JPH0711054B2 - Sintered body for high hardness tools - Google Patents
Sintered body for high hardness toolsInfo
- Publication number
- JPH0711054B2 JPH0711054B2 JP1307264A JP30726489A JPH0711054B2 JP H0711054 B2 JPH0711054 B2 JP H0711054B2 JP 1307264 A JP1307264 A JP 1307264A JP 30726489 A JP30726489 A JP 30726489A JP H0711054 B2 JPH0711054 B2 JP H0711054B2
- Authority
- JP
- Japan
- Prior art keywords
- sintered body
- binder
- cbn
- cutting
- high hardness
- 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.)
- Expired - Lifetime
Links
Description
【発明の詳細な説明】 〔産業上の利用分野〕 本発明は、立方晶窒化硼素（以下cBNと略記する）を用
いた高硬度工具用焼結体に関する。TECHNICAL FIELD The present invention relates to a sintered body for high hardness tools using cubic boron nitride (hereinafter abbreviated as cBN).
cBNはダイヤモンドに次ぐ高硬度を有し、その焼結体は
種々の切削工具に使用されている。cBN has the second highest hardness after diamond, and its sintered body is used in various cutting tools.
切削工具に適したcBN焼結体の一例として、特公昭57-36
31号公報には、cBNを80〜40体積％含有し、残部が周期
律表の4A、5A、6A族元素の炭化物、窒化物、硼化物、珪
化物若しくはこれらの混合物又は相互固溶体化合物を主
体とし、この化合物が焼結体組織中で連続した結合相を
なす高硬度工具用焼結体が開示されている。この焼結体
は切削工具として一般的に高い性能を示すが、例えば高
硬度焼入鋼の連続切削のような特に厳しい衝撃力が加わ
る用途では、刃先の強度不足や摩耗により刃先が欠損し
やすい欠点があつた。As an example of cBN sintered compact suitable for cutting tools,
No. 31, gazette contains 80 to 40% by volume of cBN, and the balance is mainly 4A, 5A, 6A group carbides, nitrides, borides, silicides or their mixtures or mutual solid solution compounds of the periodic table. And a sintered body for a high hardness tool in which this compound forms a continuous binder phase in the sintered body structure is disclosed. This sintered body generally exhibits high performance as a cutting tool, but in applications where particularly severe impact force is applied, such as continuous cutting of hardened hardened steel, the cutting edge is prone to chipping due to insufficient strength or wear of the cutting edge. There was a flaw.
かかる刃先の欠損をなくすため、刃先の強度や摩耗を改
善した高硬度工具用焼結体が特開昭62-228450号公報に
示されている。この焼結体においては、結合材が25〜50
重量％のAlと、Tiの炭化物等のTiを含む化合物と、Tiを
含む化合物中に含まれるか又はWCとして含まれる４〜40
重量％のＷとを含み、これらが焼結時にcBNと反応して
硼化アルミニウムや硼化チタン等を生成し、cBNと結合
材又は結合材同士を強固に結合させている。Japanese Unexamined Patent Publication (Kokai) No. 62-228450 discloses a sintered body for a high hardness tool in which the strength and wear of the cutting edge are improved in order to eliminate such damage of the cutting edge. In this sintered body, the binder is 25-50
4-40 contained in a compound containing Ti such as Al in a weight percentage and Ti carbide and contained in a compound containing Ti or as WC
% Of W, which reacts with cBN during sintering to form aluminum boride, titanium boride, etc., and firmly bond the cBN to the binder or the binders.
しかしながら、上記の特公昭57-3631号公報及び特開昭6
2-228450号公報に記載された焼結体であつても、鋳鉄切
削用の工具としては尚下記のような問題を有していた。
例えば、高強度黒鉛鋳鉄の切削やねずみ鋳鉄の高速切削
においては、刃先摩耗が急激に進行して短期間に寿命に
至つたり、刃先にクレーター摩耗が発生して刃先が欠損
する等の問題が依然として残されていた。However, the above Japanese Patent Publication No. 57-3631 and Japanese Patent Laid-Open No.
