JP2000104137A - Magnesium alloy forging stock, forged member and production of the forged member - Google Patents
Magnesium alloy forging stock, forged member and production of the forged memberInfo
- Publication number
- JP2000104137A JP2000104137A JP10278507A JP27850798A JP2000104137A JP 2000104137 A JP2000104137 A JP 2000104137A JP 10278507 A JP10278507 A JP 10278507A JP 27850798 A JP27850798 A JP 27850798A JP 2000104137 A JP2000104137 A JP 2000104137A
- Authority
- JP
- Japan
- Prior art keywords
- forging
- forged
- magnesium alloy
- temperature
- weight
- 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.)
- Pending
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/06—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of magnesium or alloys based thereon
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21K—MAKING FORGED OR PRESSED METAL PRODUCTS, e.g. HORSE-SHOES, RIVETS, BOLTS OR WHEELS
- B21K1/00—Making machine elements
- B21K1/20—Making machine elements valve parts
-
- 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
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
- F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
- F01L1/00—Valve-gear or valve arrangements, e.g. lift-valve gear
- F01L1/12—Transmitting gear between valve drive and valve
- F01L1/14—Tappets; Push rods
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
- F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
- F01L3/00—Lift-valve, i.e. cut-off apparatus with closure members having at least a component of their opening and closing motion perpendicular to the closing faces; Parts or accessories thereof
- F01L3/02—Selecting particular materials for valve-members or valve-seats; Valve-members or valve-seats composed of two or more materials
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
- F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
- F01L2303/00—Manufacturing of components used in valve arrangements
Abstract
Description
【０００１】[0001]
【発明の属する技術分野】この発明は、少なくともアル
ミニウムとカルシウムとを含有したマグネシウム合金鍛
造素材及び鍛造部材並びに該鍛造部材の製造方法に関す
る。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a forged magnesium alloy material and a forged member containing at least aluminum and calcium, and a method for manufacturing the forged member.
【０００２】[0002]
【従来の技術】周知のように、マグネシウム（以下、適
宜、その元素記号Ｍｇで表示する。）合金は、現在実用
化されている金属材料の中で最も低密度(軽量)であり、
例えば、より一層の燃費向上が求められている自動車な
どにおいても、更なる軽量化を達成することなどを目的
として、従来用いられていた軽量材料としてのアルミニ
ウム（以下、適宜、その元素記号Ａｌで表示する。）合
金などに替えて、各種部品等の材料としてその採用が拡
大しつつある。2. Description of the Related Art As is well known, a magnesium (hereinafter, appropriately denoted by an element symbol Mg) alloy is the lowest density (light weight) among metal materials currently put into practical use.
For example, even in automobiles and the like that are required to further improve fuel efficiency, for the purpose of achieving further weight reduction, aluminum as a conventionally used lightweight material (hereinafter referred to as the element symbol Al as appropriate) Indicated.) Instead of alloys, their use is expanding as a material for various parts.
【０００３】上記Ｍｇ合金は、鍛造を含む塑性加工ある
いは鋳造や射出成形を含む成形などにより加工が可能
で、例えば、本願出願人は、特許第２６７６４６６号
（以下、これを従来技術１と称する。）において、６重
量％〜１２重量％のＡｌを含有したＭｇ合金からなる鋳
造部材を鍛造し、その鍛造後に所謂Ｔ６熱処理（溶体化
処理後に人工時効処理を行う熱処理）を施すようにした
Ｍｇ合金製部材を提案した。The above-mentioned Mg alloy can be processed by plastic working including forging or molding including casting or injection molding. For example, the applicant of the present application discloses Japanese Patent No. 2676466 (hereinafter referred to as prior art 1). )), A forged cast member made of an Mg alloy containing 6 to 12% by weight of Al, and a so-called T6 heat treatment (a heat treatment for performing an artificial aging treatment after a solution treatment) after the forging. Proposed components were proposed.
【０００４】また、本願出願人は、特開平９−２７２９
４５号公報（以下、これを従来技術２と称する。）にお
いて、耐クリープ特性を確保しつつ優れた成形性や延び
率を得ることなどを目的として、２重量％〜６重量％の
Ａｌおよび０.５重量％〜４重量％のカルシウム（以
下、適宜、その元素記号Ｃａで表示する。）を含有し、
かつ、Ｃａ／Ａｌ比が０.８以下のＭｇ合金を、半溶融
状態で射出成形するようにした耐熱Ｍｇ合金部材を開示
した。[0004] The applicant of the present invention has disclosed Japanese Patent Application Laid-Open No. 9-2729.
No. 45 (hereinafter referred to as Conventional Technique 2) discloses that 2% to 6% by weight of Al and 0% is used for the purpose of obtaining excellent moldability and elongation while ensuring creep resistance. 0.5% to 4% by weight of calcium (hereinafter, appropriately represented by the element symbol Ca),
Also disclosed is a heat-resistant Mg alloy member in which a Mg alloy having a Ca / Al ratio of 0.8 or less is injection-molded in a semi-molten state.
【０００５】更に、特開平９−２６３８７１号公報（以
下、これを従来技術３と称する。）では、高温と室温の
両方について強度の信頼性が求められる自動車用エンジ
ン部品として適用し得る室温強度および高温強度に優れ
たＭｇ合金製部品を得ることなどを目的として、希土類
−Ｃａ又はＹ系のＭｇ合金を熱間鍛造するようにした高
強度Ｍｇ合金製の熱間鍛造品が開示されている。Further, Japanese Patent Application Laid-Open No. Hei 9-263871 (hereinafter referred to as "prior art 3") discloses a room-temperature strength and a room-temperature strength which can be applied as an automobile engine component requiring strength reliability at both high temperature and room temperature. A hot-forged product made of a high-strength Mg alloy in which a rare-earth-Ca or Y-based Mg alloy is hot-forged for the purpose of obtaining a component made of an Mg alloy having excellent high-temperature strength is disclosed.
【０００６】上記Ｍｇ合金は、例えば自動車においても
ホイールなどの材料として既に実用に供されているので
あるが、このＭｇ合金を、温度的あるいは強度的により
使用条件が厳しい例えば内燃機関（エンジン）周りの機
構部品（例えばエンジン吸排気バルブのバルブリフタ
等）などの材料として適用することを考えた場合、常温
での強度特性はもとより、例えば、１５０℃程度の高温
においても一定以上（例えば２２０ＭＰａ以上）の高い
引張強度や優れた耐クリープ特性が求められる。更に、
上記バルブリフタの場合、シリンダヘッドの孔部壁面お
よびカムと摺接する（若しくはカムと摺接する調整シム
と接する）冠面部には高い耐磨耗特性が要求される。The above Mg alloy has already been put into practical use as a material for wheels and the like in automobiles, for example. When it is considered to be applied as a material for a mechanical part (e.g., a valve lifter of an engine intake / exhaust valve) or the like, not only the strength characteristics at room temperature but also a certain level (e.g., 220 MPa or higher) even at a high temperature of about 150 ° C. High tensile strength and excellent creep resistance are required. Furthermore,
In the case of the valve lifter, high wear resistance is required for the wall surface of the hole of the cylinder head and the crown surface that comes into sliding contact with the cam (or comes into contact with the adjusting shim that comes into sliding contact with the cam).
【０００７】上記のようなある程度の高温（例えば１５
０℃程度）で一定以上（例えば２２０ＭＰａ以上）の高
い引張強度や優れた耐クリープ特性などの機械的特性を
確保することが求められる場合、鋳造や射出成形などの
成形加工では所要の特性を安定して得ることは一般に難
しく、加工時に緻密な材料組織が得られる塑性加工、特
に、一定以上の鍛造率で鍛造することが最も好ましい。
従って、Ｍｇ合金としては、上記のような機械的特性を
得る上で、良好な鍛造成を確保する必要がある。[0007] A certain high temperature (for example, 15
When it is required to secure mechanical properties such as high tensile strength of not less than a certain level (for example, 220 MPa or more) at a temperature of about 0 ° C. and excellent creep resistance, required properties are stabilized in molding processes such as casting and injection molding. In general, it is difficult to obtain such a material, and it is most preferable to perform forging at a forging ratio of a certain value or more, in particular, for plastic working capable of obtaining a dense material structure during working.
Therefore, it is necessary for the Mg alloy to ensure good forging in order to obtain the above mechanical properties.
【０００８】[0008]
【発明が解決しようとする課題】しかしながら、上記従
来技術１の場合には、鍛造性は確保できるものの、Ａｌ
含有量が多いので耐クリープ特性が低く、高温での使用
に適するものではない。ＡｌとＭｇとは耐クリープ特性
等の高温特性に悪影響を及ぼす化合物を形成し易いこと
が知られており、Ａｌ含有量が一定以上多いと、高温域
でこの有害な化合物が多数析出して耐クリープ特性を確
保できなくなるからである。また、従来技術２の場合に
は、あくまでも射出成形品であるので、鍛造品のような
高い機械的特性、特に高温での安定した強度を確保する
ことが難しく、適用可能な対象範囲は、鍛造品に比べて
かなり限られたものと成らざるを得ない。更に、従来技
術３の場合には、高価な希土類元素を含有するものであ
るので、非常にコスト高となり、実用性に欠けるという
難点があった。However, in the case of the above-mentioned prior art 1, although forgeability can be ensured, Al
Due to its high content, it has low creep resistance and is not suitable for use at high temperatures. It is known that Al and Mg are apt to form compounds that adversely affect high-temperature properties such as creep resistance. If the Al content is higher than a certain level, many of these harmful compounds are precipitated at high temperatures to prevent This is because the creep characteristics cannot be secured. Further, in the case of the prior art 2, since it is an injection-molded product, it is difficult to ensure high mechanical properties such as a forged product, particularly, stable strength at a high temperature. It must be quite limited compared to the product. Furthermore, in the case of the prior art 3, since it contains an expensive rare earth element, there is a problem that the cost is extremely high and the practicability is lacking.
【０００９】この発明は、上記諸問題に鑑みてなされた
もので、常温および高温での機械的特性に優れ、また、
鍛造性に優れ、かつ比較的低廉な、マグネシウム合金鍛
造素材及び鍛造部材並びに該鍛造部材の製造方法を提供
することを目的とする。The present invention has been made in view of the above-mentioned problems, and has excellent mechanical properties at ordinary and high temperatures.
It is an object of the present invention to provide a magnesium alloy forging material and a forged member which are excellent in forgeability and are relatively inexpensive, and a method for manufacturing the forged member.
【００１０】[0010]
【課題を解決するための手段】本願発明者らは、上記の
技術的課題に鑑みて鋭意研究を重ねた結果、少なくとも
Ａｌ及びＣａを含有したＭｇ合金製の鍛造素材におい
て、Ｃａ量が一定以下（４重量％以下）の範囲において
はこのＣａ含有量が高いほど耐クリープ特性が向上する
こと、及びＡｌ量が一定以下（６重量％以下）の範囲で
は耐クリープ特性が良好に維持されること、また、Ａｌ
量が一定以上（２重量％以上）の範囲では高温(１５０
℃)で高い引張強度(２２０ＭＰａ以上)が確保できるこ
と、更に、Ｃａ／Ａｌ比（Ａｌ含有量（重量）に対する
Ｃａ含有量（重量）の比率）が一定以下(０.８以下)の
範囲では所要の鍛造率を確保した上で高速鍛造における
割れ発生率を極めて低く抑制できること、また更に、鍛
造素材の平均結晶粒径が小さいほど鍛造時に高い限界据
え込み率を確保できることを見出した。Means for Solving the Problems The inventors of the present invention have conducted intensive studies in view of the above technical problems, and as a result, it has been found that, in a forged material made of a Mg alloy containing at least Al and Ca, the amount of Ca is equal to or less than a certain value. In the range of (4% by weight or less), the higher the Ca content, the more the creep resistance is improved. In the range of the Al content below a certain level (6% by weight or less), the creep resistance is preferably maintained. And also Al
If the amount is within a certain range (2% by weight or more), a high temperature (150%
℃), high tensile strength (220 MPa or more) can be ensured, and the Ca / Al ratio (the ratio of the Ca content (weight) to the Al content (weight)) is within a certain range (0.8 or less). It has been found that the cracking rate in high-speed forging can be suppressed to a very low level while the forging rate is assured, and that the smaller the average crystal grain size of the forging material, the higher the limit upsetting rate during forging.
