JPH0830228B2 - Method for producing ceramic-metal composite - Google Patents
Method for producing ceramic-metal compositeInfo
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- JPH0830228B2 JPH0830228B2 JP62149749A JP14974987A JPH0830228B2 JP H0830228 B2 JPH0830228 B2 JP H0830228B2 JP 62149749 A JP62149749 A JP 62149749A JP 14974987 A JP14974987 A JP 14974987A JP H0830228 B2 JPH0830228 B2 JP H0830228B2
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Description
【発明の詳細な説明】 ［産業上の利用分野］ 本発明はセラミック−金属複合体の製造方法に関し、
一層詳細には、セラミック粉末と酸により溶出される気
孔形成粉末との混合粉末により成形体を得て後、前記成
形体に焼成および溶出処理を施して三次元網目構造を呈
するセラミック焼結体を形成し、さらに前記セラミック
焼結体に溶融金属を加圧充填して耐摩耗性および耐熱性
等に優れた複合体を得ることを可能にしたセラミック−
金属複合体の製造方法に関する。The present invention relates to a method for producing a ceramic-metal composite,
More specifically, after a molded body is obtained from a mixed powder of ceramic powder and pore-forming powder that is eluted by an acid, the molded body is fired and eluted to obtain a ceramic sintered body having a three-dimensional network structure. A ceramic which can be formed and further filled with molten metal under pressure to obtain a composite having excellent wear resistance and heat resistance.
The present invention relates to a method for manufacturing a metal composite.
［発明の背景］ 物理的、化学的に異なる２種類以上の材料を混合ある
いは結合して得られる複合体が一般に知られている。こ
の種の複合体として、セラミックと金属とからなる複合
体が広汎に使用されている。前記セラミック−金属複合
体では、耐熱性、耐摩耗性並びに強度等に優れるため、
例えば、シリンダヘッドのバルブシート部分、ピストン
およびロッカーアーム等のように他の部材と常時摺接す
る部分に効果的に採用されるに至っている。BACKGROUND OF THE INVENTION A composite obtained by mixing or bonding two or more kinds of physically and chemically different materials is generally known. As a composite of this type, a composite of ceramic and metal is widely used. In the ceramic-metal composite, because of excellent heat resistance, wear resistance and strength,
For example, it has come to be effectively used in a valve seat portion of a cylinder head, a portion such as a piston and a rocker arm that is always in sliding contact with another member.
ところで、前述したセラミック−金属複合体を製造す
るためには、一般的には、以下に示す方法が用いられて
いる。By the way, in order to manufacture the above-mentioned ceramic-metal composite, the following method is generally used.
すなわち、先ず、有機質発泡体に有機樹脂を用いてセ
ラミック粉末を付着させて所定形状の成形体を得、次い
で、前記成形体を乾燥固化して後、前記有機質発泡体を
燃焼させると共に、焼結処理を施し複数の気孔を有する
セラミック焼結体を成形している。さらに、このセラミ
ック焼結体に溶融金属を含浸、あるいは、所定圧力で充
填してセラミック−金属複合体を製造している。That is, first, a ceramic powder is attached to an organic foam using an organic resin to obtain a molded body having a predetermined shape, and then the molded body is dried and solidified, and then the organic foam is burned and sintered. A ceramic sintered body having a plurality of pores is formed by processing. Further, this ceramic sintered body is impregnated with molten metal or filled with a predetermined pressure to manufacture a ceramic-metal composite.
この場合、前記の従来方法によれば、有機樹脂を用い
てセラミック成形体を形成しているが、前記有機樹脂の
固着力が弱いため、この成形体が容易に変形してしま
う。従って、成形体の取扱作業が相当に煩雑なものとな
る欠点が指摘される。しかも、前述したようにして得ら
れるセラミック焼結体に溶融金属を加圧充填する際、こ
の加圧力により前記セラミック焼結体が変形し、不均一
な繊維分布を有する複合体が製造されるという問題が露
呈する。In this case, according to the above-mentioned conventional method, the ceramic molded body is formed by using the organic resin, but since the fixing force of the organic resin is weak, the molded body is easily deformed. Therefore, it is pointed out that there is a drawback that the handling work of the molded body becomes considerably complicated. Moreover, when the ceramic sintered body obtained as described above is filled with molten metal under pressure, the ceramic sintered body is deformed by this pressing force to produce a composite having an uneven fiber distribution. The problem is exposed.
