JPH01283330A - Manufacture of aluminum-based composite member - Google Patents
Manufacture of aluminum-based composite memberInfo
- Publication number
- JPH01283330A JPH01283330A JP11308588A JP11308588A JPH01283330A JP H01283330 A JPH01283330 A JP H01283330A JP 11308588 A JP11308588 A JP 11308588A JP 11308588 A JP11308588 A JP 11308588A JP H01283330 A JPH01283330 A JP H01283330A
- Authority
- JP
- Japan
- Prior art keywords
- powder
- mold
- aluminum metal
- molded body
- alloy
- 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
- 239000002131 composite material Substances 0.000 title claims abstract description 28
- 229910052782 aluminium Inorganic materials 0.000 title claims abstract description 10
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 9
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 title claims description 73
- 239000000843 powder Substances 0.000 claims abstract description 48
- 239000012779 reinforcing material Substances 0.000 claims abstract description 27
- 239000011159 matrix material Substances 0.000 claims abstract description 23
- 238000000034 method Methods 0.000 claims abstract description 18
- 229910052751 metal Inorganic materials 0.000 abstract description 22
- 239000002184 metal Substances 0.000 abstract description 22
- 239000000835 fiber Substances 0.000 abstract description 15
- 229910000838 Al alloy Inorganic materials 0.000 abstract description 14
- 238000005266 casting Methods 0.000 abstract description 11
- 238000002156 mixing Methods 0.000 abstract description 6
- 239000000463 material Substances 0.000 abstract description 5
- 230000003014 reinforcing effect Effects 0.000 abstract description 5
- 239000000203 mixture Substances 0.000 abstract description 4
- 238000000465 moulding Methods 0.000 abstract description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 abstract description 2
- 239000000919 ceramic Substances 0.000 abstract description 2
- 239000010439 graphite Substances 0.000 abstract description 2
- 229910002804 graphite Inorganic materials 0.000 abstract description 2
- 239000010445 mica Substances 0.000 abstract description 2
- 229910052618 mica group Inorganic materials 0.000 abstract description 2
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 abstract 2
- 229920000914 Metallic fiber Polymers 0.000 abstract 1
- 229910052581 Si3N4 Inorganic materials 0.000 abstract 1
- 229910052593 corundum Inorganic materials 0.000 abstract 1
- 238000001125 extrusion Methods 0.000 abstract 1
- 239000012784 inorganic fiber Substances 0.000 abstract 1
- 239000012783 reinforcing fiber Substances 0.000 abstract 1
- 229910001845 yogo sapphire Inorganic materials 0.000 abstract 1
- 239000002245 particle Substances 0.000 description 13
- 229910045601 alloy Inorganic materials 0.000 description 6
- 239000000956 alloy Substances 0.000 description 6
- 230000000694 effects Effects 0.000 description 5
- 238000010438 heat treatment Methods 0.000 description 5
- 238000005470 impregnation Methods 0.000 description 5
- 239000011812 mixed powder Substances 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 4
- 238000010298 pulverizing process Methods 0.000 description 4
- 238000005204 segregation Methods 0.000 description 4
- 239000011148 porous material Substances 0.000 description 3
- 238000003825 pressing Methods 0.000 description 3
- 238000005299 abrasion Methods 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- 238000007796 conventional method Methods 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 239000002657 fibrous material Substances 0.000 description 2
- 239000007788 liquid Substances 0.000 description 2
- 239000007791 liquid phase Substances 0.000 description 2
- 150000002739 metals Chemical class 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 238000007711 solidification Methods 0.000 description 2
- 230000008023 solidification Effects 0.000 description 2
- 238000003756 stirring Methods 0.000 description 2
- 230000007847 structural defect Effects 0.000 description 2
- 229910001250 2024 aluminium alloy Inorganic materials 0.000 description 1
- 101100041624 Arabidopsis thaliana SAC8 gene Proteins 0.000 description 1
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 1
- 241000721701 Lynx Species 0.000 description 1
- VRAIHTAYLFXSJJ-UHFFFAOYSA-N alumane Chemical compound [AlH3].[AlH3] VRAIHTAYLFXSJJ-UHFFFAOYSA-N 0.000 description 1
- 238000000889 atomisation Methods 0.000 description 1
- 239000011230 binding agent Substances 0.000 description 1
- 238000002485 combustion reaction Methods 0.000 description 1
- 238000013329 compounding Methods 0.000 description 1
- 230000008602 contraction Effects 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 239000010419 fine particle Substances 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 150000002484 inorganic compounds Chemical class 0.000 description 1
- 229910010272 inorganic material Inorganic materials 0.000 description 1
- 239000000314 lubricant Substances 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 230000035515 penetration Effects 0.000 description 1
- 239000012071 phase Substances 0.000 description 1
- 230000002265 prevention Effects 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 238000009736 wetting Methods 0.000 description 1
Landscapes
- Manufacture Of Alloys Or Alloy Compounds (AREA)
Abstract
Description
【発明の詳細な説明】
(産業上の利用分野)
この発明は、アルミニウム金属をマトリ7クスとし、こ
れを強化材で部分複合化させるアルミニウム基複合部材
の製造方法に関するものである。DETAILED DESCRIPTION OF THE INVENTION (Industrial Application Field) The present invention relates to a method for manufacturing an aluminum matrix composite member in which aluminum metal is used as a matrix and the matrix is partially composited with a reinforcing material.
