JPH09272945A - Heat resistant magnesium alloy molded member, heat resistant magnesium alloy used for the molding and molding method therefor - Google Patents

Heat resistant magnesium alloy molded member, heat resistant magnesium alloy used for the molding and molding method therefor

Info

Publication number
JPH09272945A
JPH09272945A JP8082832A JP8283296A JPH09272945A JP H09272945 A JPH09272945 A JP H09272945A JP 8082832 A JP8082832 A JP 8082832A JP 8283296 A JP8283296 A JP 8283296A JP H09272945 A JPH09272945 A JP H09272945A
Authority
JP
Japan
Prior art keywords
magnesium alloy
heat
resistant magnesium
molded member
ratio
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
Application number
JP8082832A
Other languages
Japanese (ja)
Other versions
JP3415987B2 (en
Inventor
Kazuo Sakamoto
和夫 坂本
Yukio Yamamoto
幸男 山本
Nobuo Sakate
宣夫 坂手
Shoji Hirahara
庄司 平原
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Mazda Motor Corp
Original Assignee
Mazda Motor Corp
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Mazda Motor Corp filed Critical Mazda Motor Corp
Priority to JP08283296A priority Critical patent/JP3415987B2/en
Priority to CN971050007A priority patent/CN1065003C/en
Priority to DE69706737T priority patent/DE69706737T2/en
Priority to EP97105641A priority patent/EP0799901B1/en
Priority to KR1019970012613A priority patent/KR970070224A/en
Publication of JPH09272945A publication Critical patent/JPH09272945A/en
Priority to US09/949,621 priority patent/US20020020475A1/en
Application granted granted Critical
Publication of JP3415987B2 publication Critical patent/JP3415987B2/en
Anticipated expiration legal-status Critical
Expired - Fee Related legal-status Critical Current

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C23/00—Alloys based on magnesium
    • C22C23/02—Alloys based on magnesium with aluminium as the next major constituent
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D17/00—Pressure die casting or injection die casting, i.e. casting in which the metal is forced into a mould under high pressure
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
    • B22D21/002—Castings of light metals
    • B22D21/007—Castings of light metals with low melting point, e.g. Al 659 degrees C, Mg 650 degrees C

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  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Chemical & Material Sciences (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacture Of Alloys Or Alloy Compounds (AREA)
  • Forging (AREA)
  • Injection Moulding Of Plastics Or The Like (AREA)

Abstract

PROBLEM TO BE SOLVED: To produce a heat resistant Mg allay molded member excellent in moldability and extensibility while its creep resistance is secured, in an Mg-Al- Ca-Mn alloy, by specifying its compsn. and regulating the ratio of Ca/Al to a specified value or below. SOLUTION: An Mg alloy having a compsn. contg., by weight, 2 to 6% Al, 0.5 to 4% Ca, and the balance Mg, and in which the ratio of Ca/Al is regulated to <=0.8 is subjected to half-melting injection molding at a liquids temp. or below in which solid phases and liq. phases are coexistent. In this way, the heat resistant Mg alloy molded member such as automobile transmission parts or engine parts excellent in creep resistance can be obtd. Al is required by >=2%, but, in the case of >6%, its elongation deteriorates even if the half- melting injection molding is executed. Ca is added for increasing its high temp. strength tending toward reduction accompanying the addition of Mg to Al, but, for preventing the reduction of its moldability and the elongation of the molded member, the ratio of Ca/Al is required to be suppressed to <=0.8. Moreover, <=0.15% Sr is preferably added as a refining agent.

Description

【発明の詳細な説明】Detailed Description of the Invention

【０００１】[0001]

【発明の属する技術分野】本発明は耐クリープ性を確保
しつつ、特に成形性、伸び性に優れる耐熱マグネシウム
合金成形部材、その成形に用いる耐熱マグネシウム合金
およびその成形方法に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a heat-resistant magnesium alloy molded member excellent in moldability and extensibility while ensuring creep resistance, a heat-resistant magnesium alloy used for molding, and a molding method thereof.

【０００２】[0002]

【従来の技術】マグネシウム合金は現在実用化されてい
る金属材料の中でも最も低密度であり、今後の自動車用
軽量材として強く期待されている。現在最も一般的に用
いられているマグネシウム合金はＭｇ−Ａｌ−Ｚｎ−Ｍ
ｎ系合金（例えばＡＺ９１Ｄ合金）であり、室温強度が
高く、耐食性も良好であるため、自動車用トランスミッ
ションケース、シリンダヘッドカバーなどに適用されて
いる。しかしながら、１２０℃を越える温度域では強度
特性が低下し始め、特に耐クリープ性が劣るという欠点
があり、実部品レベルではネジ締結部の座面がへたるな
どの問題に繋がる。2. Description of the Related Art Magnesium alloy has the lowest density of metallic materials currently in practical use and is strongly expected as a lightweight material for automobiles in the future. The most commonly used magnesium alloy at present is Mg-Al-Zn-M.
Since it is an n-based alloy (for example, AZ91D alloy), has high room temperature strength and good corrosion resistance, it is applied to automobile transmission cases, cylinder head covers, and the like. However, in the temperature range exceeding 120 ° C., the strength characteristics begin to deteriorate, and especially the creep resistance is inferior, and at the level of actual parts, this leads to a problem such as the depression of the seat surface of the screw fastening part.

