JPS596906B2 - Sintered body for tools - Google Patents
Sintered body for toolsInfo
- Publication number
- JPS596906B2 JPS596906B2 JP54042177A JP4217779A JPS596906B2 JP S596906 B2 JPS596906 B2 JP S596906B2 JP 54042177 A JP54042177 A JP 54042177A JP 4217779 A JP4217779 A JP 4217779A JP S596906 B2 JPS596906 B2 JP S596906B2
- Authority
- JP
- Japan
- Prior art keywords
- sintered body
- cutting
- tic
- tin
- tool
- 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
Links
Landscapes
- Powder Metallurgy (AREA)
Description
【発明の詳細な説明】
近年、機械加工の高能率化の要素が高まり、使用する工
具の性能向上の為に広汎な研究開発が行われている。DETAILED DESCRIPTION OF THE INVENTION In recent years, the need for higher efficiency in machining has increased, and extensive research and development has been carried out to improve the performance of the tools used.
特に切削加工用工具では超高圧焼結技術を使って最も高
硬度の物質であるダイヤモンドやこれに次いで高い硬度
を有する立方晶型窒化硼素(以下CBNと略す)の焼結
体が作られ、従来の工具材料では得られなかった高性能
の工具として期待されている。In particular, for cutting tools, ultra-high pressure sintering technology is used to create sintered bodies of diamond, which is the hardest substance, and cubic boron nitride (hereinafter abbreviated as CBN), which has the second highest hardness. It is expected to be a high-performance tool that cannot be obtained with other tool materials.
しかし、これ等の新しい工具材料も万能ではなく、使用
用途は限定されたものである。However, these new tool materials are not universal and have limited uses.
近年開発されたTiCやTi(C,N)を主成分とする
化合物なNi等の金属で結合したサーメットは、従来の
WC基超硬合金よりも鋼の切削加工において耐磨耗性が
優れているが、これは工具刃先に熱衝撃が加わるような
、例えば切削油を使用し且つ断続切削する場合に使用す
ると、刃先に熱亀裂を生じ欠損するといった欠点がある
。Recently developed cermets bonded with metals such as TiC and Ni, which are compounds mainly composed of Ti(C,N), have better wear resistance in steel cutting than conventional WC-based cemented carbide. However, if this method is used when a thermal shock is applied to the cutting edge of the tool, for example, when cutting oil is used and cutting is interrupted, it has the disadvantage that the cutting edge will thermally crack and break.
またTiC等をWC基超硬合金母材に化学蒸着法を用い
て約5ミクロンの厚さで被覆した工具も、WC基超硬合
金の耐磨耗性を改良する効果はあるが、例えば鋭い工具
刃先形状が要求されるような鋼や鋳鉄の仕上げ切削加工
においては、被覆層が切削初期に剥離してしまうといっ
た欠点がある。Tools coated with TiC or the like on a WC-based cemented carbide base material to a thickness of about 5 microns using the chemical vapor deposition method also have the effect of improving the wear resistance of the WC-based cemented carbide. In finishing cutting of steel or cast iron, which requires a tool edge shape, there is a drawback that the coating layer peels off at the initial stage of cutting.
さらに、A 1 2 03 k主体としたセラミック工
具は、鋼や鋳鉄の高速切削に適しているが、本質的に靭
性が他の工具材料より劣っており、また高温での熱伝導
が低い為に熱衝撃に弱い欠点がある。Furthermore, although A1203k-based ceramic tools are suitable for high-speed cutting of steel and cast iron, they are inherently inferior in toughness to other tool materials and have low heat conductivity at high temperatures. The disadvantage is that it is susceptible to thermal shock.
本発明者等は、特に一般的な鋼、鋳鉄を力旺する用途に
対して従来の超硬合金、サーメット、セラミック工具の
性能を大巾に上回る工具材料について鋭意研究を重ねた
結果、本発明に到達した。The inventors of the present invention have conducted extensive research on tool materials that greatly exceed the performance of conventional cemented carbide, cermet, and ceramic tools, especially for applications that rely heavily on general steel and cast iron. reached.
鉄族金属を結合相としたサーメットにおいては鉄族金属
の軟化湛度が低いため高温での変形が問題となる。In cermets using iron group metals as a binder phase, deformation at high temperatures becomes a problem because the iron group metals have a low degree of softening.