また、有機質発泡体を燃焼除去した後にセラミックの
焼結を行っており、セラミック焼結体の寸法精度を確保
するためにはこの有機質発泡体の除去後、直ちに焼成作
業を開始する必要がある。このため、通常、低温で焼結
促進機能を発揮する焼結助剤を使用して低温下でセラミ
ックの焼結を遂行しており、この結果、セラミック焼結
体の強度低下を招来することになる。従って、前記セラ
ミック焼結体に溶融金属を所定の加圧力で充填する際、
この加圧力によりセラミック焼結体が変形してしまい、
品質に優れた複合体を製造することが不可能となる不都
合が指摘される。Further, the ceramic is sintered after burning off the organic foam, and in order to ensure the dimensional accuracy of the ceramic sintered body, it is necessary to start the firing operation immediately after removing the organic foam. For this reason, usually, a sintering aid that exerts a sintering promoting function at a low temperature is used to sinter the ceramic at a low temperature, and as a result, the strength of the ceramic sintered body is reduced. Become. Therefore, when the molten metal is filled into the ceramic sintered body under a predetermined pressure,
The ceramic sintered body is deformed by this pressing force,
It is pointed out that it is impossible to produce a composite having high quality.
さらに、有機質発泡体に形成されている気孔に対応し
てこのセラミック焼結体に気孔が設けられるため、前記
セラミック焼結体の気孔が、実質上、大きなものとなっ
てしまう。従って、セラミック焼結体全体に亘り微細な
気孔を略均一に分布させることは到底不可能となる。こ
のため、セラミック焼結体の強度が低いものとなり、前
述したように、このセラミック焼結体に溶融金属を加圧
充填する際、前記セラミック焼結体が変形するという不
都合から回避出来ない。結果的に、このように大きな気
孔を有するセラミック焼結体では、複合体の製造工程に
使用することが実質上不可能となってしまう。Furthermore, since the ceramic sintered body is provided with pores corresponding to the pores formed in the organic foam, the pores of the ceramic sintered body become substantially large. Therefore, it is extremely impossible to distribute fine pores substantially uniformly over the entire ceramic sintered body. For this reason, the strength of the ceramic sintered body becomes low, and as described above, it is unavoidable because the ceramic sintered body is deformed when the molten metal is pressurized and filled in the ceramic sintered body. As a result, such a ceramic sintered body having large pores is practically impossible to use in the manufacturing process of the composite.
しかも、このような複数の気孔を有する、所謂、三次
元網目構造の有機質発泡体を製造するためには多くの工
程を要し、前記製造作業が極めて煩雑であるという問題
が生じている。In addition, many steps are required to manufacture an organic foam having a so-called three-dimensional network structure having a plurality of pores, and the manufacturing work is extremely complicated.
［発明の目的］ 本発明は前記の不都合を克服するためになされたもの
であって、セラミック粉末と酸により溶出し得る気孔形
成粉末との混合粉末を用いて成形体を成形し、次いで、
前記成形体に焼結処理を施してセラミック焼結体を得て
後、溶出処理により前記気孔形成粉末を溶出除去し、さ
らに、前記焼結体に溶融金属を加圧充填して複合体を製
造することにより、全体に亘り微細な気孔を略均一に分
布させたセラミック焼結体を得ることが出来、しかも、
有機質発泡体を用いる際のように成形体が変形すること
を阻止すると共に、前記成形体を所望の焼結条件で焼結
処理し、これによって耐摩耗性や耐熱強度等に優れた複
合体を得ることを可能としたセラミック−金属複合体の
製造方法を提供することを目的とする。[Object of the Invention] The present invention has been made to overcome the above-mentioned inconvenience, and a molded body is molded using a mixed powder of a ceramic powder and a pore-forming powder that can be eluted by an acid, and then,
After subjecting the molded body to a sintering treatment to obtain a ceramic sintered body, the pore forming powder is eluted and removed by an elution treatment, and further, a molten metal is pressure-filled into the sintered body to manufacture a composite body. By doing so, it is possible to obtain a ceramic sintered body in which fine pores are distributed almost uniformly over the whole, and moreover,
While preventing the molded body from being deformed as in the case of using an organic foam, the molded body is subjected to a sintering treatment under desired sintering conditions, whereby a composite excellent in abrasion resistance, heat resistance strength, etc. is obtained. It is an object of the present invention to provide a method for producing a ceramic-metal composite that enables the production.