【００１１】そこで、本願の請求項１の発明(以下、第
１の発明という)に係るＭｇ合金鍛造素材は、少なくと
もＡｌとＣａとを含有し、３００℃において７０％以上
の限界据え込み率を有することを特徴としたものであ
る。Therefore, the forged Mg alloy material according to the invention of claim 1 of the present application (hereinafter, referred to as the first invention) contains at least Al and Ca and has a critical upsetting ratio of 70% or more at 300 ° C. It is characterized by having.
【００１２】ここに、限界据え込み率を７０％以上とし
たのは、上記Ｍｇ合金鍛造素材を鍛造して得られる鍛造
部材を、例えばエンジンのバルブリフタなど一定以上の
高い強度を要する部材・部品等に用いる場合には、７０
％以上の限界据え込み率を確保することが好ましいから
である。また、この場合において、鍛造温度が３００℃
であれば、鍛造温度の上昇による鍛造性向上効果が飽和
する温度よりも低く、かつ、高温酸化が問題となる４０
０℃よりも十分に低く、高温での酸化による悪影響も回
避できる。Here, the reason why the limit upsetting ratio is set to 70% or more is that a forged member obtained by forging the above-mentioned Mg alloy forging material is a member / part that requires a certain strength or more such as an engine valve lifter. When used for
This is because it is preferable to secure a critical upsetting ratio of at least%. In this case, the forging temperature is 300 ° C.
If so, the temperature is lower than the temperature at which the effect of improving the forgeability by increasing the forging temperature is saturated, and high-temperature oxidation becomes a problem.
The temperature is sufficiently lower than 0 ° C., and adverse effects due to oxidation at high temperatures can be avoided.
【００１３】また、本願の請求項２の発明(以下、第２
の発明という)に係るＭｇ合金鍛造素材は、２重量％以
上で６重量％以下のＡｌ及び０.５重量％以上で４重量
％以下のＣａを含有し、平均結晶粒径が３００μｍ以下
であることを特徴としたものである。The invention of claim 2 of the present application (hereinafter referred to as the second invention)
The forged Mg alloy material according to the present invention contains Al of 2 wt% or more and 6 wt% or less and Ca of 0.5 wt% or more and 4 wt% or less, and has an average crystal grain size of 300 μm or less. It is characterized by the following.
【００１４】ここに、Ａｌ含有量の下限値を２重量％と
したのは、Ａｌ量がこの値を下回ると高温（１５０℃）
で十分な引張強度（２２０ＭＰａ以上）を確保すること
が難しくなるからであり、また、Ａｌ含有量の上限値を
６重量％としたのは、Ａｌ量がこの値を越えると耐クリ
ープ特性が低下するからである。一方、Ｃａ含有量の下
限値を０.５重量％としたのは、Ｃａ量がこの値を下回
ると耐クリープ特性が低下するからであり、また、Ｃａ
含有量の上限値を４重量％としたのは、Ｃａ量がこの値
を越えて増加しても耐クリープ特性向上の効果が飽和す
るからである。更に、鍛造素材の平均結晶粒径が３００
μｍ以下としたのは、平均結晶粒径がこの値を下回る
と、所要の（５０％以上の）限界据え込み率を確保する
ことが難しくなるからである。The reason why the lower limit of the Al content is set to 2% by weight is that if the Al content falls below this value, the temperature becomes high (150 ° C.).
The reason for this is that it is difficult to ensure sufficient tensile strength (at least 220 MPa) in the case of (1), and the upper limit of the Al content is set to 6% by weight. Because you do. On the other hand, the reason why the lower limit of the Ca content is set to 0.5% by weight is that if the amount of Ca is less than this value, the creep resistance is reduced.
The upper limit of the content is set to 4% by weight, because the effect of improving the creep resistance characteristics is saturated even if the Ca content exceeds this value. Furthermore, the average grain size of the forged material is 300
The reason why the diameter is not more than μm is that if the average crystal grain size is below this value, it becomes difficult to secure a required (50% or more) critical upsetting ratio.
【００１５】更に、本願の請求項３に係る発明(以下、
第３の発明という)は、上記第１または第２の発明にお
いて、Ａｌ含有量に対するＣａ含有量の比率（Ｃａ／Ａ
ｌ比）が０.８以下であることを特徴としたものであ
る。Further, the invention according to claim 3 of the present application (hereinafter referred to as “the invention”)
The third invention) is a method according to the first or second invention, wherein the ratio of the Ca content to the Al content (Ca / A
1 ratio) is 0.8 or less.
【００１６】ここに、上記Ｃａ／Ａｌ比を０.８以下と
したのは、この範囲であれば、所要の鍛造率（５０％）
を確保した上で、高速鍛造においても割れ発生率を極め
て低く抑えることができるからである。Here, the reason why the Ca / Al ratio is set to 0.8 or less is that the required forging ratio (50%) is within this range.
The reason for this is that the cracking rate can be kept extremely low even in high-speed forging after ensuring the above.
【００１７】また、更に、本願の請求項４に係る発明
(以下、第４の発明という)は、上記第１〜第３のいずれ
か一の発明において、鍛造加工に先立って射出成形にて
所定形状に予備成形されていることを特徴としたもので
ある。Further, the invention according to claim 4 of the present application.
(Hereinafter, referred to as a fourth invention) is characterized in that in any one of the first to third inventions, prior to forging, preforming into a predetermined shape by injection molding. .
【００１８】また、更に、本願の請求項５の発明(以
下、第５の発明という)に係るＭｇ合金鍛造部材の製造
方法は、上記第１〜第４の発明のいずれか一に係るＭｇ
合金鍛造素材であって２重量％以上で６重量％以下のＡ
ｌ及び０.５重量％以上で４重量％以下のＣａを含有し
たＭｇ合金鍛造素材を熱間鍛造することを特徴としたも
のである。Further, the method for manufacturing a forged Mg alloy member according to the invention of claim 5 of the present application (hereinafter referred to as a fifth invention) is a method for manufacturing a forged Mg alloy member according to any one of the first to fourth inventions.
A forged alloy material with 2% by weight or more and 6% by weight or less
The present invention is characterized by hot forging a Mg alloy forging material containing 1 and 0.5 wt% or more and 4 wt% or less of Ca.
【００１９】ここに、Ａｌ含有量の下限値を２重量％と
したのは、Ａｌ量がこの値を下回ると高温（１５０℃）
で十分な引張強度（２２０ＭＰａ以上）を確保すること
が難しくなるからであり、また、Ａｌ含有量の上限値を
６重量％としたのは、Ａｌ量がこの値を越えると耐クリ
ープ特性が低下するからである。一方、Ｃａ含有量の下
限値を０.５重量％としたのは、Ｃａ量がこの値を下回
ると耐クリープ特性が低下するからであり、また、Ｃａ
含有量の上限値を４重量％としたのは、Ｃａ量がこの値
を越えて増加しても耐クリープ特性向上の効果が飽和す
るからである。The reason why the lower limit of the Al content is set to 2% by weight is that if the Al content is lower than this value, a high temperature (150 ° C.)
The reason for this is that it is difficult to ensure sufficient tensile strength (at least 220 MPa) in the case of (1), and the upper limit of the Al content is set to 6% by weight. Because you do. On the other hand, the reason why the lower limit of the Ca content is set to 0.5% by weight is that if the amount of Ca is less than this value, the creep resistance is reduced.
The upper limit of the content is set to 4% by weight, because the effect of improving the creep resistance characteristics is saturated even if the Ca content exceeds this value.
【００２０】また、更に、本願の請求項６に係る発明
(以下、第６の発明という)は、上記第５の発明におい
て、上記Ｍｇ合金鍛造素材であってＡｌ含有量に対する
Ｃａ含有量の比率（Ｃａ／Ａｌ比）が０.８以下のもの
を、４００［ｍｍ／秒］以上の鍛造速度で熱間鍛造する
ことを特徴としたものである。Further, the invention according to claim 6 of the present application is further provided.
(Hereinafter referred to as a sixth invention) is the above-mentioned fifth invention, wherein the Mg alloy forging material, wherein the ratio of Ca content to Al content (Ca / Al ratio) is 0.8 or less, Hot forging is performed at a forging speed of 400 [mm / sec] or more.
【００２１】ここに、上記Ｃａ／Ａｌ比を０.８以下と
したのは、この範囲であれば、所要の鍛造率（５０％）
を確保した上で、高速鍛造においても割れ発生率を極め
て低く抑えることができるからである。また、鍛造速度
を４００［ｍｍ／秒］以上としたのは、例えばエンジン
のバルブリフタなどの機構部品等の部品類を製造する際
には、この程度の鍛造速度を確保して生産性を高めるこ
とが求められるからである。The reason why the Ca / Al ratio is set to 0.8 or less is that the required forging ratio (50%) is within this range.
The reason for this is that the cracking rate can be kept extremely low even in high-speed forging after ensuring the above. The reason why the forging speed is set to 400 [mm / sec] or more is to increase productivity by securing such a forging speed when manufacturing components such as mechanical parts such as a valve lifter of an engine. Is required.
【００２２】また、更に、本願の請求項７に係る発明
(以下、第７の発明という)は、上記第５または第６の発
明において、上記熱間鍛造における鍛造温度が２５０℃
〜４００℃の範囲であることを特徴としたものである。Further, the invention according to claim 7 of the present application is further provided.
(Hereinafter, referred to as a seventh invention) according to the fifth or sixth invention, wherein the forging temperature in the hot forging is 250 ° C.
It is characterized by being in the range of -400 ° C.
【００２３】ここに、鍛造温度の下限値を２５０℃とし
たのは、鍛造温度がこの値以上であれば、良好な限界据
え込み率（７０％以上）を確保して、例えばエンジンの
バルブリフタなど一定以上の高い強度を要する部材・部
品等にも適用することが可能だからであり、また、鍛造
温度の上限値を４００℃としたのは、鍛造温度がこの値
を越えると、鍛造温度の上昇による鍛造性向上効果が飽
和し、しかも、酸化し易くなるからである。The reason why the lower limit of the forging temperature is set to 250 ° C. is that if the forging temperature is equal to or higher than this value, a good limit upsetting rate (70% or more) is ensured, for example, a valve lifter of an engine. This is because it can be applied to members and parts that require a certain strength or higher, and the upper limit of the forging temperature is set to 400 ° C. When the forging temperature exceeds this value, the forging temperature rises. This is because the effect of improving the forgeability by saturating becomes saturated, and moreover, it becomes easy to oxidize.
【００２４】また、更に、本願の請求項８に係る発明
(以下、第８の発明という)は、上記第５〜第７の発明の
いずれか一において、上記熱間鍛造に先立って上記鍛造
素材に、３００℃〜５００℃の温度範囲で５時間〜５０
時間保持する熱処理を施すことを特徴としたものであ
る。Further, the invention according to claim 8 of the present application.
(Hereinafter referred to as an eighth invention) according to any one of the fifth to seventh inventions, wherein the forged material is subjected to a temperature range of 300 ° C to 500 ° C for 5 hours to 50 hours prior to the hot forging.
It is characterized by performing a heat treatment for holding for a time.