【０００３】他方、耐熱性を改善した合金としてはＭｇ
−Ａｌ−Ｓｉ系のＡＳ４１マグネシウム合金が使用され
ている。しかしながら、耐クリープ性に関しては上記Ａ
Ｚ９１Ｄよりも良好であるが、使用温度が１５０℃近傍
では不十分な特性となり、しかも室温、高温とも引張強
度特性が低いため、要求強度を確保するには厚肉とせざ
るを得ず、マグネシウムの軽量化効果が減少するという
問題が生ずる。On the other hand, Mg is an alloy having improved heat resistance.
An -Al-Si based AS41 magnesium alloy is used. However, regarding creep resistance, the above A
Although it is better than Z91D, it has insufficient properties near the operating temperature of 150 ° C, and has low tensile strength properties at both room temperature and high temperature. There is a problem that the weight reduction effect is reduced.

【０００４】その他、耐熱性を改善した合金として銀や
希土類元素などを添加したＱＥ２２などの合金がある
が、高価であり、鋳造性の点でダイキャストには適さな
いなどの欠点がある。[0004] Other alloys having improved heat resistance include alloys such as QE22 to which silver or a rare earth element is added, but they are disadvantageous in that they are expensive and are not suitable for die casting in terms of castability.

【０００５】そのため、新たに高温強度に優れる、Ｍｇ
−Ａｌ−Ｃａ−Ｍｎ系合金（特開平６−２５７９０号）
が提案されるに至った。ここでは、特にＣａ／Ａｌの比
を０．７、好ましくは０．７５以上にするとマグネシウ
ム合金中に晶出する析出物の組織形態が変化し、Ｍｇ−
Ｃａ化合物が晶出して優れた高温強度特性を示すように
なるとしている。Therefore, Mg, which is newly excellent in high temperature strength,
-Al-Ca-Mn-based alloy (JP-A-6-25790)
Came to be proposed. Here, in particular, when the Ca / Al ratio is set to 0.7, preferably 0.75 or more, the morphology of precipitates crystallized in the magnesium alloy changes, and Mg-
It is said that the Ca compound crystallizes and exhibits excellent high temperature strength characteristics.

【０００６】[0006]

【発明が解決しようとする課題】しかしながら、Ｃａ／
Ａｌ比の高いマグネシウム合金ではダイキャストにおい
て部材を成形しようとする場合、熱間割れが発生しやす
く、溶湯温度が高いと金型への焼付きが発生しやすいな
どの問題を残している。本発明は、このような従来技術
の有する課題に鑑み、自動車などのエンジン部品等に適
する物性、特に耐クリープ性を確保しつつ、成形性、伸
び性に優れる耐熱マグネシウム合金成形部材を提供する
ことを第１の目的とする。本発明の第２の目的は汎用さ
れるダイキャストに代え、上記耐熱マグネシウム合金成
形部材の適切な成形方法を提供することにある。更に、
本発明の第３の目的は上記耐クリープ性を確保しつつ、
成形性、伸び性に優れる耐熱マグネシウム合金成形部材
を製造するに適する合金組成を提供することにある。[Problems to be Solved by the Invention] However, Ca /
With magnesium alloys having a high Al ratio, when a member is to be formed by die casting, hot cracking is likely to occur, and if the melt temperature is high, seizure on the mold is likely to occur. In view of the problems of the prior art, the present invention provides a heat-resistant magnesium alloy molded member that is excellent in moldability and elongation while securing physical properties suitable for engine parts of automobiles and the like, particularly creep resistance. Is the first purpose. A second object of the present invention is to provide an appropriate molding method for the heat-resistant magnesium alloy molded member, instead of general-purpose die casting. Furthermore,
A third object of the present invention is to secure the above creep resistance,
An object of the present invention is to provide an alloy composition suitable for producing a heat-resistant magnesium alloy molded member having excellent formability and elongation.

【０００７】[0007]

【課題を解決するための手段】本発明者らは上記の課題
を解決するために種々検討を重ねた結果、Ａｌ−Ｃａ系
マグネシウム合金ではダイキャスト法に代え、固相と液
相が混在した状態で射出成形を行う半溶融成形法を適用
とすると、金型の焼き付きを防止できると同時に、成形
される部材に優れた強度を付与することができることを
見い出したが、その固相と液相が混在した状態を維持す
るためにはアルミニウムの添加量を極力増大することが
必要となる。他方、アルミニウムはマグネシウムに固溶
し、時効硬化性を示し、合金の機械的性質を高めるため
に添加するが、マグネシウムへのアルミニウムの添加に
伴い、低下する傾向にある高温強度を増強するためにＣ
ａ／Ａｌ比を０．７以上に保持するようにカルシウムを
添加することが推奨されている（特開平６−２５７９０
号）。しかしながら、このカルシウム量が多いと、成形
時に鋳造割れ及び金型への焼き付きが発生し易い上、Ｍ
ｇ−Ｃａ系化合物が多量に晶出するため、成形物の伸び
が低下する傾向があり、むしろＣａ／Ａｌ比を０．８以
下にする必要があることを見い出した。Means for Solving the Problems The inventors of the present invention have conducted various studies in order to solve the above problems, and as a result, in the Al--Ca magnesium alloy, a solid phase and a liquid phase were mixed instead of the die casting method. It was found that if a semi-melt molding method in which injection molding is performed in a state is applied, seizure of the mold can be prevented and at the same time excellent strength can be imparted to the molded member. In order to maintain the mixed state, it is necessary to increase the addition amount of aluminum as much as possible. On the other hand, aluminum forms a solid solution in magnesium, exhibits age hardening, and is added to enhance the mechanical properties of the alloy, but in order to enhance the high temperature strength that tends to decrease with the addition of aluminum to magnesium, C
It is recommended to add calcium so as to keep the a / Al ratio at 0.7 or more (Japanese Patent Laid-Open No. 6-25790).
issue). However, when the amount of calcium is large, casting cracks and seizure on the mold are likely to occur during molding, and M
It was found that the g-Ca-based compound crystallizes in a large amount, so that the elongation of the molded product tends to decrease, and rather the Ca / Al ratio needs to be 0.8 or less.