［目的を達成するための手段］ 前記の目的を達成するために、本発明は、セラミック
粉末と酸により溶出される気孔形成粉末との混合粉末を
用いて加圧成形法または射出成形法により成形体を成形
する第１の工程と、 前記成形体に焼結処理を施して焼結体を得る第２の工
程と、 前記焼結体を酸溶液中に浸漬した状態で所定時間超音
波振動を付与することにより、気孔成形粉末を溶出除去
する第３の工程と、 前記溶出処理終了後の焼結体を焼成する第４の工程
と、 前記焼成後の焼結体に溶融金属を加圧充填して複合体
を得る第５の工程と、 を有することを特徴とする。[Means for Achieving the Purpose] In order to achieve the above-mentioned object, the present invention uses a mixed powder of a ceramic powder and a pore-forming powder that is eluted by an acid to perform molding by a pressure molding method or an injection molding method. A first step of molding a body, a second step of subjecting the molded body to a sintering treatment to obtain a sintered body, and ultrasonic vibration for a predetermined time while the sintered body is immersed in an acid solution. A third step of eluting and removing the pore-forming powder by applying, a fourth step of firing the sintered body after completion of the elution treatment, and a molten metal pressure filling into the sintered body after firing. And a fifth step of obtaining a complex.
［実施態様］ 次に、本発明に係るセラミック−金属複合体の製造方
法について好適な実施態様を挙げ、添付の図面を参照し
ながら以下詳細に説明する。[Embodiment] Next, preferred embodiments of the method for producing a ceramic-metal composite according to the present invention will be described in detail below with reference to the accompanying drawings.
この場合、セラミック粉末としては、直径20μｍ以下
のSi3N4、サイアロン、SiC、Al2O3およびZrO2等の単独
粉末、あるいはこれらの混合粉末が用いられる。また、
Ti、Mo、Cr、Ta、Hf、ｗおよびZr等の炭化物、窒化物等若し
くは硼化物等を単独あるいは複合させたもの、またはこ
れらにSi3N4,Al2O3、SiCおよびサイアロン等を複合させ
たものが採用される。In this case, as the ceramic powder, a single powder such as Si 3 N 4 , sialon, SiC, Al 2 O 3 and ZrO 2 having a diameter of 20 μm or less, or a mixed powder thereof is used. Also,
T i, M o, C r , T a, H f, carbides such as w and Z r, which nitrides or borides etc. was alone or complexed, or Si 3 N 4 thereto, Al 2 O 3 , A combination of SiC, sialon, etc. is adopted.
一方、気孔形成粉末はセラミック焼結体に積極的に微
細な気孔を形成して所定の気孔率を有し且つ３次元網目
構造を呈する前記セラミック焼結体を得るために用いら
れるものであり、この気孔形成粉末としては以下に示す
２種のものがある。On the other hand, the pore forming powder is used to positively form fine pores in the ceramic sintered body to obtain the ceramic sintered body having a predetermined porosity and a three-dimensional network structure, The pore-forming powder includes the following two types.
すなわち、Na2O（８〜40重量％）、Al2O3（20重量％
以下）、BO3（30〜65重量％）およびSiO2（40重量％以
下）の混合粉末にCaO、MgOの少なくとも１種を添加して
溶融、粉砕の各工程を経て得られたガラス質で直径１μ
ｍ〜５μｍのAl2O3−Na2O−B2O3−S1O2系粉末が第１の
気孔形成粉末である。また、Al2O3（20重量％以下）、B
2O3（30〜65重量％）、S1O2（40重量％以下）およびK2O
（40重量％以下）の混合粉末にCaO、MgOの少なくとも１
種を添加して、前記と同様に溶融、粉砕の各工程を経て
得られたガラス質で直径１μｍ〜５μｍのAl2O3−B2O3
−S1O2−K2O系粉末が第２の気孔形成粉末である。That is, Na 2 O (8-40% by weight), Al 2 O 3 (20% by weight)
Below), BO 3 (30 to 65% by weight) and SiO 2 (40% by weight or less), and at least one of CaO and MgO added to a mixed powder to obtain a glassy material obtained through each step of melting and crushing. Diameter 1μ
The Al 2 O 3 —Na 2 O—B 2 O 3 —S 1 O 2 based powder of m to 5 μm is the first pore forming powder. In addition, Al 2 O 3 (20 wt% or less), B
2 O 3 (30-65 wt%), S 1 O 2 (40 wt% or less) and K 2 O
At least 1 of CaO and MgO in the mixed powder (40% by weight or less)
Al 2 O 3 —B 2 O 3 having a glassy and diameter of 1 μm to 5 μm obtained by adding each seed and melting and crushing in the same manner as described above.
-S 1 O 2 -K 2 O-based powder is in a second pore forming powders.