【００２５】ここに、熱処理温度の下限値を３００℃と
したのは、それ未満では、熱処理による鍛造成形性の向
上効果が小さいからであり、また、熱処理温度の上限値
を５００℃としたのは、それより高くしても鍛造成形性
の向上効果が飽和する上に、酸化や部分的な溶解の起こ
ることが有り、メリットが無いからである。一方、熱処
理温度保持時間の下限値を５時間としたのは、それ未満
では、熱処理による鍛造成形性の向上効果が小さいから
であり、また、熱処理温度保持時間の上限値を５０時間
としたのは、それより長時間熱処理しても鍛造成形性の
向上効果は飽和するからである。The reason why the lower limit of the heat treatment temperature is set to 300 ° C. is that if it is lower than that, the effect of improving the forging formability by heat treatment is small, and the upper limit of the heat treatment temperature is set to 500 ° C. This is because, even if it is higher than that, the effect of improving the forgeability is saturated, and in addition, oxidation or partial dissolution may occur, and there is no merit. On the other hand, the reason why the lower limit of the heat treatment temperature holding time is set to 5 hours is that if it is less than that, the effect of improving the forging formability by the heat treatment is small, and the upper limit of the heat treatment temperature holding time is set to 50 hours. This is because the effect of improving the forgeability is saturated even if the heat treatment is performed for a longer time.
【００２６】また、更に、本願の請求項９に係る発明
(以下、第９の発明という)は、上記第５〜第８の発明の
いずれか一において、上記熱間鍛造における鍛造率が１
０％以上であることを特徴としたものである。Further, the invention according to claim 9 of the present application is further provided.
(Hereinafter referred to as a ninth invention) is the hot forging according to any one of the fifth to eighth inventions, wherein the forging ratio in the hot forging is 1
0% or more.
【００２７】ここに、上記鍛造率を１０％以上としたの
は、鍛造率がこの値を下回ると、実用上、鍛造前の素材
内部の微視的な欠陥を潰して素材を鍛錬する効果を得る
ことが難しいからである。The reason why the forging ratio is set to 10% or more is that when the forging ratio is lower than this value, the effect of crushing the microscopic defects inside the material before forging and forging the material is practically used. Because it is difficult to obtain.
【００２８】また、更に、本願の請求項１０に係る発明
(以下、第１０の発明という)は、上記第５〜第９の発明
のいずれか一において、上記熱間鍛造で得られた鍛造部
材に、１００℃〜２５０℃の温度範囲で５時間〜５０時
間保持する熱処理を施すことを特徴としたものである。Further, the invention according to claim 10 of the present application.
(Hereinafter, referred to as a tenth invention) is a method according to any one of the fifth to ninth inventions, wherein the forged member obtained by the hot forging is heated for 5 hours to 50 hours at a temperature range of 100 ° C to 250 ° C. It is characterized by performing a heat treatment for holding for a time.
【００２９】ここに、熱処理温度の下限値を１００℃と
したのは、それ未満では、熱処理による強度向上効果が
小さいからであり、また、熱処理温度の上限値を２５０
℃としたのは、それより高いと、熱処理による強度向上
効果は飽和するからである。一方、熱処理温度保持時間
の下限値を５時間としたのは、それ未満では、熱処理に
よる強度向上効果が小さいからであり、また、熱処理温
度保持時間の上限値を５０時間としたのは、それより長
時間熱処理しても、強度向上効果は飽和するからであ
る。The reason why the lower limit of the heat treatment temperature is set to 100 ° C. is that if it is lower than that, the effect of improving the strength by the heat treatment is small.
The reason for setting the temperature to ° C. is that if the temperature is higher than that, the effect of improving the strength by heat treatment is saturated. On the other hand, the reason why the lower limit of the heat treatment temperature holding time is set to 5 hours is that if it is less than that, the strength improvement effect by the heat treatment is small, and the upper limit of the heat treatment temperature holding time is set to 50 hours. This is because the strength improvement effect is saturated even if the heat treatment is performed for a longer time.
【００３０】また、更に、本願の請求項１１の発明(以
下、第１１の発明という)に係るＭｇ合金鍛造部材は、
少なくともＡｌとＣａとを含有するＭｇ合金鍛造素材を
鍛造して得られる鍛造部材であって、１５０℃において
２２０ＭＰａ以上の引張強度を有することを特徴とした
ものである。Further, the forged Mg alloy member according to the invention of claim 11 of the present application (hereinafter, referred to as an eleventh invention),
A forged member obtained by forging a Mg alloy forging material containing at least Al and Ca, and having a tensile strength of 220 MPa or more at 150 ° C.
【００３１】ここに、１５０℃における引張強度を２２
０ＭＰａ以上としたのは、例えばエンジンのバルブリフ
タなど１５０℃程度の高温下で一定以上の高い強度（２
２０ＭＰａ以上の引張強度）を要する部材・部品等に用
いることができるようにするためである。Here, the tensile strength at 150 ° C. was 22
The reason why the pressure is set to 0 MPa or more is that, for example, a high strength (2
This is so that it can be used for members and parts that require a tensile strength of 20 MPa or more).
【００３２】また、更に、本願の請求項１２に係る発明
(以下、第１２の発明という)は、上記第１１の発明にお
いて、上記Ｍｇ合金鍛造部材が、内燃機関に組み込まれ
るバルブリフタであることを特徴としたものである。Further, the invention according to claim 12 of the present application.
According to a twelfth aspect, in the eleventh aspect, the forged Mg alloy member is a valve lifter incorporated in an internal combustion engine.
【００３３】また、更に、本願の請求項１３に係る発明
(以下、第１３の発明という)は、上記第１２の発明にお
いて、上記バルブリフタの冠面部の鍛造率が２０％以上
であることを特徴としたものである。Further, the invention according to claim 13 of the present application is further provided.
According to a thirteenth aspect, in the twelfth aspect, a forging ratio of a crown portion of the valve lifter is 20% or more.
【００３４】ここに、上記バルブリフタの冠面部の鍛造
率を２０％以上としたのは、高い強度が求められるこの
部分について、鍛造前の素材内部の微視的な欠陥を潰し
て素材を鍛錬する効果を得るためであり、また、所要の
引張強度（室温で２５０ＭＰａ以上）を確保するためで
ある。The reason why the forging rate of the crown surface of the valve lifter is set to 20% or more is that in this part where high strength is required, the material is forged by crushing microscopic defects inside the material before forging. This is for obtaining the effect and for ensuring the required tensile strength (at least 250 MPa at room temperature).
【００３５】また、更に、本願の請求項１４に係る発明
(以下、第１４の発明という)は、上記第１３の発明にお
いて、上記バルブリフタの冠面部の表面にニッケルメッ
キ処理が施されていることを特徴としたものである。Further, the invention according to claim 14 of the present application.
(Hereinafter referred to as a fourteenth invention) is characterized in that, in the thirteenth invention, the surface of the crown surface of the valve lifter is subjected to nickel plating.
【００３６】また、更に、本願の請求項１５に係る発明
(以下、第１５の発明という)は、上記第１３の発明にお
いて、上記バルブリフタの冠面部の表面に鉄（Ｆｅ）溶
射処理が施されていることを特徴としたものである。Further, the invention according to claim 15 of the present application.
A thirteenth invention is characterized in that, in the thirteenth invention, the surface of the crown surface of the valve lifter is subjected to an iron (Fe) spraying treatment.
【００３７】[0037]
【発明の実施の形態】以下、本発明の実施の形態を、添
付図面を参照しながら詳細に説明する。図１１〜図１３
は、本実施の形態に係るマグネシウム合金鍛造素材を用
いて鍛造部材のサンプルを得る方法を模式的に示したも
のである。本実施の形態では、図１に示すように、縦Ａ
１×横Ｂ１×長さＬ１の直方体状のマグネシウム合金製
鍛造素材Ｍ１を用意し、図２に示すように、この素材Ｍ
の例えば横方向を一対の固定プレートＰ１で挟んで拘束
し、この状態で縦方向（図２における紙面方向）に圧縮
荷重を加えて塑性加工（鍛造）を行い、鍛造部材のサン
プルを作成した。Embodiments of the present invention will be described below in detail with reference to the accompanying drawings. 11 to 13
5 schematically shows a method for obtaining a sample of a forged member using the forged magnesium alloy material according to the present embodiment. In the present embodiment, as shown in FIG.
1. A rectangular parallelepiped magnesium alloy forging material M1 of 1 × width B1 × length L1 was prepared, and as shown in FIG.
For example, a horizontal direction was sandwiched between a pair of fixed plates P1 and constrained. In this state, a compressive load was applied in the vertical direction (the direction of the paper surface in FIG. 2) to perform plastic working (forging) to produce a sample of a forged member.
【００３８】この結果、素材Ｍ１の縦方向寸法は、初期
のＡ１からＡ２に変化し（短くなり）、また、長さは初
期のＬ１からＬ２に変化する（長くなる）。この場合、
この鍛造による鍛造率は次式で算出される。 鍛造率＝（Ａ１−Ａ２）／Ａ１×１００［％］… 尚、本実施の形態では、マグネシウム合金鍛造素材Ｍ１
の初期（図１１参照）の基本寸法を、例えば、Ａ１＝Ａ
２＝１２［ｍｍ］，Ｌ１＝５０［ｍｍ］とした。このよ
うにして得られた鍛造部材サンプルをそれぞれ供試材と
し、これら供試材から各種試験に適応した寸法・形状の
試験片を切り出して作成し、以下に述べるような各種の
試験を行った。As a result, the vertical dimension of the material M1 changes from A1 to A2 (short), and the length changes from L1 to L2 (long). in this case,
The forging rate by this forging is calculated by the following equation. Forging rate = (A1−A2) / A1 × 100 [%] In this embodiment, forged magnesium alloy material M1
The initial basic dimensions (see FIG. 11) are, for example, A1 = A
2 = 12 [mm] and L1 = 50 [mm]. The forged member samples thus obtained were used as test materials, and test pieces having dimensions and shapes suitable for various tests were cut out from the test materials, and various tests as described below were performed. .
【００３９】表１は、本実施の形態に係るマグネシウム
合金鍛造素材の特性を調べるための各種試験に用いた試
料（本発明実施例１〜６及び比較例１〜４）の化学成分
およびＣａ／Ａｌ比（アルミニウム含有量に対するカル
シウム含有量の比率）を示している。つまり、表１に示
した各試料（鍛造素材）を用いてそれぞれ鍛造部材のサ
ンプルを製作し、以下に述べるような各種試験に供し
た。尚、表１において、各数値は重量％を示しており、
また、Ａｌ（アルミニウム），Ｃａ（カルシウム），Ｍ
ｎ（マンガン），Ｓｉ（珪素）及びその他（不純物）以
外の残部は、Ｍｇ（マグネシウム）である。Table 1 shows the chemical components and Ca / C of samples (Examples 1 to 6 of the present invention and Comparative Examples 1 to 4) used for various tests for examining the characteristics of the forged magnesium alloy material according to the present embodiment. The Al ratio (the ratio of the calcium content to the aluminum content) is shown. That is, samples of forged members were manufactured using the respective samples (forged materials) shown in Table 1, and subjected to various tests as described below. In Table 1, each numerical value indicates% by weight,
Al (aluminum), Ca (calcium), M
The balance other than n (manganese), Si (silicon) and other (impurities) is Mg (magnesium).
【００４０】[0040]
【表１】 [Table 1]
【００４１】まず、主要な添加元素であるＡｌ（アルミ
ニウム），Ｃａ（カルシウム）の含有量が鍛造部材の高
温での機械的性質に及ぼす影響を調べる試験を行った。
図１および図２は、Ｃａ含有量およびＡｌ含有量が鍛造
部材の定常クリープ速度に及ぼす影響を調べた試験結果
をそれぞれ示している。尚、これらクリープ試験の試験
条件および供試材の設定条件は、以下の通りとした。 ・試験温度：１５０℃ ・荷重条件：１００ＭＰａ ・供試材の鍛造率：５０％First, a test was conducted to examine the effect of the contents of Al (aluminum) and Ca (calcium), which are main additive elements, on the mechanical properties of a forged member at high temperatures.
