effect is saturated and it is uneconomical.
上記人工時効処理は、加熱温度170〜200℃×加熱時間
６〜10Hrの条件で行うのが好適である。この処理におい
て、可加熱温度が170℃以下では時効が不十分となる一
方、200℃以上にすると過時効となりアルミニウム合金
素材１が軟化してしまうことになる。又、この時の加熱
時間も、6Hr以下では時効が不十分となる一方、10Hr以
上加熱してもそれ以上効果は上がらないので不経済であ
る。The artificial aging treatment is preferably performed under the conditions of a heating temperature of 170 to 200 ° C. and a heating time of 6 to 10 hours. In this treatment, if the heatable temperature is 170 ° C. or lower, the aging becomes insufficient, while if it is 200 ° C. or higher, the aluminum alloy material 1 is softened due to over-aging. Also, if the heating time at this time is 6 hours or less, the aging becomes insufficient, while if heating is performed for 10 hours or more, the effect does not increase any more, which is uneconomical.
このような熱処理手順とすることによって、レーザー
ビーム２照射に伴う熱伝導作用で第３図にクロス・ハッ
チングで示すように再溶融部1a近傍に生成する軟化域1c
が、溶体化の加熱で消失する一方、アルミニウム合金素
材１全体は、溶体化・焼入れ→人工時効の処理過程すな
わちT6処理が施されることになる。従って再溶融部1aの
近傍には軟化域1cが残在せず耐熱疲労強度が向上すると
共に、アルミニウム合金素材１に対して強度向上のた
め、通常施されるT6処理が上記母材部分1bに施されるこ
とになる。又、再溶融部1aも、この部分に点在する共晶
SiがT6処理により球状化するので、切欠き靭性が上がり
耐熱疲労強度が更に向上することになる。By adopting such a heat treatment procedure, the softening zone 1c generated in the vicinity of the remelted portion 1a as shown by cross hatching in FIG.
However, while it disappears by heating for solution heat treatment, the entire aluminum alloy material 1 is subjected to solution heat treatment / quenching → artificial aging treatment process, that is, T 6 treatment. Therefore, the softening zone 1c does not remain in the vicinity of the remelted portion 1a, and the thermal fatigue strength is improved, and in order to improve the strength of the aluminum alloy raw material 1, the T 6 treatment which is usually performed is the above base material portion 1b. Will be applied to. In addition, the remelted portion 1a also has a eutectic scattered in this portion.
Since Si is spheroidized by the T 6 treatment, the notch toughness is increased and the thermal fatigue strength is further improved.
本実施例の熱処理による特徴と、その時の再溶融部1a
および母材部分1bの硬度を、それぞれ表２の（１）欄に
示している。Features of the heat treatment of the present embodiment, and the remelted portion 1a at that time
The hardness of the base material portion 1b and the hardness of the base material portion 1b are shown in column (1) of Table 2, respectively.
又、この時の再溶融部1a組織を拡大したものを第４図
（倍率100倍）および第５図（倍率400倍）に、この時の
母材部分1bの組織を拡大したものを第６図（倍率100
倍）および第７図（倍率400倍）にそれぞれ示してい
る。第８図は、この時のアルミニウム合金部材の硬さ分
布を示すグラフである。Further, an enlarged structure of the remelted portion 1a at this time is shown in FIG. 4 (magnification of 100 times) and FIG. 5 (magnification of 400 times), and an enlarged structure of the base metal portion 1b at this time is shown in FIG. Figure (magnification 100
) And FIG. 7 (400 times magnification). FIG. 8 is a graph showing the hardness distribution of the aluminum alloy member at this time.
本実施例の結果を他の熱処理手順による場合と比較す
るために、第９図にフロー図で示す手順により前記実施
例と同じ素材を熱処理した場合、および第10図にフロー
図で示す手順により同じ素材を熱処理した場合の各々の
特徴と、その時の再溶融部、母材部分および軟化域の硬
さを前記表２の（２）および（３）の各欄にそれぞれ示
している。これら比較例における各処理過程での条件
は、前記実施例の場合と同じである。In order to compare the result of this example with the case of another heat treatment procedure, the same material as the above example was heat treated by the procedure shown in the flow chart of FIG. 9 and the procedure shown in the flow chart of FIG. The respective characteristics when the same material is heat-treated and the hardnesses of the remelted portion, the base material portion and the softened area at that time are shown in the columns (2) and (3) of Table 2 above. The conditions in each processing step in these comparative examples are the same as those in the above-mentioned embodiment.