この場合、セラミック粉末の焼結性を向上させるた
め、必要に応じて焼結助剤粉末が使用される。この種の
焼結助剤粉末としては、直径0.1μｍ〜１μｍのAl2O3、
Y2O2、MgOおよびS1O2等の単独粉末、あるいはこれらの
混合粉末が採用されている。In this case, in order to improve the sinterability of the ceramic powder, a sintering aid powder is used if necessary. As this kind of sintering aid powder, Al 2 O 3 having a diameter of 0.1 μm to 1 μm,
A single powder such as Y 2 O 2 , MgO and S 1 O 2 or a mixed powder thereof is adopted.
そして、前述したセラミック粉末、焼結助剤粉末およ
び気孔形成粉末を夫々の中から選択すると共に、所定の
配合量（セラミック粉末を75〜97重量％、焼結助剤粉末
を10重量％以下および気孔形成粉末を15重量％以下）で
混合して混合粉末を得る。次いで、この混合粉末を用い
て、例えば、加圧成形法または射出成形法等の各種成形
法により所望の形状を呈する成形体を成形する。Then, the ceramic powder, the sintering aid powder and the pore forming powder described above are selected from the respective ones, and a predetermined compounding amount (ceramic powder 75 to 97% by weight, sintering aid powder 10% by weight or less and The porosity forming powder is mixed at 15% by weight or less) to obtain a mixed powder. Next, using this mixed powder, a molded body having a desired shape is molded by various molding methods such as a pressure molding method or an injection molding method.
さらに、前記成形体を800℃〜2200℃で0.5時間〜24時
間焼成することによりセラミック焼結体を得て後、この
セラミック焼結体を30℃〜60℃のHClあるいはNNO3の単
一酸、またはこれらの混酸よりなる酸溶液中に所定時間
浸漬して気孔形成粉末を溶出除去する。この場合、溶出
作業を終了したセラミック焼結体を約1700℃で焼成すれ
ば、このセラミック焼結体の際摩耗性および耐熱強度を
一層向上させることが出来る。Further, after obtaining a ceramic sintered body by firing the molded body at 800 ℃ ~ 2200 ℃ for 0.5 hours ~ 24 hours, the ceramic sintered body is 30 ℃ ~ 60 ℃ HCl or NNO 3 single acid Alternatively, the pore-forming powder is eluted and removed by immersing in an acid solution composed of these mixed acids for a predetermined time. In this case, if the ceramic sintered body that has undergone the elution work is fired at about 1700 ° C., the wear resistance and heat resistance of this ceramic sintered body can be further improved.
なお、セラミック粉末としてSi3N4を使用し、1200℃
の焼成温度に選択した際の気孔形成粉末の配合量とセラ
ミック焼結体の曲げ強度との関係を第１図に示す。第２
図はセラミック粉末としてSi3N4（図中、Ａ参照）とSiC
（図中、Ｂ参照）とを用い、1200℃で焼結処理を行った
際の夫々のセラミック粉末に配合される気孔形成粉末の
配合量と空隙率との関係を示したものである。また、第
３図はセラミック粉末としてSi3N4を使用し、焼成温度
を1200℃（図中、Ｃ参照）と1700℃（図中、Ｄ参照）と
に選択した際の気孔形成粉末の配合量と空隙率との関係
を示したものである。さらに、酸溶出後のセラミック焼
結体を1700℃の焼成温度で１時間焼成した時の空隙率と
曲げ強度との関係を第４図に示す。従って、第１図乃至
第４図を参照し、所定の曲げ強度並びに空隙率等に対応
して気孔形成粉末の配合量等を選択すればよい。Note that Si 3 N 4 is used as the ceramic powder and the temperature is 1200 ° C.
FIG. 1 shows the relationship between the blending amount of the pore-forming powder and the bending strength of the ceramic sintered body when the firing temperature was selected. Second
The figure shows Si 3 N 4 (see A in the figure) and SiC as ceramic powder.
(See B in the figure) is used to show the relationship between the porosity and the blending amount of the pore-forming powder blended in each ceramic powder when the sintering treatment is performed at 1200 ° C. Further, FIG. 3 shows the composition of the pore-forming powder when Si 3 N 4 is used as the ceramic powder and the firing temperature is selected to be 1200 ° C. (see C in the figure) and 1700 ° C. (see D in the figure). It shows the relationship between the amount and the porosity. Further, FIG. 4 shows the relationship between the porosity and the bending strength when the ceramic sintered body after acid elution was fired at a firing temperature of 1700 ° C. for 1 hour. Therefore, referring to FIG. 1 to FIG. 4, the compounding amount of the pore-forming powder and the like may be selected in accordance with the predetermined bending strength, porosity and the like.