(従来の技術)
従来、アルミニウム金属を部分強化する手段の一つとし
て繊維体を複合化させる高圧鋳造法が知られている。(Prior Art) Conventionally, a high-pressure casting method in which a fiber body is composited is known as one of the means for partially reinforcing aluminum metal.
この方法ではSiC,5iaN4などの短繊維を成形し
て繊維体を製造し、この繊維体を鋳型内に配置してアル
ミニウム金属溶湯を注入するとともに、加圧して鋳造す
る。アルミニウム金属溶湯は加圧により繊維体中に含浸
して、繊維体とアルミニウム金属とが複合一体止される
。In this method, short fibers such as SiC, 5iaN4, etc. are molded to produce a fibrous body, the fibrous body is placed in a mold, molten aluminum metal is injected, and the mold is cast under pressure. The molten aluminum metal is impregnated into the fibrous body under pressure, and the fibrous body and the aluminum metal are integrally bonded.
(発明か解決しようとする課題)
しかしなから、従来の高圧鋳造法によれば、アルミニウ
ム金属溶湯の含浸に際し、アルミニウム金属と繊維との
ある種反応などにより成分偏析を生じ、組織欠陥の原因
になるという問題点があり、これに対しては一方向加圧
により反応部を系外に排出する方法か提案されている(
特開昭62−238062号)。(Problem to be solved by the invention) However, according to the conventional high-pressure casting method, when impregnating molten aluminum metal, component segregation occurs due to a certain reaction between aluminum metal and fibers, which causes structural defects. To solve this problem, a method has been proposed in which the reaction part is discharged from the system by unidirectional pressurization (
JP-A No. 62-238062).
しかし、この方法においても、成分偏析の防止は十分で
はなく(反応部と未反応部との境界も明確てはない)、
また歩留りが低下するという問題点かある。However, even with this method, prevention of component segregation is not sufficient (the boundary between the reacted part and the unreacted part is not clear),
Another problem is that the yield is reduced.
さらに、高圧鋳造法では、含浸時に繊維体の収縮を伴う
ことがあり、V5 (繊維体容積比)のコントロールが
困難であり、また繊維体の相対密度が高い場合には溶湯
の含浸は困難となる。特に溶湯と繊維との濡れ性が悪い
場合には、困難性はより顕著となり、繊維体の種別など
の制約が大きいという問題点がある。Furthermore, in the high-pressure casting method, the fiber body may shrink during impregnation, making it difficult to control V5 (fiber volume ratio), and impregnation with molten metal may be difficult when the relative density of the fiber body is high. Become. In particular, when the wettability between the molten metal and the fibers is poor, the difficulty becomes more pronounced, and there is a problem in that there are significant restrictions such as the type of fiber body.
また粒子状の強化材によりグリフ1−ム体を成形する場
合には、プリフォーム体の強化材密度が高いなめ、溶湯
の含浸は困難であり、事実上、粒子状強化材を使用する
ことは困難である。Furthermore, when forming a glyph body using particulate reinforcing material, impregnation with molten metal is difficult due to the high density of the reinforcing material in the preform, and in fact, it is impossible to use particulate reinforcing material. Have difficulty.
以上のように、高圧鋳造法では繊維体への含浸を達成す
るために、例えば1000kg/cJ以上の高圧が必要
とされ、大型の設備を要し、設備費がかさむという問題
点もある。As described above, the high-pressure casting method requires a high pressure of, for example, 1000 kg/cJ or more to achieve impregnation into the fibrous body, requiring large-sized equipment and increasing equipment costs.
この発明は、上記問題点を解決することを基本的な目的
とし、強化材の選択の制約か少なくて、組織欠陥のない
複合部材を歩留りよく得られるアルミニウム基複合部材
の製造方法を提供するものである。The basic objective of the present invention is to solve the above problems, and to provide a method for producing an aluminum matrix composite member that has fewer restrictions on the selection of reinforcing materials and can produce composite members without structural defects at a high yield. It is.
(課題を解決する為の手段)
上記目的を達成するため本願発明のアルミニウム基複合
部材の製造方法は、アルミニウム金属粉末と、強化材と
を混合して所定形状に成形し、この成形体を予備加熱し
て鋳型内に配置しておき、次いで鋳型内に複合部材のマ
トリックスとなるアルミニウム金属溶湯を注湯して加圧
鋳造することを特徴とするものである。(Means for Solving the Problems) In order to achieve the above object, the method for manufacturing an aluminum matrix composite member of the present invention includes mixing aluminum metal powder and a reinforcing material and molding the mixture into a predetermined shape, and preparing this molded body. It is characterized in that it is heated and placed in a mold, and then molten aluminum metal, which will become the matrix of the composite member, is poured into the mold and pressure cast.
なお、成形体の予備加熱温度は、粉末用アルミニウム金
属の固相線温度以上とするのが望ましい。Note that it is desirable that the preheating temperature of the compact be equal to or higher than the solidus temperature of the powdered aluminum metal.
上記のアルミニウム金属粉末は、原材料として、アルミ
ニウム合金は勿論のこと、純アルミニウムを用いること
も可能であり、しかもアルミニウム合金の種別が特に制
限されるものでのではなく、複合部材の目的などに応じ
適宜選択することができる。例えば一般用展伸材である
JIS6061合金やAC8AC12JIS2024合
金などを用いる。For the above aluminum metal powder, not only aluminum alloy but also pure aluminum can be used as a raw material, and there are no particular restrictions on the type of aluminum alloy, and it can be used depending on the purpose of the composite member etc. It can be selected as appropriate. For example, JIS6061 alloy, AC8AC12JIS2024 alloy, etc., which are general wrought materials, are used.
