JP4275419B2 - Aluminum alloy casting method - Google Patents
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- JP4275419B2 JP4275419B2 JP2003014921A JP2003014921A JP4275419B2 JP 4275419 B2 JP4275419 B2 JP 4275419B2 JP 2003014921 A JP2003014921 A JP 2003014921A JP 2003014921 A JP2003014921 A JP 2003014921A JP 4275419 B2 JP4275419 B2 JP 4275419B2
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- 238000005266 casting Methods 0.000 title claims description 39
- 238000000034 method Methods 0.000 title claims description 25
- 229910000838 Al alloy Inorganic materials 0.000 title claims description 22
- 238000001556 precipitation Methods 0.000 claims description 54
- 229910045601 alloy Inorganic materials 0.000 claims description 26
- 239000000956 alloy Substances 0.000 claims description 26
- 238000001816 cooling Methods 0.000 claims description 21
- 238000010438 heat treatment Methods 0.000 claims description 17
- 229910052782 aluminium Inorganic materials 0.000 claims description 16
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 16
- 229910000765 intermetallic Inorganic materials 0.000 claims description 15
- 229910052751 metal Inorganic materials 0.000 claims description 11
- 239000002184 metal Substances 0.000 claims description 11
- 239000002244 precipitate Substances 0.000 claims description 10
- 229910018182 Al—Cu Inorganic materials 0.000 claims description 7
- 229910018134 Al-Mg Inorganic materials 0.000 claims description 3
- 229910018467 Al—Mg Inorganic materials 0.000 claims description 3
- 229910006776 Si—Zn Inorganic materials 0.000 claims description 3
- 229910001316 Ag alloy Inorganic materials 0.000 claims description 2
- 230000000630 rising effect Effects 0.000 claims description 2
- 238000007710 freezing Methods 0.000 claims 2
- 230000008014 freezing Effects 0.000 claims 2
- 238000007711 solidification Methods 0.000 description 7
- 230000008023 solidification Effects 0.000 description 7
- 239000012071 phase Substances 0.000 description 6
- 239000000047 product Substances 0.000 description 6
- 238000000465 moulding Methods 0.000 description 5
- 238000001953 recrystallisation Methods 0.000 description 5
- 238000004073 vulcanization Methods 0.000 description 5
- 210000001787 dendrite Anatomy 0.000 description 4
- 238000004519 manufacturing process Methods 0.000 description 4
- 230000015572 biosynthetic process Effects 0.000 description 3
- 238000010586 diagram Methods 0.000 description 3
- 230000000694 effects Effects 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 230000002093 peripheral effect Effects 0.000 description 2