次いで、このようにして得られるセラミック焼結体と
複合化される金属材料としては、Al、Mg,Zr,Cu,Pbおよ
びSn等の金属、またはこれらの金属の合金が使用され
る。Then, as the metal material to be composited with the ceramic sintered body thus obtained, a metal such as Al, M g , Z r , C u , P b and S n , or an alloy of these metals is used. To be done.
そして、セラミック焼結体を溶融金属が含浸し易いよ
うに、予め、100℃〜1000℃の温度に加温しておき、こ
のセラミック焼結体に前記溶融金属を50kg/cm2〜1500kg
/cm2の加圧力で充填する。これによって、所定時間冷却
後、所望のセラミック−金属複合体が製造されるに至
る。この場合、溶融金属とのぬれ性や密着性を向上させ
るべくセラミック焼結体に金属、合金またはセラミック
材等を蒸着等の方法により被覆しておくと好適である。Then, to facilitate impregnation of the ceramic sintered body with the molten metal, the ceramic sintered body is preheated to a temperature of 100 ° C to 1000 ° C, and the molten metal is added to the ceramic sintered body at 50 kg / cm 2 to 1500 kg.
Fill with a pressure of / cm 2 . This leads to the production of the desired ceramic-metal composite after cooling for a predetermined time. In this case, it is preferable to coat the ceramic sintered body with a metal, an alloy, a ceramic material, or the like by a method such as vapor deposition in order to improve the wettability and the adhesiveness with the molten metal.
そこで、本実施態様では、セラミック−金属複合体の
一例であるシリンダヘッドの製造方法について詳細に説
明する。Therefore, in this embodiment, a method for manufacturing a cylinder head, which is an example of a ceramic-metal composite, will be described in detail.
すなわち、第５図において、参照符号10は本発明に係
る方法を用いて製造されるシリンダヘッドを示す。この
場合、前記シリンダヘッド10はアルミニウム合金で鋳造
成形されており、シリンダ室12と吸気路14並びに前記シ
リンダ室12と排気路16との間にはバルブガイド孔18a、1
8bと同軸的にバルブシート20a、20bが設けられる。前記
バルブシート20a、20bは実質的には、第６図に示すよう
に、リング状のセラミック焼結体24を成形して後、この
セラミック焼結体24に後述するようにアルミニウム合金
を加圧充填してシリンダヘッド10と一体的に鋳造され
る。That is, in FIG. 5, reference numeral 10 indicates a cylinder head manufactured using the method according to the present invention. In this case, the cylinder head 10 is cast and formed of an aluminum alloy, and the valve guide holes 18a, 1 are provided between the cylinder chamber 12 and the intake passage 14 and between the cylinder chamber 12 and the exhaust passage 16.
Valve seats 20a and 20b are provided coaxially with 8b. As shown in FIG. 6, the valve seats 20a and 20b are formed by forming a ring-shaped ceramic sintered body 24, and then pressurizing the ceramic sintered body 24 with an aluminum alloy as described later. It is filled and cast integrally with the cylinder head 10.
このように構成されるシリンダヘッド10において、先
ず、前記セラミック焼結体24を成形する。In the cylinder head 10 thus configured, first, the ceramic sintered body 24 is molded.
この場合、実質的にはセラミック粉末としてSi3N4、
焼結助剤粉末としてAl2O3および気孔形成粉末としてガ
ラス質で直径１μｍ〜５μｍのAl2O3−Na2O−B2O3−SiO
2系粉末を用いる。そして、夫々の粉末を所定の配合量
で混合し、加圧成形法により成形圧力75MPaにて第６図
に示すセラミック焼結体24に対応するリング状の成形体
を成形する。In this case, substantially Si 3 N 4 as ceramic powder,
Al 2 O 3 as a sintering aid powder and glassy Al 2 O 3 —Na 2 O—B 2 O 3 —SiO having a diameter of 1 μm to 5 μm as a pore forming powder.
2 system powder is used. Then, the respective powders are mixed in a predetermined mixing amount, and a ring-shaped molded body corresponding to the ceramic sintered body 24 shown in FIG. 6 is molded by a pressure molding method at a molding pressure of 75 MPa.
次いで、この成形体を1500℃の温度で８時間焼成し、
セラミック焼結体24を得る。さらに、前記セラミック焼
結体24を50℃に加温された4NのHNO3中に浸漬し、このHN
O3に超音波振動を付与した状態で所定時間保持する。従
って、気孔形成粉末および不純物が溶出された３次元網
目構造を有するセラミック焼結体24が得られる。これに
よって、直径0.5μｍ〜３μｍの微細な気孔を全体に亘
り略均一に分布したセラミック焼結体24が製造されるに
至る。Then, the molded body is fired at a temperature of 1500 ° C. for 8 hours,
A ceramic sintered body 24 is obtained. Further, the ceramic sintered body 24 is immersed in 4N HNO 3 heated to 50 ° C.