第９図に示す手順の比較例では、溶融・急冷処理され
た再溶融部は、その次の過程で人工時効処理されるの
で、再溶融部近傍に生成された軟化域が最後まで残り、
耐熱疲労強度を低下させることになる。反面、再溶融部
は、次に施される人工時効処理によって硬さが一層向上
することになる。 In the comparative example of the procedure shown in FIG. 9, the remelted portion subjected to the melting / quenching treatment is subjected to artificial aging treatment in the subsequent process, so that the softened region generated near the remelted portion remains until the end,
The thermal fatigue strength will be reduced. On the other hand, the hardness of the remelted portion is further improved by the artificial aging treatment performed next.
又、第10図に示す手順の比較例では、溶融・急冷処理
が最後の過程で行われるので、この場合も再溶融部近傍
に生成された軟化域はそのまま残存し、耐熱疲労強度の
低下を来すことになる。Further, in the comparative example of the procedure shown in FIG. 10, since the melting / quenching treatment is performed in the final process, the softened region generated in the vicinity of the remelting portion remains as it is, and the thermal fatigue strength decreases. Will come.
第９図に示す手順の比較例の場合のアルミニウム合金
部材の再溶融部組織を拡大したものを第11図（倍率100
倍）および第12図（倍率400倍）に、又この時の硬さ分
布を第13図にグラフで示している。更に、第10図に示す
手順の比較例の場合のアルミニウム合金部材の再溶融部
組織を拡大したものを第14図（倍率100倍）および第15
図（倍率400倍）に示し、この時の硬さ分布を第16図に
グラフで示している。An enlarged view of the remelted portion structure of the aluminum alloy member in the case of the comparative example of the procedure shown in FIG. 9 is shown in FIG.
Times) and FIG. 12 (magnification 400 times), and the hardness distribution at this time is shown in a graph in FIG. Further, an enlarged view of the remelted part structure of the aluminum alloy member in the case of the comparative example of the procedure shown in FIG. 10 is shown in FIG. 14 (magnification 100 times) and FIG.
It is shown in the figure (magnification 400 times), and the hardness distribution at this time is shown in the graph in FIG.
次に、本実施例の手順により得られるアルミニウム合
金部材を、第９図の手順の比較例の場合のアルミニウム
合金部材、並びにレーザービーム照射による局部溶融・
急冷処理を施さないT6処理アルミニウム合金（実施例、
比較例と同じAC8A）と比較して、その耐熱疲労強度を測
定した結果について説明する。Next, the aluminum alloy member obtained by the procedure of the present example was used as the aluminum alloy member of the comparative example of the procedure of FIG. 9 and local melting / irradiation by laser beam irradiation.
T 6 treated aluminum alloy without quenching treatment (Example,
The results of measuring the thermal fatigue strength of the same will be described in comparison with AC8A) which is the same as the comparative example.
上記テストは、各試片３を第17図（ａ）、（ｂ）に示
す寸法、形状に揃えて加工し、第18図に示すように両端
を拘束したこれら各試片１に対して、ガスバーナ４によ
る加熱と水５による冷却とを繰り返し、試片３の狭幅加
工部3aにクラックが生じるまでの加熱・冷却のサイクル
数を測定したものである。In the above test, the test pieces 3 were processed into the dimensions and shapes shown in FIGS. 17 (a) and 17 (b), and both ends were restrained as shown in FIG. The heating by the gas burner 4 and the cooling by the water 5 were repeated, and the number of heating / cooling cycles until a crack was generated in the narrow processed portion 3a of the sample 3 was measured.
このテストにおいて、本実施例の熱処理手順により得
られるアルミニウム合金部材の試片３は、上記加熱・冷
却を1700サイクル繰り返してもクラックは発生しなかっ
た。In this test, the sample 3 of the aluminum alloy member obtained by the heat treatment procedure of the present example did not cause cracks even when the above heating / cooling was repeated 1700 cycles.