Even the sintered body described in JP-A-2-228450 still has the following problems as a tool for cutting cast iron.
For example, in the cutting of high-strength graphite cast iron and high-speed cutting of gray cast iron, there is a problem that the cutting edge wear rapidly progresses to reach the end of its life, and crater wear occurs on the cutting edge and the cutting edge is lost. It was still left.
本発明はかかる従来の事情に鑑み、立方晶窒化硼素焼結
体からなり、強度及び耐摩耗性に優れ、鋳鉄に対しても
優れた切削性能を示す高硬度工具用焼結体を提供するこ
とを目的とする。In view of such conventional circumstances, the present invention provides a sintered body for a high hardness tool, which is made of a cubic boron nitride sintered body, has excellent strength and wear resistance, and exhibits excellent cutting performance even for cast iron. With the goal.
上記目的を達成するため、本発明の高硬度工具用焼結体
においては、cBN粉末45〜75体積％と残部の結合材粉末
とを超高圧焼結して得られた焼結体であつて、前記結合
材が５〜25重量％のAlを含み、残部が（Hf1-zMz）Ｃ
（但し、ＭはHfを除く周期律表の4A、5A、6A族元素を意
味し、０≦ｚ≦0.3である）で表わされる化合物の少な
くとも一種からなることを特徴とする。In order to achieve the above object, in the sintered body for a high hardness tool of the present invention, a sintered body obtained by super-high pressure sintering of cBN powder 45 to 75% by volume and the remaining binder powder is provided. The binder contains 5 to 25% by weight of Al, and the balance is (Hf 1-z M z ) C
(Wherein M means 4A, 5A, and 6A group elements in the periodic table excluding Hf, and 0 ≦ z ≦ 0.3), and at least one compound represented by the formula is characterized.
本発明の焼結体が強度及び耐摩耗性に優れている理由
は、結合材が５〜25重量％のAlと残部の（Hf1-zMz）Ｃ
化合物とからなるので、これらが高温高圧下での焼結時
にcBNと反応して硼化アルミニウム（AlB2）や窒化アル
ミニウム（AlN）又は硼化ハフニウム（HfB2）を生成し
たり、Alと（Hf1-zMz）Ｃ化合物とが反応したりして、
これら反応生成物が耐摩耗性に優れたcBNと結合材を強
固に接合しあるいは結合材同士を強固に接合するためと
推測される。尚、焼結体中にはAlが酸化アルミニウムと
しても微量に存在することがＸ線回折により確認された
が、本発明の作用効果に何等支障を与えるものではな
い。The reason why the sintered body of the present invention is excellent in strength and wear resistance is that the binder is 5 to 25% by weight of Al and the balance (Hf 1-z M z ) C.
Since they are composed of a compound, they react with cBN during sintering under high temperature and high pressure to form aluminum boride (AlB 2 ) or aluminum nitride (AlN) or hafnium boride (HfB 2 ), or with Al ( Hf 1-z M z ) C compound reacts,
It is speculated that these reaction products strongly bond the cBN and the binder, which have excellent wear resistance, or the binders. It was confirmed by X-ray diffraction that Al was present in the sintered body in a trace amount as aluminum oxide, but this does not hinder the operation and effect of the present invention.
又、HfC等の（Hf1-zMz）Ｃ化合物、並びにHfB2等の前記
反応生成物は、鋳鉄切削等で刃先が高温になるのに対し
充分な耐熱性と耐酸化性を付与することが出来る他、優
れた耐摩耗性と高温強度を有し、結合材自体の強度や耐
摩耗性、耐熱性等を改善向上させることが出来る。Further, (Hf 1-z M z ) C compounds such as HfC, and the above reaction products such as HfB 2 impart sufficient heat resistance and oxidation resistance to the high temperature of the cutting edge during cutting of cast iron. Besides, it has excellent wear resistance and high-temperature strength, and can improve and improve the strength, wear resistance, heat resistance, etc. of the binder itself.