It is kept for a predetermined time with ultrasonic vibration applied to O 3 . Therefore, the ceramic sintered body 24 having a three-dimensional network structure in which the pore-forming powder and impurities are eluted can be obtained. As a result, a ceramic sintered body 24 in which fine pores having a diameter of 0.5 μm to 3 μm are substantially uniformly distributed over the whole is manufactured.
さらに、図示しない高圧鋳造用金型において、バルブ
シート20a、20bに対応する位置にセラミック焼結体24を
配置し、このセラミック焼結体24を、予め、略250℃の
温度に加温しておく。次に、図示しない金型内に略730
℃の温度で溶融しているアルミニウム合金（AC2B）の溶
湯を充填し、略200kg/cm2の加圧力で所定時間保持す
る。このため、前記アルミニウム合金の一部はセラミッ
ク焼結体24内に充填され、バルブシート20a、20bがシリ
ンダヘッド10と一体的に鋳造成形されるに至る。Further, in a high-pressure casting die not shown, a ceramic sintered body 24 is arranged at a position corresponding to the valve seats 20a, 20b, and the ceramic sintered body 24 is preheated to a temperature of about 250 ° C. deep. Next, in the mold not shown, approximately 730
A molten aluminum alloy (AC2B) melted at a temperature of ℃ is filled, and the pressure is maintained at a pressure of approximately 200 kg / cm 2 for a predetermined time. Therefore, a part of the aluminum alloy is filled in the ceramic sintered body 24, and the valve seats 20a and 20b are integrally cast with the cylinder head 10.
この場合、本実施態様によれば、セラミック焼結体24
内に分散している気孔形成粉末を酸により溶出させるた
め、全体に亘って略均一に分布された微細な気孔を有す
るセラミック焼結体24を製造することが出来る。このた
め、前記セラミック焼結体24は十分な強度を有すると共
に、セラミック粉末の体積率を良好に且つ高く確保する
ことが可能となる。しかも、セラミック成形体を所望の
温度で焼結し得るため、強度に優れたセラミック焼結体
24を製造することが出来る。これによって、セラミック
焼結体24にアルミニウム合金の溶湯を加圧充填する際に
この加圧力（略200kg/cm2）により前記セラミック焼結
体24が変形することがない。In this case, according to the present embodiment, the ceramic sintered body 24
Since the pore forming powder dispersed therein is eluted by the acid, it is possible to manufacture the ceramic sintered body 24 having fine pores distributed substantially uniformly throughout the whole. Therefore, the ceramic sintered body 24 has sufficient strength, and it is possible to secure a good and high volume ratio of the ceramic powder. Moreover, since the ceramic molded body can be sintered at a desired temperature, the ceramic sintered body has excellent strength.
24 can be manufactured. This prevents the ceramic sintered body 24 from being deformed by the applied pressure (approximately 200 kg / cm 2 ) when the ceramic sintered body 24 is pressurized and filled with the molten aluminum alloy.
また、一般に、セラミック粉末にはセラミック焼結体
24としての強度低下の要因となる不純物を含有している
場合が多いが、本実施態様では、この不純物が溶出処理
によってセラミック焼結体24から除去されるため、当該
セラミック焼結体24の強度を一層向上させるという利点
が顕在化する。Generally, ceramic powder is a ceramic sintered body.
In many cases, it contains impurities that cause a decrease in strength as 24, but in the present embodiment, since the impurities are removed from the ceramic sintered body 24 by elution treatment, the strength of the ceramic sintered body 24 is high. The advantage of further improving is realized.
さらに、従来のように、有機質発泡体を用いることが
ないため、セラミック成形体が変形することを阻止する
ことが出来る。従って、セラミック成形体の取扱作業が
一挙に簡易化すると共に、高精度なセラミック焼結体24
が得られる。その上、製造が煩雑な有機質発泡体を用い
るものに比べ、セラミック焼結体24の生産効率を一挙に
向上させるという効果が挙げられる。Further, unlike the conventional case, since the organic foam is not used, it is possible to prevent the ceramic molded body from being deformed. Therefore, the handling work of the ceramic molded body is simplified at once, and the highly accurate ceramic sintered body 24
Is obtained. In addition, there is an effect that the production efficiency of the ceramic sintered body 24 is improved at once, as compared with the one using an organic foam which is complicated to manufacture.