このため鉄族金属の代りにWなどの高融点金属を結合材
として粉末冶金法で作る考えが古くから提案されてきて
いる。For this reason, the idea of using a high melting point metal such as W as a binder instead of an iron group metal by powder metallurgy has been proposed for a long time.
しかし、いずれも成功していない。However, none of them were successful.
その中で一度は企業化に成功したかにみえたのが、米国
特許3703368号によるTi−W−C系の共晶点を
利用した(TttW)C,,−W合金である。Among them, one that seemed to have been successfully commercialized at one time was the (TttW) C, -W alloy, which utilizes the eutectic point of the Ti-W-C system, as disclosed in US Pat. No. 3,703,368.
これは27oo℃以上の高温で溶解し、鋳造して作られ
たものである。This is made by melting and casting at a high temperature of 27°C or higher.
この合金は耐磨耗性、高温での耐塑性変形性は従来の超
硬合金に比べ、はるかに優れ、また靭性向でもセラミッ
クなどよりはるかにしなやかで、工具材料として、かな
り魅力的なものであった。This alloy has much better wear resistance and plastic deformation resistance at high temperatures than conventional cemented carbide, and its toughness is much more flexible than ceramics, making it quite attractive as a tool material. there were.
聞題は高湿溶解一特殊な方法による鋳造という製法で作
られ鋳造時複雑な形状が作れないのみか単純形状の場合
でも得られるもの〜寸法・精度が著しく悪いという欠点
がある。The problem is that it is manufactured using a special method of high-humidity melting and casting, and it has the disadvantage that complex shapes cannot be made during casting, or even simple shapes can be obtained, with extremely poor dimensions and accuracy.
更に悪いことには、大変な難加工材料であることである
。What is worse is that it is a material that is extremely difficult to process.
ダイヤモンド工具や種々のその他の加工方法を採用して
も、その切断や研磨は容易ではない。Even with diamond tools and various other machining methods, cutting and polishing is not easy.
又熔解・鋳造と(・5方法で作るので、その組成が共晶
点近傍に限られてしまう。Also, since it is made by melting, casting, and (5) methods, its composition is limited to the vicinity of the eutectic point.
従って共晶組成よりも炭化物相の多い材料を作ることは
難かしい。Therefore, it is difficult to create a material with more carbide phase than eutectic composition.
このためこの合金を粉末冶金法で作ろうとする試みが、
すい分なされたようであるが、いずれも成功していない
。For this reason, attempts to make this alloy using powder metallurgy
It seems that many attempts have been made, but none have been successful.
それは焼結性が著しく悪いためである。This is because the sinterability is extremely poor.
添加物を加えて焼結性をあげることは出来るが、高湛強
度の低下を伴ない成功していない。It is possible to improve the sinterability by adding additives, but this has not been successful as this results in a decrease in high sintering strength.
以上Ti−W−C系について述べたが、TI=Mo−C
についても同様である。Although the Ti-W-C system has been described above, TI=Mo-C
The same applies to
最近(Ti,Mo ) C 1 −X Mo系合金の
高湿特性について、九州大学の吉永教授らから発表がな
されている。Recently, Professor Yoshinaga of Kyushu University and his colleagues have made a presentation on the high-humidity characteristics of (Ti,Mo)C1-XMo-based alloys.
この高温特性も工具材料という観点からみた場合に大変
魅力的である。This high-temperature property is also very attractive from the viewpoint of tool materials.
しかし、これも熔解一鋳造法で作られている。However, this is also made using the melt-casting method.
本発明は、ダイヤモンドや立方晶型窒化硼素の焼結に用
いられている超高圧を用いて、この難焼結性材料を焼結
せんと着眼したことにより達成されたものである。The present invention was achieved by focusing on sintering this difficult-to-sinter material using the ultra-high pressure used for sintering diamond and cubic boron nitride.
TiCは、高硬質で融点も高く、また原子間結合状態が
共有結合的性格を有するもので、高溝においても、金属
やイオン結合による化合物に比較して原子の移動が困難
である。TiC is highly hard and has a high melting point, and its interatomic bonds have a covalent character, making it difficult for atoms to move even in high grooves compared to metals or compounds with ionic bonds.
