JPH0762481A - High strength wear resistant ceramic and its production - Google Patents
High strength wear resistant ceramic and its productionInfo
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- JPH0762481A JPH0762481A JP5206224A JP20622493A JPH0762481A JP H0762481 A JPH0762481 A JP H0762481A JP 5206224 A JP5206224 A JP 5206224A JP 20622493 A JP20622493 A JP 20622493A JP H0762481 A JPH0762481 A JP H0762481A
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Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は高強度・耐摩耗性セラミ
ックスに係り、特に、耐摩耗性に優れたセラミックスお
よびその製法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to high-strength and wear-resistant ceramics, and more particularly to ceramics having excellent wear resistance and a method for producing the same.
【０００２】[0002]
【従来の技術】一般にセラミックスは難焼結材料であ
る。特に、ＳｉＣ，Ｓｉ3Ｎ4，ＴｉＢ2などの非酸化物
系セラミックスは焼結性が悪いために、焼結助剤により
粒間を結合する必要がある。こうした焼結助剤として従
来から各種の焼結助剤が検討されている。例えば、Ｓｉ
ＣではＢ＋Ｃ，ＢｅＯ，Ａｌ2Ｏ3が知られている（炭化
珪素セラミックス、内田老鶴圃出版）。ＳｉＣの場合に
は、拡散で焼結が進行するために焼結助剤が限られてい
る。2. Description of the Related Art Generally, ceramics are hardly sintered materials. In particular, since non-oxide ceramics such as SiC, Si 3 N 4 , and TiB 2 have poor sinterability, it is necessary to bond the grains with a sintering aid. Various sintering aids have been studied as such sintering aids. For example, Si
For C, B + C, BeO, and Al 2 O 3 are known (silicon carbide ceramics, Uchida Ryotsuho Publishing). In the case of SiC, the sintering aid is limited because sintering progresses by diffusion.
【０００３】また、Ｓｉ3Ｎ4ではＭｇＯ，Ｙ2Ｏ3，Ａｌ
2Ｏ3，ＳｉＯ2などが知られている（窒化珪素セラミッ
クス，窒化珪素セラミックス２，内田老鶴圃出版）。Ｓ
ｉ3Ｎ4では、焼結助剤から得られる合金相あるいはガラ
ス相で粒子間が結合されているために、その特性が合金
相あるいはガラス相によって大きく支配される。特に、
耐摩耗性，高温強度の優れたＳｉ3Ｎ4を開発するため
に、各種の助剤が検討されているが、高温領域で優れた
耐摩耗特性を有するセラミックスは得られていない。For Si 3 N 4 , MgO, Y 2 O 3 , Al
2 O 3 , SiO 2 and the like are known (silicon nitride ceramics, silicon nitride ceramics 2, Uchida Otsuruho Publishing). S
In i 3 N 4 , the properties are largely controlled by the alloy phase or the glass phase because the particles are bound by the alloy phase or the glass phase obtained from the sintering aid. In particular,
Various auxiliaries have been investigated in order to develop Si 3 N 4 having excellent wear resistance and high-temperature strength, but ceramics having excellent wear resistance in the high temperature region have not been obtained.
【０００４】[0004]
【発明が解決しようとする課題】本発明の目的は、セラ
ミックスの粒子間を耐摩耗性に優れた合金相で結合する
ことにより高強度・耐摩耗性セラミックスおよびその製
法を提供することにある。SUMMARY OF THE INVENTION An object of the present invention is to provide a high-strength and abrasion-resistant ceramic and a method for producing the same by connecting the grains of the ceramic with an alloy phase having excellent abrasion resistance.
【０００５】[0005]
【課題を解決するための手段】本発明者らは、優れた特
性のセラミックスを開発するために、焼結助剤について
鋭意検討を行ってきた。その結果、Ｎｂ−Ａｌ系（但
し、Ｃｕ，Ｃｏ，Ｎｉ，Ｆｅ系金属を除く）合金を焼結
助剤として用いることにより、従来にない優れた高強度
・耐摩耗性セラミックスが得られることが分かった。特
に、Ｎｂ−Ａｌ系，Ｎｂ−Ａｌ−Ｎ系，Ｎｂ−Ａｌ−Ｃ
系，Ｎｂ−Ａｌ−Ｏ系，Ｎｂ−Ａｌ−Ｃ−Ｏ系，Ｎｂ−
Ａｌ−Ｎ−Ｏ系，Ｎｂ−Ａｌ−Ｎ−Ｃ系，Ｎｂ−Ａｌ−
Ｎ−Ｃ−Ｏ系，Ｎｂ−Ａｌ−Ｔｉ−Ｃ系，Ｎｂ−Ａｌ−
Ｔｉ−Ｎ系，Ｎｂ−Ａｌ−Ｔｉ−Ｃ−Ｏ系，Ｎｂ−Ａｌ
−Ｔｉ−Ｎ−Ｏ系，Ｎｂ−Ａｌ−Ｔｉ−Ｃ−Ｂ−Ｏ系，
Ｎｂ−Ａｌ−Ｔｉ−Ｎ−Ｂ−Ｏ系，Ｎｂ−Ａｌ−Ｚｒ−
Ｎ系，Ｎｂ−Ａｌ−Ｚｒ−Ｏ系，Ｎｂ−Ａｌ−Ｚｒ−Ｃ
系，Ｎｂ−Ａｌ−Ｚｒ−Ｎ−Ｏ系，Ｎｂ−Ａｌ−Ｚｒ−
Ｃ−Ｏ系，Ｎｂ−Ａｌ−Ｚｒ−Ｎ−Ｂ−Ｏ系，Ｎｂ−Ａ
ｌ−Ｚｒ−Ｃ−Ｂ−Ｏ系，Ｎｂ−Ａｌ−Ｓｉ−Ｎ系，Ｎ
ｂ−Ａｌ−Ｓｉ−Ｃ系，Ｎｂ−Ａｌ−Ｓｉ−Ｎ−Ｏ系，
Ｎｂ−Ａｌ−Ｓｉ−Ｃ−Ｏ系，Ｎｂ−Ａｌ−Ｃｒ−Ｎ
系，Ｎｂ−Ａｌ−Ｃｒ−Ｃ系，Ｎｂ−Ａｌ−Ｃｒ−Ｎ−
Ｏ系，Ｎｂ−Ａｌ−Ｃｒ−Ｃ−Ｏ系，Ｎｂ−Ａｌ−Ｈｆ
−Ｎ系，Ｎｂ−Ａｌ−Ｈｆ−Ｃ系，Ｎｂ−Ａｌ−Ｈｆ−
Ｎ−Ｏ系，Ｎｂ−Ａｌ−Ｈｆ−Ｃ−Ｏ系，Ｎｂ−Ａｌ−
Ｔａ−Ｎ系，Ｎｂ−Ａｌ−Ｔａ−Ｃ系，Ｎｂ−Ａｌ−Ｔ
ａ−Ｎ−Ｏ系，Ｎｂ−Ａｌ−Ｔａ−Ｃ−Ｏ系，Ｎｂ−Ａ
ｌ−Ｔａ−Ｎ−Ｂ−Ｏ系，Ｎｂ−Ａｌ−Ｔａ−Ｃ−Ｂ−
Ｏ系，Ｎｂ−Ａｌ−Ｂ−Ｎ系，Ｎｂ−Ａｌ−Ｂ−Ｃ系，
Ｎｂ−Ａｌ−Ｂ−Ｎ−Ｏ系，Ｎｂ−Ａｌ−Ｂ−Ｃ−Ｏ系
合金の少なくとも１種で粒界を構成することにより、従
来にない高強度・耐摩耗性セラミックスが得られること
がわかった。Means for Solving the Problems The present inventors have conducted extensive studies on sintering aids in order to develop ceramics having excellent properties. As a result, by using an Nb-Al-based (excluding Cu, Co, Ni, and Fe-based metals) alloy as a sintering aid, it is possible to obtain an unprecedentedly superior high-strength and wear-resistant ceramics. Do you get it. In particular, Nb-Al-based, Nb-Al-N-based, Nb-Al-C
System, Nb-Al-O system, Nb-Al-C-O system, Nb-
Al-N-O system, Nb-Al-N-C system, Nb-Al-
N-C-O system, Nb-Al-Ti-C system, Nb-Al-
Ti-N type, Nb-Al-Ti-C-O type, Nb-Al
-Ti-N-O system, Nb-Al-Ti-C-B-O system,
Nb-Al-Ti-N-B-O system, Nb-Al-Zr-
N type, Nb-Al-Zr-O type, Nb-Al-Zr-C
System, Nb-Al-Zr-NO system, Nb-Al-Zr-
C-O system, Nb-Al-Zr-N-B-O system, Nb-A
1-Zr-C-B-O system, Nb-Al-Si-N system, N
b-Al-Si-C system, Nb-Al-Si-N-O system,
Nb-Al-Si-C-O system, Nb-Al-Cr-N
System, Nb-Al-Cr-C system, Nb-Al-Cr-N-
O type, Nb-Al-Cr-C-O type, Nb-Al-Hf
-N type, Nb-Al-Hf-C type, Nb-Al-Hf-
N-O system, Nb-Al-Hf-C-O system, Nb-Al-
Ta-N system, Nb-Al-Ta-C system, Nb-Al-T
a-N-O system, Nb-Al-Ta-C-O system, Nb-A
1-Ta-N-B-O system, Nb-Al-Ta-C-B-
O type, Nb-Al-B-N type, Nb-Al-B-C type,
By forming the grain boundaries with at least one of Nb-Al-B-N-O type and Nb-Al-B-C-O type alloys, it is possible to obtain unprecedented high strength and wear resistant ceramics. all right.