このように種別が定められたアルミニウム金属を、粉化
する方法も特に限定されるものではなく、従来用いられ
ている機械的粉砕法や物理化学的製粉法などの各種方法
を用いることができる。しかも得られた金属粉には酸化
被膜か形成されていてもよいので、不活性カスを用いた
高価なアトマイズ粉などを用いなければならない必要性
□はなく、原材料の制限が少ない。また製造されたアル
ミニウム金属粉の形状は、片状、針状などでもよいが、
高密度を得るように球状、もしくはその変形であるもの
(例えば細球形)が好ましい。またその粒度は、強度、
WA摩耗性に優れた複合部材を得たいような場合には0
.1〜100IfIR程度とし、潤滑性に優れた材料を
得たい場合には200珈〜ll11m程度とするのが望
ましいが、この範囲に限定されるものではない。The method of pulverizing the aluminum metal whose type has been determined in this way is not particularly limited, and various methods such as conventionally used mechanical pulverization methods and physicochemical pulverization methods can be used. Moreover, since an oxide film may be formed on the obtained metal powder, there is no need to use expensive atomized powder using inert dregs, and there are fewer restrictions on raw materials. In addition, the shape of the produced aluminum metal powder may be flaky, acicular, etc.
In order to obtain high density, a spherical shape or a modified shape thereof (for example, a slender spherical shape) is preferable. In addition, the particle size is determined by strength,
WA 0 if you want to obtain a composite member with excellent wear resistance.
.. If IR is about 1 to 100 IfIR, and if a material with excellent lubricity is desired, it is preferably about 200 to 111 m, but it is not limited to this range.
以上説明したアルミニウム金属粉末と混合する強化材と
しては、強化粒子や繊維材料を用いる。As the reinforcing material to be mixed with the aluminum metal powder described above, reinforcing particles or fiber materials are used.
強化粒子としては、AI 203などに代表されるセラ
ミック粉末などの無機物や他種金属などを用いるが、そ
の形状、粒度は限定されず、2種以上のものでもよい。As the reinforcing particles, inorganic substances such as ceramic powder such as AI 203 and other metals are used, but the shape and particle size are not limited, and two or more types may be used.
例えば粒度としては0.5〜10−5 = 珈程度とする。For example, the particle size is 0.5 to 10-5 = It should be about the same level as coffee.
繊維材料としては、SiC,5iaN+などの短繊維、
長繊維があり、さらに雲母、黒鉛、AI 20 a、F
e20aなどの無機化合物、W、「eなどの金属を用い
ることができる。また繊維は単結晶(ウィスカー)、多
結晶であることを問わす、非晶質のものであってもよい
。As fiber materials, short fibers such as SiC, 5iaN+, etc.
Contains long fibers, as well as mica, graphite, AI 20 a, F
Inorganic compounds such as e20a and metals such as W and e can be used.Furthermore, the fiber may be single crystal (whisker), polycrystalline, or amorphous.
上記したアルミニウム金属と強化材との混合比は、限定
されないが、強化材の容積比が5〜60%となるように
混合するのが望ましい。この混合においては、潤滑剤や
結合剤などを添加してもよく、ボールミルなどを用いて
均一に撹拌混合する。The mixing ratio of the above-mentioned aluminum metal and the reinforcing material is not limited, but it is desirable that they be mixed so that the volume ratio of the reinforcing material is 5 to 60%. In this mixing, a lubricant, a binder, etc. may be added, and the mixture is uniformly stirred using a ball mill or the like.
なお、この撹拌混合では、強化粒子の凝集材を分解する
ことができ、しかもアルミニウム金属粉末の粉砕を伴わ
ない程度の撹拌力による混合条件が必要である。Note that this stirring and mixing requires a mixing condition with a stirring force that is capable of decomposing the agglomerated material of the reinforcing particles and does not involve pulverization of the aluminum metal powder.
このようにして得られた混合粉は、所定形状に成形する
。The mixed powder thus obtained is molded into a predetermined shape.
この成形は冷間、温間を問わないものであり、温間では
100〜400℃(好ましくは再結晶温変態−1ユて2
00〜300°C)の範囲て加熱し、さらに所望により
相対密度が60%以上(好ましくは65%以−4−)と
なるように加圧成形する。この相対密度か小さいと、形
崩れを生しやすく、取扱いか難しくなる。但し、相対密
度を大きくするために加圧力を増大させると、アルミニ
ウム金属粉末か塑性変形なとする。このなめ所望により
生成さぜな表面の酸化被膜が破壊されてしまう。しなか
って必要以−トに相対密度を高めるのは望ましくなく、
85%以干程度とするのが望ましい(より好ましくは7
5%以下)。このように密度が増加した成形体は保管や
移送が容易となる。また成形体は一体物てよいことは勿
論てあろが、複数の分割成形体としておくことも可能で
ある。This molding is carried out regardless of whether it is cold or warm; warm temperatures are preferably 100 to 400°C (preferably recrystallization temperature transformation -1 to 2
00 to 300[deg.] C.) and, if desired, pressure molded so that the relative density becomes 60% or more (preferably 65% or more -4-). If this relative density is low, it will easily lose its shape and will be difficult to handle. However, if the pressing force is increased to increase the relative density, the aluminum metal powder will be plastically deformed. This licking process destroys the oxidized film on the surface that has not yet been formed. It is undesirable to increase the relative density more than necessary without doing so.
It is desirable to set it to about 85% or more (more preferably 7
5% or less). A molded article with increased density can be easily stored and transported. The molded body may of course be an integral body, but it is also possible to form a plurality of divided molded bodies.