これに対し、第９図に示す比較例の熱処理手順により
得られるアルミニウム合金部材の試片３では、加熱・冷
却を1400サイクル繰り返した時点で、第19図に示すよう
に再溶融部1aと母材部分1bの境界の軟化域1cに長さ2.0m
m、深さ1.5mmのクラック６が発生した。On the other hand, in the sample 3 of the aluminum alloy member obtained by the heat treatment procedure of the comparative example shown in FIG. 9, when the heating / cooling was repeated 1400 cycles, as shown in FIG. Length 2.0m in softened area 1c at the boundary of material part 1b
A crack 6 having a depth of m and a depth of 1.5 mm was generated.
又、局部溶融・急冷処理を施さないT6処理材の試片３
では、加熱・冷却を800サイクル繰り返した時点で、第2
0図に示すように試片３の最狭幅部を横切る深さ3mmのク
ラック６が発生した。Also, a sample 3 of T 6 treated material that is not subjected to local melting / quenching treatment 3
Then, when heating and cooling are repeated 800 cycles, the second
As shown in FIG. 0, a crack 6 having a depth of 3 mm crossing the narrowest width portion of the sample 3 was generated.
以上のテスト結果から明らかなように、本実施例の手
順による熱処理では、レーザービーム照射による表面改
質処理に伴ってその再溶融部近傍に生成される軟化域が
最終的に消失し、耐熱疲労強度を大幅に向上させること
が出来るものである。As is clear from the above test results, in the heat treatment according to the procedure of the present example, the softened region generated near the remelted portion due to the surface modification treatment by laser beam irradiation finally disappeared, and the heat fatigue resistance The strength can be greatly improved.
〔実施例２〕 次に、本発明の第２の実施例について説明する。Second Embodiment Next, a second embodiment of the present invention will be described.
本実施例はアルミニウム合金素材としてAC4Dを適用し
たものであって、その素材寸法、処理手順、レーザービ
ーム照射条件などは先の実施例と同じである。In this embodiment, AC4D is applied as an aluminum alloy material, and the material dimensions, processing procedure, laser beam irradiation conditions, etc. are the same as those in the previous embodiments.
この場合の溶体化・焼入れ処理では、加熱温度480〜5
25℃×加熱時間４〜10Hrとするのが好適であり、焼入れ
は前記実施例と同様に水冷によって行っている。In this case, in the solution heat treatment, the heating temperature is 480-5
It is preferable to set 25 ° C. × heating time to 4 to 10 hours, and quenching is performed by water cooling as in the above-mentioned embodiment.
又、人工時効処理では、加熱温度160〜200℃×加熱時
間６〜10Hrとするのが好適である。In the artificial aging treatment, the heating temperature is preferably 160 to 200 ° C. and the heating time is 6 to 10 hours.
この実施例による表面改質および耐熱疲労強度向上の
結果は、前記第１の実施例と略同様である。The results of the surface modification and the improvement of the thermal fatigue strength in this example are substantially the same as those in the first example.
〔実施例３〕 本発明の第３図の実施例を次に説明する。[Third Embodiment] The third embodiment of the present invention will be described below.
本実施例はアルミニウム合金素材としてAC4Bを適用し
たものであって、その素材寸法、処理手順、レーザービ
ーム照射条件などは先の第１の実施例と同様である。In this embodiment, AC4B is applied as an aluminum alloy material, and the material dimensions, processing procedure, laser beam irradiation conditions, etc. are the same as those in the first embodiment.
この場合の溶体化・焼入れ処理では、加熱温度480〜5
00℃×加熱時間４〜10Hrとするのが好適であり、焼入れ
は前記第１の実施例と同様に水冷により行っている。In this case, in the solution heat treatment, the heating temperature is 480-5
It is preferable that the heating time is 00 ° C. × 4 to 10 hours, and the quenching is performed by water cooling as in the first embodiment.
又、人工時効処理では、加熱温度160〜200℃×加熱時
間６〜10Hrとするが好適である。In the artificial aging treatment, it is preferable that the heating temperature is 160 to 200 ° C. and the heating time is 6 to 10 hours.