- 238000004781 supercooling Methods 0.000 description 2
- 238000007546 Brinell hardness test Methods 0.000 description 1
- 229910000881 Cu alloy Inorganic materials 0.000 description 1
- 229910018565 CuAl Inorganic materials 0.000 description 1
- 229910000990 Ni alloy Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 229910002056 binary alloy Inorganic materials 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 230000008021 deposition Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 239000007791 liquid phase Substances 0.000 description 1
- 230000004807 localization Effects 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 239000011505 plaster Substances 0.000 description 1
- 238000012805 post-processing Methods 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
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Description
【０００１】
【発明の属する技術分野】
この発明は、アルミニウム系合金、特にAl−Cu系合金に代表される、金属間化合物を析出するアルミニウム系合金の鋳造に関するものである。
【０００２】
【従来の技術】
物を製造する際の成形工程で用いる金型は、製品に応じて多種多様であり、その材質も鋼材は勿論、銅合金やニッケル合金、そしてアルミニウム合金など、多岐にわたっている。
【０００３】
例えば、ゴム製品の典型例であるタイヤは、その周面にトレッドパターンと呼ばれる凹凸模様を有するのが通例であり、このタイヤの製造の最終工程である、加硫成形を司る加硫金型は、凹凸模様を転写するための凸凹形状に、その内周面が形成されている。かような凸凹形状を有するタイヤ製造用の金型は、軽量で熱伝導性が良好である事、また、加工が容易である事の理由から、アルミニウム系合金を用いた鋳造によって製造されるのが一般的である。
【０００４】
例えば、アルミニウム系合金を用いた金型の鋳造に関して、特許文献１には、タイヤ成形用金型をアルミニウム合金にて製造することが記載されている。
【０００５】
【特許文献１】
特開２００１−１５０４４４号公報
【０００６】
【発明が解決しようとする課題】
しかしながら、アルミニウム合金で鋳込んだ鋳物は、凝固冷却時の変形が大きく、精度の高い品物を得るのが困難であるため、鋳造後に加工して品物（金型）精度を確保しなくてはならない、という問題があった。さらに、凝固冷却のばらつきによって強度も大きくばらつくことも問題であった。
【０００７】
そこで、この発明は、アルミニウム系合金を用いて、例えば金型を鋳造にて製造する際に問題となる、鋳造後の形状精度および製品の強度を有利に改善する方途について提案することを目的とするものである。
【０００８】
【課題を解決するための手段】
この発明の要旨構成は、つぎの通りである。
（１）金属間化合物を析出するアルミニウム系合金の溶湯を、鋳型に注入して鋳造を行うに当たり、この鋳型内において前記溶湯を金属間化合物の析出点以下まで冷却して凝固させたのち、一旦析出点を超える温度域に昇温してから再び析出点以下の温度域まで冷却する、熱処理操作を、少なくとも３回は行うことを特徴とするアルミニウム系合金の鋳造方法。
【０００９】
（２）金属間化合物を析出するアルミニウム系合金の溶湯を、鋳型に注入して鋳造を行うに当たり、この鋳型内において前記溶湯を金属間化合物の析出点以下まで冷却して凝固させたのち、一旦析出点を超え（析出点＋５０℃）以下の温度域に昇温してから再び析出点以下の温度域まで冷却する、熱処理操作を、少なくとも１回は行うことを特徴とするアルミニウム系合金の鋳造方法。
【００１０】
（３）金属間化合物を析出するアルミニウム系合金の溶湯を、鋳型に注入して鋳造を行うに当たり、この鋳型内において前記溶湯を金属間化合物の析出点以下まで冷却して凝固させたのち、一旦析出点を超える温度域に昇温してから再び析出点以下（析出点−５０℃）以上での温度域まで冷却する、熱処理操作を、少なくとも１回は行うことを特徴とするアルミニウム系合金の鋳造方法。
【００１２】
（４）熱処理操作を１回当たり、３００秒の時間内に行うことを特徴とする上記（１）ないし（３）のいずれかに記載のアルミニウム系合金の鋳造方法。
【００１３】
（５）溶湯からの冷却速度が、1〜1000℃／ｓであることを特徴とする上記（１）ないし（４）のいずれかに記載のアルミニウム系合金の鋳造方法。
【００１４】
（６）析出点を超える温度域から析出点以下の温度域まで冷却する際の冷却速度が、1〜100℃／ｓであることを特徴とする上記（１）ないし（５）のいずれかに記載のアルミニウム系合金の鋳造方法。
【００１５】
（７）析出点以下の温度域から析出点を超える温度域に昇温する際の昇温速度が、1〜100℃／ｓであることを特徴とする上記（１）ないし（６）のいずれかに記載のアルミニウム系合金の鋳造方法。
【００１６】
（８）アルミニウム系合金が、Al−Cu系、Al−Si−Zn系、Al−Mg系またはAl−Ag系合金であることを特徴とする上記（１）ないし（７）のいずれかに記載のアルミニウム系合金の鋳造方法。