FIG. 1 and FIG. 2 show test results of examining the effects of the Ca content and the Al content on the steady-state creep rate of a forged member, respectively. In addition, the test conditions of these creep tests and the setting conditions of the test material were as follows.・ Test temperature: 150 ° C. ・ Load condition: 100 MPa ・ Forging rate of test material: 50%
【００４２】図１の試験結果に示されるように、定常ク
リープ速度は、Ｃａ量が０.５重量％(本発明実施例２)
から４重量％（本発明実施例５）の範囲では、Ｃａ量が
増加するに連れて低下しており、この範囲ではＣａ含有
量の増加に伴なって耐クリープ特性が向上することが分
かった。一方、Ｃａ量が４重量％を越えると（比較例
２）、定常クリープ速度は略一定となっており、Ｃａ含
有量の増加による耐クリープ特性向上の効果がこの値
（４重量％）を超えると飽和することが分かった。尚、
Ｃａを全く含まない比較例１の場合には、クリープ速度
が定常状態に至らず、試験開始後１０［ｈｒ］(時間)で
試験片が破断しており、対クリープ特性が著しく劣って
いることが分かった。As shown in the test results in FIG. 1, the steady-state creep rate was such that the Ca amount was 0.5% by weight (Example 2 of the present invention).
In the range of 1 to 4% by weight (Example 5 of the present invention), it decreased as the Ca amount increased. In this range, it was found that the creep resistance improved with the increase of the Ca content. . On the other hand, when the Ca amount exceeds 4% by weight (Comparative Example 2), the steady-state creep rate is substantially constant, and the effect of improving the creep resistance characteristics by increasing the Ca content exceeds this value (4% by weight). Was found to be saturated. still,
In the case of Comparative Example 1 containing no Ca, the creep rate did not reach a steady state, the test piece broke at 10 [hr] (hour) after the start of the test, and the creep characteristics were significantly poor. I understood.
【００４３】また、図２の試験結果から良く分かるよう
に、定常クリープ速度は、Ａｌ量が６重量％（本発明実
施例６）以下の範囲では略一定の低い値に維持される
が、Ａｌ量がこの値を超えると急速に上昇している。す
なわち、Ａｌ含有量を６重量％以下とすることにより、
良好な耐クリープ特性が得られることが分かった。As can be clearly understood from the test results shown in FIG. 2, the steady-state creep rate is maintained at a substantially constant low value when the amount of Al is not more than 6% by weight (Example 6 of the present invention). When the amount exceeds this value it rises rapidly. That is, by setting the Al content to 6% by weight or less,
It was found that good creep resistance was obtained.
【００４４】図３は、高温での引張強度に及ぼすＡｌ含
有量の影響を示している。この高温引張試験の試験条件
および供試材の設定条件は、以下の通りとした。 ・試験温度：１５０℃ ・供試材の鍛造率：５０％FIG. 3 shows the effect of the Al content on the tensile strength at high temperatures. The test conditions of this high-temperature tensile test and the setting conditions of the test material were as follows.・ Test temperature: 150 ° C ・ Forging rate of test material: 50%
【００４５】この図３の試験結果から良く分かるよう
に、高温での引張強度はＡｌ量が３重量％（本発明実施
例１）以上の範囲では略一定の高い値に維持され、Ａｌ
量がこの値を下回って２重量％（本発明実施例７）にな
ると若干の低下傾向を示すようになるが、依然として高
い値（２２０ＭＰａ以上）を保っている。すなわち、Ａ
ｌ含有量が２重量％以上であれば、高温(１５０℃)でも
十分な引張強度を確保することができ、更に、より好ま
しくは、３重量％以上であれば、より高い引張強度をよ
り安定して維持できることが分かった。As can be clearly understood from the test results shown in FIG. 3, the tensile strength at a high temperature is maintained at a substantially constant high value when the Al content is not less than 3% by weight (Example 1 of the present invention).
When the amount falls below this value and becomes 2% by weight (Example 7 of the present invention), a slight downward tendency is exhibited, but the value still remains high (220 MPa or more). That is, A
When the l content is 2% by weight or more, sufficient tensile strength can be ensured even at a high temperature (150 ° C.). More preferably, when the content is 3% by weight or more, higher tensile strength is more stable. And found that it could be maintained.
【００４６】この高温引張強度としては、鍛造部材を例
えばエンジンのバルブリフタなど、１５０℃程度の高温
雰囲気下で一定以上の高い強度を要する部材・部品等に
用いる場合には、実用上、少なくとも２２０ＭＰａ以上
を確保することが好ましい。図３の高温引張試験で用い
た各試料の場合には、いずれも、１５０℃の高温雰囲気
下で２２０ＭＰａ以上の引張強度を確保することがで
き、上記のような一定以上の高い強度を要する部材・部
品等に対しても十分に適用することができる。When the forged member is used for a member or a component which requires a certain high strength in a high temperature atmosphere of about 150 ° C., such as an engine valve lifter, for example, the high temperature tensile strength is practically at least 220 MPa or more. Is preferably ensured. In the case of each of the samples used in the high-temperature tensile test in FIG. 3, a member that can secure a tensile strength of 220 MPa or more in a high-temperature atmosphere of 150 ° C. and requires a certain high strength as described above. -It can be sufficiently applied to parts and the like.
【００４７】次に、Ｃａ／Ａｌ比がＭｇ合金鍛造素材の
鍛造性に及ぼす影響を調べる試験を行った。図４は、高
速鍛造を行った場合における割れ発生率に及ぼすＣａ／
Ａｌ比の影響を示している。尚、本明細書中において、
「高速鍛造」とは、略１００［ｍｍ／秒］以上の鍛造速
度で行う鍛造を言うものとする。上記図４の高速鍛造試
験の試験条件および供試材の設定条件は、以下の通りと
した。 ・鍛造温度：３５０℃ ・鍛造速度：４００［ｍｍ／秒］ ・鍛造率：１０％，２５％，５０％の３種類Next, a test was conducted to examine the effect of the Ca / Al ratio on the forgeability of the forged Mg alloy material. FIG. 4 shows the effect of Ca / on the crack occurrence rate when high-speed forging was performed.
This shows the effect of the Al ratio. In the present specification,
“High-speed forging” refers to forging performed at a forging speed of about 100 [mm / sec] or more. The test conditions for the high-speed forging test in FIG. 4 and the setting conditions for the test material were as follows. -Forging temperature: 350 ° C-Forging speed: 400 [mm / sec]-Forging rate: 10%, 25%, 50%
【００４８】図４の試験結果から良く分かるように、Ｃ
ａ／Ａｌ比が０.８（本発明実施例４）以下の範囲で
は、鍛造率の如何に拘わらず、割れ発生率は最高でも
０.１％以下と極めて低い値に抑制することができる。
一方、Ｃａ／Ａｌ比が０.８を越えると（本発明実施例
５）、鍛造率が２５％及び５０％のものについては割れ
発生率が急速に高くなる。しかし、鍛造率が１０％のも
のについては、Ｃａ／Ａｌ比が０.８以下の場合と同じ
く、割れの発生は全く認められなかった。以上より、実
用性は比較的低いものの鍛造率が１０％であれば、Ｃａ
／Ａｌ比の如何に拘わらず高速鍛造においても割れは発
生せず、また、鍛造率が２５％以上（２５％及び５０
％）の場合には、Ｃａ／Ａｌ比を０.８以下とすること
により、高速鍛造における割れ発生率を極めて低く抑制
して、十分な鍛造性を確保できることが分かった。As can be clearly understood from the test results shown in FIG.
In the range where the a / Al ratio is 0.8 or less (Example 4 of the present invention), the crack generation rate can be suppressed to an extremely low value of 0.1% or less at most, regardless of the forging rate.
On the other hand, when the Ca / Al ratio exceeds 0.8 (Example 5 of the present invention), the crack generation rate rapidly increases for the forging rates of 25% and 50%. However, when the forging ratio was 10%, as in the case where the Ca / Al ratio was 0.8 or less, no cracking was observed. As described above, if the forging ratio is 10% although the practicality is relatively low, Ca
Cracking did not occur even in high-speed forging regardless of the / Al ratio, and the forging rate was 25% or more (25% and 50%).
%), It was found that by setting the Ca / Al ratio to 0.8 or less, the crack occurrence rate in high-speed forging can be suppressed to an extremely low level, and sufficient forgeability can be secured.
【００４９】尚、上記の高速鍛造試験とは別に、略１０
［ｍｍ／秒］の低速での鍛造試験（鍛造温度：３５０
℃）を行ったところ、鍛造率が１０％の場合は勿論のこ
と、鍛造率が２５％及び５０％の場合でも、Ｃａ／Ａｌ
比の如何に拘わらず割れの発生は全く認められなかっ
た。すなわち、鍛造速度が低い場合には、鍛造率および
Ｃａ／Ａｌ比の如何に拘わらず割れ発生はなく、鍛造性
に何ら問題が無いことが分かった。In addition to the above-mentioned high-speed forging test, approximately 10
Forging test at a low speed of [mm / sec] (forging temperature: 350
° C), it was found that Ca / Al not only when the forging rate was 10%, but also when the forging rate was 25% and 50%.
No cracking was observed regardless of the ratio. That is, it was found that when the forging speed was low, no cracking occurred regardless of the forging ratio and the Ca / Al ratio, and there was no problem in the forgeability.
【００５０】次に、供試材の高温強度（引張強度）およ
び鍛造性（限界据え込み率）に及ぼす熱処理の影響を調
べる試験を行った。図５は、鍛造後の熱処理が高温引張
強度に及ぼす影響を示している。この図５に示した高温
引張試験の試験条件および供試材の設定条件は、以下の
通りとした。 ・試験温度：１５０℃ ・供試材の種類：本発明実施例４ ・供試材の鍛造率：５０％ ・供試材の熱処理条件：熱処理無し／鍛造後に１５０℃
で３０時間保持した後に空冷Next, a test was conducted to examine the effect of heat treatment on the high-temperature strength (tensile strength) and forgeability (critical upsetting ratio) of the test material. FIG. 5 shows the effect of heat treatment after forging on high-temperature tensile strength. The test conditions of the high-temperature tensile test and the setting conditions of the test material shown in FIG. 5 were as follows.・ Test temperature: 150 ° C. ・ Type of test material: Example 4 of the present invention ・ Forging rate of test material: 50% ・ Heat treatment condition of test material: No heat treatment / 150 ° C. after forging
Air cooling after holding for 30 hours at
【００５１】この試験結果から良く分かるように、鍛造
後に熱処理を施すことによって、熱処理を行わなかった
場合に比べて、高温(１５０℃)での引張強度は大幅に高
くなっており、鍛造後の熱処理による高温引張強度向上
の効果を確認することができた。尚、この高温引張強度
としては、上述のように、鍛造部材を例えばエンジンの
バルブリフタなど、１５０℃程度の高温雰囲気下で一定
以上の高い強度を要する部材・部品等に用いる場合に
は、実用上、少なくとも２２０ＭＰａ以上を確保するこ
とが好ましいが、図５の試験で示した本発明実施例４の
試料の場合には、鍛造後の熱処理の有無に拘わらず、１
５０℃の高温雰囲気下で２２０ＭＰａ以上の引張強度は
十分に確保されており、上記のような高温雰囲気下で一
定以上の高い強度を要する部材・部品等に対しても十分
に適用できることが、改めて確認された。As can be clearly understood from the test results, the heat treatment after the forging significantly increased the tensile strength at a high temperature (150 ° C.) as compared with the case where the heat treatment was not performed. The effect of improving the high-temperature tensile strength by the heat treatment could be confirmed. As described above, when the forged member is used for a member / part requiring a certain or higher strength under a high temperature atmosphere of about 150 ° C., such as a valve lifter for an engine, as described above, , It is preferable to secure at least 220 MPa, but in the case of the sample of Example 4 of the present invention shown in the test of FIG.
A tensile strength of 220 MPa or more is sufficiently ensured in a high-temperature atmosphere of 50 ° C., and it can be applied to members and components that require a certain high strength in a high-temperature atmosphere as described above. confirmed.