この成形体は、成形用型1ノ東もしくは成形用型外部に
おいて予備加熱する。また、この予備加熱は、予備加熱
用の型や後述する鋳型内で行なうことも可能である。This molded body is preheated in the mold 1 or outside the mold. Moreover, this preheating can also be performed in a preheating mold or a mold described later.
さらに、予備加熱の温度は、具体的には300°C以−
1−程度とし、好ましくは粉末用アルミニウム= 7−
金属の固相線温度以上とする。また、固液共存域さらに
、液相線温度以上の場合でも、アルミニウム金属粉末の
表面が酸化被膜で覆われノご状態を維持することにより
、同様に定形性か保ノコれる。したかって、液相線温度
U、上で予備加熱する場合には、酸化膜を維持てきる温
度、例えば液相線温度+(20〜150°C)程度で加
熱する。Furthermore, the preheating temperature is specifically 300°C or higher.
The temperature should be approximately 1-1, preferably at least the solidus temperature of powder aluminum = 7-metal. In addition, even in the solid-liquid coexistence region and even at temperatures above the liquidus line, the surface of the aluminum metal powder is covered with an oxide film and maintains the sawn state, thereby maintaining its shape. Therefore, when preheating is performed above the liquidus temperature U, heating is performed at a temperature that maintains the oxide film, for example, about the liquidus temperature + (20 to 150° C.).
上記成形体を鋳型内に配置し7て、複合部材のマ)・リ
ックスとなるアルミニウム金属溶湯を注湯する。鋳型内
への成形体の配置は、前述した分割成形体の設置により
行なうことも可能である。また所望により複数部位を強
化すべく、複数箇所に成形体を配置することもできる。The molded body is placed in a mold and molten aluminum metal, which will become the matrix of the composite member, is poured into the mold. The molded body can also be placed in the mold by installing the divided molded body as described above. Further, molded bodies can be placed at multiple locations in order to strengthen multiple locations as desired.
この場合、成形体は同一のものを複数配置することも可
能であるが、粉末用アルミニウム金属、強化材、密度、
形状などを代えた異種の成形体を配置することも可能で
ある。In this case, it is possible to arrange multiple identical molded bodies, but powder aluminum metal, reinforcing material, density,
It is also possible to arrange different types of molded bodies with different shapes.
次に前記71〜リツクス用アルミニウム金属には、一般
に成形体における粉末用アルミニウム金属と同種のもの
を用いるか、これとは異なり異種のアルミニウム金属を
用いることも可能である。このマトリックス川アルミニ
ウム金属は、自身の液相線温度+50〜150°Cに加
熱して溶湯とする。Next, as the aluminum metal for the 71~Rix, it is generally possible to use the same kind of aluminum metal as the powdered aluminum metal in the compact, or it is also possible to use a different kind of aluminum metal. This matrix aluminum metal is heated to its own liquidus temperature +50 to 150°C to form a molten metal.
具体的には、例えばJIS6061合金では750°C
程度とする。Specifically, for example, JIS6061 alloy has a temperature of 750°C.
degree.
上記の溶湯を鋳型内に注湯して加圧鋳造をする際の加圧
力は、71〜リンクスのアルミニウム金属溶湯の凝固時
に必要な加圧力で、500kg/−以−1−とするのが
望ましい。たたし、マトリックスのアルミニウム金属溶
湯が成形体内部にまで含浸する必要はない。The pressure when pouring the above molten metal into a mold and performing pressure casting is the pressure required for solidifying the molten aluminum metal of 71 to Lynx, and is preferably 500 kg/- or more. . However, it is not necessary that the molten aluminum metal of the matrix impregnates the inside of the molded body.
なお、成形体の表面に酸化被膜が形成されていて、この
成形体を粉末用アルミニウム金属の固相線温変態」ニー
、望ましくは液相線温度以上に加熱した場合には、前記
加圧力はアルミニニウム金属粉末の酸化被膜内の溶湯か
酸化被膜外へ排出される圧力以上とするのが望ましい。Note that if an oxide film is formed on the surface of the compact and the compact is heated to a temperature above the solidus temperature of the aluminum metal powder, preferably above the liquidus temperature, the pressing force will be It is desirable that the pressure be higher than the pressure at which the molten metal within the oxide film of the aluminum metal powder is discharged to the outside of the oxide film.
(発明の作用)
この発明によれば、成形体を鋳型内に配置して加圧鈎造
することにより、成形体と71〜リンクスとの界面近傍
でマトリックスのアルミニウム金属溶湯による浸透が生
じ、さらに、この溶湯と成形体のアルミニウム金属粉末
が溶解した溶湯とが混合し、成形体と71へリックスと
か高強度を有する状態て接合されて複合一体止する。(Function of the invention) According to the present invention, by placing the molded body in a mold and pressurizing the molded body, penetration by the molten aluminum metal of the matrix occurs near the interface between the molded body and the links 71 to 71. This molten metal and the molten metal in which the aluminum metal powder of the molded body has been melted are mixed, and the molded body and the molded body are joined in a high-strength state such as a 71 helix to form a composite body.