【００１７】
【発明の実施の形態】
以下に、この発明のアルミニウム系合金の鋳造方法について、タイヤの加硫金型、特に分割金型に多用されるAl−Cu系合金を例に、詳しく説明する。
例えば、Al−4.0mass％Cu系合金の鋳造は、図１に示すAl−Cu系平衡状態図において、Ａ点からＧ点へ到る冷却過程を経て、凝固を進行させることで行われる。すなわち、鋳型内に装入された溶湯は、鋳型の冷却に伴って、Ａ点（液相Ｌ）から、Ｂ点そしてＣ点の固液共存相を経てＤ点に到り、このＤ点で凝固が始まりＥ点（α相）を経てＦ点に達すると、金属間化合物（ここではCuAl2）が析出し始め、Ｇ点においてα相にてθ相の介在物が成長する。
【００１８】
かような凝固過程において、まず図２に熱処理履歴を示すように、Ｄ点から金属間化合物の析出点であるＦ点（以下、析出点という）または析出点Ｆ以下の温度域までＴ１時間内に一気に冷却したのち、一旦析出点Ｆを超える温度域、例えばＦ＋５０℃の温度までＴ２時間をかけて昇温してから、Ｔ３時間内に、析出点Ｆ以下の温度域、例えばＦ−５０℃の温度まで冷却する、熱処理操作を、少なくとも１回、図示例で３回行うことが肝要である。この熱処理操作後は、Ｇ点以下へ冷却する。
【００１９】
すなわち、アルミニウム系合金を鋳造する際、その冷却過程において、析出点以下で冷却を停止し、一旦析出点Ｆを超える温度域まで昇温してから析出点以下の温度域まで冷却する、熱処理操作を、１回または複数回行うことによって、微細な鋳造組織および球状介在物が生成することから、鋳型内寸法に合致した高強度の鋳造物を得ることが可能になる。
【００２０】
なぜなら、凝固完了（α相晶出）の時点（Ｄ点）から急速に過冷すると、大量の原子空孔が生成し、この原子空孔を核としてθ相が生成し、この不均一θ相の生成から成長を上記の熱処理操作にて均一化することによって、微細な鋳造組織と球状介在物とを得ることができるからである。
【００２１】
この効果は、上記の熱処理操作を少なくとも１回行うことで得られるが、好ましくは３回、より好ましくは５回以上とする。なお、上限は特に設ける必要はないが、鋳造生産性（鋳造サイクル）の観点から、７回以下とすることが有利である。
【００２２】
ここで、析出点を超える温度域は、析出点を超え（析出点＋５０℃）以下であることが好ましい。すなわち、この温度域が析出点以下では上記した微細な鋳造組織および球状介在物の獲得が難しくなり、一方（析出点＋５０℃）を超えると、
再結晶による組織の拡大化や、介在物の板状や針状成長の局在が発生するからである。
【００２３】
同様に、析出点以下の温度域は、析出点以下（析出点−５０℃）以上であることが好ましい。すなわち、この温度域が析出点を超えると、上記した微細な鋳造組織および球状介在物の獲得が難しくなり、一方（析出点−５０℃）未満では、再結晶は発生しないものの、介在物のデンドライト化（樹枝状成長）が進み球状介在物の維持が図れないからである。
【００２４】
また、上記熱処理操作を１回当たり、３００秒以内、好ましくは１８０秒以内、より好ましくは６０秒以内に行うことが有利である。なぜなら、３００秒をこえると、析出点＋５０℃以上で再結晶しやすく、また析出点−５０℃ではデンドライト成長しやすいからである。
【００２５】
より具体的には、図２に示した時間Ｔ１〜Ｔ７を、それぞれ１０〜３０秒の範囲内で制御することが、寸法精度と生産性とを両立する上で好ましい。
【００２６】
さらに、溶湯からの冷却速度、つまり図２においてＤ点からＦ点以下に到る冷却速度は、１〜１０００℃／ｓ、好ましくは１００〜５００℃／ｓであることが推奨される。なぜなら、この領域温度（Ｄ点〜Ｆ点）の冷却速度が１０００℃／ｓより速いと鋳型割れが生じやすく、一方１℃／ｓより遅いと鋳物の凝固変形が大きくなるからである。
【００２７】
同様に、析出点を超える温度域から析出点以下の温度域まで冷却する際の冷却速度が、１〜１００℃／ｓ、好ましくは１０℃／ｓ以下であることが推奨される。なぜなら、１００℃／ｓより速い過冷現象により析出生成が不均一になり、一方１℃／ｓより遅いと、デンドライト成長しやすくなるためである。したがって、均一になり、１℃／ｓより遅いとデンドライト成長しやすくなるためである。したがって均一析出させるためには１〜１００℃／ｓが好ましい。
【００２８】
一方、析出点以下の温度域から析出点を超える温度域に昇温する際の昇温速度は、１〜１００℃／ｓ、好ましくは１０℃／ｓ以下であることが推奨される。なぜなら、１００℃／ｓより速いと析出物を不均一再固溶する事が困難になり、一方１℃／ｓより遅いと、析出物、固溶と同時に再結晶が進み微細組織でかつ均一球状介在物（析出物）を得る事が困難になるためである。
【００２９】
同様に、析出点以下の温度域から析出点を超える温度域に再昇温する際の昇温速度は、１〜１００℃／ｓ、好ましくは１０℃／ｓ以下であることが推奨される。なぜなら、１００℃／ｓより速いと一度生成した球状介在物は針状又は板状に変化しながら再固溶し、球状介在物を維持する事が難しくなる。一方、１℃／ｓよりも遅いと球状介在物は均一に再固溶するものの、再結晶化が進み微細組織を得ることが困難になる。
【００３０】
なお、アルミニウム系合金としては、上記のAl−Cu系のほか、Al−Si−Zn系、Al−Mg系またはAl−Ag系合金等を用いることができ、さらに、これら二元系を基本として他の成分を添加した、三元系以上であってもよい。
【００３１】
【実施例】
JIS Ｈ5202（1992）に規定されたＡＣ２Ｂに準拠した成分組成のアルミニウム系合金を、タイヤパターン部は石膏で、他は温度調節ができる金型の鋳型に装入して、表１に示す条件に従う鋳型内での熱処理操作を行って鋳造し、タイヤの加硫成形に供するセグメント金型を製造した。また、比較として、鋳型内での熱処理操作を行うことなく、鋳造後に鋳型から取り出して放冷する、従来の手法（従来例）によっても金型の製造を行った。なお、鋳造条件は、溶湯押し時間が３．５分間および背圧が０．５kgf／mm2であった。.