【００５２】上記の鍛造後の熱処理における加熱温度お
よび保持時間としては、熱間鍛造で得られた鍛造部材
に、１００℃〜２５０℃の温度範囲で５時間〜５０時間
保持することが好ましい。この場合、熱処理温度の下限
値を１００℃としたのは、それ未満では、熱処理による
強度向上効果が小さいからであり、また、熱処理温度の
上限値を２５０℃としたのは、それより高いと、熱処理
による強度向上効果は飽和するからである。一方、熱処
理温度保持時間の下限値を５時間としたのは、それ未満
では、熱処理による強度向上効果が小さいからであり、
また、熱処理温度保持時間の上限値を５０時間としたの
は、それより長時間熱処理しても、強度向上効果は飽和
するからである。As the heating temperature and the holding time in the heat treatment after the forging, it is preferable that the forged member obtained by hot forging is held at a temperature of 100 ° C. to 250 ° C. for 5 hours to 50 hours. In this case, the reason why the lower limit of the heat treatment temperature is set to 100 ° C. is that if it is less than that, the strength improvement effect by the heat treatment is small, and if the upper limit of the heat treatment temperature is set to 250 ° C., it is higher. This is because the effect of improving the strength by the heat treatment is saturated. On the other hand, the reason why the lower limit value of the heat treatment temperature holding time is set to 5 hours is that if it is less than that, the strength improvement effect by the heat treatment is small.
The reason why the upper limit of the heat treatment temperature holding time is set to 50 hours is that even if the heat treatment is performed for a longer time, the strength improvement effect is saturated.
【００５３】また、図６は、鍛造温度および鍛造前熱処
理が鍛造時の限界据え込み率に及ぼす影響を示してい
る。この図６に示した限界据え込み率試験の試験条件お
よび供試材の設定条件は、以下の通りとした。 ・供試材の種類：本発明実施例４ ・供試材の熱処理条件：熱処理無し／鍛造前に４１０℃
で１６時間保持した後に空冷FIG. 6 shows the effect of the forging temperature and the pre-forging heat treatment on the critical upsetting ratio during forging. The test conditions of the limit upsetting rate test and the setting conditions of the test material shown in FIG. 6 were as follows. -Type of test material: Example 4 of the present invention-Heat treatment condition of test material: No heat treatment / 410 ° C before forging
Air cooling after holding for 16 hours at
【００５４】ここに、限界据え込み率とは、図１４に模
式的に示すように、直径Ｄ×長さＬ３の円柱状の試験片
Ｍ２を用意し、この試験片Ｍ２に対しその長手方向に圧
縮荷重を加えて、図１５に模式的に示すように試験片を
圧縮変形（変形後の長さＬ４）させた場合に、当該試験
片にクラック（割れ）が発生する限界の据え込み率を言
う。上記図１４および図１５の例で、初期長さL３の試
験片Ｍ２を長さL４まで圧縮変形させたときに微小クラ
ックが発生したとすると、この場合の限界据え込み率
は、次式で算出される。 限界据え込み率＝（L３‐L４）／L３×１００［％］… 尚、本実施の形態では、上記試験片Ｍ２の初期（図１４
参照）の基本寸法を、Ｄ＝１６［ｍｍ］，Ｌ３＝２４
［ｍｍ］とした。Here, the critical upsetting ratio is, as schematically shown in FIG. 14, a column-shaped test piece M2 having a diameter D × length L3 is prepared, and the test piece M2 is moved in the longitudinal direction. When a test piece is compressed and deformed (length L4 after deformation) as schematically shown in FIG. 15 by applying a compressive load, the limit upsetting ratio at which a crack (crack) occurs in the test piece is determined. To tell. In the examples of FIGS. 14 and 15 described above, if a small crack occurs when the test piece M2 having the initial length L3 is compressed and deformed to the length L4, the critical upsetting ratio in this case is calculated by the following equation. Is done. Limit upsetting rate = (L3−L4) / L3 × 100 [%] In this embodiment, the initial state of the test piece M2 (FIG. 14)
Basic dimensions of D = 16 [mm], L3 = 24
[Mm].
【００５５】図６の試験結果から良く分かるように、熱
処理の有無に拘わらず、鍛造温度が略４００℃以下の範
囲では、鍛造温度が上昇するに連れて限界据え込み率は
高くなっており、この範囲では、鍛造温度を高めること
による鍛造性向上の効果を確認することができた。一
方、鍛造温度が４００℃を越えると鍛造性向上の効果は
飽和し、しかも、酸化し易くなる。従って、鍛造温度と
しては、４００℃以下が好ましく、酸化防止の観点から
は３５０℃以下であることがより好ましい。また、鍛造
前に熱処理を施した場合には、熱処理を行わなかった場
合に比べて、限界据え込み率が上昇しており、鍛造前の
熱処理による限界据え込み率度向上の効果を確認するこ
とができた。As can be clearly understood from the test results shown in FIG. 6, regardless of the presence or absence of the heat treatment, when the forging temperature is in the range of about 400 ° C. or less, the critical upsetting ratio increases as the forging temperature increases. In this range, the effect of improving the forgeability by increasing the forging temperature could be confirmed. On the other hand, when the forging temperature exceeds 400 ° C., the effect of improving the forgeability is saturated, and moreover, it is easily oxidized. Therefore, the forging temperature is preferably 400 ° C. or lower, and more preferably 350 ° C. or lower from the viewpoint of preventing oxidation. In addition, when heat treatment was performed before forging, the marginal upsetting rate was higher than when heat treatment was not performed, and the effect of heat treatment before forging to improve the marginal upsetting rate was confirmed. Was completed.
【００５６】この限界据え込み率としては、一般に、実
用上、少なくとも５０％以上を確保することが好まし
く、特に、鍛造部材を例えばエンジンのバルブリフタな
どの一定以上の高い強度を要する部材・部品等に用いる
場合には、７０％以上を確保することがより好ましい。
本発明実施例４の試料の場合には、鍛造前に熱処理を施
さなくても、２５０℃を下回る鍛造温度でも７０％以上
の限界据え込み率を確保することができ、上記のような
一定以上の高い強度を要する部材・部品等に対しても十
分に適用することができる。In general, it is preferable to secure at least 50% or more for practical use as the critical upsetting ratio. In particular, forged members are required to be used for members and parts that require a certain high strength, such as engine valve lifters. When used, it is more preferable to secure 70% or more.
In the case of the sample of Example 4 of the present invention, a critical upsetting rate of 70% or more can be ensured even at a forging temperature lower than 250 ° C. without performing a heat treatment before forging, and the above-mentioned certain level or more can be secured. The present invention can be sufficiently applied to members and parts requiring high strength.
【００５７】上記の鍛造前の熱処理における加熱温度お
よび保持時間としては、上記鍛造素材に、３００℃〜５
００℃の温度範囲で５時間〜５０時間保持する熱処理を
施すことが好ましい。この場合、熱処理温度の下限値を
３００℃としたのは、それ未満では、熱処理による鍛造
成形性の向上効果が小さいからであり、また、熱処理温
度の上限値を５００℃としたのは、それより高くしても
鍛造成形性の向上効果が飽和する上に、酸化や部分的な
溶解の起こることが有り、メリットが無いからである。
一方、熱処理温度保持時間の下限値を５時間としたの
は、それ未満では、熱処理による鍛造成形性の向上効果
が小さいからであり、また、熱処理温度保持時間の上限
値を５０時間としたのは、それより長時間熱処理しても
鍛造成形性の向上効果は飽和するからである。The heating temperature and the holding time in the heat treatment before forging are as follows.
It is preferable to perform a heat treatment of maintaining the temperature in a temperature range of 00 ° C. for 5 hours to 50 hours. In this case, the reason why the lower limit of the heat treatment temperature is set to 300 ° C. is that if it is less than that, the effect of improving the forging formability by the heat treatment is small, and the upper limit of the heat treatment temperature is set to 500 ° C. This is because, even if it is higher, the effect of improving the forgeability is saturated, and oxidation or partial dissolution may occur, and there is no merit.
On the other hand, the reason why the lower limit of the heat treatment temperature holding time is set to 5 hours is that if it is less than that, the effect of improving the forging formability by the heat treatment is small, and the upper limit of the heat treatment temperature holding time is set to 50 hours. This is because the effect of improving the forgeability is saturated even if the heat treatment is performed for a longer time.
【００５８】図７および図８は、鍛造率が鍛造後の比重
および室温での引張強度に及ぼす影響をそれぞれ示して
いる。尚、これらの試験では、供試材の種類として本発
明実施例４の試料を用いた。図７の試験結果から良く分
かるように、鍛造率が略２５％以下の範囲では、鍛造率
が高まるに連れて比重も高くなるが、鍛造率がこの値
(２５％)を越えると、鍛造率上昇による比重上昇の効果
は飽和している。また、鍛造率１０％未満では、鍛造前
の素材内部の微視的な欠陥を潰して素材を鍛錬する効果
が低いので、鍛造率としては、一般に、実用上、少なく
とも１０％以上を確保することが好ましく、特に、鍛造
部材を例えばエンジンのバルブリフタなどの一定以上の
高い強度を要する部材・部品等に用いる場合には、２０
％以上を確保することがより好ましい。FIGS. 7 and 8 show the effect of the forging ratio on the specific gravity after forging and the tensile strength at room temperature, respectively. In these tests, the sample of Example 4 of the present invention was used as the kind of the test material. As can be clearly understood from the test results in FIG. 7, in the range where the forging ratio is approximately 25% or less, the specific gravity increases as the forging ratio increases.
(25%), the effect of the increase in specific gravity due to the increase in the forging rate is saturated. If the forging ratio is less than 10%, the effect of crushing the microscopic defects inside the material before forging and forging the material is low. Therefore, in general, the forging ratio should be at least 10% in practical use. In particular, when the forged member is used for a member or a component requiring a certain strength or higher such as a valve lifter of an engine, for example, 20
% Is more preferably secured.
【００５９】また、図８の試験結果に示されるように、
室温での引張強度は、鍛造率が上昇するに連れて高くな
り、特に、鍛造率が略２５％以下の範囲では、この値を
越える範囲に比べて、鍛造率上昇による引張強度向上効
果が高くなっている。鍛造部材を例えばエンジンのバル
ブリフタなどの一定以上の高い強度を要する部材・部品
等に用いる場合には、常温で２５０ＭＰａ以上の引張強
度を確保することが好ましく、このため、鍛造率として
は２０％以上を確保することが好ましい。Also, as shown in the test results of FIG.
The tensile strength at room temperature increases as the forging ratio increases. Particularly, in the range where the forging ratio is approximately 25% or less, the effect of improving the tensile strength by increasing the forging ratio is higher than in the range exceeding this value. Has become. In the case where the forged member is used for a member or a component that requires a certain high strength, such as a valve lifter of an engine, it is preferable to secure a tensile strength of 250 MPa or more at room temperature. Therefore, the forging ratio is 20% or more. Is preferably ensured.
【００６０】更に、図９は、Ｍｇ合金鍛造素材の平均結
晶粒径が鍛造時の限界据え込み率に及ぼす影響を示して
いる。この図９の限界据え込み試験の試験条件および供
試材の設定条件は、以下の通りとした。 ・鍛造温度：４００℃ ・供試材の種類：本発明実施例４ 上記図９の試験結果から良く分かるように、鍛造素材の
平均結晶粒径が細かいほど、限界据え込み率が高くなっ
ており、５０％の限界据え込み率を確保するには、平均
結晶粒径を３００［μｍｍ］以下にすれば良い。FIG. 9 shows the effect of the average crystal grain size of the forged Mg alloy material on the critical upsetting ratio during forging. The test conditions of the limit upsetting test and the setting conditions of the test material in FIG. 9 are as follows.・ Forging temperature: 400 ° C. ・ Type of test material: Example 4 of the present invention As can be clearly understood from the test results in FIG. 9, the smaller the average crystal grain size of the forged material, the higher the critical upsetting ratio. In order to secure a critical upsetting ratio of 50%, the average crystal grain size may be set to 300 [μmm] or less.