なお、成形体をアルミニウム金属粉末の固相線以下の温
度て予備加熱した場合にもマトリックスの溶湯と接触し
た成形体界面付近の温度がアルミニウム金属粉末の同相
線温度以上となれは、アルミニウム金属粉末の一部は溶
解し、又、粉末が酸化膜て覆われているときにも加圧に
より酸化膜か破られ、溶解したアルミニウム金属が周囲
の空洞を埋めるとともに、強化材を濡らして複合化か達
成される。従って、成形体のアルミごニウム金属粉末と
7トリンクスのアルミニウム金属溶湯が成形体とマトリ
ックスとの界面近傍で混合することになる。In addition, even if the compact is preheated at a temperature below the solidus line of the aluminum metal powder, if the temperature near the interface of the compact in contact with the molten metal of the matrix exceeds the homophase line temperature of the aluminum metal powder, the aluminum metal powder Part of the aluminum metal melts, and even when the powder is covered with an oxide film, the oxide film is broken by pressure, and the melted aluminum metal fills the surrounding cavity and wets the reinforcing material to form a composite. achieved. Therefore, the aluminum metal powder of the compact and the molten aluminum metal of 7 Trinks mix near the interface between the compact and the matrix.
なお、成形体の大部分(成形体内部)では、71〜リツ
クスのアルミニウム金属溶湯の含浸はほとんどない。成
形体内部ては、成形体をアルミごニラム金属粉末の固相
線温度以上に加熱することにより、又、固相線未満であ
っても、マトリックスのアルミニウム金属溶湯からの伝
熱により成形体のアルミニウム金属粉末が固相線温度具
−Fとなり、粉末のアルミニウム金属の溶湯が周囲の強
化材を濡らし、成形体内部でも複合化か生ずる。In addition, in most of the molded body (inside the molded body), there is almost no impregnation with molten aluminum metal having a thickness of 71 to 60. Inside the molded body, the molded body is heated to a temperature higher than the solidus temperature of the aluminum nilum metal powder, or even if the temperature is lower than the solidus temperature, the molded body is heated by heat transfer from the molten aluminum metal in the matrix. The aluminum metal powder becomes a solidus temperature tool-F, and the molten aluminum metal powder wets the surrounding reinforcing material, and compounding also occurs inside the compact.
また、成形体を粉末用アルミニウム金属の液相線温度以
上に加熱する場合には、アルミニウム金属粉末の表面を
酸化被膜で覆われた状態としておく。すなわち、予備加
熱前、または加熱に従い酸化被膜を形成する。Further, when the compact is heated to a temperature higher than the liquidus temperature of the aluminum metal powder, the surface of the aluminum metal powder is left covered with an oxide film. That is, an oxide film is formed before preheating or during heating.
この発明の実施にあたっては、酸化膜の厚さか適当とな
るように粉体製造時の雰囲気や、製造後の管理状筋を調
整することも可能であり、また液相線に達するまでの予
備加熱制御により酸化被膜の厚さを調整することもでき
る。成・形体をアルミニウム金属の液相線以上の温度で
加熱することにより、成形体における酸化被膜で覆われ
たアルミニウム金属が溶融する。一方、酸化被膜は液相
状態とならないように加熱する。従ってアルミニラム金
属粉末の単体では内部のアルミニウム金属のみが溶融し
た状態にあり、各単体の独立性か維持される。さらに加
圧鋳造により成形体も加圧され、酸化被膜が破壊されて
内部の溶融金属が浸出する。In implementing this invention, it is possible to adjust the atmosphere during powder production and the control pattern after production so that the thickness of the oxide film is appropriate, and it is also possible to adjust the preheating until the liquidus is reached. The thickness of the oxide film can also be adjusted through control. By heating the molded body at a temperature equal to or higher than the liquidus line of the aluminum metal, the aluminum metal covered with the oxide film in the molded body is melted. On the other hand, the oxide film is heated so as not to enter a liquid phase. Therefore, in a single unit of aluminum aluminum metal powder, only the internal aluminum metal is in a molten state, and the independence of each unit is maintained. Furthermore, the molded body is also pressurized by pressure casting, the oxide film is destroyed, and the molten metal inside leaches out.
溶融金属は流動性に富んでおり、アルミニウム金属粉末
と強化材との隙間に効率よくしみ込んで、アルミニウム
金属粉体と強化材とを強制的に濡れさせる。また成形体
内に残存していた空気や加熱により発生ずるカスを成形
体外部に強制排除し、気孔の発生を阻止して相対密度の
高い複合材が得られる。前記加圧では、加圧力を一定も
しくは変化させて、アルミニウム金属か凝固するまで続
行させることにより、凝固収縮による気孔などの発生を
阻止できる。すなわち初期の加圧力は酸化被膜破壊によ
る複合化に必要な大きさが求められ、その後は凝固収縮
による気孔発生を阻止する加圧力が必要とされる。The molten metal has high fluidity and efficiently penetrates into the gap between the aluminum metal powder and the reinforcing material, forcibly wetting the aluminum metal powder and the reinforcing material. In addition, the air remaining in the molded body and the scum generated by heating are forcibly removed to the outside of the molded body, thereby preventing the formation of pores and yielding a composite material with a high relative density. In the pressurization, the pressurization force is kept constant or varied and is continued until the aluminum metal solidifies, thereby preventing the generation of pores due to solidification shrinkage. That is, the initial pressure is required to be large enough to cause the oxide film to break down into a composite material, and thereafter the pressure to prevent the formation of pores due to solidification and contraction is required.
なお、破壊された酸化被膜は、微細粒子として強度向上
に寄与する。Note that the destroyed oxide film contributes to improving the strength as fine particles.
以上のように、成形体が複合化されて、この複合材にり
マトリックスのアルミニウム金属か部分複合化されて複
合部材が得られる。As described above, the molded body is composited, and the aluminum metal of the matrix is partially composited with this composite material to obtain a composite member.