【００３２】
かくして得られた、各金型について、その背面反り量および強度を調査した。その結果を表２に示す。
なお、背面反り量は、金型の設計背面を基準とする、ずれの最大値を測定して評価するものであり、この背面反り量が０．１mm以下であれば、後加工なしに鋳型として供することができる。また、強度は、JIS Ｚ2243（1992）に準拠したブリネル硬さ試験を行って評価した。
【００３３】
【表１】
【表２】
【発明の効果】
この発明によれば、アルミニウム系合金を用いた鋳造において、鋳造後の形状精度および製品の強度が向上されるから、特に細密な形状が要求されるタイヤ加硫成形用の金型の製造に有効な方途を提供することができる。
【図面の簡単な説明】
【図１】 Al−Cu系の平衡状態図である。
【図２】 この発明に従う熱処理操作の手順を示す図である。[0001]
BACKGROUND OF THE INVENTION
The present invention relates to casting of an aluminum-based alloy, particularly an aluminum-based alloy on which an intermetallic compound is deposited, represented by an Al-Cu-based alloy.
[0002]
[Prior art]
There are a wide variety of molds used in the molding process when manufacturing products, and there are a wide variety of materials such as copper alloys, nickel alloys, and aluminum alloys as well as steel materials.
[0003]
For example, a tire, which is a typical example of a rubber product, usually has a concavo-convex pattern called a tread pattern on its peripheral surface, and the vulcanization mold for vulcanization molding, which is the final process of manufacturing the tire, is The inner peripheral surface is formed in an uneven shape for transferring the uneven pattern. The mold for manufacturing tires having such an uneven shape is manufactured by casting using an aluminum-based alloy because of its light weight, good thermal conductivity, and easy processing. Is common.
[0004]
For example, regarding casting of a mold using an aluminum-based alloy, Patent Document 1 describes that a tire molding mold is manufactured from an aluminum alloy.
[0005]
[Patent Document 1]
Japanese Patent Laid-Open No. 2001-150444
[Problems to be solved by the invention]
However, castings cast with an aluminum alloy have large deformation during solidification and cooling, and it is difficult to obtain highly accurate products. Therefore, it is necessary to process after casting to ensure the accuracy of the product (die). There was a problem. In addition, the strength also varies greatly due to variations in solidification cooling.
[0007]
Therefore, the object of the present invention is to propose a method for advantageously improving the shape accuracy after casting and the strength of the product, which becomes a problem when, for example, a mold is manufactured by casting using an aluminum-based alloy. To do.
[0008]
[Means for Solving the Problems]
The gist of the present invention is as follows.
(1) When casting a molten aluminum alloy that precipitates an intermetallic compound into a mold, the molten metal is cooled to below the precipitation point of the intermetallic compound in the mold and solidified. A method for casting an aluminum-based alloy, wherein a heat treatment operation is performed at least three times, wherein the temperature is raised to a temperature range exceeding the precipitation point and then cooled again to a temperature range below the precipitation point.
[0009]
(2) When casting a molten aluminum alloy that precipitates an intermetallic compound into a mold, the molten metal is cooled to below the precipitation point of the intermetallic compound in the mold and solidified. Casting of an aluminum-based alloy characterized in that the heat treatment operation is performed at least once by raising the temperature to a temperature range exceeding the precipitation point (precipitation point + 50 ° C.) and then cooling again to the temperature range below the precipitation point. Way .
