JPH05319935A - Sintered tib2 ceramic - Google Patents
Sintered tib2 ceramicInfo
- Publication number
- JPH05319935A JPH05319935A JP3282730A JP28273091A JPH05319935A JP H05319935 A JPH05319935 A JP H05319935A JP 3282730 A JP3282730 A JP 3282730A JP 28273091 A JP28273091 A JP 28273091A JP H05319935 A JPH05319935 A JP H05319935A
- Authority
- JP
- Japan
- Prior art keywords
- binder
- tib2
- tib
- tin
- sintered body
- 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.)
- Withdrawn
Links
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、ＴｉＢ2 セラミックス
焼結体に関し、特に例えば軸受鋼等の高硬度材料の高速
切削加工に用いて最適なものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a TiB 2 ceramics sintered body, and is most suitable for high speed cutting of a high hardness material such as bearing steel.
【０００２】[0002]
【従来の技術】従来において、被削材の硬度がロック・
ウェル硬さ（ＨRC）で、６０以上の高硬度材料の加工
は、切削加工が困難であるため、主としてダイヤモンド
砥粒等による研削加工を行っている。しかしながら該研
削加工は、加工速度が遅いため、工程短縮が思うように
ならない。2. Description of the Related Art Conventionally, the hardness of the work material is locked.
Since it is difficult to cut a high hardness material having a well hardness (H RC ) of 60 or more, a grinding process is mainly performed by using diamond abrasive grains or the like. However, since the grinding process has a low processing speed, the process cannot be shortened.
【０００３】この問題を解決するため、高硬度材料を切
削加工する工具として、ＷＣ−Ｃｏを主成分とする超
硬合金工具、ＴｉＣ−ＴｉＮと−Ｎｉ−Ｍｏ系のサー
メット工具、Ａｌ2 Ｏ3 を主成分とするセラミックス
工具、ＣＢＮ粒子を高温高圧で焼結したＣＢＮ焼結工
具が種々開発されており、新しい機械加工の分野が展開
されつつある。そしてこの高硬度材料の切削加工用工具
としては、（イ）工具摩耗量が小さいこと、（ロ）切削
された被削材料の加工面粗さが良好なこと、等の性能が
必要とされている。[0003] To solve this problem, a tool for cutting a high-hardness material, cemented carbide tools mainly composed of WC-Co, TiC-TiN and -Ni-Mo cermet tool, Al 2 O 3 Various ceramic tools containing C as a main component and CBN sintering tools obtained by sintering CBN particles at high temperature and high pressure have been developed, and a new field of machining is being developed. And as a cutting tool for this high hardness material, performance such as (a) small amount of tool wear, (b) good cut surface roughness of the cut work material, etc. is required. There is.
【０００４】[0004]
【発明が解決しようとする課題】しかしながら上述した
高硬度材料用工具のうち、超硬合金工具やサーメット工
具は金属バインダが加工時の発熱により塑性変形を起こ
し、摩耗が短時間に進行するため適用できないという問
題がある。また、セラミックス工具は、超硬合金やサー
メットと比較して欠損しやすいこと、及びピッチング
（微小領域での剥離亀裂現象をいう）を起こしやすいこ
とから、加工面の粗さが悪く、適用できないという問題
がある。更に、ＣＢＮ焼結工具は高硬度材料の切削加工
用の要求性能には合致しているものの、ＣＢＮを焼結す
るために１６００℃以上の高温及び５万気圧以上の高圧
が必要であると共に製造設備が特殊なもので高価とな
り、該ＣＢＮ焼結工具の製造は非常に高価になるという
問題がある。However, among the above-mentioned tools for high hardness materials, cemented carbide tools and cermet tools are applied because the metal binder causes plastic deformation due to heat generated during processing and wear progresses in a short time. There is a problem that you can not. In addition, ceramic tools are more likely to be chipped than cemented carbide or cermet, and are more likely to cause pitting (which is a phenomenon of peeling cracks in a minute area), so that the roughness of the machined surface is poor and it cannot be applied. There's a problem. Further, although the CBN sintering tool meets the required performance for cutting hard materials, it requires a high temperature of 1600 ° C or higher and a high pressure of 50,000 atmospheres or more to sinter CBN. There is a problem that the equipment is special and expensive, and the manufacturing of the CBN sintering tool is very expensive.