【０００８】そこで、本発明は、上記両者の知見に基づ
き、アルミニウム２〜６重量％及びカルシウム０．５〜
４重量％を含有し、残部がマグネシウムと不可避の不純
物からなり、Ｃａ／Ａｌ比が０．８以下のマグネシウム
合金から成形された成形部材であり、耐クリープ性を確
保しつつ、成形性、伸び性に優れるマグネシウム合金成
形部品を提供することにある。一般に、マグネシウム合
金ではマグネシウムに固溶し、時効硬化性を示し、合金
の機械的性質を高めるためにアルミニウム２〜１０重量
％を添加するのが好ましいとされている。これに対し、
本発明ではアルミニウムは２重量％以上添加される必要
があるが、６重量％を越えると、半溶融射出成形を行っ
ても伸びが低下する。そのため、半溶融射出成形を行い
つつ所期の効果を達成するため、６重量％以下に制限さ
れる。他方、カルシウムはマグネシウムへのアルミニウ
ムの添加に伴い、低下する傾向にある高温強度を増強す
るために添加されるが、成形性と成形部材の伸びを低下
しないようにＣａ／Ａｌ比を０．８以下に押さえる必要
があり、しかも０．５〜４重量％に制限される。Therefore, the present invention is based on the findings of both of the above, 2 to 6% by weight of aluminum and 0.5 to 5 of calcium.
A molded member containing 4% by weight, the balance consisting of magnesium and unavoidable impurities, and molded from a magnesium alloy with a Ca / Al ratio of 0.8 or less, while ensuring creep resistance, moldability and elongation. It is to provide a magnesium alloy molded part having excellent properties. In general, it is said that it is preferable to add 2 to 10% by weight of aluminum in a magnesium alloy in order to form a solid solution in magnesium, exhibit age hardening, and enhance the mechanical properties of the alloy. In contrast,
In the present invention, it is necessary to add aluminum in an amount of 2% by weight or more, but if it exceeds 6% by weight, the elongation will decrease even if semi-molten injection molding is performed. Therefore, in order to achieve the desired effect while performing the semi-melt injection molding, the content is limited to 6% by weight or less. On the other hand, calcium is added to increase the high temperature strength, which tends to decrease with the addition of aluminum to magnesium, but the Ca / Al ratio is set to 0.8 so as not to reduce the formability and the elongation of the molded member. It should be kept below, and is limited to 0.5-4% by weight.

【０００９】ストロンチウムはマグネシウムの鋳造にお
いて微細化剤として使用されるが、本発明に係る半溶融
射出成形法においても固相の微細化効果を発揮すること
ができるので、添加するのが好ましい。添加量は０．１
５重量％以下が適当である。Although strontium is used as a refining agent in magnesium casting, it is preferably added because it can exert the effect of refining the solid phase in the semi-melt injection molding method according to the present invention. Addition amount is 0.1
5% by weight or less is suitable.

【００１０】上記成形部品は結晶粒径が３０μm以下で
引張強度１８０ＭＰａ（２９８°Ｋ：図９参照）以上に
あり、しかも試験温度１５０℃、試験荷重５０ＭＰａで
の最小クリープ速度４×１０-10／Ｓ以下である優れた
耐クリープ性を示す（ＪＩＳＺ ２２７１「金属材料の
引張クリープ試験方法」による）。したがって、自動車
用トランスミッション部品またはエンジン部品に適す
る。特に、Ｃａ／Ａｌ比が０．６以下である場合は耐ク
リープ性に優れる。The above-mentioned molded part has a crystal grain size of 30 μm or less and a tensile strength of 180 MPa (298 ° K: see FIG. 9) or more, and a minimum creep rate of 4 × 10 -10 / at a test temperature of 150 ° C. and a test load of 50 MPa. It shows an excellent creep resistance of S or less (according to JIS Z 2271 “Tensile creep test method for metallic materials”). Therefore, it is suitable for automobile transmission parts or engine parts. Particularly, when the Ca / Al ratio is 0.6 or less, the creep resistance is excellent.