結果的に、このようなセラミック焼結体24を介して鋳
造成形されるバルブシート20a、20bは十分な耐摩耗性、
耐熱強度および耐圧強度等を有することが可能となる。As a result, the valve seats 20a, 20b that are cast and molded through such a ceramic sintered body 24 have sufficient wear resistance,
It becomes possible to have heat resistance strength and pressure resistance strength.
［発明の効果］ 以上のように、本発明によれば、セラミック粉末と酸
により溶出し得る気孔形成粉末との混合粉末を用いて成
形体を成形し、この成形体に焼結処理並びに溶出処理を
施して複数の微細な気孔を有するセラミック焼結体を
得、さらにこのセラミック焼結体に溶融金属を加圧充填
してセラミック−金属複合体を製造している。このた
め、有機質発泡体を用いて成形体を得る際のように、こ
の成形体が変形することがなく、前記成形体の取扱作業
が簡易化する。しかも、セラミック粉末を所望の焼結条
件で焼結し得ると共に、セラミック焼結体に微細な気孔
が形成されるため、高強度なセラミック焼結体を製造す
ることが出来る。従って、前記セラミック焼結体に溶融
金属を所定の圧力で充填する際、このセラミック焼結体
が変形することがない。結局、耐摩耗性並びに耐熱性等
に優れた高品質な複合体を確実に且つ効果的に製造する
ことが出来るという効果が得られる。[Effects of the Invention] As described above, according to the present invention, a molded body is molded using a mixed powder of a ceramic powder and a pore-forming powder that can be eluted by an acid, and the molded body is subjected to a sintering treatment and an elution treatment. Is performed to obtain a ceramic sintered body having a plurality of fine pores, and a molten metal is pressure-filled into the ceramic sintered body to manufacture a ceramic-metal composite. Therefore, unlike the case where a molded body is obtained by using the organic foam, the molded body is not deformed, and the work of handling the molded body is simplified. Moreover, the ceramic powder can be sintered under desired sintering conditions, and since fine pores are formed in the ceramic sintered body, a high-strength ceramic sintered body can be manufactured. Therefore, when the molten metal is filled in the ceramic sintered body at a predetermined pressure, the ceramic sintered body is not deformed. After all, it is possible to reliably and effectively produce a high-quality composite having excellent wear resistance and heat resistance.
さらに、従来のように、製造工程の煩雑な有機質発泡
体を用いるものに比べ、セラミック焼結体を一挙に容易
に且つ短時間で製造することが出来、複合体を効率的に
製造し得るという実質的な利点も挙げられる。Further, compared with the conventional one using an organic foam, which has a complicated manufacturing process, a ceramic sintered body can be manufactured all at once easily and in a short time, and a composite can be manufactured efficiently. There are also substantial advantages.
以上、本発明について好適な実施態様を挙げて説明し
たが、本発明はこの実施態様に限定されるものではな
く、本発明の要旨を逸脱しない範囲において種々の改良
並びに設計の変更が可能なことは勿論である。Although the present invention has been described above with reference to the preferred embodiments, the present invention is not limited to these embodiments, and various improvements and design changes can be made without departing from the scope of the present invention. Of course.
第１図はセラミック成形体に添加される気孔形成粉末の
配合量とセラミック焼結体の曲げ強度との関係を示すグ
ラフ、 第２図はセラミック粉末としてSiCとSi3N4とを用い、夫
々に添加される気孔形成粉末の配合量と空隙率との関係
を示すグラフ、 第３図はセラミック粉末としてSi3N4を用い、２種の異
なる焼結温度における気孔形成粉末の配合量と空隙率と
の関係を示すグラフ、 第４図はセラミック焼結体を1700℃で１時間焼成した際
の空隙率と曲げ強度との関係を示すグラフ、 第５図は本発明に係るセラミック−金属複合体の製造方
法により鋳造成形されるシリンダヘッドの概略構成を示
す縦断面図、 第６図は第５図に示すシリンダヘッドに組み込まれるセ
ラミック焼結体の斜視図である。 10…シリンダヘッド 20a、20b…バルブシート 24…セラミック焼結体FIG. 1 is a graph showing the relationship between the blending amount of the pore-forming powder added to the ceramic compact and the bending strength of the ceramic sintered body, and FIG. 2 uses SiC and Si 3 N 4 as the ceramic powder, respectively. Fig. 3 is a graph showing the relationship between the porosity forming powder content and the porosity added to the powder. Fig. 3 shows the composition and porosity of the porosity forming powder at two different sintering temperatures using Si 3 N 4 as the ceramic powder. 4 is a graph showing the relationship with the porosity, FIG. 4 is a graph showing the relationship between the porosity and the bending strength when the ceramic sintered body is fired at 1700 ° C. for 1 hour, and FIG. 5 is the ceramic-metal composite according to the present invention. FIG. 6 is a vertical cross-sectional view showing a schematic configuration of a cylinder head which is cast and molded by the method for manufacturing a body, and FIG. 6 is a perspective view of a ceramic sintered body incorporated in the cylinder head shown in FIG. 10 ... Cylinder head 20a, 20b ... Valve seat 24 ... Ceramic sintered body