【００６１】Ｍｇ合金鍛造素材の結晶粒径を細かくする
上で、素材を射出成形によって成形することが非常に有
効であることが知られている。このように素材を射出成
形によって成形することにより、素材の平均結晶粒径を
細かくして鍛造性を向上させる（限界据え込み率を高く
する）ことができる。しかも、この射出成形で鍛造部材
としての最終形状に近い形状に予備成形することによ
り、後続する鍛造による塑性加工を容易化かつ簡略化す
ることができ、鍛造工程の生産効率を大幅に高めること
ができる。It is known that molding a material by injection molding is very effective in reducing the crystal grain size of a forged Mg alloy material. By molding the material by injection molding in this way, the average crystal grain size of the material can be reduced, and forgeability can be improved (the limit upsetting rate can be increased). Moreover, by preforming a shape close to the final shape as a forged member by this injection molding, plastic working by subsequent forging can be facilitated and simplified, and the production efficiency of the forging process can be greatly increased. it can.
【００６２】本実施の形態に係るＭｇ合金鍛造素材を用
いた鍛造部材をエンジンのバルブリフタに適用すること
を考えた場合、図１６に示すように、バルブリフタＷの
冠面部Ｗａは、その側面がシリンダヘッドＨｃと高速で
繰り返し摺接し、また、その頂部も、カムＳと摺接する
調整シムＣｍと接するので高い耐磨耗性が要求される。
そこで、Ｍｇ合金鍛造素材を鍛造して形成したバルブリ
フタＷの冠面部Ｗａの側面および頂部表面を含む表面Ｗ
ｆにメッキあるいは溶射等の表面処理を施してエンジン
に組み込み、所謂モータリング試験を行った。このモー
タリング試験の試験条件および供試材の設定条件は、以
下の通りとした。 ・エンジン回転数：３０００［ｒｐｍ］（カムシャフト
回転数：１５００［ｒｐｍ］） ・試験時間：１００時間 バルブリフタ冠面部の表面処理：表面処理無し／Ｎｉメ
ッキ／Ｆｅ溶射Considering that a forged member using a forged Mg alloy material according to the present embodiment is applied to a valve lifter of an engine, as shown in FIG. The head Hc is repeatedly brought into sliding contact with the head Hc at a high speed, and the top is also in contact with the adjusting shim Cm that comes into sliding contact with the cam S, so that high wear resistance is required.
Therefore, the surface W including the side surface and the top surface of the crown surface Wa of the valve lifter W formed by forging the Mg alloy forging material.
f was subjected to a surface treatment such as plating or thermal spraying and incorporated into an engine, and a so-called motoring test was performed. The test conditions of this motoring test and the setting conditions of the test material were as follows. -Engine speed: 3000 [rpm] (Camshaft speed: 1500 [rpm])-Test time: 100 hours Surface treatment of the valve lifter crown: No surface treatment / Ni plating / Fe spraying
【００６３】上記モータリング試験の試験結果を図１０
に示す。この図１０のグラフにおいて、バルブリフタ冠
面にＮｉメッキ処理またはＦｅ溶射処理を施した場合の
磨耗量は、表面処理を全く行わなかった場合の磨耗量を
基準（１）として表示されている。上記図１０の試験結
果から良く分かるように、バルブリフタ冠面にＮｉメッ
キ処理またはＦｅ溶射処理を施すことにより、何らの表
面処理を行わなかった場合に比べて、磨耗量が著しく少
なくなっており、耐磨耗性が大幅に向上している。上記
のような表面処理を行うに際して、メッキ処理は電気メ
ッキあるいは無電解メッキのいずれでも良く、また、Ｎ
ｉメッキの代わりに、Ｐ（燐）含有量の高いＮｉ‐Ｐメ
ッキを施すようにしても良い。FIG. 10 shows the test results of the motoring test.
Shown in In the graph of FIG. 10, the amount of wear when the Ni plating process or the Fe spraying process is performed on the crown surface of the valve lifter is displayed based on the amount of wear when no surface treatment is performed as a reference (1). As can be clearly understood from the test results in FIG. 10 described above, by performing Ni plating or Fe spraying on the crown surface of the valve lifter, the amount of wear is significantly reduced as compared with the case where no surface treatment is performed. Abrasion resistance is greatly improved. When performing the surface treatment as described above, the plating treatment may be either electroplating or electroless plating.
Instead of i-plating, Ni-P plating having a high P (phosphorus) content may be applied.
【００６４】尚、本発明は、以上の実施態様に限定され
るものではなく、その要旨を逸脱しない範囲において、
種々の改良あるいは設計上の変更が可能であることは言
うまでもない。The present invention is not limited to the above-described embodiment, but may be modified without departing from the scope of the invention.
It goes without saying that various improvements or design changes are possible.
【００６５】[0065]
【発明の効果】本願の第１の発明に係るＭｇ合金鍛造素
材によれば、７０％以上の限界据え込み率を有している
ので、Ｍｇ合金鍛造素材を鍛造して得られる鍛造部材
を、例えばエンジンのバルブリフタなど一定以上の高い
強度を要する部材・部品等に対して適用することができ
る。また、この場合において、鍛造温度が３００℃であ
るので、鍛造温度の上昇による鍛造性向上効果が飽和す
る温度よりも低く、従って経済的であり、かつ、高温酸
化が問題となる４００℃よりも十分に低いので、高温で
の酸化による悪影響も回避できる。According to the forged Mg alloy material according to the first invention of the present application, the forged member obtained by forging the forged Mg alloy material has a critical upsetting ratio of 70% or more. For example, the present invention can be applied to members and parts that require a certain high strength, such as a valve lifter of an engine. In this case, the forging temperature is 300 ° C., which is lower than the temperature at which the effect of improving the forgeability by increasing the forging temperature is saturated. Therefore, it is economical and more than 400 ° C. at which high-temperature oxidation becomes a problem. Since it is sufficiently low, adverse effects due to oxidation at high temperatures can also be avoided.
【００６６】また、本願の第２の発明に係るＭｇ合金鍛
造素材によれば、２重量％以上のＡｌを含有しているの
で、高温（１５０℃）で十分な引張強度（２２０ＭＰａ
以上）を確保することができ、また、０.５重量％以上
のＣａを含有し、かつ、Ａｌ含有量が６重量％以下であ
るので、良好な耐クリープ性を確保することができる。
この場合において、Ｃａ含有量は４重量％以下であるの
で、Ｃａ量増加による耐クリープ特性向上の効果を得る
上で経済的である。更に、鍛造素材の平均結晶粒径が３
００μｍ以下であるので、所要の（５０％以上の）限界
据え込み率を確保することができる。According to the forged Mg alloy material according to the second aspect of the present invention, since Al is contained in an amount of 2% by weight or more, sufficient tensile strength (220 MPa) at a high temperature (150 ° C.) is obtained.
Above), and contains 0.5% by weight or more of Ca and an Al content of 6% by weight or less, so that good creep resistance can be ensured.
In this case, since the Ca content is 4% by weight or less, it is economical to obtain the effect of improving the creep resistance by increasing the amount of Ca. Furthermore, the average grain size of the forged material is 3
Since it is not more than 00 μm, a required (up to 50%) critical upsetting ratio can be secured.
【００６７】更に、本願の第３の発明によれば、基本的
には、上記第１または第２の発明と同様の効果を奏する
ことができる。しかも、その上、Ａｌ含有量に対するＣ
ａ含有量の比率（Ｃａ／Ａｌ比）が０.８以下であるの
で、所要の鍛造率（５０％）を確保した上で、高速鍛造
においても割れ発生率を極めて低く抑えることができ、
良好な鍛造性を得ることができる。Further, according to the third aspect of the present invention, basically the same effects as those of the first or second aspect can be obtained. In addition, the C content relative to the Al content
Since the ratio of the a content (Ca / Al ratio) is 0.8 or less, the required forging rate (50%) can be ensured, and the crack generation rate can be extremely low even in high-speed forging.
Good forgeability can be obtained.
【００６８】また、更に、本願の第４の発明によれば、
基本的には、上記第１〜第３の発明のいずれか一と同様
の効果を奏することができる。特に、鍛造加工に先立っ
て射出成形にて所定形状に予備成形されているので、鍛
造素材を射出成形によって成形するで素材の平均結晶粒
径を細かくして鍛造性を向上させる（限界据え込み率を
高くする）ことができる。しかも、この射出成形で鍛造
部材としての最終形状に近似した形状に予備成形するこ
とにより、後続する鍛造による塑性加工を容易化かつ簡
略化することができ、鍛造工程の生産効率を大幅に高め
ることができる。Further, according to the fourth invention of the present application,
Basically, the same effect as any one of the first to third inventions can be obtained. In particular, since it is preformed into a predetermined shape by injection molding prior to forging, the forged material is formed by injection molding to reduce the average crystal grain size of the material and improve forgeability (critical upsetting rate) Higher). Moreover, by preforming into a shape similar to the final shape as a forged member by this injection molding, plastic working by subsequent forging can be facilitated and simplified, and the production efficiency of the forging process can be greatly increased. Can be.
【００６９】また、更に、本願の第５の発明によれば、
Ｍｇ合金鍛造素材が、２重量％以上のＡｌを含有してい
るので、これを熱間鍛造することにより、高温（１５０
℃）で十分な引張強度（２２０ＭＰａ以上）を確保する
ことができ、また、０.５重量％以上のＣａを含有し、
かつ、Ａｌ含有量が６重量％以下であるので、良好な耐
クリープ性を確保することができる。この場合におい
て、Ｃａ含有量は４重量％以下であるので、Ｃａ量増加
による耐クリープ特性向上の効果を得る上で経済的であ
る。Further, according to the fifth invention of the present application,
Since the Mg alloy forging material contains 2% by weight or more of Al, the material is hot forged to a high temperature (150%).
° C), a sufficient tensile strength (220 MPa or more) can be secured, and 0.5% by weight or more of Ca is contained,
In addition, since the Al content is 6% by weight or less, good creep resistance can be ensured. In this case, since the Ca content is 4% by weight or less, it is economical to obtain the effect of improving the creep resistance by increasing the amount of Ca.
【００７０】また、更に、本願の第６の発明によれば、
基本的には、上記第５の発明と同様の効果を奏すること
ができる。しかも、その上、Ａｌ含有量に対するＣａ含
有量の比率（Ｃａ／Ａｌ比）が０.８以下であるので、
所要の鍛造率（５０％）を確保した上で、高速鍛造にお
いても割れ発生率を極めて低く抑えることができ、良好
な鍛造性を得ることができ、また、４００［ｍｍ／秒］
以上の鍛造速度で熱間鍛造するので、例えば自動車用エ
ンジンのバルブリフタなどの機構部品等の部品類を製造
するに際して、十分に高い生産性を確保することができ
る。Further, according to the sixth invention of the present application,
Basically, the same effects as those of the fifth aspect can be obtained. Moreover, since the ratio of the Ca content to the Al content (Ca / Al ratio) is 0.8 or less,
After securing the required forging rate (50%), the rate of occurrence of cracks can be extremely low even in high-speed forging, and good forgeability can be obtained, and 400 [mm / sec]
Since hot forging is performed at the above-described forging speed, sufficiently high productivity can be ensured when manufacturing components such as mechanical components such as a valve lifter of an automobile engine.
【００７１】また、更に、本願の第７の発明によれば、
基本的には、上記第５または第６の発明と同様の効果を
奏することができる。特に、上記熱間鍛造における鍛造
温度が２５０℃〜４００℃の範囲であるので、良好な限
界据え込み率（７０％以上）を確保して、例えばエンジ
ンのバルブリフタなど一定以上の高い強度を要する部材
・部品等にも適用することができ、また、鍛造温度の上
限値を４００℃であるので、鍛造温度の上昇による鍛造
性向上の効果を得る上で経済的であり、しかも、高温酸
化による悪影響の回避も図ることができる。Further, according to the seventh invention of the present application,
Basically, the same effect as the fifth or sixth invention can be obtained. In particular, since the forging temperature in the hot forging is in the range of 250 ° C. to 400 ° C., a member that requires a certain high strength such as a valve lifter of an engine, for example, ensuring a good limit upsetting rate (70% or more). -It can be applied to parts, etc., and the upper limit of the forging temperature is 400 ° C., so that it is economical to obtain the effect of improving the forgeability by increasing the forging temperature, and furthermore, has the adverse effect of high-temperature oxidation. Can also be avoided.