【０００５】本発明はこのような事情に鑑み、高硬度材
料の高速切削加工に用いて最適なＴｉＢ2 セラミックス
焼結体を提供することを目的とする。In view of such circumstances, it is an object of the present invention to provide an optimal TiB 2 ceramics sintered body which is used for high speed cutting of a high hardness material.
【０００６】[0006]
【課題を解決するための手段】前記目的を達成する本発
明に係るＴｉＢ2 セラミックス焼結体は、３０〜７０体
積％のＴｉＢ2 と、バインダの主成分としてのＴｉＮと
混合粉末を焼結してなることを特徴とし、また、上記Ｔ
ｉＢ2 セラミックス焼結体バインダの一部をＡｌＮ，Ｓ
ｉＣ，Ａｌ2 Ｏ3 及びＺｒＯ2 より選ばれた一種以上で
置換したことを特徴とする。A TiB 2 ceramics sintered body according to the present invention, which achieves the above object, is obtained by sintering 30 to 70% by volume of TiB 2 and TiN as a main component of a binder and a mixed powder. In addition, the above T
Part of the iB 2 ceramics sintered body binder is AlN, S
It is characterized in that it is substituted with one or more selected from iC, Al 2 O 3 and ZrO 2 .
【０００７】以下、本発明の内容を説明する。本発明Ｔ
ｉＢ2 セラミックス焼結体の模式断面図を図１に示す。
ＴｉＢ2 セラミックス焼結体１１は主成分のＴｉＢ2 粒
子１２と、バインダ１３とで構成されてなるものであ
る。本発明に係るＴｉＢ2 セラミックス焼結体は、Ｔｉ
Ｂ2 粒子１２を３０〜７０体積％用いる。本発明でＴｉ
Ｂ2 を主成分とするのは、ＣＢＮやダイヤモンドに次ぐ
硬さを備えており、優れた耐摩耗性を示すためである。
またＣＢＮ等と異なり、特殊な圧力を必要とせず焼結で
き作業性が向上する。ここでＴｉＢ2 粒子１２を３０〜
７０体積％とするのは、３０体積％未満では、硬さが低
下し欠損しやすくなり、一方、７０体積％を超えても、
ＴｉＢ2 粒子の脱落をバインダが防止できず、被削材の
表面粗さを低下させるため、共に好ましくないからであ
る。また、図１に示したように本発明では、骨格層とし
てＴｉＢ2 粒子１２を用いており、従って、サブミクロ
ン単位のものより、0.５μｍ以上、５μｍ以下程度の原
料が望ましい。これは微細な粒子を用いると、バインダ
部に混入しバインダの接着特性を大きく低下させ好まし
くないからである。The contents of the present invention will be described below. Invention T
A schematic sectional view of the iB 2 ceramics sintered body is shown in FIG.
The TiB 2 ceramics sintered body 11 is composed of TiB 2 particles 12 as a main component and a binder 13. The TiB 2 ceramics sintered body according to the present invention is made of Ti
30 to 70% by volume of B 2 particles 12 are used. In the present invention Ti
The main component of B 2 is that it has hardness second only to CBN and diamond and exhibits excellent wear resistance.
Further, unlike CBN or the like, it can be sintered without requiring a special pressure and workability is improved. Here, the TiB 2 particles 12 are
When the content is 70% by volume, when the content is less than 30% by volume, the hardness is lowered and the chip tends to be lost.
This is because the binder cannot prevent the TiB 2 particles from coming off and the surface roughness of the work material is reduced, which is not preferable. Further, as shown in FIG. 1, in the present invention, the TiB 2 particles 12 are used as the skeleton layer. Therefore, it is preferable to use a raw material having a size of 0.5 μm or more and 5 μm or less rather than a submicron unit. This is because the use of fine particles is not preferable because it mixes in the binder portion and the adhesive property of the binder is greatly deteriorated.