この実施例による表面改質および耐熱疲労強度向上の
結果も、前記第１の実施例と略同様である。The results of the surface modification and the improvement of the thermal fatigue strength according to this embodiment are almost the same as those of the first embodiment.
本発明のアルミニウム合金部材の製造方法は、高密度
エネルギ熱線でアルミニウム合金素材を局部的に溶融・
急冷して表面改質処理を施した後に、このアルミニウム
合金素材に対して溶体化・焼入れ→人工時効の手順より
なるT6処理を施すようにしたから、溶融・急冷した再溶
融部近傍に生成する軟化域が次のT6処理により消失する
ことなり、耐熱疲労強度が向上するという効果を奏す
る。The method for manufacturing an aluminum alloy member of the present invention is a method of locally melting an aluminum alloy material with high-density energy heat rays.
After subjected to surface modification treatment quenching to, it is so arranged subjected to T 6 treatment consisting procedure for solution-hardening → artificial aging against the aluminum alloy material, generating the remelting portion vicinity of melting and quenching The softening zone is removed by the subsequent T 6 treatment, and the effect of improving the thermal fatigue strength is obtained.
また、上記方法は、用いたアルミニウム合金素材にSi
を含む場合、再溶融部を含むアルミニウム合金素材の全
体にT6処理が施されるため、再溶融部では共晶Siが球状
化して切欠き靭性が上がり耐熱疲労強度が一層向上する
一方、上記再溶融部と異なるアルミニウム合金素材の他
の部分もT6処理によりその強度が大幅に向上するなどの
効果を奏する。In addition, the above method uses Si
In the case of containing T, since the entire aluminum alloy material including the remelted portion is subjected to T 6 treatment, the eutectic Si is spheroidized in the remelted portion to improve notch toughness and further improve the thermal fatigue resistance, while Other parts of the aluminum alloy material different from the remelted part also have the effect that the strength is significantly improved by the T 6 treatment.
第１図は本発明の第１の実施例の熱処理手順を示すフロ
ー図、第２図はそのレーザービーム照射の過程を示す斜
視図、第３図は再溶融部近傍に生成する軟化域を示す断
面図、第４図および第５図はそれぞれ第１の実施例によ
り得られたアルミニウム合金部材の再溶融部の組織の拡
大図、第６図および第７図はそれぞれ第１の実施例によ
るアルミニウム合金部材の母材部分の組織の拡大図、第
８図は第１の実施例によるアルミニウム合金部材の硬さ
分布を示すグラフ、第９図は第１の比較例の熱処理手順
を示すフロー図、第10図は第２の比較例の熱処理手順を
示すフロー図、第11図および第12図はそれぞれ第１の比
較例によるアルミニウム合金部材の再溶融部の組織の拡
大図、第13図は第１の比較例によるアルミニウム合金部
材の硬さ分布を示すグラフ、第14図および第15図はそれ
ぞれ第２の比較例によるアルミニウム合金部材の再溶融
部の組織の拡大図、第16図は第２の比較例によるアルミ
ニウム合金部材の硬さ分布を示すグラフ、第17図（ａ）
・（ｂ）は耐熱疲労強度試験に供する試片の寸法、形状
を示す平面図および側面図、第18図は耐熱疲労強度試験
の方法を示す斜視図、第19図は第１の比較例によるアル
ミニウム合金部材試片の試験結果を示す平面図、第20図
はT6処理材試片の試験結果を示す平面図である。 １はアルミニウム合金素材、1aは再溶融部、1bは母材部
分、1cは軟化域である。FIG. 1 is a flow chart showing the heat treatment procedure of the first embodiment of the present invention, FIG. 2 is a perspective view showing the process of laser beam irradiation, and FIG. 3 shows a softened region formed near the remelted portion. Sectional views, FIGS. 4 and 5 are enlarged views of the structure of the remelted portion of the aluminum alloy member obtained by the first embodiment, and FIGS. 6 and 7 are aluminum according to the first embodiment. An enlarged view of the structure of the base material portion of the alloy member, FIG. 8 is a graph showing the hardness distribution of the aluminum alloy member according to the first embodiment, and FIG. 9 is a flow chart showing the heat treatment procedure of the first comparative example. FIG. 10 is a flow chart showing the heat treatment procedure of the second comparative example, FIGS. 11 and 12 are enlarged views of the structure of the remelted portion of the aluminum alloy member according to the first comparative example, and FIG. The hardness distribution of the aluminum alloy member according to the comparative example of 1 is shown. Rough, FIGS. 14 and 15 are enlarged views of the structure of the remelted portion of the aluminum alloy member according to the second comparative example, and FIG. 16 is a graph showing the hardness distribution of the aluminum alloy member according to the second comparative example. , Fig. 17 (a)