【０００６】本発明において、上記Ｎｂ−Ａｌ系合金中
のＮｂ−Ａｌの含有量は５０原子％以上が望ましい。但
し、ＮｂだけあるいはＡｌだけでは特性は改善はできな
い。Ｎｂ−Ａｌ系合金を用いることにより、初めてその
特性を改善できるのである。In the present invention, the Nb-Al content in the Nb-Al alloy is preferably 50 atomic% or more. However, the characteristics cannot be improved only by Nb or Al. The characteristics can be improved only by using the Nb-Al alloy.
【０００７】さらにまた、Ｎｂ−Ａｌ系合金に窒素，酸
素，炭素を固溶させることにより耐摩耗性が改善できる
ことが分かった。特に、Ｎｂ−Ａｌ系に窒素，炭素，他
金属元素を固溶させることにより耐摩耗性をより改善で
きる。ここで、低融点のＣｕあるいはＣｕ合金（Ｃｕ−
Ｎｉ，Ｃｕ−Ｆｅ，Ｃｕ−Ｃｏなど）の含有は、（１）
耐熱性が低下する、（２）摩耗時に生じる発熱により凝
着を起こす、（３）溶融金属と反応する、などの理由の
ために好ましくない。Furthermore, it has been found that the wear resistance can be improved by solid-dissolving nitrogen, oxygen and carbon in the Nb-Al type alloy. In particular, the wear resistance can be further improved by solid-dissolving nitrogen, carbon, and other metal elements in the Nb-Al system. Here, low melting point Cu or Cu alloy (Cu-
The content of Ni, Cu-Fe, Cu-Co, etc. is (1)
It is not preferable for the reasons that the heat resistance is lowered, (2) adhesion is caused by heat generated during wear, and (3) it reacts with molten metal.
【０００８】マトリックスとなるセラミックスとして
は、非酸化物セラミックスの方が酸化物セラミックスよ
りも好ましい。酸化物セラミックスでは、Ａｌ酸化物が
生成して、高温特性が低下する。従って、切削工具など
の比較的低温で使用される耐摩耗部材としては十分であ
る。As the matrix ceramics, non-oxide ceramics are preferable to oxide ceramics. In oxide ceramics, Al oxide is generated and the high temperature characteristics deteriorate. Therefore, it is sufficient as a wear resistant member such as a cutting tool used at a relatively low temperature.
【０００９】非酸化物セラミックスの中でもＳｉＣ，Ｓ
ｉ3Ｎ4，ＴｉＣ，ＴｉＮ，ＺｒＣ，ＡｌＮ，ＺｒＮ，Ｃ
ｒ2Ｎ，Ｃｒ3Ｃ2，ＣｒＢ2，ＴｉＢ2，ＺｒＢ2，Ｈｆ
Ｎ，ＨｆＣ，ＴａＮ，ＴａＣ，ＴａＢ2，Ｂ4Ｃ，ＢＮが
耐熱性，硬度などの点で好ましい。Among non-oxide ceramics, SiC, S
i 3 N 4 , TiC, TiN, ZrC, AlN, ZrN, C
r 2 N, Cr 3 C 2 , CrB 2 , TiB 2 , ZrB 2 , Hf
N, HfC, TaN, TaC, TaB 2 , B 4 C and BN are preferable in terms of heat resistance and hardness.
【００１０】本発明は、セラミック中に上記Ｎｂ−Ａｌ
系合金が２〜５０vol％含有させることにより目的を達
成することができる。２vol％未満では十分に結合され
ないために十分な強度が得られず、５０vol％より多く
なるとセラミックスの耐熱特性が十分発揮されない。な
お、Ｎｂ−Ａｌ系合金の配合量は用途によって上記の範
囲内から選択される。The present invention is based on the above Nb-Al in ceramic.
The purpose can be achieved by containing 2 to 50 vol% of the system alloy. If it is less than 2 vol%, sufficient bonding cannot be obtained because it is not sufficiently bonded, and if it is more than 50 vol%, the heat resistance characteristics of the ceramics are not sufficiently exhibited. The blending amount of the Nb-Al alloy is selected from the above range depending on the application.
【００１１】また、本発明のセラミックスは、Ｎｂ−Ａ
ｌ系合金が低抵抗の導電性を有するために、導電性セラ
ミックスへの用途としても好適である。例えば、絶縁性
のＳｉ3Ｎ4や半導体のＳｉＣに適用し、その添加量を制
御することにより絶縁性から導電性（１０12Ωｍオーダ
ーから１０~7Ωｍオーダー）のセラミックスを得ること
も可能である。つまり、導電性を有する高強度・耐摩耗
性セラミックスを得ることができる。The ceramic of the present invention is Nb-A.
Since the l-based alloy has low resistance conductivity, it is also suitable for use in conductive ceramics. For example, it can be applied to insulating Si 3 N 4 or semiconductor SiC, and by controlling the amount of addition, it is possible to obtain insulating to conductive ceramics (10 12 Ωm order to 10 to 7 Ωm order). is there. That is, it is possible to obtain a high-strength, wear-resistant ceramic having conductivity.
【００１２】本発明のセラミックスは、炭化物，窒化
物，硼化物，酸化物の少なくとも１種を含む粉末とＮｂ
−Ａｌ系合金粉末２〜５０vol％および成形バインダの
混合粉末を用いて成形体を作製し、該成形体を真空中，
不活性ガス中あるいは不活性ガスと還元性ガスとの混合
ガス中で、１７００〜２４００℃，５〜３００分加熱す
ることにより焼結することができる。特に、不活性ガス
あるいは不活性ガス＋還元性ガス中での焼結が好まし
い。真空中ではＡｌが蒸発し、また、Ａｌ系化合物が生
成して焼結体の特性を低下させるからである。The ceramics of the present invention include powder containing at least one of carbide, nitride, boride and oxide, and Nb.