【００１１】また、本発明では、上記マグネシウム合金
成形部品の成形に用いる合金素材として、アルミニウム
２〜６重量％及びカルシウム０．５〜４重量％を含有
し、残部がマグネシウムと不可避の不純物、好ましくは
更に０．１５重量％以下のＳｒを含有してなり、要すれ
ば、Ｃａ／Ａｌ比が０．８以下、好ましくはＣａ／Ａｌ
比が０．６以下に調整された、半溶融射出成形によって
優れた耐クリープ性を確保しつつ、成形性、伸び性に優
れる耐熱マグネシウム合金を提供しようとするものでも
ある。In the present invention, the alloy material used for forming the magnesium alloy molded part contains 2 to 6% by weight of aluminum and 0.5 to 4% by weight of calcium, and the balance is magnesium and inevitable impurities, preferably Further contains 0.15 wt% or less of Sr, and if necessary, the Ca / Al ratio is 0.8 or less, preferably Ca / Al.
It is also an object of the present invention to provide a heat-resistant magnesium alloy excellent in moldability and elongation while ensuring excellent creep resistance by semi-melt injection molding with the ratio adjusted to 0.6 or less.

【００１２】特に、合金素材としては、半溶融射出成形
法で成形する場合、内部歪みを導入した金属粒またはペ
レット形態であるのが結晶微細化に有効であることが見
い出されている（図１０参照）。その加工法としては切
削加工がコスト的に有利である。In particular, it has been found that, as the alloy material, in the case of molding by a semi-melt injection molding method, it is effective for crystal refining that it is in the form of metal particles or pellets with internal strain introduced (FIG. 10). reference). As the processing method, cutting is cost effective.

【００１３】さらに、ダイキャスト法に代え、固相と液
相が混在した状態で射出成形を行う半溶融射出成形法を
適用とする場合、ダイキャスト法より低温の液相線以下
の温度で実施することができる。したがって、本発明は
上記記載のマグネシウム合金を液相線温度以下の固相と
液相の混在する状態で半溶融成形することを特徴とする
耐クリープ性を確保しつつ、成形性、伸び性に優れる耐
熱マグネシウム合金部材の成形方法を提供するものでも
ある。Further, when the semi-melt injection molding method in which the solid phase and the liquid phase are mixed is applied instead of the die casting method, the semi-molten injection molding method is applied at a temperature below the liquidus line which is lower than that of the die casting method. can do. Therefore, the present invention, while ensuring the creep resistance, characterized in that the magnesium alloy described above is subjected to semi-melt forming in a state where the solid phase and the liquid phase below the liquidus temperature coexist, in the formability and elongation It also provides an excellent method for forming a heat-resistant magnesium alloy member.

【００１４】ダイキャストは一般的に溶融温度上３０〜
５０℃の溶湯温度で金型中に射出するのに対し、本発明
の半溶融射出成形では液相線以下の温度で射出するた
め、少なくとも射出温度は３０〜６０℃以上低下するこ
とになる。したがって、金型への焼き付きを防止できる
ことになる。Die casting generally has a melting temperature of 30-
Injecting into the mold at a molten metal temperature of 50 ° C., the semi-molten injection molding of the present invention injects at a temperature below the liquidus line, so the injection temperature is lowered by at least 30 to 60 ° C. or more. Therefore, it is possible to prevent the seizure on the mold.

【００１５】そもそも半溶融からの凝固であるので凝固
応力が小さくなることからこの方法を使用することによ
り熱間割れの発生を抑制することができると思われる。Since solidification begins with semi-melting, the solidification stress is small. Therefore, it is thought that the occurrence of hot cracking can be suppressed by using this method.

【００１６】特に、これらの防止および効果は半溶融成
形法において固相率３０％以下において流動長に及ぼす
影響が顕著となり（図８参照）、熱間割れの発生を抑制
に効果的である。したがって、この半溶融成形を行う
際、半溶融状態時の固相率が３０％以下であるのが好ま
しい。一般に固相率が高いほど焼付きも凝固応力も有利
と思われるが、本発明方法では固相率が高いと流動性が
低下するため、充填性の低下や湯境いの発生が起こり易
く、健全な成形部材を得ることが困難となる。In particular, these preventions and effects have a remarkable effect on the flow length when the solid fraction is 30% or less in the semi-melt forming method (see FIG. 8), and are effective in suppressing the occurrence of hot cracking. Therefore, when performing this semi-melt molding, it is preferable that the solid phase ratio in the semi-molten state is 30% or less. Generally, the higher the solid fraction, the more likely the seizure and the solidification stress are, but in the method of the present invention, when the solid fraction is high, the fluidity is lowered, so that the filling property is lowered and the molten metal is likely to occur. It becomes difficult to obtain a sound molded member.

【００１７】特にこれらの凝固組織の平均粒径が３０μ
ｍ以下の時、特に伸び値が大きく向上することが見い出
された。Particularly, the average particle size of these solidified structures is 30 μm.
It has been found that the elongation value is greatly improved especially when m or less.

【００１８】上記マグネシウム合金が更に亜鉛、マンガ
ン、ジルコニウム、及びケイ素からなる群から選ばれた
少なくとも１種の元素を２重量％以下、及び／又は希士
類元素（例えば、イットリウム、ネオジウム、ランタ
ン、セリウム、ミッシュメタル）４重量％以下を含有し
てもよい。これらはその上限以下で上記マグネシウム合
金の強度または高温強度を有効に向上させるものであ
る。The magnesium alloy further contains 2% by weight or less of at least one element selected from the group consisting of zinc, manganese, zirconium, and silicon, and / or rare earth elements (eg, yttrium, neodymium, lanthanum, Cerium, misch metal) 4 wt% or less may be contained. Below these upper limits, the strength or high temperature strength of the magnesium alloy is effectively improved.