[0010]
(3) When casting a molten aluminum alloy that precipitates an intermetallic compound into a mold, the molten metal is cooled to below the precipitation point of the intermetallic compound in the mold and solidified. An aluminum alloy characterized by performing a heat treatment operation at least once by raising the temperature to a temperature range exceeding the precipitation point and then cooling again to a temperature range below the precipitation point (precipitation point −50 ° C.) or more. Casting method.
[0012]
(4) The aluminum alloy casting method according to any one of the above (1) to (3) , wherein the heat treatment operation is performed within 300 seconds per time.
[0013]
(5) The method for casting an aluminum alloy according to any one of (1) to (4) , wherein the cooling rate from the molten metal is 1 to 1000 ° C./s.
[0014]
(6) The cooling rate at the time of cooling from a temperature range exceeding the precipitation point to a temperature range below the precipitation point is 1 to 100 ° C./s, according to any one of the above (1) to (5) The aluminum alloy casting method described.
[0015]
(7) Any one of the above (1) to (6) , wherein the temperature rising rate when the temperature is raised from a temperature range below the precipitation point to a temperature range exceeding the precipitation point is 1 to 100 ° C./s A method for casting an aluminum alloy according to claim 1.
[0016]
(8) The aluminum alloy is an Al—Cu alloy, an Al—Si—Zn alloy, an Al—Mg alloy, or an Al—Ag alloy, according to any one of the above (1) to (7). A casting method for aluminum alloys.
[0017]
DETAILED DESCRIPTION OF THE INVENTION
The aluminum alloy casting method of the present invention will be described in detail below, taking as an example an Al—Cu alloy that is frequently used in tire vulcanization molds, particularly split molds.
For example, casting of an Al-4.0 mass% Cu-based alloy is performed by proceeding with solidification through a cooling process from point A to point G in the Al-Cu-based equilibrium diagram shown in FIG. That is, as the mold cools, the molten metal charged in the mold reaches the point D through the solid-liquid coexistence phase of the points B and C, from the point A (liquid phase L). When solidification starts and reaches the F point through the E point (α phase), an intermetallic compound (CuAl 2 in this case) begins to precipitate, and inclusions in the θ phase grow in the α phase at the G point.
[0018]
In such a solidification process, first, as shown in FIG. 2, the heat treatment history is shown within T1 time from point D to point F which is the precipitation point of the intermetallic compound (hereinafter referred to as precipitation point) or temperature range below the precipitation point F. After cooling at once, the temperature is raised over a temperature range exceeding the precipitation point F, for example, F + 50 ° C. over a period of T2 hours, and then within a temperature range below the precipitation point F, for example, F-50 ° C. within T3 time. It is important to perform the heat treatment operation for cooling to a temperature of at least once, in the illustrated example three times. After this heat treatment operation, it is cooled below the G point.
[0019]
That is, when casting an aluminum-based alloy, in the cooling process, the cooling is stopped below the precipitation point, the temperature is once raised to a temperature range above the precipitation point F, and then cooled to a temperature range below the precipitation point. By performing once or a plurality of times, a fine cast structure and spherical inclusions are generated, so that it becomes possible to obtain a high-strength cast that matches the dimensions in the mold.
[0020]
This is because, when supercooling rapidly from the time of solidification completion (α phase crystallization) (point D), a large amount of atomic vacancies are generated, and a θ phase is generated using these atomic vacancies as nuclei. This is because a fine cast structure and spherical inclusions can be obtained by making the growth from the formation of the above uniform by the above heat treatment operation.
[0021]
This effect can be obtained by performing the above heat treatment operation at least once, but preferably 3 times, more preferably 5 times or more. The upper limit is not particularly required, but is preferably 7 times or less from the viewpoint of casting productivity (casting cycle).
[0022]
Here, it is preferable that the temperature range exceeding the precipitation point exceeds the precipitation point (precipitation point + 50 ° C.) or less. That is, if this temperature range is below the precipitation point, it becomes difficult to obtain the fine cast structure and spherical inclusions described above, and if it exceeds one (precipitation point + 50 ° C.),
This is because enlargement of the structure due to recrystallization and localization of inclusions such as plate-like and needle-like growth occur.
[0023]
Similarly, the temperature range below the precipitation point is preferably equal to or lower than the precipitation point (deposition point−50 ° C.). That is, when this temperature range exceeds the precipitation point, it becomes difficult to obtain the above-described fine cast structure and spherical inclusions. On the other hand, if it is less than (precipitation point −50 ° C.), recrystallization does not occur, but inclusion dendrites. This is because the formation (dendritic growth) proceeds and the spherical inclusions cannot be maintained.