【０００８】バインダ１３は、ＴｉＮを主成分とする。
ＴｉＮとセラミックスのなかでは特殊な室温でも塑性変
形する金属的な性質を持っている。また、ＴｉＢ2 粒子
１２との接合性も高いため、これ等により、焼結体を強
固で粘り強いものにする効果がある。但し、硬さが、他
のセラミックス材と比較して小さいため、これを改善す
るため、高硬度材加工等、高硬度が必要な場合にはその
一部をＡｌＮ，ＳｉＣ，Ａｌ2 Ｏ3 及びＺｒＯ2 等で置
換する。これらの置換材は、焼結体中でSialon化合物を
形成し高強度の焼結体にする。また、この反応により、
ＳｉＣのＣが遊離するため、このＣがＴｉＮの硬さを上
げる効果が見られる。The binder 13 has TiN as a main component.
Among TiN and ceramics, it has a metallic property of being plastically deformed even at a special room temperature. Further, since it has a high bondability with the TiB 2 particles 12, these have an effect of making the sintered body strong and tenacious. However, since the hardness is smaller than that of other ceramic materials, in order to improve this, when high hardness is required such as in processing of high hardness material, a part of AlN, SiC, Al 2 O 3 and Substitute with ZrO 2 . These substitution materials form a Sialon compound in the sintered body to make a high-strength sintered body. Also, due to this reaction,
Since C of SiC is released, this C has an effect of increasing the hardness of TiN.
【０００９】以上のように構成された焼結体は、特に、
従来のセラミックス工具の課題であった高硬度被削材の
断続切削加工時の耐欠損性を著しく高める作用がある。The sintered body constructed as above is
It has the effect of significantly increasing the fracture resistance during interrupted cutting of high hardness work materials, which has been a problem of conventional ceramics tools.
【００１０】[0010]
【実施例】以下、本発明の好適な一実施例について詳細
に説明する。DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS A preferred embodiment of the present invention will be described in detail below.
【００１１】（焼結体の製造方法例）ＴｉＢ2 粒子は、
平均径が１μｍの市販の研磨材用を用いた。ＴｉＮ，Ａ
ｌＮ，ＳｉＣ，Ａｌ2 Ｏ3 ，ＺｒＮ2 のバインダ成分
は、気相合成法や、共沈法等、製法は異なるが、いずれ
も一次粒子の平均径が、0.５μｍ以下のサブミクロン粒
子を用いた。これらを原料として用い、下記「表１」に
記載の組成に配合し、更にエタノールを加えて湿式混合
し、次いで乾燥して原料粉を得た。この原料粉を所定の
温度で真空中でホットプレス（圧力４００kgf ／cm2 ）
し、焼結した。その後、スローアウェイチップ（ＩＳＯ
記号ＳＮＭＮ４３2(加工後寸法１2.７mm×１2.７mm×4.
７６mm、コーナ半径0.８mm））の形状に加工して工具と
した。(Example of method for producing sintered body) TiB 2 particles are
A commercially available abrasive having an average diameter of 1 μm was used. TiN, A
The binder components of 1N, SiC, Al 2 O 3 and ZrN 2 are different in the production method such as the vapor phase synthesis method and the coprecipitation method, but the average diameter of the primary particles is submicron particles of 0.5 μm or less. Using. Using these as raw materials, they were blended to the composition shown in the following "Table 1", ethanol was further added and wet mixed, and then dried to obtain raw material powder. This raw material powder is hot pressed in a vacuum at a predetermined temperature (pressure 400 kgf / cm 2 ).
And sintered. After that, throw away tip (ISO
Symbol SNMN432 (Dimensions after processing 12.7 mm x 12.7 mm x 4.
76 mm, corner radius 0.8 mm)) and processed into a tool.
【００１２】得られた工具を用い、以下の条件で切削試
験を行ない、それぞれの評価を行った。 ・被削材：ＳＵＪ２（ＨRC６２程度） ・切削速度：１００ｍ／min ・切り込み：0.１mm／rev ・送り：0.１mm／rev ・断続性能：欠損までの断続回数 この切削試験結果を表１に示す。尚、ここで比較材とし
たＣＢＮ焼結工具は、他社市販品である。Using the obtained tools, a cutting test was carried out under the following conditions to evaluate each of them. -Work material: SUJ2 (H RC 62 or so) -Cutting speed: 100 m / min-Cutting depth: 0.1 mm / rev-Feeding: 0.1 mm / rev-Intermittent performance: Intermittent frequency until breakage This cutting test result is shown. Shown in 1. The CBN sintering tool used as a comparative material here is a commercial product of another company.