【００１９】[0019]

【発明の実施の形態】図１に本発明に係る半溶融成形法
に用いられる成形機１の全体構成を示す。本発明の成形
方法では、図中のホッパー８に機械の切削等の方法で作
製されたマグネシウム合金金属粒またはペレット（径３
ｍｍ以上）の原料３を投入する。原料３はホッパー８か
らアルゴン雰囲気の通入口７を通ってシリンダ４内に供
給される。このシリンダ４内ではスクリュー２によって
原料３は前方に送られながら、加熱される。この加熱ゾ
ーンを１０で示す。加熱温度が略液相線ではマグネシウ
ム合金原料３は溶融状態となるが、液相線以下の温度で
は図示したように固相と液相が混在した半溶融状態とな
る。また、半溶融状態にあるマグネシウム合金はスクリ
ューの回転撹拌により、図示のようにその剪断力が固相
を細かく分断する。ここで、後方の高速射出機構５でス
クリュー２を前方に押し出すと、半溶融状態で細かく固
相が細断された溶湯が図示のようにノズル９より高速射
出され、金型６内に充填されることになる。ここで、凝
固まで金型内を加圧保持し、凝固後型を開き成形製品を
取り出す。FIG. 1 shows the overall structure of a molding machine 1 used in the semi-melt molding method according to the present invention. In the molding method of the present invention, magnesium alloy metal particles or pellets (diameter 3
(mm or more) raw material 3 is charged. The raw material 3 is supplied into the cylinder 4 from the hopper 8 through the argon atmosphere passage 7. In the cylinder 4, the raw material 3 is heated while being fed forward by the screw 2. This heating zone is shown at 10. When the heating temperature is substantially the liquidus, the magnesium alloy raw material 3 is in a molten state, but at a temperature below the liquidus, it is in a semi-molten state in which a solid phase and a liquid phase are mixed as illustrated. In addition, as shown in the figure, the shearing force of the magnesium alloy in the semi-molten state causes the solid phase to be finely divided by the rotational stirring of the screw. Here, when the screw 2 is pushed forward by the high-speed injection mechanism 5 on the rear side, the melt in which the solid phase is finely cut in the semi-molten state is high-speed injected from the nozzle 9 as shown in the figure, and is filled in the mold 6. Will be. Here, the inside of the mold is pressurized and held until the solidification, and after the solidification, the mold is opened and the molded product is taken out.

【００２０】実施例１〜７及び比較例１〜５ 低周波炉に鉄ルツボを設置し、ＳＦ6ガス１％（残はド
ライエア）を溶湯表面に流動させながら実施例および比
較例の成分の合金を溶製した。これらの合金を板上に鋳
造し、フライス加工にて３〜５ｍｍ径のペレットを製造
し、これらを原料として上記成形機を用いて、半溶融成
形を行った。Examples 1 to 7 and Comparative Examples 1 to 5 An iron crucible was placed in a low-frequency furnace, and an alloy of the components of the Examples and Comparative Examples was prepared while flowing SF 6 gas 1% (the rest was dry air) on the surface of the molten metal. Was melted. These alloys were cast on a plate, milled to produce pellets having a diameter of 3 to 5 mm, and these were used as raw materials for semi-melt molding using the above-mentioned molding machine.

【００２１】[0021]

【表１】 [Table 1]

【００２２】半溶融成形は型締め力４５０ｔのマシンを
用い、その条件は共に射出速度は金型ゲート部において
５０ｍ／ｓ、射出圧力約７００ｋｇ／ｃｍ2であり、ノ
ズル部の合金の温度を液相線以下の温度５５０〜５８０
℃に設定した。以上の成形条件にて、引張試験片（ＪＩ
Ｓ４号試験片）を作成し、ＪＩＳ Ｚ ２２７１に基づ
く引張クリープ試験方法により１５０℃、５０ＭＰａで
のクリープ特性を検討した。結果を図２に示す。本発明
に係るマグネシウム合金は比較例３のＡＺ９１Ｄより耐
クリープ性に優れるとされたＡＳ４１より耐クリープ特
性に優れることが分かる。The semi-melt molding uses a machine having a mold clamping force of 450 t under the conditions that the injection speed is 50 m / s at the mold gate and the injection pressure is about 700 kg / cm 2 , and the temperature of the alloy at the nozzle is liquid. Temperatures below the phase line 550-580
Set to ° C. Under the above molding conditions, tensile test pieces (JI
No. S4 test piece) was prepared and the creep characteristics at 150 ° C. and 50 MPa were examined by the tensile creep test method based on JIS Z 2271. The results are shown in FIG. It can be seen that the magnesium alloy according to the present invention is superior in creep resistance to AS41 which is said to be superior in creep resistance to AZ91D of Comparative Example 3.