【００７２】また、更に、本願の第８の発明によれば、
基本的には、上記第５〜第７の発明のいずれか一と同様
の効果を奏することができる。特に、上記熱間鍛造に先
立って上記鍛造素材に熱処理を施すようにしたので、限
界据え込み率をより高めることができる。Further, according to the eighth invention of the present application,
Basically, the same effect as any one of the fifth to seventh inventions can be obtained. In particular, since the heat treatment is performed on the forged material prior to the hot forging, the critical upsetting ratio can be further increased.
【００７３】また、更に、本願の第９の発明によれば、
基本的には、上記第５〜第８の発明のいずれか一と同様
の効果を奏することができる。特に、上記熱間鍛造にお
ける鍛造率が１０％以上であるので、鍛造前の素材内部
の微視的な欠陥を潰して素材を実用上有効に鍛錬する効
果を得ることができる。Further, according to the ninth invention of the present application,
Basically, the same effect as any one of the fifth to eighth inventions can be obtained. In particular, since the forging ratio in the hot forging is 10% or more, it is possible to obtain an effect of crushing microscopic defects inside the material before forging and effectively forging the material for practical use.
【００７４】また、更に、本願の第１０の発明によれ
ば、基本的には、上記第５〜第９の発明のいずれか一と
同様の効果を奏することができる。特に、上記熱間鍛造
で得られた鍛造部材に熱処理を施すようにしたので、高
温（１５０℃）での引張強度を高めることができる。Further, according to the tenth aspect of the present invention, basically the same effects as in any one of the fifth to ninth aspects can be obtained. In particular, since the heat treatment is performed on the forged member obtained by the hot forging, the tensile strength at a high temperature (150 ° C.) can be increased.
【００７５】また、更に、本願の第１１の発明に係るＭ
ｇ合金鍛造部材によれば、１５０℃において２２０ＭＰ
ａ以上の引張強度を有しているので、例えばエンジンの
バルブリフタなど１５０℃程度の高温下で一定以上の高
い強度（２２０ＭＰａ以上の引張強度）を要する部材・
部品等に対して適用することができる。Further, according to the eleventh invention of the present application, M
According to the g alloy forged member, 220MP at 150 ° C
A member that requires a certain high strength (tensile strength of 220 MPa or more) at a high temperature of about 150 ° C., such as a valve lifter of an engine, because it has a tensile strength of at least a.
It can be applied to parts and the like.
【００７６】また、更に、本願の第１２の発明によれ
ば、基本的には、上記第１１の発明と同様の効果を奏す
ることができる。特に、上記Ｍｇ合金鍛造部材が、内燃
機関に組み込まれるバルブリフタであるので、バルブリ
フタを鍛造によって製造するに際して、１５０℃程度の
高温下で一定以上の高い強度（２２０ＭＰａ以上の引張
強度）を付与することができる。Further, according to the twelfth aspect of the present invention, basically the same effects as those of the eleventh aspect can be obtained. In particular, since the forged Mg alloy member is a valve lifter to be incorporated into an internal combustion engine, when manufacturing the valve lifter by forging, it is necessary to impart a certain strength or higher (tensile strength of 220 MPa or more) at a high temperature of about 150 ° C. Can be.
【００７７】また、更に、本願の第１３の発明によれ
ば、基本的には、上記第１２の発明と同様の効果を奏す
ることができる。特に、上記バルブリフタの冠面部の鍛
造率が２０％以上であるので、より高い強度が求められ
るこの部分について、鍛造前の素材内部の微視的な欠陥
を潰して素材を鍛錬する効果を得ることができ、また、
所要の引張強度（室温で２５０ＭＰａ以上）を確保する
ことができる。Further, according to the thirteenth aspect of the present invention, basically the same effects as those of the twelfth aspect can be obtained. In particular, since the forging ratio of the crown surface of the valve lifter is 20% or more, in this portion where higher strength is required, it is possible to obtain the effect of forging the material by crushing microscopic defects inside the material before forging. Can also be
The required tensile strength (250 MPa or more at room temperature) can be secured.
【００７８】また、更に、本願の第１４の発明によれ
ば、基本的には、上記第１３の発明と同様の効果を奏す
ることができる。特に、上記バルブリフタの冠面部の表
面にニッケルメッキ処理が施されているので、相手側部
材と繰り返し摺接するこの部分に対して十分に高い耐磨
耗性を付与することができる。Further, according to the fourteenth aspect of the present invention, basically the same effects as those of the thirteenth aspect can be obtained. In particular, since the surface of the crown surface of the valve lifter is nickel-plated, a sufficiently high wear resistance can be imparted to this portion that repeatedly slides with the mating member.
【００７９】また、更に、本願の第１５の発明によれ
ば、基本的には、上記第１３の発明と同様の効果を奏す
ることができる。特に、上記バルブリフタの冠面部の表
面に鉄（Ｆｅ）溶射処理が施されているので、相手側部
材と繰り返し摺接するこの部分に対して十分に高い耐磨
耗性を付与することができる。Further, according to the fifteenth invention of the present application, basically the same effects as those of the thirteenth invention can be obtained. In particular, since the surface of the crown surface of the valve lifter is subjected to the iron (Fe) thermal spraying treatment, it is possible to impart sufficiently high wear resistance to this portion that repeatedly slides with the mating member.
【図１】 マグネシウム合金鍛造部材の定常クリープ速
度に及ぼすカルシウム含有量の影響を示すグラフであ
る。FIG. 1 is a graph showing the effect of the calcium content on the steady-state creep rate of a forged magnesium alloy member.
【図２】 マグネシウム合金鍛造部材の定常クリープ速
度に及ぼすアルミニウム含有量の影響を示すグラフであ
る。FIG. 2 is a graph showing the effect of the aluminum content on the steady-state creep rate of a forged magnesium alloy member.
【図３】 マグネシウム合金鍛造部材の高温引張強度に
及ぼすアルミニウム含有量の影響を示すグラフである。FIG. 3 is a graph showing the effect of aluminum content on the high-temperature tensile strength of a forged magnesium alloy member.
【図４】 高速鍛造における割れ発生率に及ぼすＣａ／
Ａｌ火の影響を示すグラフである。FIG. 4 shows the effect of Ca / on the crack generation rate in high-speed forging.
It is a graph which shows the influence of Al fire.
【図５】 鍛造後の熱処理が高温引張強度に及ぼす影響
を示すグラフである。FIG. 5 is a graph showing the effect of heat treatment after forging on high-temperature tensile strength.
【図６】 限界据え込み率に及ぼす鍛造温度と鍛造前熱
処理の影響を示すグラフである。FIG. 6 is a graph showing the effect of forging temperature and heat treatment before forging on the critical upsetting ratio.
【図７】 鍛造後の比重に及ぼす鍛造率の影響を示すグ
ラフである。FIG. 7 is a graph showing the effect of the forging ratio on the specific gravity after forging.
【図８】 室温での引張強度に及ぼす鍛造率の影響を示
すグラフである。FIG. 8 is a graph showing the effect of the forging ratio on the tensile strength at room temperature.
【図９】 限界据え込み率に及ぼす鍛造素材の平均結晶
粒径の影響を示すグラフである。FIG. 9 is a graph showing the influence of the average grain size of the forged material on the critical upsetting ratio.
【図１０】 マグネシウム合金鍛造部材製バルブリフタ
のモータリング試験後の磨耗量を示すグラフである。FIG. 10 is a graph showing the amount of wear of a valve lifter made of a forged magnesium alloy member after a motoring test.
【図１１】 本実施の形態に係るマグネシウム合金鍛造
素材の斜視図である。FIG. 11 is a perspective view of a forged magnesium alloy material according to the present embodiment.
【図１２】 上記マグネシウム合金鍛造素材の鍛造工程
を模式的に示す説明図である。FIG. 12 is an explanatory view schematically showing a forging step of the magnesium alloy forging material.
【図１３】 上記鍛造工程後のマグネシウム合金鍛造部
材サンプルの説明図である。FIG. 13 is an explanatory view of a magnesium alloy forged member sample after the forging step.
【図１４】 本実施の形態に係るマグネシウム合金製鍛
造素材の限界据え込み率試験の初期状態を示す説明図で
ある。FIG. 14 is an explanatory diagram showing an initial state of a critical upsetting test of the forged magnesium alloy material according to the present embodiment.
【図１５】 上記限界据え込み率試験の鍛造時における
マグネシウム合金製鍛造素材を模式的に示す説明図であ
る。FIG. 15 is an explanatory view schematically showing a magnesium alloy forged material at the time of forging in the critical upsetting test.
【図１６】 本実施の形態に係るバルブリフタの要部を
示す部分断面説明図である。FIG. 16 is a partial cross-sectional explanatory view showing a main part of the valve lifter according to the present embodiment.
Ｍ１，Ｍ２…Ｍｇ合金鍛造素材 Ｗ…バルブリフタ Ｗａ…バルブリフタの冠面部 Ｗｆ…冠面部の表面 M1, M2: Forged Mg alloy material W: Valve lifter Wa: Crown surface of valve lifter Wf: Surface of crown surface
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.7 識別記号 ＦＩ テーマコート゛(参考） // Ｃ２２Ｆ 1/00 ６３０ Ｃ２２Ｆ 1/00 ６３０Ｋ ６５０ ６５０Ａ ６８２ ６８２ ６８３ ６８３ ６９１ ６９１Ｂ ６９１Ｃ ６９４ ６９４Ａ ６９４Ｂ ６９４Ｚ (72)発明者 石田 恭聡 広島県安芸郡府中町新地３番１号 マツダ 株式会社内 Ｆターム(参考） 3G016 AA19 BB04 EA07 EA08 FA04 FA16 FA22 FA23 GA00 GA02 GA05 4E087 AA05 AA10 BA01 BA03 CA31 CB01 CB04 CB12 DB11 DB14 DB18 DB22 EC01 HA13 HA67 HA82 ──────────────────────────────────────────────────の Continued on the front page (51) Int.Cl. 7 Identification symbol FI Theme coat (Reference) // C22F 1/00 630 C22F 1/00 630K 650 650A 682 682 683 683 683 691 691B 691C 694 694A 694B 694Z (72 ) Inventor Yasuaki Ishida 3-1 Shinchi, Fuchu-cho, Aki-gun, Hiroshima F-term in Mazda Co., Ltd. (Reference) 3G016 AA19 BB04 EA07 EA08 FA04 FA16 FA22 FA23 GA00 GA02 GA05 4E087 AA05 AA10 BA01 BA03 CA31 CB01 CB04 CB12 DB11 DB18 DB22 EC01 HA13 HA67 HA82
Claims (15)
を含有し、３００℃において７０％以上の限界据え込み
率を有することを特徴とするマグネシウム合金鍛造素
材。1. A forged magnesium alloy material containing at least aluminum and calcium and having a limited upsetting ratio of at least 70% at 300 ° C.
ウム及び０.５重量％以上で４重量％以下のカルシウム
を含有し、平均結晶粒径が３００μｍ以下であることを
特徴とするマグネシウム合金鍛造素材。2. A magnesium alloy containing 2% by weight or more and 6% by weight or less of aluminum and 0.5% by weight or more and 4% by weight or less of calcium and having an average crystal grain size of 300 μm or less. Forged material.
含有量の比率が０.８以下であることを特徴とする請求
項１または請求項２に記載のマグネシウム合金鍛造素
材。3. The magnesium alloy forging material according to claim 1, wherein the ratio of the calcium content to the aluminum content is 0.8 or less.