【００１３】[0013]
【表１】 [Table 1]
【００１４】表１の結果より、本発明焼結体は、従来の
セラミックス工具と比較して、優れた耐欠損性を備えて
おり、高価なＣＢＮ焼結工具並の切削性能を持つことが
わかる。From the results shown in Table 1, it can be seen that the sintered body of the present invention has excellent fracture resistance as compared with the conventional ceramics tool and has cutting performance comparable to that of an expensive CBN sintered tool. ..
【００１５】[0015]
【発明の効果】以上実施例と共に説明したように本発明
によれば、欠損や結晶粒の脱落によるチッピングが防止
されたＴｉＢ2 セラミックス焼結体を提供でき、例えば
特に軸受鋼等の高硬度材の切削加工等に使用した場合、
優れた性能を発揮できるという効果を奏する。According to the present invention, as described above with reference to the embodiments, it is possible to provide a TiB 2 ceramics sintered body in which chipping due to defects and drop of crystal grains is prevented. For example, particularly high hardness materials such as bearing steels can be provided. When used for cutting, etc.,
It has the effect of exhibiting excellent performance.
【図１】ＴｉＢ2 セラミックス焼結体の拡大断面模式図
である。FIG. 1 is an enlarged schematic sectional view of a TiB 2 ceramics sintered body.
１１ ＴｉＢ2 セラミックス焼結体 １２ ＴｉＢ2 粒子 １３ バインダ11 TiB 2 ceramics sintered body 12 TiB 2 particles 13 binder
───────────────────────────────────────────────────── フロントページの続き (72)発明者 市来崎 哲雄 広島県広島市西区観音新町四丁目６番22号 三菱重工業株式会社広島研究所内 (72)発明者 高階 純 東京都千代田区丸の内二丁目５番１号 三 菱重工業株式会社内 ─────────────────────────────────────────────────── ─── Continuation of front page (72) Inventor Tetsuo Ikuzaki 4-6-22 Kannon Shinmachi, Nishi-ku, Hiroshima City, Hiroshima Prefecture Mitsubishi Heavy Industries Ltd. Hiroshima Research Institute (72) Inventor Jun Takashina 2-5 Marunouchi, Chiyoda-ku, Tokyo No. 1 Sanryo Heavy Industries Co., Ltd.
Claims (2)
ダの主成分としてのＴｉＮとの混合粉末を焼結してなる
ことを特徴とするＴｉＢ2 セラミックス焼結体。1. A TiB 2 ceramics sintered body obtained by sintering a mixed powder of 30 to 70% by volume of TiB 2 and TiN as a main component of a binder.
において、バインダの一部をＡｌＮ，ＳｉＣ，ＴｉＢ2
及びＺｒＯ2 より選ばれた一種以上で置換したことを特
徴とするＴｉＢ2 セラミックス焼結体。 2. The TiB 2 ceramics sintered body according to claim 1, wherein a part of the binder is AlN, SiC, TiB 2
And a TiB 2 ceramics sintered body characterized by being substituted with one or more selected from ZrO 2 .
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3282730A JPH05319935A (en) | 1991-10-29 | 1991-10-29 | Sintered tib2 ceramic |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3282730A JPH05319935A (en) | 1991-10-29 | 1991-10-29 | Sintered tib2 ceramic |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH05319935A true JPH05319935A (en) | 1993-12-03 |
Family
ID=17656301
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP3282730A Withdrawn JPH05319935A (en) | 1991-10-29 | 1991-10-29 | Sintered tib2 ceramic |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH05319935A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2007110149A1 (en) * | 2006-03-24 | 2007-10-04 | Esk Ceramics Gmbh & Co. Kg | Sintered wear-resistant boride material, sinterable powder mixture for producing said material, method for producing the material and use thereof |
-
1991
- 1991-10-29 JP JP3282730A patent/JPH05319935A/en not_active Withdrawn
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2007110149A1 (en) * | 2006-03-24 | 2007-10-04 | Esk Ceramics Gmbh & Co. Kg | Sintered wear-resistant boride material, sinterable powder mixture for producing said material, method for producing the material and use thereof |
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Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A300 | Withdrawal of application because of no request for examination |
Free format text: JAPANESE INTERMEDIATE CODE: A300 Effective date: 19990107 |