【００２３】また、インストロン引張試験機によりクロ
スヘッド速度１０ｍｍ／分、測定温度２５℃で破断強度
と破断伸びを測定した。結果を表２に示す。アルミニウ
ムが本発明の範囲２〜６重量を越える比較例２、アルミ
ニウム及びカルシウムは本発明の範囲にあるが、Ｃａ／
Ａｌ比が０．８を越える比較例４に対し、アルミニウム
２〜６重量％、カルシウム０．５〜４重量％を含有し、
Ｃａ／Ａｌ比が０．８以下の実施例は優れた伸びを示す
ことが分かる。Further, breaking strength and breaking elongation were measured by an Instron tensile tester at a crosshead speed of 10 mm / min and a measuring temperature of 25 ° C. Table 2 shows the results. Comparative Example 2 in which aluminum exceeds the range of 2 to 6 weight of the present invention, aluminum and calcium are within the range of the present invention, but Ca /
2 to 6% by weight of aluminum and 0.5 to 4% by weight of calcium are included in Comparative Example 4 in which the Al ratio exceeds 0.8,
It can be seen that the examples in which the Ca / Al ratio is 0.8 or less show excellent elongation.

【００２４】[0024]

【表２】 [Table 2]

【００２５】そこで、実施例と比較例において、Ｃａ／
Ａｌ比率と上記伸びとの関係を図３に図示した。これか
らＣａ／Ａｌ比が０．８を越えると伸びが急激に低下す
ることが分かる。そこで、Ｃａ／Ａｌ比と最小クリープ
歪速度との関係をみると、図６に示すように、Ｃａ／Ａ
ｌ比が０．６以下の場合（実施例２）にはより小さなク
リープ歪速度となり、更に耐クリープ特性に優れること
が分かる。Therefore, in the examples and comparative examples, Ca /
The relationship between the Al ratio and the elongation is shown in FIG. From this, it can be seen that the elongation sharply decreases when the Ca / Al ratio exceeds 0.8. Therefore, looking at the relationship between the Ca / Al ratio and the minimum creep strain rate, as shown in FIG.
It can be seen that when the l ratio is 0.6 or less (Example 2), the creep strain rate becomes smaller and the creep resistance is further excellent.

【００２６】また、図４に示す試験用金型を用い、図示
の湯流れを確保して半溶融成形を行うと、表３に示す結
果が得られた。これよりＣａ／Ａｌ比率が１に近づくと
鋳造割れが円筒部上端オーバーフロー側に生ずるが、Ｃ
ａ／Ａｌが０．８以下ではこのような鋳造割れは一切発
生しなかった。When the test mold shown in FIG. 4 was used and semi-melt molding was performed while securing the flow of molten metal shown in the figure, the results shown in Table 3 were obtained. As a result, when the Ca / Al ratio approaches 1, casting cracks occur on the upper end overflow side of the cylinder, but C
When a / Al was 0.8 or less, such casting crack did not occur at all.

【００２７】[0027]

【表３】 [Table 3]

【００２８】一般に鋳造時の滞留時間が長くなると、固
相径が急激に増大する（図５の実施例２）が、ストロン
チウムを添加しておくと、結晶微細化効果が働き、滞留
時間による固相径の増大を抑制することができることが
分かる。Generally, when the residence time during casting becomes long, the solid phase diameter rapidly increases (Example 2 in FIG. 5). However, when strontium is added, the crystal refining effect is exerted and the solidification due to the residence time is increased. It can be seen that the increase in phase diameter can be suppressed.

【００２９】実施例２の合金素材を用い、図７に示す湯
流れ性評価用金型に半溶融成形温度を変化させて溶湯中
の固相率を変化させ、図示の方向に溶湯を侵入させ、そ
の湯流れ性を評価した。結果を図８に示す。この結果よ
り固相率３０％を越えると流動長が急激に降下する。こ
の湯流れは成形部材の組織結晶粒径に影響を与えるの
で、半溶融成形法では固相率３０％以下の状態で成形す
るのが好ましいことが分かる。Using the alloy material of Example 2, the mold for melt flowability evaluation shown in FIG. 7 was changed to change the semi-melt forming temperature to change the solid phase ratio in the melt, and the melt was allowed to enter in the direction shown in the drawing. , Its hot water flowability was evaluated. The results are shown in Fig. 8. As a result, when the solid fraction exceeds 30%, the flow length drops sharply. Since this molten metal flow has an effect on the texture crystal grain size of the molded member, it is understood that it is preferable to mold in the state of the solid fraction of 30% or less in the semi-melt molding method.

【００３０】半溶融成形ではマグネシウム合金素材を金
属粒またはペレットの形態にして使用するが、この金属
粒は内部に切削加工などで加工歪を与えておくと、加熱
後しばらくした後再結晶粒の核を生成し、固相径を増大
していくので、加工歪のない金属粒を用いる場合と加工
歪を有する金属粒を比較すると、図１０に示すように固
相の成長速度が異なり、成形部材の結晶粒径の微細化に
は後者のほうが優れていることが理解できる。In the semi-melt forming, the magnesium alloy material is used in the form of metal particles or pellets. If the metal particles are subjected to processing strain by cutting or the like, they will be recrystallized after a while after heating. Since the nuclei are generated and the diameter of the solid phase is increased, when the metal particles having no processing strain are compared with the metal particles having the processing strain, the growth rate of the solid phase is different as shown in FIG. It can be understood that the latter is superior in reducing the crystal grain size of the member.