[0024]
Further, it is advantageous to perform the above heat treatment operation within 300 seconds, preferably within 180 seconds, more preferably within 60 seconds per time. This is because if it exceeds 300 seconds, recrystallization is likely to occur at a precipitation point of + 50 ° C. or more, and dendrite growth is likely to occur at a precipitation point of −50 ° C.
[0025]
More specifically, it is preferable to control the times T1 to T7 shown in FIG. 2 within a range of 10 to 30 seconds, respectively, in order to achieve both dimensional accuracy and productivity.
[0026]
Further, it is recommended that the cooling rate from the molten metal, that is, the cooling rate from the point D to the point F or lower in FIG. 2 is 1 to 1000 ° C./s, preferably 100 to 500 ° C./s. This is because if the cooling rate of this region temperature (D point to F point) is faster than 1000 ° C./s, mold cracking is likely to occur, and if it is slower than 1 ° C./s, the solidification deformation of the casting increases.
[0027]
Similarly, it is recommended that the cooling rate when cooling from a temperature range exceeding the precipitation point to a temperature range below the precipitation point is 1 to 100 ° C./s, preferably 10 ° C./s or less. This is because the precipitate formation becomes non-uniform due to the supercooling phenomenon faster than 100 ° C./s, and when it is slower than 1 ° C./s, the dendrite grows easily. Therefore, it becomes uniform, and if it is slower than 1 ° C./s, it becomes easy to grow dendrite. Therefore, 1-100 ° C./s is preferable for uniform precipitation.
[0028]
On the other hand, it is recommended that the rate of temperature rise when raising the temperature from the temperature range below the precipitation point to the temperature range above the precipitation point is 1 to 100 ° C./s, preferably 10 ° C./s or less. This is because if it is faster than 100 ° C./s, it becomes difficult to re-dissolve the precipitate in a non-uniform manner, while if it is slower than 1 ° C./s, recrystallization proceeds simultaneously with the precipitate and the solid solution, resulting in a fine structure and uniform spherical shape. This is because it becomes difficult to obtain inclusions (precipitates).
[0029]
Similarly, it is recommended that the rate of temperature rise when the temperature is raised again from a temperature range below the precipitation point to a temperature range above the precipitation point is 1 to 100 ° C./s, preferably 10 ° C./s or less. This is because if it is faster than 100 ° C./s, the spherical inclusions once generated are dissolved again while changing to a needle shape or a plate shape, and it becomes difficult to maintain the spherical inclusions. On the other hand, if it is slower than 1 ° C./s, the spherical inclusions re-dissolve uniformly, but recrystallization proceeds and it becomes difficult to obtain a fine structure.
[0030]
In addition to the above Al-Cu system, Al-Si-Zn system, Al-Mg system, Al-Ag system alloy, etc. can be used as an aluminum system alloy. Furthermore, on the basis of these binary systems It may be a ternary system or higher with other components added.
[0031]
【Example】
Insert aluminum alloy with component composition in accordance with AC2B specified in JIS H5202 (1992) into the mold of the mold that can control the temperature with plaster for the tire pattern part, and follow the conditions shown in Table 1 A segment die for vulcanization molding of a tire was manufactured by performing a heat treatment operation in the mold. For comparison, the mold was also manufactured by a conventional method (conventional example) in which the mold was taken out from the mold after casting and allowed to cool without performing a heat treatment operation in the mold. The casting conditions were that the molten metal pressing time was 3.5 minutes and the back pressure was 0.5 kgf / mm 2 . .
[0032]
The back warp amount and strength of each mold thus obtained were investigated. The results are shown in Table 2.
The back warp amount is evaluated by measuring the maximum deviation based on the design back of the mold, and if this back warp amount is 0.1 mm or less, it can be used as a mold without post-processing. Can be provided. The strength was evaluated by conducting a Brinell hardness test in accordance with JIS Z2243 (1992).
[0033]
[Table 1]
[Table 2]
【The invention's effect】
According to this invention, in casting using an aluminum-based alloy, the shape accuracy after casting and the strength of the product are improved. Therefore, it is effective for manufacturing a mold for tire vulcanization molding that requires a particularly fine shape. Can provide a variety of ways.
[Brief description of the drawings]
FIG. 1 is an equilibrium diagram of an Al—Cu system.
FIG. 2 is a diagram showing a procedure of a heat treatment operation according to the present invention.
Claims (8)
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