通常このような物質を焼結するには高温でホットプレス
する手段が用いられている。Typically, hot pressing at high temperatures is used to sinter such materials.
たとえば、黒鉛製の型を使用して2 0 0 kg/c
m2程度の圧力下で約1800℃の高温において約30
分間ホットプレスすると、殆んど理論密度に近い焼結体
が得られる。For example, using a graphite mold, 200 kg/c
Approximately 30% at a high temperature of approximately 1800℃ under a pressure of approximately m2
Hot pressing for a minute yields a sintered body with almost theoretical density.
しかし、このような条件でホットプレスして得られる焼
結体は、結晶粒子が焼結中に著しく粒成長しており、1
ミクロン以下の結晶粒からなる焼結体は得られない。However, in the sintered body obtained by hot-pressing under such conditions, the crystal grains grow significantly during sintering, and 1
A sintered body consisting of crystal grains smaller than microns cannot be obtained.
このようなホットプレス焼結中における粒成長の機構に
ついては、未だ充分解明されていないが、これが結晶粒
界を横切る原子の拡散によって起ることは当然のことで
ある。The mechanism of grain growth during hot press sintering has not yet been fully elucidated, but it is natural that this occurs due to the diffusion of atoms across grain boundaries.
また一般に焼結中の結晶粒成長の速度式は で与えられる。In general, the rate equation for grain growth during sintering is is given by
ここでDは時間tのときの結晶粒度、Doはt=oでの
粒度、K,mは常数で、mは約1のオーダーの値をとる
。Here, D is the grain size at time t, Do is the grain size at t=o, K and m are constants, and m takes a value on the order of about 1.
従って焼結に要する時間が短いと微粒の焼結体が得られ
る。Therefore, if the time required for sintering is short, a fine-grained sintered body can be obtained.
焼結において 密化を促進する機構としては各種のもの
が考えられるが、ホットプレスによる焼結機構を、通常
の黒鉛型等を用いる数百K9/cfn2の圧力下から、
ダイヤモンドの焼結に用いられるような超高圧の領域ま
で含めて、物質の変形機構と対応させて考えると、例え
ばAshby の分類によると、次の4つに大別され
る。Various mechanisms can be considered to promote densification during sintering.
When considered in relation to the deformation mechanism of materials, including ultra-high pressure regions such as those used in diamond sintering, they can be roughly divided into the following four categories, for example, according to Ashby's classification.
(M.F.Ashby− Actamet. 2 08
87 ( 1 97 2 ) )(1)焼結する物質の
理論剪断強度を越える応カ条件下では、物質は無限大の
歪速度で変形し得る。(M.F. Ashby-Actamet. 2 08
87 (1972)) (1) Under stress conditions that exceed the theoretical shear strength of the material to be sintered, the material can deform at an infinite strain rate.
物質の理論剪断強度τ.は、その物質の剛性率G
を叶す6′!″” TH ”〒丁であ仏
(2)高湿下では、TiC等の化合物も転位の移動によ
り辷り変形を起し得る。Theoretical shear strength of a material τ. is 6' which satisfies the rigidity G of the material. (2) Under high humidity, compounds such as TiC can also undergo sliding deformation due to the movement of dislocations.
この場合の歪速度は で与えられる。The strain rate in this case is is given by
Uは、転位の移動に要する活性化エネルギーで、加えら
れる応力σの関数でありKはポルツマン定数、Tは絶対
温度である。U is the activation energy required for dislocation movement and is a function of the applied stress σ, K is the Portzmann constant, and T is the absolute temperature.
ここで(2)式が成立するのはσ〉σ0 (σ。Here, equation (2) holds true when σ>σ0 (σ.
:flowstress)である。:flowstress).
すなわち物質の剛性率をGとした場合、加わる応力σが
犬体σ/゛G≧10−2を満足すれば、この変形が支配
的に生じる。That is, when the rigidity of the material is G, if the applied stress σ satisfies the relationship σ/゛G≧10−2, this deformation occurs dominantly.