-Molded powder is prepared by using a mixed powder of 2 to 50 vol% of Al-based alloy powder and a molding binder, and the molded body is vacuumed.
Sintering can be performed by heating in an inert gas or a mixed gas of an inert gas and a reducing gas at 1700 to 2400 ° C. for 5 to 300 minutes. In particular, sintering in an inert gas or an inert gas + reducing gas is preferable. This is because Al evaporates in a vacuum and an Al-based compound is generated to deteriorate the characteristics of the sintered body.
【００１３】また、Ａｒ，Ｎ2，Ｈｅなどの不活性ガ
ス、Ｈ2，ＣＯなどの還元性ガスあるいはこれらの混合
ガス中における焼結は、Ｎｂ−Ａｌ系合金の蒸発，酸化
を抑制できる。Ｎｂ−Ａｌ系合金に炭素，窒素，他金属
の固溶は高温強度の低下は少ないが、酸素が多量に固溶
すると高温強度が大きく低下するので好ましくない。Sintering in an inert gas such as Ar, N 2 or He, a reducing gas such as H 2 or CO, or a mixed gas thereof can suppress evaporation and oxidation of the Nb-Al alloy. The solid solution of carbon, nitrogen and other metals in the Nb-Al alloy does not cause a decrease in high temperature strength, but a large amount of solid solution of oxygen causes a large decrease in high temperature strength, which is not preferable.
【００１４】焼結温度は、マトリックスとなるセラミッ
クスの種類によって異なり、焼結可能な温度領域であれ
ば必ずしも前記の温度に限定されない。The sintering temperature varies depending on the type of ceramics used as a matrix, and is not limited to the above temperature as long as it is a temperature range in which sintering is possible.
【００１５】本発明の耐熱・高強度セラミックスは、ホ
ットプレス，ＨＩＰをはじめ無加圧でも焼結可能であ
り、成形も射出成形，プレス成形，鋳込み成形，ラバー
プレス成形，押出し成形，金型粉末成形などによって行
うことができる。形状と要求特性に応じて成形方法は選
択でき、特に、複雑形状の高強度・耐摩耗性セラミック
スを得ることができる。The heat-resistant and high-strength ceramics of the present invention can be sintered without pressure, including hot pressing and HIP, and can be molded by injection molding, press molding, cast molding, rubber press molding, extrusion molding, mold powder. It can be performed by molding or the like. The molding method can be selected according to the shape and the required characteristics, and in particular, high-strength and wear-resistant ceramics having a complicated shape can be obtained.
【００１６】また本発明のセラミックス中に、短繊維や
長繊維を分散させることにより高靭性の複合材を得るこ
とも可能である。さらに、ナノ粒子をセラミックス中に
分散させることによりナノ強化材を得ることも可能であ
る。特に、切削工具用にはウイスカーを分散させた構造
が耐摩耗性が優れているので好適である。It is also possible to obtain a high toughness composite material by dispersing short fibers or long fibers in the ceramic of the present invention. Further, it is possible to obtain a nano-reinforcement material by dispersing nanoparticles in ceramics. In particular, a structure in which whiskers are dispersed is suitable for a cutting tool because it has excellent wear resistance.
【００１７】本発明の高強度・耐摩耗性セラミックス
は、無加圧焼結ができるため、原子力プラントの中の核
融合炉第１壁部品、火力プラントの中のガスタービン用
動翼部品，静翼部品，燃焼器部品，シュラウド部品、連
続溶融金属めっき用ロール、軸受、エンジン部品、切削
工具、金属溶湯用部品、摺動部材などに適用可能であ
る。Since the high-strength and wear-resistant ceramics of the present invention can be pressureless sintered, it can be used as a first wall component of a fusion reactor in a nuclear power plant, a gas turbine moving blade component in a thermal power plant, and a static turbine. It can be applied to blade parts, combustor parts, shroud parts, rolls for continuous hot metal plating, bearings, engine parts, cutting tools, parts for molten metal, sliding members and the like.
【００１８】[0018]
【作用】本発明は、炭化物，窒化物，硼化物，酸化物の
セラミックスで、複雑形状品にも対応できる高強度・耐
摩耗性セラミックスである。これはセラミックスの粒子
間がＮｂ−Ａｌ系合金で結合されているので、特に、高
温領域や金属浴中などの特殊環境下で高強度で耐摩耗性
の優れた特性のものが得らる。The present invention is a ceramic of carbide, nitride, boride, or oxide, which is a high-strength and wear-resistant ceramic that can be applied to a product having a complicated shape. This is because the particles of the ceramics are bonded by the Nb-Al-based alloy, so that it is possible to obtain a material having high strength and excellent wear resistance especially in a special environment such as a high temperature region or in a metal bath.
【００１９】[0019]
【実施例】本発明を実施例により具体的に説明する。EXAMPLES The present invention will be specifically described with reference to examples.
【００２０】〔実施例１〜８〕表１に示すように０.２
μｍのβ−ＳｉＣ粉末と５μｍのＮｂ75Ａｌ25合金（金
属間化合物）粉末に、プレス成形用のバインダを有機溶
剤と共に２wt％混合し、乾燥して成形用原料を得た。こ
れをプレス成形して直径５０ｍｍ×厚さ１０ｍｍの成形
体を作製した。得られた成形体を１ｋｇ／ｃｍ2のアル
ゴン雰囲気中で２１００℃まで加熱し、２時間保持して
焼結した。[Examples 1 to 8] As shown in Table 1, 0.2
A β-SiC powder of 5 μm and an Nb 75 Al 25 alloy (intermetallic compound) powder of 5 μm were mixed with a binder for press molding in an amount of 2 wt% together with an organic solvent and dried to obtain a raw material for molding. This was press-molded to produce a molded body having a diameter of 50 mm and a thickness of 10 mm. The obtained molded body was heated to 2100 ° C. in an argon atmosphere of 1 kg / cm 2 and held for 2 hours for sintering.
【００２１】上記焼結体のＸ線回折分析より、焼結体の
構造はいずれもβ−ＳｉＣ，Ｎｂ−Ａｌ系合金組成およ
びＮｂ−Ａｌ−Ｃ系合金組成からなることが分かった。From the X-ray diffraction analysis of the above sintered body, it was found that the structure of each sintered body was composed of β-SiC, Nb-Al alloy composition and Nb-Al-C alloy composition.
【００２２】また、焼結体の室温における曲げ強度は３
５０ＭＰａ以上の高強度を有することが分かった。表１
に曲げ強度を示す。Ｎｂ75Ａｌ25が２vol％では、焼結
体の緻密化が不十分なために強度が若干低い。また、Ｎ
ｂ75Ａｌ25が６０vol％ではＮｂ75Ａｌ25の強度が支配
的になり、明らかに強度の低下が認められる。これらの
結果からＮｂ75Ａｌ25の配合量は２〜５０vol％が好ま
しい。β−ＳｉＣの代わりにα−ＳｉＣ粉末を用いても
同様に高強度セラミックス材が得られた。The bending strength of the sintered body at room temperature is 3
It was found to have a high strength of 50 MPa or more. Table 1
Shows the bending strength. When Nb 75 Al 25 is 2 vol%, the strength is slightly low due to insufficient densification of the sintered body. Also, N
When b 75 Al 25 is 60 vol%, the strength of Nb 75 Al 25 becomes dominant, and a clear decrease in strength is observed. From these results, the compounding amount of Nb 75 Al 25 is preferably 2 to 50 vol%. Even if α-SiC powder was used instead of β-SiC, a high-strength ceramic material was similarly obtained.