───────────────────────────────────────────────────── フロントページの続き (72)発明者 桑原 光雄 埼玉県狭山市新狭山１−10−１ ホンダエ ンジニアリング株式会社内 (56)参考文献 特開 昭59−145742（ＪＰ，Ａ) 特開 昭61−222970（ＪＰ，Ａ) 特開 昭61−222966（ＪＰ，Ａ) ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Mitsuo Kuwahara 1-10-1 Shin-Sayama, Sayama-shi, Saitama Honda Engineering Co., Ltd. (56) References JP-A-59-145742 (JP, A) JP-A-SHO 61-222970 (JP, A) JP-A-61-222966 (JP, A)
Claims (1)
形成粉末との混合粉末を用いて加圧成形法または射出成
形法により成形体を成形する第１の工程と、 前記成形体に焼結処理を施して焼結体を得る第２の工程
と、 前記焼結体を酸溶液中に浸漬した状態で所定時間超音波
振動を付与することにより、気孔成形粉末を溶出除去す
る第３の工程と、 前記溶出処理終了後の焼結体を焼成する第４の工程と、 前記焼成後の焼結体に溶融金属を加圧充填して複合体を
得る第５の工程と、 を有することを特徴とするセラミック−金属複合体の製
造方法。1. A first step of molding a molded body by a pressure molding method or an injection molding method using a mixed powder of a ceramic powder and a pore-forming powder eluted by an acid, and a sintering treatment on the molded body. And a third step of subjecting the sintered body to ultrasonic vibration for a predetermined time while being immersed in an acid solution to elute and remove the pore-forming powder. A fourth step of firing the sintered body after completion of the elution treatment, and a fifth step of pressure-filling the fired sintered body with molten metal to obtain a composite body. And a method for producing a ceramic-metal composite.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62149749A JPH0830228B2 (en) | 1987-06-15 | 1987-06-15 | Method for producing ceramic-metal composite |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62149749A JPH0830228B2 (en) | 1987-06-15 | 1987-06-15 | Method for producing ceramic-metal composite |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS63312931A JPS63312931A (en) | 1988-12-21 |
| JPH0830228B2 true JPH0830228B2 (en) | 1996-03-27 |
Family
ID=15481921
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP62149749A Expired - Lifetime JPH0830228B2 (en) | 1987-06-15 | 1987-06-15 | Method for producing ceramic-metal composite |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0830228B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112941427A (en) * | 2021-01-29 | 2021-06-11 | 郑承盛 | Magnesium-based composite material and preparation method thereof |
Families Citing this family (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB8919466D0 (en) * | 1989-08-26 | 1989-10-11 | Wellworthy Ltd | Pistons |
| WO2000051765A1 (en) * | 1999-03-01 | 2000-09-08 | Shaochien Tseng | Process of producing a porous metal matrix composite using hollow ceramic balls |
| KR100472002B1 (en) * | 2000-08-24 | 2005-03-07 | 재단법인 포항산업과학연구원 | Method of preparing porous sialon |
| JP4088270B2 (en) * | 2004-06-16 | 2008-05-21 | 本田技研工業株式会社 | Cylinder block |
| JP4693399B2 (en) * | 2004-12-01 | 2011-06-01 | 京セラ株式会社 | Method for producing ceramic-metal composite |
| JP2014005486A (en) * | 2012-06-22 | 2014-01-16 | Aisin Seiki Co Ltd | Method for producing aluminum composite material |
Family Cites Families (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS59145742A (en) * | 1983-02-10 | 1984-08-21 | Agency Of Ind Science & Technol | Production of particle dispersion-reinforced type composite material |
| JPS61222966A (en) * | 1985-03-27 | 1986-10-03 | 日立造船株式会社 | Manufacture of silicon nitride porous body |
| JPS61222970A (en) * | 1985-03-27 | 1986-10-03 | 三井造船株式会社 | Manufacture of porous ceramics |
-
1987
- 1987-06-15 JP JP62149749A patent/JPH0830228B2/en not_active Expired - Lifetime
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112941427A (en) * | 2021-01-29 | 2021-06-11 | 郑承盛 | Magnesium-based composite material and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JPS63312931A (en) | 1988-12-21 |
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