状に予備成形されて成ることを特徴とする請求項１〜請
求項３のいずれか一に記載のマグネシウム合金鍛造素
材。4. The magnesium alloy forging material according to claim 1, wherein the forging material is preformed into a predetermined shape by injection molding prior to forging.
マグネシウム合金鍛造素材であって２重量％以上で６重
量％以下のアルミニウム及び０.５重量％以上で４重量
％以下のカルシウムを含有したマグネシウム合金鍛造素
材を熱間鍛造することを特徴とするマグネシウム合金鍛
造部材の製造方法。5. The forged magnesium alloy material according to claim 1, wherein the forged material is at least 2% by weight and at most 6% by weight, and at least 0.5% by weight and at most 4% by weight of calcium. A method for producing a forged magnesium alloy member, comprising hot-forging a forged magnesium alloy material containing.
アルミニウム含有量に対するカルシウム含有量の比率が
０.８以下のものを、４００［ｍｍ／秒］以上の鍛造速
度で熱間鍛造することを特徴とする請求項５記載のマグ
ネシウム合金鍛造部材の製造方法。6. A hot forging of the magnesium alloy forging material having a ratio of calcium content to aluminum content of 0.8 or less at a forging speed of 400 [mm / sec] or more. The method for producing a forged magnesium alloy member according to claim 5.
℃〜４００℃の範囲であることを特徴とする請求項５ま
たは請求項６に記載のマグネシウム合金鍛造部材の製造
方法。7. The forging temperature in the hot forging is 250.
The method for producing a forged magnesium alloy member according to claim 5 or 6, wherein the temperature is in a range of from 400C to 400C.
に、３００℃〜５００℃の温度範囲で５時間〜５０時間
保持する熱処理を施すことを特徴とする請求項５〜請求
項７のいずれか一に記載のマグネシウム合金鍛造部材の
製造方法。8. The method according to claim 5, wherein prior to the hot forging, the forging material is subjected to a heat treatment for maintaining the temperature in a temperature range of 300 ° C. to 500 ° C. for 5 hours to 50 hours. The method for producing a forged magnesium alloy member according to any one of the preceding claims.
上であることを特徴とする請求項５〜請求項８のいずれ
か一に記載のマグネシウム合金鍛造部材の製造方法。9. The method according to claim 5, wherein a forging ratio in the hot forging is 10% or more.
１００℃〜２５０℃の温度範囲で５時間〜５０時間保持
する熱処理を施すことを特徴とする請求項５〜請求項９
のいずれか一に記載のマグネシウム合金鍛造部材の製造
方法。10. The forged member obtained by the hot forging described above,
10. A heat treatment which is carried out in a temperature range of 100 DEG C. to 250 DEG C. for 5 hours to 50 hours.
The method for producing a forged magnesium alloy member according to any one of the above.
とを含有するマグネシウム合金鍛造素材を鍛造して得ら
れる鍛造部材であって、１５０℃において２２０ＭＰａ
以上の引張強度を有することを特徴とするマグネシウム
合金鍛造部材。11. A forged member obtained by forging a forged magnesium alloy material containing at least aluminum and calcium, wherein the forged member is 220 MPa at 150 ° C.
A forged magnesium alloy member having the above tensile strength.
燃機関に組み込まれるバルブリフタであることを特徴と
する請求項１１記載のマグネシウム合金鍛造部材。12. The forged magnesium alloy member according to claim 11, wherein the forged magnesium alloy member is a valve lifter incorporated in an internal combustion engine.
２０％以上であることを特徴とする請求項１２記載のマ
グネシウム合金鍛造部材。13. The forged magnesium alloy member according to claim 12, wherein a forging ratio of a crown portion of the valve lifter is 20% or more.
ッケルメッキ処理が施されていることを特徴とする請求
項１３記載のマグネシウム合金鍛造部材。14. The forged magnesium alloy member according to claim 13, wherein the surface of the crown surface of the valve lifter is nickel-plated.
溶射処理が施されていることを特徴とする請求項１３記
載のマグネシウム合金鍛造部材。15. The forged magnesium alloy member according to claim 13, wherein the surface of the crown surface of the valve lifter is subjected to an iron spraying process.
Priority Applications (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10278507A JP2000104137A (en) | 1998-09-30 | 1998-09-30 | Magnesium alloy forging stock, forged member and production of the forged member |
| EP99117054A EP0990710A1 (en) | 1998-09-30 | 1999-08-30 | Magnesium alloy forging material and forged member, and method for manufacturing the forged member |
| CN99118462A CN1249355A (en) | 1998-09-30 | 1999-08-30 | Magnesium alloy forged material and member, and method for mfg. forged member |
| KR1019990041639A KR20000023503A (en) | 1998-09-30 | 1999-09-28 | Magnesium alloy forging material, and forging member and manufacturing method of said forging member |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10278507A JP2000104137A (en) | 1998-09-30 | 1998-09-30 | Magnesium alloy forging stock, forged member and production of the forged member |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JP2000104137A true JP2000104137A (en) | 2000-04-11 |
Family
ID=17598280
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP10278507A Pending JP2000104137A (en) | 1998-09-30 | 1998-09-30 | Magnesium alloy forging stock, forged member and production of the forged member |
Country Status (4)
| Country | Link |
|---|---|
| EP (1) | EP0990710A1 (en) |
| JP (1) | JP2000104137A (en) |
| KR (1) | KR20000023503A (en) |
| CN (1) | CN1249355A (en) |
Cited By (12)
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|---|---|---|---|---|
| JP2004162090A (en) * | 2002-11-11 | 2004-06-10 | Toyota Industries Corp | Heat resistant magnesium alloy |
| JP2004232060A (en) * | 2003-01-31 | 2004-08-19 | Toyota Industries Corp | Heat resistant magnesium alloy for casting and heat resistant magnesium alloy casting |
| JP2008231488A (en) * | 2007-03-19 | 2008-10-02 | Mitsui Mining & Smelting Co Ltd | Magnesium alloy for plastic working, and plastically worked member of magnesium alloy |
| JP2008260976A (en) * | 2007-04-10 | 2008-10-30 | Mitsui Mining & Smelting Co Ltd | Magnesium alloy to be plastic-worked, and forged and molded member of magnesium alloy |
| JP2009007676A (en) * | 2008-07-30 | 2009-01-15 | Toyota Industries Corp | Heat resistant magnesium alloy for casting, and heat resistant magnesium alloy casting |
| WO2010038893A1 (en) * | 2008-10-03 | 2010-04-08 | 株式会社豊田自動織機 | Heat-resistant magnesium alloy |
| JP2011074461A (en) * | 2009-09-30 | 2011-04-14 | Nagaoka Univ Of Technology | Rolled material of magnesium alloy and method for manufacturing the same |
| US8123877B2 (en) | 2003-01-31 | 2012-02-28 | Kabushiki Kaisha Toyota Jidoshokki | Heat-resistant magnesium alloy for casting heat-resistant magnesium alloy cast product, and process for producing heat-resistant magnesium alloy cast product |
| WO2012057329A1 (en) | 2010-10-29 | 2012-05-03 | サンデン株式会社 | Magnesium-alloy member, compressor for use in air conditioner, and method for manufacturing magnesium-alloy member |
| KR101591941B1 (en) | 2013-07-25 | 2016-02-04 | 한국기계연구원 | Method for manufacturing magnesium alloy sheet having high strength and magnesium alloy sheet manufactured thereby |
| WO2020203041A1 (en) * | 2019-03-29 | 2020-10-08 | 株式会社栗本鐵工所 | Heat-resistant magnesium alloy for casting |
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|---|---|---|---|---|
| JP3861720B2 (en) * | 2002-03-12 | 2006-12-20 | Ｔｋｊ株式会社 | Forming method of magnesium alloy |
| JP4539572B2 (en) * | 2006-01-27 | 2010-09-08 | 株式会社豊田中央研究所 | Magnesium alloys and castings for casting |
| CN101652489A (en) * | 2007-04-03 | 2010-02-17 | 株式会社丰田自动织机 | Heat-resistant magnesium alloy |
| KR101385685B1 (en) * | 2011-03-30 | 2014-04-16 | 한국생산기술연구원 | Mg-Al-Ca MASTER ALLOYS FOR Mg ALLOYS AND MANUFACTURING METHOD THEREOF |
| CN103212572B (en) * | 2013-04-17 | 2015-04-29 | 燕山大学 | Method for rolling magnesium alloy plate |
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| JPH0681089A (en) * | 1992-09-02 | 1994-03-22 | Sumitomo Metal Ind Ltd | Method for hot-working magnesium alloy |
| JPH07224344A (en) * | 1993-12-17 | 1995-08-22 | Mazda Motor Corp | Magnesium alloy casting stock for plastic working, magnesium alloy member using the same and production thereof |
| JPH09272945A (en) * | 1996-04-04 | 1997-10-21 | Mazda Motor Corp | Heat resistant magnesium alloy molded member, heat resistant magnesium alloy used for the molding and molding method therefor |
Cited By (15)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2004162090A (en) * | 2002-11-11 | 2004-06-10 | Toyota Industries Corp | Heat resistant magnesium alloy |
| JP2004232060A (en) * | 2003-01-31 | 2004-08-19 | Toyota Industries Corp | Heat resistant magnesium alloy for casting and heat resistant magnesium alloy casting |
| US8123877B2 (en) | 2003-01-31 | 2012-02-28 | Kabushiki Kaisha Toyota Jidoshokki | Heat-resistant magnesium alloy for casting heat-resistant magnesium alloy cast product, and process for producing heat-resistant magnesium alloy cast product |
| JP2008231488A (en) * | 2007-03-19 | 2008-10-02 | Mitsui Mining & Smelting Co Ltd | Magnesium alloy for plastic working, and plastically worked member of magnesium alloy |
| JP2008260976A (en) * | 2007-04-10 | 2008-10-30 | Mitsui Mining & Smelting Co Ltd | Magnesium alloy to be plastic-worked, and forged and molded member of magnesium alloy |
| JP2009007676A (en) * | 2008-07-30 | 2009-01-15 | Toyota Industries Corp | Heat resistant magnesium alloy for casting, and heat resistant magnesium alloy casting |
| JP2010090405A (en) * | 2008-10-03 | 2010-04-22 | Toyota Industries Corp | Heat-resistant magnesium alloy |
| WO2010038893A1 (en) * | 2008-10-03 | 2010-04-08 | 株式会社豊田自動織機 | Heat-resistant magnesium alloy |
| JP2011074461A (en) * | 2009-09-30 | 2011-04-14 | Nagaoka Univ Of Technology | Rolled material of magnesium alloy and method for manufacturing the same |
| WO2012057329A1 (en) | 2010-10-29 | 2012-05-03 | サンデン株式会社 | Magnesium-alloy member, compressor for use in air conditioner, and method for manufacturing magnesium-alloy member |
| JP2012097309A (en) * | 2010-10-29 | 2012-05-24 | Sanden Corp | Magnesium alloy member, compressor for air conditioner, and method for manufacturing magnesium alloy member |
| KR101591941B1 (en) | 2013-07-25 | 2016-02-04 | 한국기계연구원 | Method for manufacturing magnesium alloy sheet having high strength and magnesium alloy sheet manufactured thereby |
| US10808301B2 (en) | 2015-05-27 | 2020-10-20 | Honda Motor Co., Ltd. | Magnesium alloy and method of manufacturing same |
| WO2020203041A1 (en) * | 2019-03-29 | 2020-10-08 | 株式会社栗本鐵工所 | Heat-resistant magnesium alloy for casting |
| US11959155B2 (en) | 2019-03-29 | 2024-04-16 | Kurimoto, Ltd. | Heat-resistant magnesium alloy for casting |
Also Published As
| Publication number | Publication date |
|---|---|
| CN1249355A (en) | 2000-04-05 |
| EP0990710A1 (en) | 2000-04-05 |
| KR20000023503A (en) | 2000-04-25 |
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