【００２３】また、表２の比較例より、ＮｂあるいはＡ
ｌのみの添加では、その効果はほとんど得られないこと
が分かる。Further, according to the comparative example of Table 2, Nb or A
It can be seen that the effect is hardly obtained when only 1 is added.
【００２４】[0024]
【表１】 [Table 1]
【００２５】[0025]
【表２】 [Table 2]
【００２６】〔実施例９〜２７〕実施例１と同様に、Ｓ
ｉＣの代わりに他の非酸化物系セラミックスとの組合せ
について検討を行なった。結果を表３に示す。Ｎｂ75Ａ
ｌ25合金の添加量は１０vol％一定とした。表３の曲げ
強度から分かるように、いずれの焼結体も優れた強度を
有する。[Embodiments 9 to 27] As in Embodiment 1, S
The combination with other non-oxide type ceramics was examined instead of iC. The results are shown in Table 3. Nb 75 A
The addition amount of the l 25 alloy was 10 vol% constant. As can be seen from the bending strength in Table 3, all the sintered bodies have excellent strength.
【００２７】いずれもＮｂ75Ａｌ25合金が非酸化物系セ
ラミックスと反応して生成したＮｂ−Ａｌ−Ｃ系、Ｎｂ
−Ａｌ−Ｎ系、Ｎｂ−Ａｌ−Ｂ系などの合金組成が粒界
を構成しており、これが優れた強度をもたらしていると
推定される。In both cases, Nb 75 Al 25 alloy was formed by reacting with non-oxide ceramics, Nb-Al-C system, Nb
It is presumed that an alloy composition such as -Al-N-based or Nb-Al-B-based constitutes a grain boundary, which brings about excellent strength.
【００２８】[0028]
【表３】 [Table 3]
【００２９】〔実施例２８〜６６〕実施例１と同様に、
各種のＮｂ−Ａｌ系合金を添加し検討を行った。結果を
表４，表５に示す。[Embodiments 28 to 66] Similar to Embodiment 1,
Various Nb-Al based alloys were added and studied. The results are shown in Tables 4 and 5.
【００３０】各合金は、各金属粉末を溶解しこれに必要
な元素を添加させることにより作製することができる。
これを粉砕し微粒化し焼結助剤として使用する。また、
焼結中にセラミック粉末とＮｂ−Ａｌ系合金とを反応さ
せることにより粒界を形成することも可能である。Ｎｂ
−Ａｌ系合金を添加することにより優れた強度を示すこ
とが分かった。Each alloy can be prepared by melting each metal powder and adding necessary elements thereto.
This is crushed into fine particles and used as a sintering aid. Also,
It is also possible to form grain boundaries by reacting the ceramic powder and the Nb-Al-based alloy during sintering. Nb
It has been found that the addition of the -Al-based alloy exhibits excellent strength.
【００３１】[0031]
【表４】 [Table 4]
【００３２】[0032]
【表５】 [Table 5]
【００３３】〔実施例６７〜７５〕実施例２と同様に、
組成比の異なるＮｂ−Ａｌ合金を添加し検討を行った。
結果を表６に示す。これにより、Ｎｂ−Ａｌ合金の組成
比はＮｂ90Ａｌ10〜Ｎｂ10Ａｌ90合金が適していること
が分かる。[Examples 67 to 75] Similar to Example 2,
A study was conducted by adding Nb-Al alloys having different composition ratios.
The results are shown in Table 6. From this, it is understood that the composition ratio of the Nb-Al alloy is preferably Nb 90 Al 10 to Nb 10 Al 90 alloy.
【００３４】[0034]
【表６】 [Table 6]
【００３５】〔実施例７６〕上記実施例１〜７５で得ら
れた焼結体表面に、溶射によりＺｒＯ2をコーティング
した。そして、大気中１５００℃で１００時間耐酸化試
験を行った。その結果、ＺｒＯ2とＮｂ−Ａｌ合金とは
密着性が優れており剥離が生じることも無く優れた耐酸
化性を示した。本発明の焼結体の表面をＺｒＯ2、Ａｌ2
Ｏ3などの酸化物で溶射またはＰＶＤなどでコ−ティン
グすることより耐酸化性を向上させることが可能であ
る。Example 76 The surface of the sintered body obtained in Examples 1 to 75 was coated with ZrO 2 by thermal spraying. Then, an oxidation resistance test was performed at 1500 ° C. in the air for 100 hours. As a result, ZrO 2 and the Nb-Al alloy were excellent in adhesiveness and showed excellent oxidation resistance without peeling. If the surface of the sintered body of the present invention is ZrO 2 , Al 2
Oxidation resistance can be improved by thermal spraying with an oxide such as O 3 or coating with PVD.
【００３６】〔実施例７７〜８０〕Ｓｉ3Ｎ4にＮｂ75Ａ
ｌ25合金とその他の助剤を添加した場合について検討を
行なった。結果を表６に示す。得られたセラミックス材
を連続溶融アルミ金属めっき用ロール軸に適用した。図
１は、その連続溶融アルミ金属めっき装置を示し、ロー
ル軸８、サポートロール５に適用した。なお、軸受９に
はＣ／Ｃコンポジットを適用した。[Examples 77 to 80] Si 3 N 4 and Nb 75 A
It was performed studied case of adding l 25 alloy and other auxiliaries. The results are shown in Table 6. The obtained ceramic material was applied to a roll shaft for continuous hot dip aluminum metal plating. FIG. 1 shows the continuous molten aluminum metal plating apparatus, which is applied to a roll shaft 8 and a support roll 5. A C / C composite was applied to the bearing 9.
【００３７】上記の装置を６５０℃のＡｌ浴中で連続め
っき作業を行いその摩耗による寿命を比較した、結果を
表７に示す。The above equipment was subjected to continuous plating work in an Al bath at 650 ° C., and the lives due to abrasion were compared, and the results are shown in Table 7.
【００３８】従来の鋼ロール軸および軸受の寿命が３日
であるのに対して、本実施例のものは３か月以上の連続
使用にも異常な摩耗は見受けられず、均一なめっき作業
を行なうことができた。In contrast to the conventional steel roll shaft and bearing having a life of 3 days, in the case of this embodiment, no abnormal wear is observed even after continuous use for 3 months or more, and uniform plating work is performed. I was able to do it.
【００３９】これより、Ｎｂ75Ａｌ25合金が添加されて
いない焼結体（実施例７８，８０）では寿命が短く耐摩
耗性に劣る。本実施例のものが優れているのはＮｂ−Ａ
ｌ系＋焼結助剤によるサーメット組織により耐摩耗性が
著しく向上したものと考える。As a result, the sintered bodies (Examples 78 and 80) to which the Nb 75 Al 25 alloy was not added had a short life and poor wear resistance. The thing of this example is excellent in Nb-A.
It is considered that the wear resistance was remarkably improved by the cermet structure of the 1 type + sintering aid.
【００４０】[0040]
【表７】 [Table 7]
【００４１】〔実施例８１〜８２〕酸化物系セラミック
スとの組合せについて検討を行なった結果を表８に示
す。Ｎｂ75Ａｌ25合金の添加量は１０vol％一定とし実
施例１と同様に焼結した。各焼結体の強度を表８に示
す。Ｎｂ75Ａｌ25合金と酸化物系セラミックスとが反応
して生成したＮｂ−Ａｌ−Ｏ系、Ｎｂ−Ａｌ−Ｚｒ−Ｏ
系などの合金が粒界を構成し、これが優れた強度をもた
すものと考える。[Examples 81 to 82] Table 8 shows the results of an examination of combinations with oxide-based ceramics. Sintering was performed in the same manner as in Example 1 with the addition amount of the Nb 75 Al 25 alloy being constant at 10 vol%. Table 8 shows the strength of each sintered body. Nb 75 Al 25 alloy as oxide ceramics and is produced by the reaction was Nb-Al-O system, Nb-Al-Zr-O
It is considered that alloys such as a system form grain boundaries, which have excellent strength.