【００３１】[0031]

【発明の効果】以上の説明で明らかなように、本発明に
よれば、Ｍｇ−Ａｌ−Ｃａ系耐熱マグネシウム合金部材
においてＣａ／Ａｌ比を制御して高温における耐クリー
プ特性に優れる成形部材を得ることができるので、クラ
ッチピストンおよびクラッチドラムなどの自動車用トラ
ンスミッション部品およびロッカーアームなどのエンジ
ン部品を軽量マグネシウム合金で製造して十分な耐久性
を持たせることができる。また、本発明では、液相線以
下の温度で半溶融成形することにより、従来ダイキャス
ト法で熱間割れや金型への焼付きの課題を解決しつつ、
従来法と同等またはそれ以上の常温および高温強度並び
に伸びを保持することができる。As is apparent from the above description, according to the present invention, a Mg-Al-Ca heat-resistant magnesium alloy member having a Ca / Al ratio controlled to obtain a molded member excellent in creep resistance at high temperatures. Therefore, it is possible to manufacture automobile transmission parts such as clutch pistons and clutch drums and engine parts such as rocker arms from a lightweight magnesium alloy so as to have sufficient durability. Further, in the present invention, by semi-melt molding at a temperature below the liquidus, while solving the problems of hot cracking and seizure to the mold by the conventional die casting method,
It is possible to maintain ordinary temperature and high temperature strength and elongation equal to or higher than those of conventional methods.

【図面の簡単な説明】[Brief description of drawings]

【図１】本発明に係る半溶融成形法及び射出成形法に用
いられる成形機の構成を示す概要図。FIG. 1 is a schematic diagram showing a configuration of a molding machine used in a semi-melt molding method and an injection molding method according to the present invention.

【図２】 各種マグネシウム合金成形部材のクリープ特
性を比較するためのグラフである。FIG. 2 is a graph for comparing creep characteristics of various magnesium alloy molded members.

【図３】 各種マグネシウム合金成形部材のＣａ／Ａｌ
比と室温伸びの関係を示すグラフである。FIG. 3 Ca / Al of various magnesium alloy molded members
It is a graph which shows the relationship between a ratio and room temperature elongation.

【図４】 鋳造割れ試験用金型を示す概略図である。FIG. 4 is a schematic view showing a mold for casting crack test.

【図５】 固相径と滞留時間との関係を示すグラフであ
る。FIG. 5 is a graph showing the relationship between solid phase diameter and residence time.

【図６】 各種マグネシウム合金成形部材の最小クリー
プ歪速度を示すグラフである。FIG. 6 is a graph showing the minimum creep strain rate of various magnesium alloy molded members.

【図７】 各種マグネシウム合金の湯流れ性評価用金型
を示す概要図である。FIG. 7 is a schematic view showing a mold for evaluating melt flowability of various magnesium alloys.

【図８】 図７の金型を使用して測定した実施例２の合
金組成における固相率と流動長との関係を示すグラフで
ある。8 is a graph showing the relationship between the solid fraction and the flow length in the alloy composition of Example 2 measured using the mold of FIG.

【図９】 実施例３の合金組成から成形された部材の平
均結晶粒径と引張強度との関係を示すグラフである。9 is a graph showing the relationship between the average crystal grain size and the tensile strength of a member molded from the alloy composition of Example 3. FIG.

【図１０】 加工歪のない金属粒と加工歪のある金属粒
を使用した場合の固相成長段階を示す模式図である。FIG. 10 is a schematic diagram showing a solid phase growth stage in the case of using metal grains without work strain and metal grains with work strain.

【符号の説明】[Explanation of symbols]

１…射出成形機 ２…スクリュー ３…原料ペレット ４…シリンダー ５…高速射出機構 ６…金型 ７…シリンダーへの材料通入路 ８…ホッパ ９…ノズル ｌ０…加熱ゾーン 1 ... Injection molding machine 2 ... Screw 3 ... Raw material pellet 4 ... Cylinder 5 ... High-speed injection mechanism 6 ... Mold 7 ... Material passage to cylinder 8 ... Hopper 9 ... Nozzle 10 ... Heating zone

───────────────────────────────────────────────────── フロントページの続き (72)発明者 平原 庄司 広島県安芸郡府中町新地３番１号 マツダ 株式会社内 ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Shoji Hirahara 3-1, Shinchi, Fuchu-cho, Aki-gun, Hiroshima Mazda Motor Corporation

Claims (12)