結合材中のAlの含有量が５重量％未満では、AlとcBNの
反応が不充分なために結合材によるcBNの保持力が弱く
なり、25重量％を超えるとAlB2等が多くなりcBNと結合
材の結合強度は強くなるものの、AlB2等よりも耐摩耗性
に優れたHfCのような（Hf1-zMz）Ｃ化合物の相対的な含
有量が低下するので、結合材自体の硬度が低下し、焼結
体として鋳鉄切削等に対して充分な耐摩耗性が得られな
い。If the content of Al in the binder is less than 5% by weight, the reaction between Al and cBN is insufficient, so the cBN holding force by the binder becomes weak, and if it exceeds 25% by weight, AlB 2 etc. increases and cBN increases. Although the bond strength of the binder is increased, the relative content of the (Hf 1-z M z ) C compound such as HfC, which has better wear resistance than AlB 2, etc., decreases, so the binder itself The hardness is decreased, and sufficient wear resistance as a sintered body against cast iron cutting cannot be obtained.
又、結合材中の式（Hf1-zMz）Ｃで表わされる化合物と
しては、ｚ＝０の場合のHfCのほか、０＜ｚの場合にはH
fと共にTi、Mo、Ｗ等を含む多くの炭化物があるが、特
にTi又はＷを含む炭化物は結合材の耐摩耗性や強度を改
善し、良好な特性を示すので好ましい。しかし、上記式
においてｚが0.3を超えると相対的に耐摩耗性に優れたH
fCの含有量が減少するので、ｚは0.3以下とする。The compound represented by the formula (Hf 1-z M z ) C in the binder includes HfC in the case of z = 0 and H in the case of 0 <z.
There are many carbides containing Ti, Mo, W, etc. in addition to f, but carbides containing Ti or W are particularly preferred because they improve the wear resistance and strength of the binder and show good properties. However, in the above formula, when z exceeds 0.3, H, which is relatively excellent in wear resistance,
Since the content of fC decreases, z is set to 0.3 or less.
更に、結合材中に鉄族元素を少なくとも一種添加するこ
とによつて、結合材の強度及び硬度が更に高くなり、焼
結体の特性が一層改善される。これは鉄族元素とHfB2、A
lB2等の硼化物との濡れ性が高いため、硼化物が結合材
により強固に結合するためと考えられる。Furthermore, by adding at least one iron group element to the binder, the strength and hardness of the binder are further increased, and the characteristics of the sintered body are further improved. This is an iron group element and HfB 2 , A
It is considered that the boride is strongly bonded to the binder because it has high wettability with boride such as lB 2 .
本発明において、cBNの量を45〜75体積％とするのは、4
5体積％未満では焼結体の強度及び硬度が低下し、又相
対的に結合材が多くなることで、例えば鋳鉄に含有され
る高硬度の黒鉛やマトリツクス中のパーライト素地やオ
ーステナイト処理を行なつた素地等の高硬度の部分によ
る機械的摩耗の進展が早くなつたり、衝撃によるクラツ
クが発生しやすくなるからである。又、cBNの量が75体
積％を超えるとcBN同士が接触するようになるため、高
強度の被削材の場合や刃先に高圧力が負荷される断続切
削の場合に粒子同士の接触部にクラツクが発生し、更に
は相対的に結合材が減少するため、結合材とcBNとの結
合強度が低下して焼結体の強度低下をもたらすためであ
る。In the present invention, the amount of cBN is 45 to 75% by volume is 4
If it is less than 5% by volume, the strength and hardness of the sintered body will be reduced, and the amount of binder will be relatively large. For example, high hardness graphite contained in cast iron or pearlite matrix in matrix or austenite treatment This is because the progress of mechanical wear due to the high hardness portion of the base material is accelerated, and cracking due to impact is likely to occur. Also, when the amount of cBN exceeds 75% by volume, the cBNs come into contact with each other, so in the case of a high-strength work material or intermittent cutting in which high pressure is applied to the cutting edge, the contact area This is because cracks are generated and the amount of the binder is relatively reduced, so that the bonding strength between the binder and cBN is reduced, resulting in a decrease in strength of the sintered body.