-(B) is a plan view and a side view showing the dimensions and shape of the specimen to be subjected to the thermal fatigue strength test, Fig. 18 is a perspective view showing the method of the thermal fatigue strength test, and Fig. 19 is according to the first comparative example. FIG. 20 is a plan view showing the test results of the aluminum alloy member sample, and FIG. 20 is a plan view showing the test results of the T 6 treated material sample. Reference numeral 1 is an aluminum alloy material, 1a is a remelted portion, 1b is a base metal portion, and 1c is a softened region.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 深堀 貢 広島県安芸郡府中町新地３番１号 マツダ 株式会社内 (56)参考文献 特開 昭56−89394（ＪＰ，Ａ) 特開 昭59−108849（ＪＰ，Ａ) 特開 昭61−193773（ＪＰ，Ａ) 特開 昭53−3913（ＪＰ，Ａ) ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Mitsugu Fukahori 3-1, Shinchi Fuchu-cho, Aki-gun, Hiroshima Mazda Co., Ltd. (56) References JP-A-56-89394 (JP, A) JP-A-59- 108849 (JP, A) JP 61-193773 (JP, A) JP 53-3913 (JP, A)
Claims (1)
材を局部的に溶融・急冷処理することにより、耐熱疲労
強度の向上した再溶融部を形成した後、上記アルミニウ
ム合金素材に対してT6処理を施すことによって、上記再
溶融部の近傍に生成し、上記アルミニウム合金素材の耐
熱疲労強度を低下させる軟化域を消失させることを特徴
とするアルミニウム合金部材の製造方法。1. An aluminum alloy material is locally melted and rapidly cooled with a high-density energy heat ray to form a remelted portion having improved thermal fatigue resistance, and then the aluminum alloy material is subjected to T 6 treatment. A method for producing an aluminum alloy member, characterized in that a softening region which is generated in the vicinity of the remelted portion and reduces the thermal fatigue strength of the aluminum alloy material disappears by performing the treatment.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60086084A JPH08951B2 (en) | 1985-04-22 | 1985-04-22 | Method for manufacturing aluminum alloy member |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60086084A JPH08951B2 (en) | 1985-04-22 | 1985-04-22 | Method for manufacturing aluminum alloy member |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS61246349A JPS61246349A (en) | 1986-11-01 |
| JPH08951B2 true JPH08951B2 (en) | 1996-01-10 |
Family
ID=13876836
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP60086084A Expired - Fee Related JPH08951B2 (en) | 1985-04-22 | 1985-04-22 | Method for manufacturing aluminum alloy member |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH08951B2 (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2705953B2 (en) * | 1988-10-24 | 1998-01-28 | いすゞ自動車株式会社 | Aluminum alloy engine component and method of manufacturing the same |
| CN106148861A (en) * | 2015-04-16 | 2016-11-23 | 南京理工大学 | A kind of method using local laser to process raising T5 state 6N01 aluminium alloy bending property |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE2948057A1 (en) * | 1979-11-29 | 1981-06-04 | Karl Schmidt Gmbh, 7107 Neckarsulm | METHOD FOR DESIGNING THE EDGE OF A COMBUSTION TUB OF A LIGHT METAL PISTON |
| JPS59108849A (en) * | 1982-12-14 | 1984-06-23 | Toyota Motor Corp | Piston for internal-combustion engine |
-
1985
- 1985-04-22 JP JP60086084A patent/JPH08951B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JPS61246349A (en) | 1986-11-01 |
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