(3)物質の融点をTMとすると、約1/’2 TM以
上の温度下ではσ/’G<10−2以下の応力で転位の
上昇運動によるクリープ変形が支配的となる。(3) If the melting point of a substance is TM, then at a temperature of about 1/'2 TM or higher, creep deformation due to upward movement of dislocations becomes dominant at a stress of σ/'G<10-2 or lower.
これは、原子の拡散を伴う変形機構である。This is a deformation mechanism that involves atomic diffusion.
(4)高温下で(3)より、さらに低圧となる範囲にお
いては、原子やイオンの体積拡散あるいは粒界拡散によ
る 密化が進行する。(4) At high temperatures and in a range where the pressure is even lower than in (3), densification progresses due to volumetric diffusion or grain boundary diffusion of atoms and ions.
一般にA l 2 0 3等のセラミックを数kg /
am”の圧力下でホット7”L/スする場合の緻密化は
この機構によるものとされている。Generally, several kg of ceramic such as Al 20 3 /
It is said that the densification in the case of hot 7" L/s under the pressure of 1000 am" is due to this mechanism.
本発明の焼結体は大部分が1ミクロン以下の微細粒子よ
り成ることを特徴とするものであって、このような微細
粒子焼結体を得る為には、原料粒度を微細化すると共に
、焼結中における粒成長を抑制しなければならない。The sintered body of the present invention is characterized in that most of the particles are composed of fine particles of 1 micron or less. Grain growth during sintering must be suppressed.
この為には前記しタ広範囲な応力・温度条件下における
物質の変形機構の中で原子の拡散を伴わない(1)また
は(2)の機構が支配的である条件下で焼結できればよ
い。For this purpose, it is only necessary to sinter under conditions in which the mechanism (1) or (2), which does not involve atomic diffusion, is dominant among the deformation mechanisms of the material under the wide range of stress and temperature conditions described above.
さて、ここでTiC をホットプレスしたときの緻密化
について考えてみる。Now, let's consider the densification that occurs when TiC is hot pressed.
TiCの剛性率Gは約1. 9 x 1 0’ kg/
r/Lm2、融点TMは3340°Kである。The rigidity G of TiC is approximately 1. 9 x 10' kg/
r/Lm2, melting point TM is 3340°K.
まずTiCが(1)の機構により変形する場合に必要な
応力を求める。First, the stress required when TiC is deformed by the mechanism (1) is determined.
Ticの理論剪断強度G
けτTH: ==6.3xlOky/’in2と推
定される。Theoretical shear strength G of Tic is estimated to be ==6.3xlOky/'in2.
多結晶体では、この理論剪断強度に近い剪断応力を生じ
るためには一軸加圧であればσ=2τ1とみてよいから
必要な応力は約1 3 X 1 0kg/miと非常に
高い値となる。In a polycrystalline body, in order to generate a shear stress close to this theoretical shear strength, if uniaxial pressure is applied, it can be assumed that σ = 2τ1, so the required stress is a very high value of about 13 x 10 kg/mi. .
このような超高圧を必要とする焼結は、固体圧力媒体を
用いた超高圧装置においても実用的な使用範囲を越えて
いる。Sintering that requires such ultra-high pressure is beyond the practical range of use even in ultra-high pressure equipment using a solid pressure medium.
(2)の転位の移動により変形する場合、応力σはσ/
G≧10−2 より約200k9/朋2、温度は転位の
運動が開始される湿度が必要となる。(2) When deformation occurs due to the movement of dislocations, the stress σ is σ/
Since G≧10-2, about 200k9/tomo2 is required, and the temperature and humidity at which the movement of dislocations is initiated are required.
この湿度はTiC単結晶の機械的性質を調べた九大吉永
教授の発表(日本金属学会誌、voL.42−11、<
1978L 1039)によると、1200CKで、
これ以上の温度では転位の移動による辷り変形が起り得
る。This humidity is the result of a presentation by Professor Yoshinaga of Kyushu University who investigated the mechanical properties of TiC single crystals (Journal of the Japan Institute of Metals, vol. 42-11, <
According to 1978L 1039), 1200CK,
At temperatures above this temperature, sliding deformation may occur due to the movement of dislocations.