更に、一般的なcBN焼結体の摩耗においては、cBNが耐摩
耗性に優れるため、結合材が優先的に摩耗してcBNが脱
落するものと考えられる。従つて、組織を均一化して結
合材の優先的摩耗を抑制するため、以下の如く粒度を調
整することが好ましい。cBNの平均粒径は小さいほど好
ましく、特に４μｍを超えると結合材部分が大きくなつ
て優先的に摩耗するので４μｍ以下が好ましい。更に好
ましくは、粒径１μｍ以下のcBNが35〜80重量％及び３
〜６μｍのcBNが20〜65重量％となるようにcBNの粒度を
調整することにより、大きなcBN粒子の間に小さなcBN粒
子が充填されて組織が均一化される。又、結合材粉末の
平均粒径がcBNの平均粒径の1/3未満である微細な結合材
粉末を用いることも、結合材の均一な分散を促進するの
で、耐摩耗性向上の点で好ましい。Furthermore, in general wear of a cBN sintered body, it is considered that the binder is preferentially worn and cBN falls off because cBN has excellent wear resistance. Therefore, in order to make the structure uniform and suppress preferential wear of the binder, it is preferable to adjust the grain size as follows. The smaller the average particle size of cBN is, the more preferable. Particularly, when it exceeds 4 μm, the binder portion becomes large and is preferentially worn. Therefore, it is preferably 4 μm or less. More preferably, cBN having a particle size of 1 μm or less is 35 to 80% by weight and 3
By adjusting the particle size of cBN so that the cBN of ˜6 μm is 20 to 65% by weight, the small cBN particles are filled between the large cBN particles to make the structure uniform. Also, using a fine binder powder whose average particle diameter of the binder powder is less than 1/3 of the average particle diameter of cBN also promotes the uniform dispersion of the binder, and therefore in terms of improving wear resistance. preferable.
実施例１ Hfを含む炭化物とAl粉末とを超硬合金製ポツトとボール
を用いて粉砕混合し、平均粒径0.9μｍ以下の下記第１
表に示す組成を有する結合材粉末を作製した。これらの
結合材粉末と、平均粒径が2.5〜４μｍのcBN粉末とを体
積比で42:58となるように混合し、混合粉末をMo製容器
に入れ、真空炉にて10-4torr、1000℃で20分間加熱して
脱気した後、55Kbの圧力及び1400℃の温度で25分間焼結
した。Example 1 Carbide containing Hf and Al powder were pulverized and mixed using a cemented carbide pot and a ball, and the following first particle having an average particle size of 0.9 μm or less was used.
A binder powder having the composition shown in the table was prepared. These binder powders were mixed with cBN powder having an average particle size of 2.5 to 4 μm in a volume ratio of 42:58, the mixed powders were placed in a Mo container, and 10 −4 torr in a vacuum furnace, After heating at 1000 ° C. for 20 minutes to degas, it was sintered at a pressure of 55 Kb and a temperature of 1400 ° C. for 25 minutes.
得られた各焼結体をＸ線回折により同定したところ、全
ての焼結体について、cBNのピークとHfを含む炭化物の
ピーク、並びにHfB2、AlB2、AlNのピークが確認され、試
料によりHf以外に含まれるTi、Mo、Ｗの炭化物等のピー
クも認められた。又、焼結体組織を走査型電子顕微鏡で
観察したところ、微細なcBN粒子が結合材を介して相互
に接合していることが認められた。When each of the obtained sintered bodies was identified by X-ray diffraction, the cBN peak, the carbide peak containing Hf, and the peaks of HfB 2 , AlB 2 , and AlN were confirmed for all the sintered bodies. Peaks of Ti, Mo, W carbides, etc. contained in addition to Hf were also recognized. Also, when the structure of the sintered body was observed with a scanning electron microscope, it was found that the fine cBN particles were bonded to each other via a binder.