(実施例1)
以下にこの発明の一実施例を第1図に基づいて説明する
。(Example 1) An example of the present invention will be described below based on FIG. 1.
JIS6061アルミニウム合金をエアーアトマイズ法
により、平均粒径40珈のアルミニウム金属粉末とし、
この粉末600gと繊維長が10〜30珈で繊維径か0
.4IJRであるSiCウィスカー200gとをボール
ミル1によりアルコール溶済中で均一に混合した。JIS6061 aluminum alloy is made into aluminum metal powder with an average particle size of 40 c by the air atomization method,
With 600 g of this powder and fiber length of 10 to 30 fibers, the fiber diameter is 0.
.. 4IJR and 200 g of SiC whiskers were uniformly mixed in an alcohol solution using a ball mill 1.
この混合粉2を成形用型3内に、収容して300°Cに
加熱し、100kg/cJの圧力で加圧して相対密度6
8%の成形体4を得た。This mixed powder 2 was placed in a mold 3, heated to 300°C, and pressurized with a pressure of 100 kg/cJ to have a relative density of 6.
A molded body 4 of 8% was obtained.
この成形体4を成形用型3から取り出して予め350°
Cに加熱しておいた鋳型5内に配置して、さらにこの成
形体4を350°Cに加熱する予備加熱を行った。This molded body 4 is taken out from the mold 3 and preliminarily rotated at 350°.
The molded body 4 was placed in a mold 5 that had been heated to 350° C., and preheated to 350° C.
次いでこの鋳型5内に750’Cに加熱しなJIS60
61アルミニウム合金からなるマトリックス用アルミニ
ウム金属溶湯6を注湯し、雄型7により1000kg/
−の圧力で加圧鋳造した。Next, heat JIS60 to 750'C in this mold 5.
A molten aluminum metal 6 for the matrix made of 61 aluminum alloy is poured, and a male mold 7 is used to weigh 1000 kg/
Pressure casting was carried out at a pressure of -.
得られた複合部材は、マトリックスの溶湯6が成形体4
の界面部で含浸して接合強度が向上しており、また強化
材を配した部位内での成分偏析なとも生ずることなく耐
熱性、耐摩耗性に優れた特性を有していた。さらに熱膨
張率が低く、ヤング率、強度とも高い特性を有しており
、高温での強度などが要求される内燃機関用のピストン
などに好適の材料か得られた。In the obtained composite member, the molten metal 6 of the matrix forms the molded body 4.
The bonding strength was improved by impregnating the reinforcing material at the interface, and it had excellent heat resistance and wear resistance without causing component segregation within the region where the reinforcing material was placed. Furthermore, the material has a low coefficient of thermal expansion, high Young's modulus, and high strength, making it suitable for pistons for internal combustion engines that require strength at high temperatures.
なお、本実施例の複合部材の熱膨張率を評価するため、
JIS6061アルミニウム合金を比較例1として、熱
膨張率を測定する実験を行った。その結果は第1表に示
す通りである。In addition, in order to evaluate the thermal expansion coefficient of the composite member of this example,
An experiment was conducted to measure the coefficient of thermal expansion using a JIS6061 aluminum alloy as Comparative Example 1. The results are shown in Table 1.
は、比較例1に対し、熱膨張率の低減か顕著である。Compared to Comparative Example 1, the coefficient of thermal expansion was significantly reduced.
(実施例2)
次に他の実施例を以下に説明する。JIS2024アル
ミニウム合金を常法により401Mの粒径を有するアル
ミニウム金属粉末とし、この粉末700gと、0.5間
の粒径を有するAl 203粒子300gとをボールミ
ルにより均一となるように乾式混合した。(Example 2) Next, another example will be described below. A JIS 2024 aluminum alloy was made into aluminum metal powder having a particle size of 401M by a conventional method, and 700 g of this powder and 300 g of Al 203 particles having a particle size of between 0.5 and 300 g were dry-mixed uniformly using a ball mill.
この混合粉を成形用型内で、前記実施例同様に加熱、加
圧して相対密度71%の成形体を得た。This mixed powder was heated and pressurized in a mold in the same manner as in the previous example to obtain a molded body with a relative density of 71%.
成形体は成形用型内から取り出して、JIS2024合
金の液相′l&温度以変態である700°Cに加熱する
予備加熱を行−2な。この加熱の際に、アルミニウム金
属粉末は酸化膜で覆われた状態にあり、粉末中休の内部
か溶湯状態であっても成形体の定形性は損われず、鋳型
内に収納するハンドリンクの際にも形崩れは生じなかっ
た。The molded body is taken out of the mold and preheated to 700°C, which is the temperature above the liquid phase of the JIS2024 alloy. During this heating, the aluminum metal powder is covered with an oxide film, and even if it is inside the powder or in the molten state, the shape of the compact is not impaired, and the hand links stored in the mold are not affected. No deformation occurred at this time.
次いで前記実施例と同様にして、750°Cに加熱しな
JIS2024合金からなる溶湯を鋳型内に注湯して5
00kg/cJの圧力て加圧鋳造を行ったにの実施例で
は、アルミニウム金属粉末の酸化被膜内溶湯か強化材間
に浸透して成形体の結合性を向上させる。得られた複合
部材は、前記実施例と同様に耐熱性、耐摩耗性などの胚
特性に優れていた。Next, in the same manner as in the previous example, a molten metal made of JIS 2024 alloy that was not heated to 750°C was poured into the mold.