【００４２】酸化物セラミックスとＮｂ−Ａｌ系合金が
反応し、Ｎｂ−Ａｌ酸化物系化合物が粒界を構成すると
高温でのクリープ特性が低下するが、低温では問題な
い。When the oxide ceramics and the Nb-Al-based alloy react with each other and the Nb-Al oxide-based compound forms a grain boundary, the creep property at high temperature is deteriorated, but there is no problem at low temperature.
【００４３】[0043]
【表８】 [Table 8]
【００４４】〔実施例８３〕実施例９，１０，１２，１
７，２６，８１，８２で得られたセラミックス焼結体を
ダイヤモンド砥石で研削し、スローアウェイチップを作
製し、切削試験に共した。機械は池貝ＮＣ旋盤２５ｋＷ
を用い、送り：０.３６ｍｍ／回転、切削速度：５００
ｍ／分、切り込み：２.０ｍｍ、被削材：ＦＣ３０（直
径３００ｍｍ）、寿命判定：ＶＢ＝０.２ｍｍである。[Embodiment 83] Embodiments 9, 10, 12, 1
The ceramic sintered bodies obtained in Nos. 7, 26, 81 and 82 were ground with a diamond grindstone to produce throw-away tips, which were subjected to a cutting test. Machine is Ikegai NC lathe 25kW
With feed: 0.36 mm / revolution, cutting speed: 500
m / min, depth of cut: 2.0 mm, work material: FC30 (diameter 300 mm), life determination: VB = 0.2 mm.
【００４５】比較のために、ＴｉＣ分散Ｓｉ3Ｎ4系材
料，ＴｉＣ分散Ａｌ2Ｏ3系材料，ＮｂＣ分散Ｓｉ3Ｎ4系
材料についても同様に評価した。その結果、本発明の焼
結体の使用寿命は６０〜８０分であるのに対して、比較
材の寿命は３５〜４５分と短い。このことから、従来の
ような硬質の炭化物粒子などを分散した切削工具より
も、本発明の硬質のＮｂ−Ａｌ系のサーメット組織が存
在する切削工具が優れた耐摩耗性を有することが分かっ
た。For comparison, the TiC-dispersed Si 3 N 4 -based material, the TiC-dispersed Al 2 O 3 -based material, and the NbC-dispersed Si 3 N 4 -based material were similarly evaluated. As a result, the service life of the sintered body of the present invention is 60 to 80 minutes, while the life of the comparative material is short, 35 to 45 minutes. From this, it was found that the cutting tool having the hard Nb-Al cermet structure of the present invention has excellent wear resistance as compared with the conventional cutting tool in which hard carbide particles and the like are dispersed. .
【００４６】本発明の焼結体材料は、特に、鋳鉄製の各
種素材の切削工具として極めて有効なものである。The sintered material of the present invention is extremely effective as a cutting tool for various cast iron materials.
【００４７】〔実施例８４〕実施例９〜２７で得た焼結
体材料を、図１の連続溶融亜鉛金属めっき用ロールのロ
ール軸８、サポートロール５に適用した。軸受９にはＣ
／Ｃコンポジットを用いた。本装置を５００℃の亜鉛浴
中で連続めっき作業に使用した結果、従来の鋼のロール
軸および軸受の摩耗寿命が４日間であったのに対して、
実施例１８，１９，２６，２７は、３か月以上連続使用
しても異常な摩耗は見られず、均一なめっき作業を行な
うことができた。また、その他の実施例についても１か
月以上の寿命を有することが分かった。[Example 84] The sintered body materials obtained in Examples 9 to 27 were applied to the roll shaft 8 and the support roll 5 of the continuous hot-dip galvanizing metal roll shown in FIG. C for bearing 9
/ C composite was used. As a result of using this device for continuous plating in a zinc bath at 500 ° C., the wear life of the conventional steel roll shaft and bearing was 4 days, while
In Examples 18, 19, 26, and 27, no abnormal wear was observed even after continuous use for 3 months or more, and uniform plating work could be performed. It was also found that the other examples have a life of one month or more.
【００４８】特に，実施例２６，２７の硼化物／Ｎｂ−
Ａｌ系合金は、溶融金属との濡れ性が優れており、軸お
よび軸受の摩耗を飛躍的に低減でき、長時間メンテナン
スフリーで使用できると云う大きな効果がある。In particular, boride / Nb-of Examples 26 and 27
The Al-based alloy has excellent wettability with the molten metal, can significantly reduce wear of the shaft and the bearing, and has a great effect that it can be used for a long time without maintenance.
【００４９】また、硼化物／Ｎｂ−Ａｌ系合金の配合比
は、溶融金属との濡れ性より、５０／５０〜１０／９０
vol％が好ましく、特に、気孔率を３０vol％以下にする
ことが好ましい。The compounding ratio of boride / Nb-Al alloy is 50/50 to 10/90 depending on wettability with molten metal.
Vol% is preferable, and porosity is particularly preferably 30 vol% or less.
【００５０】〔実施例８５〕実施例９，１０，１１，１
２，８１，８２で得られた焼結体材料を用いて、図２の
エンジン用ピストンキャップ１１を作製し、鋳鉄製ピス
トン上部に焼きばめ法により嵌合してピストンを作製し
た。[Embodiment 85] Embodiments 9, 10, 11, and 1
Using the sintered body materials obtained in Nos. 2, 81 and 82, the engine piston cap 11 of FIG. 2 was manufactured and fitted to the upper part of the cast iron piston by the shrink fitting method to manufacture the piston.
【００５１】このピストンをディーゼルエンジンに組込
み、ガス温度８５０℃まで上昇させて３０分間運転し
た。いずれの部品も何ら異常は認められなかった。This piston was incorporated into a diesel engine, and the gas temperature was raised to 850 ° C. to operate for 30 minutes. No abnormality was found in any of the parts.
【００５２】また、同様にシリンダライナー（図３）、
タペット、シリンダーヘッド（図４）、バルブシート、
排気ポートライナー、ロッカーアーム（図５）、ターボ
チャージャーローターなどのエンジン部品に適用可能で
あることがわかった。Similarly, a cylinder liner (FIG. 3),
Tappet, cylinder head (Fig. 4), valve seat,
It was found to be applicable to engine parts such as exhaust port liners, rocker arms (Fig. 5), and turbocharger rotors.
【００５３】〔実施例８６〕実施例９，１０，１１，１
２，８１，８２で得られた焼結体材料の表面に溶射によ
りＺｒＯ2をコーティングした。これを用いて図６およ
び図７に示すガスタービン用動翼および静翼を作製し
た。本部材を現状の１３００℃級ガスタービンに組み込
み、１００時間運転を行なったが、何ら異常は見られな
かった。[Embodiment 86] Embodiments 9, 10, 11, and 1
The surface of the sintered material obtained in Nos. 2, 81 and 82 was coated with ZrO 2 by thermal spraying. Using this, the gas turbine moving blade and the stationary blade shown in FIGS. 6 and 7 were produced. This member was installed in a current 1300 ° C class gas turbine and operated for 100 hours, but no abnormality was observed.