更に、各焼結体を切削加工用チツプに加工し、球状黒鉛
鋳鉄FCD45材（硬度HB＝200）の切削試験を行なつた。切
削条件は、切削速度280m/min、切込み0.25mm、送り0.22
mm/revであり、乾式で20分間切削した。結果を第１表に
併せて示した。Further, each sintered body was processed into a chip for cutting, and a cutting test was performed on a spheroidal graphite cast iron FCD45 material (hardness H B = 200). Cutting conditions are: cutting speed 280m / min, depth of cut 0.25mm, feed 0.22
mm / rev, and dry-cut for 20 minutes. The results are also shown in Table 1.
実施例２ 89重量％のHfC粉末と11重量％のAl粉末とを実施例１と
同様に粉砕混合し、下記第２表に示す平均粒径の結合材
粉末を作製した。これらの結合材粉末を第２表に示すcB
N粉末と混合し、実施例１と同様に脱気した後、45Kbの
圧力及び1300℃の温度で20分間焼結して焼結体を得た。 Example 2 89% by weight of HfC powder and 11% by weight of Al powder were ground and mixed in the same manner as in Example 1 to prepare a binder powder having an average particle size shown in Table 2 below. CB shown in Table 2 for these binder powders
After mixing with N powder and degassing in the same manner as in Example 1, sintering was performed at a pressure of 45 Kb and a temperature of 1300 ° C. for 20 minutes to obtain a sintered body.
各焼結体を切削加工用チツプに加工し、球状黒鉛鋳鉄FC
D70材（硬度HB＝290）の円筒体端面を、切削速度180m/m
in、切込み0.2mm、及び送り0.17mm/revで乾式にて切削
し、逃げ面摩耗幅が0.2mmに至るまでの切削時間を測定
した。結果を第２表に併せて示した。Each sinter is processed into a chip for cutting, and spheroidal graphite cast iron FC
Cutting speed of 180m / m on the end face of the cylinder of D70 material (hardness H B = 290)
Dry cutting was performed at in, depth of cut 0.2 mm, and feed 0.17 mm / rev, and the cutting time until the flank wear width reached 0.2 mm was measured. The results are also shown in Table 2.
〔発明の効果〕 本発明によれば、結合材の強度、耐摩耗性及び耐熱性の
改善と共に、この結合材で高硬度のcBNを強固に接合し
たことにより、従来よりも強度及び耐摩耗性に優れた高
硬度工具用焼結体を提供することが出来る。 [Advantages of the Invention] According to the present invention, the strength, wear resistance and heat resistance of the binder are improved, and by strongly bonding the cBN of high hardness with this binder, the strength and wear resistance are higher than in the past. It is possible to provide a sintered body for a high hardness tool which is excellent in
本発明の高硬度工具用焼結体は、高強度黒鉛鋳鉄の切削
やねずみ鋳鉄の高速切削に特に有効であるほか、高硬度
であるため焼入鋼や耐熱合金の切削等にも好適に使用し
うる。The high-hardness tool sintered body of the present invention is particularly effective for cutting high-strength graphite cast iron and high-speed cutting of gray cast iron, and is also suitable for cutting hardened steel and heat-resistant alloys because of its high hardness. You can.