In the example in which pressure casting was performed at a pressure of 0.00 kg/cJ, the molten aluminum metal powder in the oxide film penetrated between the reinforcing materials to improve the bonding properties of the compact. The obtained composite member had excellent embryonic properties such as heat resistance and abrasion resistance as in the above example.
(実施例3)
次に成形体の予備加熱温度を変えて3種の複合部材を製
造した。(Example 3) Next, three types of composite members were manufactured by changing the preheating temperature of the molded body.
この実施例を以Tに説明する。This embodiment will be explained below.
JISAC8Aアルミニウム合金を常法により平均粒径
40虜のアルミニウム合金粉末とし、この粉末560g
と、1.7IERの粒径を有するへ120B粒子240
gとをボールミルにより均一に乾式混合した。JISAC8A aluminum alloy was made into aluminum alloy powder with an average particle size of 40 mm by a conventional method, and 560 g of this powder was prepared.
and 240 to 120B particles with a particle size of 1.7 IER.
g were uniformly dry mixed using a ball mill.
この混合粉を成形用型内に収容し、冷間て200hg/
a’&の圧力で加圧して成形体を得た。This mixed powder was placed in a mold and cooled at 200hg/
A molded article was obtained by pressing at a pressure of a'&.
この成形体を3個用意して、その1つの成形体AをJI
SAC8八アルミニ八人ルミニウム合金度(S1゛)と
液相線温度(LT)との間の固液共存域温度以干である
550’Cて予備加熱し、他の1つの成形体Bを液相線
温度量−Lの600°Cて予備加熱し、さらに他の1つ
の成形体Cを同じく液相線温度以上である650°Cで
予備加熱をした。Three of these molded bodies are prepared, and one of them, molded body A, is
The other compact B is preheated to 550'C, which is higher than the solid-liquid coexistence region temperature between the SAC8 aluminum alloy degree (S1゛) and the liquidus temperature (LT). It was preheated at 600°C, which is the phase line temperature -L, and another molded body C was also preheated at 650°C, which was also above the liquidus temperature.
これら成形体A、BおよびCをそれぞれ鋳型に収容し、
750℃に加熱したJISAC8八合金からなる溶湯を
鋳型内に注湯して、500kg/−の圧力で加圧鋳造を
行った。得られた複合部材は、成形体Aを用いたものを
実施例3Aとし、成形体Bを用いたものを実施例3Bと
し、成形体Cを用いたものを実施例3Cとした。These molded bodies A, B, and C are each housed in a mold,
Molten metal made of JISAC88 alloy heated to 750°C was poured into a mold, and pressure casting was performed at a pressure of 500 kg/-. The resulting composite members used molded body A as Example 3A, molded body B as Example 3B, and molded body C as Example 3C.
次にこれら実施例の複合部材を用いて、引張強度および
ヤング率を測定する実験を行った。その結果を図示する
と第2図の通りであり、引張強度、ヤング率ともに良好
な結果が得られた。Next, experiments were conducted to measure tensile strength and Young's modulus using the composite members of these Examples. The results are shown in Figure 2, and good results were obtained in both tensile strength and Young's modulus.
なお、引張強度においては実施例3A、3B、30間で
有意差は認められなかったが、ヤング率においては、実
施例3Aよりも実施例3Bが、実施例3Bよりも実施例
3Cがより優れていた。Although no significant difference was observed between Examples 3A, 3B, and 30 in terms of tensile strength, in terms of Young's modulus, Example 3B was superior to Example 3A, and Example 3C was superior to Example 3B. was.
次に、前記実施例3A、3B、3Cの組織状態を観察し
たところ、実施例3Aでは、成形体Aによる複合材の内
部にボイドか見られ、相対密度も90%に満なない程度
であった。実施例3Bでは実施例3Aよりもボイドが少
なく、相対密度も高かったが、実施例3Cではボイドは
殆んど、又は全く存在せず、相対密度もほぼ100%と
なった。Next, when the structural states of Examples 3A, 3B, and 3C were observed, it was found that in Example 3A, voids were observed inside the composite material made of compact A, and the relative density was also less than 90%. Ta. Example 3B had fewer voids and a higher relative density than Example 3A, whereas Example 3C had few or no voids and a relative density of almost 100%.
これは予備加熱温度か高い方か、アルミニウム金属粉末
と強化材との濡れ性か向上するためと思われる。This seems to be due to the higher preheating temperature or the improved wettability between the aluminum metal powder and the reinforcing material.
又、上記組織状態の差異によりヤング率においても差異
か生じたものと思われる。It is also believed that the difference in Young's modulus was caused by the difference in the structure state.
次に、実施例の熱膨張係数を評価するため、JISAC
8^アルミニウム合金を比較例3として、熱膨張率を測
定したところ、第2表に示されるように比較例3は20
.1 X 10−6(’C”1)であるのに対し、実施
例3A、3B、3Cは、15〜17×10’ (’C−
1>の範囲にあり、いずれも熱膨張率の低減効果か大き
いという結果か得られた。なお、実施例間では、実施例
3Cか最も低減効果が大きく、実施例3Aが低減効果が
小さいという傾向が見られた。Next, in order to evaluate the thermal expansion coefficient of the example, JISAC
8^ When the thermal expansion coefficient was measured using aluminum alloy as Comparative Example 3, as shown in Table 2, Comparative Example 3 was 20.
.. 1 x 10-6 ('C"1), whereas Examples 3A, 3B, and 3C have 15-17 x 10'('C-
1>, and both results showed that the effect of reducing the coefficient of thermal expansion was large. Note that among the Examples, there was a tendency that Example 3C had the largest reduction effect, and Example 3A had the smallest reduction effect.