またこの報告によると、12000Kで、転位が移動す
るのに必要な応カは25K9/′IIL11L2 とさ
れているが、TiC多結晶体を超高圧中で焼結する場合
、25k9/rIL一の応力でTic粒子は変形し始め
るが、光全に緻密化が進行するには、これ以上に高い応
力が必要であると考えられる。Also, according to this report, the stress required for dislocation movement at 12,000K is 25K9/'IIL11L2, but when TiC polycrystal is sintered under ultra-high pressure, the stress of 25K9/rIL- At this point, the Tic particles begin to deform, but it is thought that a higher stress than this is required for optical densification to proceed.
さらに、本発明の焼結体は1200°C〜1400℃と
1/2 TMの約1400℃に近い温度で焼結を行うが
2 5 kg/ mm2程度の低圧では前述した(3)
, (4)の拡散を伴う変形が支配的となる領域に入る
可能性がある。Furthermore, the sintered body of the present invention is sintered at a temperature close to 1200°C to 1400°C and 1/2 TM, but at a low pressure of about 25 kg/mm2 as described above (3).
, (4) may enter a region where deformation accompanied by diffusion becomes dominant.
従って、これを防止する意味において応力2 0 0
K9/ mvt’以上(圧力では約20kb以上)で、
(2)の転位の移動による緻密化が短時間で生じる範囲
で焼結体を得ることが出来れば良い。Therefore, in order to prevent this, stress 2 0 0
K9/ mvt' or higher (approximately 20 kb or higher in pressure),
It is sufficient if a sintered body can be obtained within a range in which the densification due to the movement of dislocations (2) occurs in a short period of time.
固体圧力媒体を用いた超高圧装置では、この程度の圧力
であれば問題なく使用できる。Ultra-high pressure equipment using a solid pressure medium can be used without problems at this level of pressure.
以上超高圧装置を用いれば(3L (4)の拡散を伴っ
た変形が支配的となる領域以外で焼結体を得ることが可
能であるが、焼結温度を1200゜C〜1400゜Cと
すると(3), (4)の拡散を伴った緻密化が少しで
はあるが生じ、原料粉末が粒成長する可能性がある。If an ultra-high pressure device is used as described above, it is possible to obtain a sintered body in areas other than the region where deformation accompanied by diffusion (3L (4)) is dominant, but the sintering temperature can be set to 1200°C to 1400°C. Then, the densification accompanied by the diffusion (3) and (4) may occur, albeit slightly, and the raw material powder may grow into grains.
ところが前述した如< 2 0 kb以上の高圧では短
時間で緻密化が進行するため焼結時間を短くすることが
でき、粒成長を抑制することが可能である。However, as mentioned above, at a high pressure of <20 kb or more, densification progresses in a short time, so the sintering time can be shortened and grain growth can be suppressed.
さらに本発明者等は超高圧中における焼結では、ホット
プンスと同一温度、同一時間焼結した場合、ホットプレ
ス焼結体は粒成長するにもか〜わらず、殆んど粒成長し
ないことを発見した。Furthermore, the present inventors have found that when sintered under ultra-high pressure, when sintered at the same temperature and for the same time as the hot-pressed sintered body, there is almost no grain growth, although the hot-pressed sintered body undergoes grain growth. discovered.
この理由としては、超高圧中における同相焼結において
は、ホットプンスの場合と比較して拡散速度が遅くなる
ためと考えられる。The reason for this is thought to be that in in-phase sintering under ultra-high pressure, the diffusion rate is slower than in hot sintering.
このように本発明の第1の重要な点は、1ミクロン以下
の粒度の焼結体を、まず従来その例をみない超高圧力下
焼結で得ることにある。As described above, the first important point of the present invention is to first obtain a sintered body with a particle size of 1 micron or less by sintering under ultra-high pressure, which has never been done before.
TiC単体のみですら容易に1ミクロン以下の粒度の緻
密な焼結体が得られることが判明したので、この条件下
で焼結すれば、本発明の狙っているT i −W− C
またはT i −Mo − C 系の微粒の緻密な焼結
体の生成は容易である。It has been found that a dense sintered body with a particle size of 1 micron or less can be easily obtained even with TiC alone, and if sintered under these conditions, Ti-W-C, which is the target of the present invention, can be obtained.
Alternatively, it is easy to produce a fine-grained, dense sintered body based on Ti-Mo-C.