Claims (3)
結合材粉末とを超高圧焼結して得られた焼結体であつ
て、前記結合材が５〜25重量％のAlを含み、残部が（Hf
1-zMz）Ｃ（但し、ＭはHfを除く周期律表の4A、5A、6A
族元素を意味し、０≦ｚ≦0.3である）で表わされる化
合物の少なくとも一種からなることを特徴とする高硬度
工具用焼結体。1. A sintered body obtained by super-high pressure sintering of 45 to 75% by volume of cubic boron nitride powder and the rest of binder powder, wherein the binder is 5 to 25% by weight. And the balance is (Hf
1-z M z ) C (where M is 4A, 5A, 6A in the periodic table excluding Hf)
A sintered body for a high hardness tool, comprising at least one compound represented by the formula (0 ≦ z ≦ 0.3, which means a group element).
粒径が４μｍ以下であつて、少なくとも１μｍ以下の立
方晶型窒化硼素粉末を35〜80重量％、３〜６μｍの立方
晶型窒化硼素粉末を20〜65重量％含むことを特徴とする
請求項（１）記載の高硬度工具用焼結体。2. The cubic boron nitride powder of the sintered body has an average particle size of 4 μm or less, and at least 1 μm or less of the cubic boron nitride powder is 35 to 80% by weight and 3 to 6 μm. A sintered body for a high hardness tool according to claim 1, characterized in that it contains 20 to 65% by weight of type boron nitride powder.
の平均粒径の1/3未満であることを特徴とする請求項
（１）又は（２）記載の高硬度工具用焼結体。3. The high hardness tool baking according to claim 1, wherein the average particle size of the binder is less than 1/3 of the average particle size of the cubic boron nitride powder. Union.
Priority Applications (7)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1307264A JPH0711054B2 (en) | 1989-11-27 | 1989-11-27 | Sintered body for high hardness tools |
| CA002030350A CA2030350C (en) | 1989-11-27 | 1990-11-20 | Hard sintered compact for tools |
| US07/616,599 US5034053A (en) | 1989-11-27 | 1990-11-21 | Hard sintered compact for tools |
| EP90122411A EP0430100B1 (en) | 1989-11-27 | 1990-11-23 | Hard sintered compact for tools |
| DE69018026T DE69018026T2 (en) | 1989-11-27 | 1990-11-23 | Hard sintered compact for tools. |
| KR1019900019178A KR930005896B1 (en) | 1989-11-27 | 1990-11-26 | Hard sintered compact for tools |
| ZA909467A ZA909467B (en) | 1989-11-27 | 1990-11-26 | Hard sintered compact for tools |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1307264A JPH0711054B2 (en) | 1989-11-27 | 1989-11-27 | Sintered body for high hardness tools |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH03170638A JPH03170638A (en) | 1991-07-24 |
| JPH0711054B2 true JPH0711054B2 (en) | 1995-02-08 |
Family
ID=17967018
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1307264A Expired - Lifetime JPH0711054B2 (en) | 1989-11-27 | 1989-11-27 | Sintered body for high hardness tools |
Country Status (2)
| Country | Link |
|---|---|
| JP (1) | JPH0711054B2 (en) |
| ZA (1) | ZA909467B (en) |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP3196802B2 (en) * | 1994-10-14 | 2001-08-06 | 住友電気工業株式会社 | Hard cutting tool |
| JP4836120B2 (en) * | 2006-01-11 | 2011-12-14 | タマティーエルオー株式会社 | Method for producing aluminum nitride-containing material |
| JP6213269B2 (en) * | 2014-01-30 | 2017-10-18 | 三菱マテリアル株式会社 | Surface-coated cutting tool that exhibits excellent chipping resistance over a long period of time when cutting hardened steel |
| DE112021003480T5 (en) * | 2020-06-30 | 2023-04-27 | Kyocera Corporation | USE AND CUTTING TOOL |
-
1989
- 1989-11-27 JP JP1307264A patent/JPH0711054B2/en not_active Expired - Lifetime
-
1990
- 1990-11-26 ZA ZA909467A patent/ZA909467B/en unknown
Also Published As
| Publication number | Publication date |
|---|---|
| JPH03170638A (en) | 1991-07-24 |
| ZA909467B (en) | 1991-09-25 |
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