【００５４】[0054]
【発明の効果】以上詳述したように、Ｎｂ−Ａｌ系合金
と焼結したセラミックスは、強度・耐摩耗性に優れたセ
ラミックスが得られる。また、本発明のセラミックス
は、無加圧焼結でも作製可能なため、複雑形状品に対応
でき高強度、耐摩耗性を要求される部品に適用可能であ
る。As described above in detail, the ceramics sintered with the Nb-Al alloy can provide ceramics excellent in strength and wear resistance. Further, since the ceramics of the present invention can be produced by pressureless sintering, the ceramics of the present invention can be applied to parts having complicated shapes and requiring high strength and wear resistance.
【図１】連続溶融金属めっき装置の構成図である。FIG. 1 is a configuration diagram of a continuous hot-dip metal plating apparatus.
【図２】ピストンの断面図である。FIG. 2 is a sectional view of a piston.
【図３】シリンダライナーの断面図である。FIG. 3 is a sectional view of a cylinder liner.
【図４】ピストンヘッドの断面図である。FIG. 4 is a sectional view of a piston head.
【図５】ロッカーアームの断面図である。FIG. 5 is a sectional view of a rocker arm.
【図６】セラミックガスタービン動翼の外観図である。FIG. 6 is an external view of a ceramic gas turbine rotor blade.
【図７】セラミックガスタービン静翼の外観図である。FIG. 7 is an external view of a ceramic gas turbine stationary blade.
１…スナウト、２…ストリップ、３…めっき槽、４…シ
ンクロール、５…サポートロール、６…めっき浴、７…
ワイピングノズル、８…ロール軸、９…ロール軸受、１
０…金属ピストン、１１…セラミックピストンキャッ
プ、１２…金属スリーブ、１３…セラミックライナー、
１４…セラミックピストンヘッド、１５…ロッカーアー
ム本体、１６…セラミックパッド、１７…金属製部材、
１８…翼部、１９…プラットフォーム部、２０…シール
フィン部、２１…シャンク部、２２…タブテーブル部、
２３…翼部、２４…サイドウォール部。1 ... Snout, 2 ... Strip, 3 ... Plating tank, 4 ... Sink roll, 5 ... Support roll, 6 ... Plating bath, 7 ...
Wiping nozzle, 8 ... Roll shaft, 9 ... Roll bearing, 1
0 ... metal piston, 11 ... ceramic piston cap, 12 ... metal sleeve, 13 ... ceramic liner,
14 ... Ceramic piston head, 15 ... Rocker arm body, 16 ... Ceramic pad, 17 ... Metal member,
18 ... Wing part, 19 ... Platform part, 20 ... Seal fin part, 21 ... Shank part, 22 ... Tab table part,
23 ... Wing part, 24 ... Sidewall part.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 尾花 健 茨城県日立市大みか町七丁目１番１号 株 式会社日立製作所日立研究所内 ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Ken Obana 7-1, 1-1 Omika-cho, Hitachi-shi, Ibaraki Hitachi Ltd. Hitachi Research Laboratory
Claims (14)
くとも１種を含むセラミックスの粒子がＮｂ−Ａｌ系合
金（但し、Ｃｕ，Ｃｏ，Ｎｉ，Ｆｅ系金属を除く）で結
合された焼結体からなることを特徴とする高強度・耐摩
耗性セラミックス。1. A firing method in which particles of ceramics containing at least one of carbide, nitride, boride, and oxide are combined with an Nb-Al-based alloy (excluding Cu, Co, Ni, and Fe-based metals). High-strength, wear-resistant ceramics characterized by being composed of a united body.
くとも１種を含むセラミックスの粒子が窒素，炭素，酸
素の少なくとも１種を固溶するＮｂ−Ａｌ系合金（但
し、Ｃｕ，Ｃｏ，Ｎｉ，Ｆｅ系金属を除く）で結合され
た焼結体であることを特徴とする高強度・耐摩耗性セラ
ミックス。2. An Nb-Al-based alloy (provided that Cu, Co, Cu, Co, etc.) in which particles of ceramics containing at least one of carbide, nitride, boride, and oxide form a solid solution with at least one of nitrogen, carbon, and oxygen. High-strength, wear-resistant ceramics, characterized in that it is a sintered body bonded by Ni and Fe-based metals).
が、ＳｉＣ，ＴｉＣ，ＺｒＣ，Ｃｒ3Ｃ2，ＨｆＣ，Ｔａ
Ｃ，Ｂ4Ｃ，Ｓｉ3Ｎ4，ＴｉＮ，ＡｌＮ，ＺｒＮ，Ｃｒ2
Ｎ，ＨｆＮ，ＴａＮ，ＢＮ，ＣｒＢ2，ＴｉＢ2，ＺｒＢ
2，ＴａＢ2，Ａｌ2Ｏ3，ＺｒＯ2の少なくとも１種から
なる請求項１または２に記載の高強度・耐摩耗性セラミ
ックス。3. The carbide, nitride, boride, or oxide is SiC, TiC, ZrC, Cr 3 C 2 , HfC, Ta.
C, B 4 C, Si 3 N 4 , TiN, AlN, ZrN, Cr 2
N, HfN, TaN, BN, CrB 2 , TiB 2 , ZrB
The high-strength and wear-resistant ceramics according to claim 1 or 2, comprising at least one of 2 , TaB 2 , Al 2 O 3 , and ZrO 2 .
Ｎｂ−Ａｌ−Ｎ系，Ｎｂ−Ａｌ−Ｃ系，Ｎｂ−Ａｌ−Ｏ
系，Ｎｂ−Ａｌ−Ｃ−Ｏ系，Ｎｂ−Ａｌ−Ｎ−Ｏ系，Ｎ
ｂ−Ａｌ−Ｎ−Ｃ系，Ｎｂ−Ａｌ−Ｎ−Ｃ−Ｏ系，Ｎｂ
−Ａｌ−Ｔｉ−Ｃ系，Ｎｂ−Ａｌ−Ｔｉ−Ｎ系，Ｎｂ−
Ａｌ−Ｔｉ−Ｃ−Ｏ系，Ｎｂ−Ａｌ−Ｔｉ−Ｎ−Ｏ系，
Ｎｂ−Ａｌ−Ｔｉ−Ｃ−Ｂ−Ｏ系，Ｎｂ−Ａｌ−Ｔｉ−
Ｎ−Ｂ−Ｏ系，Ｎｂ−Ａｌ−Ｚｒ−Ｏ系，Ｎｂ−Ａｌ−
Ｚｒ−Ｎ系，Ｎｂ−Ａｌ−Ｚｒ−Ｃ系，Ｎｂ−Ａｌ−Ｚ
ｒ−Ｎ−Ｏ系，Ｎｂ−Ａｌ−Ｚｒ−Ｃ−Ｏ系，Ｎｂ−Ａ
ｌ−Ｚｒ−Ｎ−Ｂ−Ｏ系，Ｎｂ−Ａｌ−Ｚｒ−Ｃ−Ｂ−