【特許請求の範囲】[Claims] 【請求項１】 アルミニウム２〜６重量％及びカルシウ
ム０．５〜４重量％を含有し、残部がマグネシウムと不
可避の不純物からなり、Ｃａ／Ａｌ比が０．８以下のマ
グネシウム合金から成形された成形部材であり、耐クリ
ープ性に優れる耐熱マグネシウム合金成形部材。1. A magnesium alloy containing 2 to 6% by weight of aluminum and 0.5 to 4% by weight of calcium, the balance being magnesium and unavoidable impurities and having a Ca / Al ratio of 0.8 or less. A heat-resistant magnesium alloy molded member that is a molded member and has excellent creep resistance. 【請求項２】 Ｃａ／Ａｌ比が０．６以下で、試験温度
１５０℃、試験荷重５０ＭＰａでの最小クリープ速度４
×１０-10／Ｓ以下の耐クリープ性を有する請求項１記
載の耐熱マグネシウム合金成形部材。2. A minimum creep rate of 4 at a test temperature of 150 ° C. and a test load of 50 MPa when the Ca / Al ratio is 0.6 or less.
The heat-resistant magnesium alloy molded member according to claim 1, which has a creep resistance of not more than × 10 -10 / S. 【請求項３】 マグネシウム合金が更に０．１５重量％
以下のＳｒを含有する請求項１または２に記載の耐熱マ
グネシウム合金成形部材。3. The magnesium alloy further comprises 0.15% by weight.
The heat-resistant magnesium alloy molded member according to claim 1, which contains the following Sr. 【請求項４】 平均結晶粒径が３０μm以下である請求
項１ないし３のいずれかに記載の耐熱マグネシウム合金
成形部材。4. The heat-resistant magnesium alloy molded member according to claim 1, having an average crystal grain size of 30 μm or less. 【請求項５】 成形部品が自動車用トランスミッション
部品またはエンジン部品である請求項１ないし４のいず
れかに記載の耐熱マグネシウム合金成形部材。5. The heat-resistant magnesium alloy molded member according to claim 1, wherein the molded component is an automobile transmission component or an engine component. 【請求項６】 アルミニウム２〜６重量％及びカルシウ
ム０．５〜４重量％を含有し、残部がマグネシウムと不
可避の不純物からなり、固相と液相が混在する液相線以
下の温度での半溶融射出成形によって優れた耐クリープ
性が得られる耐熱マグネシウム合金。6. An aluminum alloy containing 2 to 6% by weight of aluminum and 0.5 to 4% by weight of calcium, the balance being magnesium and unavoidable impurities, and having a solid phase and a liquid phase at a temperature below a liquidus line. A heat-resistant magnesium alloy with excellent creep resistance obtained by semi-melt injection molding. 【請求項７】 マグネシウム合金が更に０．１５重量％
以下のＳｒを含有する請求項６に記載の耐熱マグネシウ
ム合金。7. The magnesium alloy further comprises 0.15% by weight.
The heat-resistant magnesium alloy according to claim 6, containing the following Sr. 【請求項８】 Ｃａ／Ａｌ比が０．８以下である請求項
６または７に記載の耐熱マグネシウム合金。8. The heat-resistant magnesium alloy according to claim 6, which has a Ca / Al ratio of 0.8 or less. 【請求項９】 Ｃａ／Ａｌ比が０．６以下である請求
項８に記載の耐熱マグネシウム合金。9. The heat-resistant magnesium alloy according to claim 8, wherein the Ca / Al ratio is 0.6 or less. 【請求項１０】 内部歪みを導入した金属粒またはペレ
ット形態である請求項６ないし９のいずれかに記載の耐
熱マグネシウム合金。10. The heat-resistant magnesium alloy according to claim 6, which is in the form of metal particles or pellets introduced with internal strain. 【請求項１１】 請求項６ないし１０のいずれかに記載
のマグネシウム合金を固相と液相の混在する液相線温度
以下で半溶融射出成形することを特徴とする耐クリープ
性に優れる耐熱マグネシウム合金成形部材の成形方法。11. A heat-resistant magnesium having excellent creep resistance, characterized in that the magnesium alloy according to any one of claims 6 to 10 is subjected to semi-melt injection molding at a liquidus temperature below a temperature where a solid phase and a liquid phase coexist. A method for forming an alloy formed member. 【請求項１２】 半溶融射出成形を行う際、半溶融状態
時の固相率が３０％以下である請求項１１記載の耐熱マ
グネシウム合金部材の成形方法。12. The method for molding a heat-resistant magnesium alloy member according to claim 11, wherein the solid fraction in the semi-molten state is 30% or less when performing the semi-melt injection molding.
JP08283296A 1996-04-04 1996-04-04 Molding method of heat-resistant magnesium alloy molded member Expired - Fee Related JP3415987B2 (en)

Priority Applications (6)

Application Number Priority Date Filing Date Title
JP08283296A JP3415987B2 (en) 1996-04-04 1996-04-04 Molding method of heat-resistant magnesium alloy molded member
CN971050007A CN1065003C (en) 1996-04-04 1997-04-04 Heat-resisting magensium alloy forming member, heat-resisting magnesium alloy for forming and forming method thereof
DE69706737T DE69706737T2 (en) 1996-04-04 1997-04-04 Heat-resistant magnesium alloy
EP97105641A EP0799901B1 (en) 1996-04-04 1997-04-04 Heat-resistant magnesium alloy member
KR1019970012613A KR970070224A (en) 1996-04-04 1997-04-04 Heat-resistant magnesium alloy molding member, heat-resistant magnesium alloy and its molding method used for molding
US09/949,621 US20020020475A1 (en) 1996-04-04 2001-09-12 Heat-resistant magnesium alloy member

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
JP08283296A JP3415987B2 (en) 1996-04-04 1996-04-04 Molding method of heat-resistant magnesium alloy molded member

Publications (2)

Publication Number Publication Date
JPH09272945A true JPH09272945A (en) 1997-10-21
JP3415987B2 JP3415987B2 (en) 2003-06-09

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US (1) US20020020475A1 (en)
EP (1) EP0799901B1 (en)
JP (1) JP3415987B2 (en)
KR (1) KR970070224A (en)
CN (1) CN1065003C (en)
DE (1) DE69706737T2 (en)

Cited By (37)

* Cited by examiner, † Cited by third party
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JPH11323474A (en) * 1998-05-13 1999-11-26 Mazda Motor Corp Magnesium alloy casting member
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US20020020475A1 (en) 2002-02-21
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