第2表
(発明の効果)
以上説明したように、この発明によれば、アルミニウム
金属粉末と、強化材とを混合して所定形状に成形し、こ
の成形体を予備加熱して鋳型内に配置しておき、次いで
鋳型内にマトリックスとなるアルミニウム金属溶湯を注
湯して加圧鋳造するので、鋳造時の圧力の必要値は低く
、加圧設備費用を低減できる。さらに、強化材の種別な
どの制約も少ないという効果か得られる。Table 2 (Effects of the Invention) As explained above, according to the present invention, aluminum metal powder and a reinforcing material are mixed and molded into a predetermined shape, and this molded product is preheated and placed in a mold. Then, the molten aluminum metal that becomes the matrix is poured into the mold and pressure cast is performed, so the required pressure during casting is low and the cost of pressurizing equipment can be reduced. Furthermore, there are fewer restrictions on the type of reinforcing material.
また、成形体とマトリックスとの接合性が良好であり、
接合部の強度特性に優れている。得られた複合部材は、
強化材を配した部位で成分偏析などが生することもなく
、均一な組織状態か得られ、耐熱性、耐摩耗性に優れて
おり、さらに熱膨脹率が低くてヤング率、強度とも高い
特性か得られるという効果かある。In addition, the bondability between the molded body and the matrix is good,
Excellent strength characteristics of joints. The obtained composite member is
There is no component segregation in the areas where the reinforcing material is placed, a uniform structure is obtained, and it has excellent heat resistance and abrasion resistance. Furthermore, it has a low coefficient of thermal expansion, and has high Young's modulus and strength. There is an effect that can be obtained.
また、成形体の予備加熱温度は、粉末用アルミニウム金
属の固相線温度以上とずれは、粉末用アルミニウム金属
溶湯の強化材間での浸透により強化材の結合性が向上す
るという効果がある。Furthermore, if the preheating temperature of the compact is deviated from the solidus temperature of the powdered aluminum metal, the molten aluminum powder will penetrate between the reinforcing materials, thereby improving the bonding properties of the reinforcing materials.
第1図はこの発明の一実施例を示す工程図、第2図は実
施例3A、3B、3Cの機械的特性を示すグラフである
。
2・・・混合粉
4・・・成形体
5・・・鋳型FIG. 1 is a process diagram showing one embodiment of the present invention, and FIG. 2 is a graph showing mechanical properties of Examples 3A, 3B, and 3C. 2...Mixed powder 4...Molded body 5...Mold
Claims (1)
定形状に成形し、この成形体を予備加熱して鋳型内に配
置しておき、次いで、鋳型内に複合部材のマトリックス
となるアルミニウム金属溶湯を注湯して加圧鋳造するこ
とを特徴とするアルミニウム基複合部材の製造方法 2 成形体の予備加熱温度は、粉末用アルミニウム金属
の固相線温度以上とした請求項1記載のアルミニウム基
複合部材の製造方法[Claims] 1. Aluminum metal powder and reinforcing material are mixed and molded into a predetermined shape, this molded body is preheated and placed in a mold, and then a composite member is placed in the mold. A method for manufacturing an aluminum matrix composite member 2, characterized in that molten aluminum metal serving as a matrix is poured and pressure cast.Claim 2: The preheating temperature of the compact is equal to or higher than the solidus temperature of the aluminum metal for powder. Method for manufacturing an aluminum matrix composite member according to 1.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP11308588A JPH01283330A (en) | 1988-05-10 | 1988-05-10 | Manufacture of aluminum-based composite member |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP11308588A JPH01283330A (en) | 1988-05-10 | 1988-05-10 | Manufacture of aluminum-based composite member |
Publications (1)
Publication Number | Publication Date |
---|---|
JPH01283330A true JPH01283330A (en) | 1989-11-14 |
Family
ID=14603102
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP11308588A Pending JPH01283330A (en) | 1988-05-10 | 1988-05-10 | Manufacture of aluminum-based composite member |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPH01283330A (en) |
Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0768133A2 (en) * | 1995-10-09 | 1997-04-16 | Ahresty Corporation | Method of reforming surface of cast product |
JPH09157772A (en) * | 1995-02-22 | 1997-06-17 | Mazda Motor Corp | Production of partial composite light metal parts and preform used for the same |
KR100471649B1 (en) * | 2002-09-27 | 2005-03-08 | 국방과학연구소 | High damping aluminum matrix composite |
CN104831099A (en) * | 2015-04-07 | 2015-08-12 | 苏州阿罗米科技有限公司 | Preparation method of aluminum-carbon composite material |
-
1988
- 1988-05-10 JP JP11308588A patent/JPH01283330A/en active Pending
Cited By (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH09157772A (en) * | 1995-02-22 | 1997-06-17 | Mazda Motor Corp | Production of partial composite light metal parts and preform used for the same |
EP0768133A2 (en) * | 1995-10-09 | 1997-04-16 | Ahresty Corporation | Method of reforming surface of cast product |
EP0768133A3 (en) * | 1995-10-09 | 1998-11-11 | Ahresty Corporation | Method of reforming surface of cast product |
KR100471649B1 (en) * | 2002-09-27 | 2005-03-08 | 국방과학연구소 | High damping aluminum matrix composite |
CN104831099A (en) * | 2015-04-07 | 2015-08-12 | 苏州阿罗米科技有限公司 | Preparation method of aluminum-carbon composite material |
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