Ｏ系，Ｎｂ−Ａｌ−Ｓｉ−Ｎ系，Ｎｂ−Ａｌ−Ｓｉ−Ｃ
系，Ｎｂ−Ａｌ−Ｓｉ−Ｎ−Ｏ系，Ｎｂ−Ａｌ−Ｓｉ−
Ｃ−Ｏ系，Ｎｂ−Ａｌ−Ｃｒ−Ｎ系，Ｎｂ−Ａｌ−Ｃｒ
−Ｃ系，Ｎｂ−Ａｌ−Ｃｒ−Ｎ−Ｏ系，Ｎｂ−Ａｌ−Ｃ
ｒ−Ｃ−Ｏ系，Ｎｂ−Ａｌ−Ｈｆ−Ｎ系，Ｎｂ−Ａｌ−
Ｈｆ−Ｃ系，Ｎｂ−Ａｌ−Ｈｆ−Ｎ−Ｏ系，Ｎｂ−Ａｌ
−Ｈｆ−Ｃ−Ｏ系，Ｎｂ−Ａｌ−Ｔａ−Ｎ系，Ｎｂ−Ａ
ｌ−Ｔａ−Ｃ系，Ｎｂ−Ａｌ−Ｔａ−Ｎ−Ｏ系，Ｎｂ−
Ａｌ−Ｔａ−Ｃ−Ｏ系，Ｎｂ−Ａｌ−Ｔａ−Ｎ−Ｂ−Ｏ
系，Ｎｂ−Ａｌ−Ｔａ−Ｃ−Ｂ−Ｏ系，Ｎｂ−Ａｌ−Ｂ
−Ｎ系，Ｎｂ−Ａｌ−Ｂ−Ｃ系，Ｎｂ−Ａｌ−Ｂ−Ｎ−
Ｏ系，Ｎｂ−Ａｌ−Ｂ−Ｃ−Ｏ系合金の少なくとも１種
からなる請求項１，２または３に記載の高強度・耐摩耗
性セラミックス。4. The Nb-Al-based alloy is Nb-Al-based,
Nb-Al-N system, Nb-Al-C system, Nb-Al-O
System, Nb-Al-C-O system, Nb-Al-N-O system, N
b-Al-NC system, Nb-Al-NC-O system, Nb
-Al-Ti-C system, Nb-Al-Ti-N system, Nb-
Al-Ti-CO system, Nb-Al-Ti-NO system,
Nb-Al-Ti-C-B-O system, Nb-Al-Ti-
N-B-O type, Nb-Al-Zr-O type, Nb-Al-
Zr-N system, Nb-Al-Zr-C system, Nb-Al-Z
r-N-O system, Nb-Al-Zr-C-O system, Nb-A
1-Zr-N-B-O system, Nb-Al-Zr-C-B-
O type, Nb-Al-Si-N type, Nb-Al-Si-C
System, Nb-Al-Si-N-O system, Nb-Al-Si-
C-O type, Nb-Al-Cr-N type, Nb-Al-Cr
-C system, Nb-Al-Cr-N-O system, Nb-Al-C
r-C-O system, Nb-Al-Hf-N system, Nb-Al-
Hf-C type, Nb-Al-Hf-N-O type, Nb-Al
-Hf-CO system, Nb-Al-Ta-N system, Nb-A
1-Ta-C system, Nb-Al-Ta-NO system, Nb-
Al-Ta-CO system, Nb-Al-Ta-N-B-O
System, Nb-Al-Ta-C-B-O system, Nb-Al-B
-N system, Nb-Al-B-C system, Nb-Al-B-N-
The high-strength, wear-resistant ceramics according to claim 1, comprising at least one of O-based and Nb-Al-B-C-O-based alloys.
含む請求項１〜４のいずれかに記載の高強度・耐摩耗性
セラミックス。5. The Nb-Al alloy is 2 to 50 vol%
The high-strength and wear-resistant ceramics according to any one of claims 1 to 4.
ｉ3Ｎ4，Ｓｉ−Ｔｉ−Ｃ−Ｏ系，Ｓｉ2Ｎ2Ｏ，Ａｌ2Ｏ3
の少なくとも１種からなる短繊維ウイスカーおよび／ま
たは長繊維を含む請求項１〜５のいずれかに記載の高強
度・耐摩耗性セラミックス。6. Carbon, SiC, S in ceramics
i 3 N 4, Si-Ti -C-O -based, Si 2 N 2 O, Al 2 O 3
The high-strength and wear-resistant ceramics according to any one of claims 1 to 5, which comprises a short fiber whisker and / or a long fiber made of at least one of the above.
くとも１種を含む粉末、Ｎｂ−Ａｌ系合金（但し、Ｃ
ｕ，Ｃｏ，Ｎｉ，Ｆｅ系金属を除く）粉末および成形用
バインダの混合粉末を用いて成形体を作製し、該成形体
を真空中，不活性ガス中あるいは不活性ガスと還元性ガ
スの混合ガス中で１７００〜２４００℃，５〜３００分
加熱して焼結することを特徴とする高強度・耐摩耗性セ
ラミックスの製法。7. A powder containing at least one of carbides, nitrides, borides, and oxides, and an Nb—Al-based alloy (provided that C is used).
u, Co, Ni, Fe-based metal) and a molding binder are used to prepare a molded body, and the molded body is vacuumed, in an inert gas, or mixed with an inert gas and a reducing gas. A method for producing high-strength and wear-resistant ceramics, which comprises heating in gas at 1700 to 2400 ° C. for 5 to 300 minutes to sinter.
くとも１種を含む粉末、Ｎｂ−Ａｌ系合金（但し、Ｃ
ｕ，Ｃｏ，Ｎｉ，Ｆｅ系金属を除く）粉末、焼結促進用
酸化物粉末および成形バインダの混合粉末を用いて成形
体を作製し、該成形体を真空中，不活性ガス中あるいは
不活性ガスと還元性ガスの混合ガス中で１７００〜２４
００℃，５〜３００分加熱して焼結することを特徴とす
る高強度・耐摩耗性セラミックスの製法。8. A powder containing at least one of carbides, nitrides, borides, and oxides, and an Nb-Al-based alloy (however, C
(except u, Co, Ni, Fe-based metals) powder, sintering-promoting oxide powder, and a mixed powder of a molding binder to prepare a molded body, and the molded body is vacuumed, in an inert gas, or inert. 1700-24 in mixed gas of gas and reducing gas
A method for producing high-strength, wear-resistant ceramics, characterized by heating at 00 ° C for 5 to 300 minutes for sintering.
が、ＳｉＣ，ＴｉＣ，ＺｒＣ，Ｃｒ3Ｃ2，ＨｆＣ，Ｔａ
Ｃ，Ｂ4Ｃ，Ｓｉ3Ｎ4，ＴｉＮ，ＡｌＮ，ＺｒＮ，Ｃｒ2
Ｎ，ＨｆＮ，ＴａＮ，ＢＮ，ＣｒＢ2，ＴｉＢ2，ＺｒＢ
2，ＴａＢ2，Ａｌ2Ｏ3，ＺｒＯ2の少なくとも１種から
なる請求項７または８に記載の高強度・耐摩耗性セラミ
ックスの製法。9. The carbide, nitride, boride, or oxide is SiC, TiC, ZrC, Cr 3 C 2 , HfC, Ta.
C, B 4 C, Si 3 N 4 , TiN, AlN, ZrN, Cr 2
N, HfN, TaN, BN, CrB 2 , TiB 2 , ZrB
The method for producing a high-strength and wear-resistant ceramic according to claim 7 or 8, comprising at least one of 2 , TaB 2 , Al 2 O 3 and ZrO 2 .
Ａｌ系，Ｎｂ−Ａｌ−Ｎ系，Ｎｂ−Ａｌ−Ｃ系，Ｎｂ−
Ａｌ−Ｏ系，Ｎｂ−Ａｌ−Ｃ−Ｏ系，Ｎｂ−Ａｌ−Ｎ−
Ｏ系，Ｎｂ−Ａｌ−Ｎ−Ｃ系，Ｎｂ−Ａｌ−Ｎ−Ｃ−Ｏ
系，Ｎｂ−Ａｌ−Ｔｉ−Ｃ系，Ｎｂ−Ａｌ−Ｔｉ−Ｎ
系，Ｎｂ−Ａｌ−Ｔｉ−Ｃ−Ｏ系，Ｎｂ−Ａｌ−Ｔｉ−
Ｎ−Ｏ系，Ｎｂ−Ａｌ−Ｔｉ−Ｃ−Ｂ−Ｏ系，Ｎｂ−Ａ
ｌ−Ｔｉ−Ｎ−Ｂ−Ｏ系，Ｎｂ−Ａｌ−Ｚｒ−Ｎ系，Ｎ
ｂ−Ａｌ−Ｚｒ−Ｏ系，Ｎｂ−Ａｌ−Ｚｒ−Ｃ系，Ｎｂ
−Ａｌ−Ｚｒ−Ｎ−Ｏ系，Ｎｂ−Ａｌ−Ｚｒ−Ｃ−Ｏ
系，Ｎｂ−Ａｌ−Ｚｒ−Ｎ−Ｂ−Ｏ系，Ｎｂ−Ａｌ−Ｚ
ｒ−Ｃ−Ｂ−Ｏ系，Ｎｂ−Ａｌ−Ｓｉ−Ｎ系，Ｎｂ−Ａ
ｌ−Ｓｉ−Ｃ系，Ｎｂ−Ａｌ−Ｓｉ−Ｎ−Ｏ系，Ｎｂ−
Ａｌ−Ｓｉ−Ｃ−Ｏ系，Ｎｂ−Ａｌ−Ｃｒ−Ｎ系，Ｎｂ
−Ａｌ−Ｃｒ−Ｃ系，Ｎｂ−Ａｌ−Ｃｒ−Ｎ−Ｏ系，Ｎ
ｂ−Ａｌ−Ｃｒ−Ｃ−Ｏ系，Ｎｂ−Ａｌ−Ｈｆ−Ｎ系，
Ｎｂ−Ａｌ−Ｈｆ−Ｃ系，Ｎｂ−Ａｌ−Ｈｆ−Ｎ−Ｏ
系，Ｎｂ−Ａｌ−Ｈｆ−Ｃ−Ｏ系，Ｎｂ−Ａｌ−Ｔａ−
Ｎ系，Ｎｂ−Ａｌ−Ｔａ−Ｃ系，Ｎｂ−Ａｌ−Ｔａ−Ｎ
−Ｏ系，Ｎｂ−Ａｌ−Ｔａ−Ｃ−Ｏ系，Ｎｂ−Ａｌ−Ｔ
ａ−Ｎ−Ｂ−Ｏ系，Ｎｂ−Ａｌ−Ｔａ−Ｃ−Ｂ−Ｏ系，
Ｎｂ−Ａｌ−Ｂ−Ｎ系，Ｎｂ−Ａｌ−Ｂ−Ｃ系，Ｎｂ−
Ａｌ−Ｂ−Ｎ−Ｏ系，Ｎｂ−Ａｌ−Ｂ−Ｃ−Ｏ系合金の
少なくとも１種からなる請求項７，８または９に記載の
高強度・耐摩耗性セラミックスの製法。10. The Nb—Al alloy powder is Nb—
Al-based, Nb-Al-N-based, Nb-Al-C-based, Nb-
Al-O type, Nb-Al-C-O type, Nb-Al-N-
O type, Nb-Al-N-C type, Nb-Al-N-C-O
System, Nb-Al-Ti-C system, Nb-Al-Ti-N
System, Nb-Al-Ti-C-O system, Nb-Al-Ti-
N-O system, Nb-Al-Ti-C-B-O system, Nb-A
1-Ti-N-B-O system, Nb-Al-Zr-N system, N
b-Al-Zr-O system, Nb-Al-Zr-C system, Nb
-Al-Zr-N-O system, Nb-Al-Zr-C-O
System, Nb-Al-Zr-N-B-O system, Nb-Al-Z
r-C-B-O system, Nb-Al-Si-N system, Nb-A
1-Si-C system, Nb-Al-Si-N-O system, Nb-
Al-Si-C-O system, Nb-Al-Cr-N system, Nb
-Al-Cr-C system, Nb-Al-Cr-NO system, N
b-Al-Cr-CO system, Nb-Al-Hf-N system,
Nb-Al-Hf-C system, Nb-Al-Hf-N-O
System, Nb-Al-Hf-CO system, Nb-Al-Ta-
N type, Nb-Al-Ta-C type, Nb-Al-Ta-N
-O system, Nb-Al-Ta-C-O system, Nb-Al-T
a-N-B-O system, Nb-Al-Ta-C-B-O system,
Nb-Al-BN system, Nb-Al-BC system, Nb-
The method for producing high-strength, wear-resistant ceramics according to claim 7, 8 or 9, comprising at least one of an Al-B-N-O type alloy and an Nb-Al-B-C-O type alloy.
ｌ90〜Ｎｂ90Ａｌ10の合金である請求項７，８または９
に記載の高強度・耐摩耗性セラミックスの製法。11. The Nb—Al alloy powder is Nb 10 A.
l 90 alloy to NB 90 Al 10 claim 7, 8 or 9
Manufacturing method of high-strength and wear-resistant ceramics described in.
2Ｏ3，Ｙ2Ｏ3，ＢｅＯ，ＴｉＯ2，ＺｒＯ2，ＳｉＯ2，
Ｃｒ2Ｏ3，希土類酸化物の少なくとも１種である請求項
８に記載の高強度・耐摩耗性セラミックスの製法。12. The oxide powder for accelerating sintering is Al.
2 O 3 , Y 2 O 3 , BeO, TiO 2 , ZrO 2 , SiO 2 ,
The method for producing a high-strength, wear-resistant ceramic according to claim 8, wherein the ceramic is at least one of Cr 2 O 3 and a rare earth oxide.
む請求項７〜１２のいずれかに記載の高強度・耐摩耗性
セラミックスの製法。13. The method for producing a high-strength and wear-resistant ceramic according to claim 7, wherein the Nb-Al based alloy contains 2 to 50 vol%.
５vol％含む請求項８〜１３のいずれかに記載の高強度
・耐摩耗性セラミックスの製法。14. The oxide powder for accelerating sintering is 0.1 to 0.1.
The method for producing the high-strength and wear-resistant ceramics according to any one of claims 8 to 13, containing 5 vol%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5206224A JP2978375B2 (en) | 1993-08-20 | 1993-08-20 | High strength and wear resistant ceramics and their manufacturing method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5206224A JP2978375B2 (en) | 1993-08-20 | 1993-08-20 | High strength and wear resistant ceramics and their manufacturing method |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0762481A true JPH0762481A (en) | 1995-03-07 |
| JP2978375B2 JP2978375B2 (en) | 1999-11-15 |
Family
ID=16519824
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP5206224A Expired - Lifetime JP2978375B2 (en) | 1993-08-20 | 1993-08-20 | High strength and wear resistant ceramics and their manufacturing method |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2978375B2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103552099A (en) * | 2013-09-29 | 2014-02-05 | 河南华茂新材料科技开发有限公司 | High-strength ceramic ultrathin cutting blade and production method thereof |
| CN115323324A (en) * | 2022-07-28 | 2022-11-11 | 中国科学院金属研究所 | Wear-resistant, corrosion-resistant and oxidation-resistant fiber crystal chromium-nitrogen thick film and preparation method thereof |
-
1993
- 1993-08-20 JP JP5206224A patent/JP2978375B2/en not_active Expired - Lifetime
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103552099A (en) * | 2013-09-29 | 2014-02-05 | 河南华茂新材料科技开发有限公司 | High-strength ceramic ultrathin cutting blade and production method thereof |
| CN115323324A (en) * | 2022-07-28 | 2022-11-11 | 中国科学院金属研究所 | Wear-resistant, corrosion-resistant and oxidation-resistant fiber crystal chromium-nitrogen thick film and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2978375B2 (en) | 1999-11-15 |
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