工具として使用する場合には粒度は細かい方が好ましい
。When used as a tool, the finer the particle size, the better.
前述した黒鉛型を用いて作ることの出来る如きTiC数
10ミクロンの粒度の焼結体は強度が低く、工具材とし
て実用に耐えない性能しか示さない。A TiC sintered body with a particle size of several tens of microns, which can be made using the graphite mold described above, has low strength and exhibits performance that cannot be used in practical use as a tool material.
本発明のT i −W − CまたはTi −Mo−C
系の焼結体において良好な工具性能を得るためには、耐
磨耗性という点からみれば高融点金属の含有量が少ない
方が望ましく、靭性という点からみれば粒界に析出する
高融点金属の量が多いほど良い。Ti-W-C or Ti-Mo-C of the present invention
In order to obtain good tool performance in the sintered body of the system, it is desirable to have a low content of high melting point metals from the viewpoint of wear resistance, and from the viewpoint of toughness, it is desirable to have a low content of high melting point metals that precipitate at grain boundaries. The more metal the better.
従って、耐磨耗性能と靭件の双方を上げるためには、焼
結体に含有される高融点金属を減少させ、且つ、粒界に
高融点金属を存在させるという相反したことなせねばな
らず、発明者等はこの点について鋭意研究した結果、T
ic (Ti,W)C −W1 もしくはTiC
(Ti ,Mo )C−Moの3相から成る焼結体を
作れば良いという知見に達した。Therefore, in order to improve both wear resistance and toughness, it is necessary to reduce the high melting point metal contained in the sintered body and to make the high melting point metal exist in the grain boundaries. As a result of intensive research on this point, the inventors
ic (Ti,W)C -W1 or TiC
We have reached the knowledge that it is sufficient to make a sintered body consisting of three phases: (Ti, Mo)C-Mo.
即ち第1図aはT i −MO −C の三元状態図で
、A点における組成の合金は均一溶体になるが、もし各
TiC粒子において完全に均一固液体とならず、TiC
粒子の芯がTiCとして残留した場合、固溶体部分のM
oの割合は増し粒界にMoが析出し、MOの含有量を少
なくしてもMoを析出させることができ、TiC −
( Ti p Mo ) C−Moの3相からなる靭性
と耐磨耗性の優れた焼結体を得ることが可能である。In other words, Figure 1a is a ternary phase diagram of Ti-MO-C, and the alloy with the composition at point A becomes a homogeneous solution, but if each TiC particle does not become a completely homogeneous solid-liquid and the TiC
If the core of the particle remains as TiC, the M of the solid solution part
The ratio of o increases and Mo precipitates at the grain boundaries, and even if the MO content is reduced, Mo can be precipitated.
(TipMo) It is possible to obtain a sintered body consisting of three phases of C-Mo and having excellent toughness and wear resistance.
さらにTiC の常温における強度は非常に高いが高温
になるに従ってその強度は急速に低下する傾向があるが
、( T it Mo ) C の強度は1200〜1
300℃までは温度依存性が少なく、800〜900℃
以上ではTiCの強度よりも(Ti,Mo)C の強度
が高くなり、Ti −(Ti,Mo )C−Mo中に(
Ti,Mo)Cが存在することにより、高温時における
強度低下を防ぐことができ、高温強度の優れた焼結体を
得ることが可能である。Furthermore, the strength of TiC at room temperature is very high, but as the temperature increases, the strength tends to decrease rapidly, but the strength of (T it Mo ) C is 1200~1
Less temperature dependence up to 300℃, 800-900℃
In this case, the strength of (Ti, Mo)C becomes higher than that of TiC, and (Ti,Mo)C in Ti-(Ti,Mo)C-Mo
The presence of Ti, Mo)C can prevent a decrease in strength at high temperatures, making it possible to obtain a sintered body with excellent high-temperature strength.
実際超高圧焼結においては前述した如く、比較的低湿短
時間で焼結することが可能であり、さらには通常のホッ
トプンス時より拡散速度が遅いため、第3図に示すよう
な微粒で3相より成る焼結体を容易に得ることができ、
その工具性能も非常に優れている。In fact, in ultra-high pressure sintering, as mentioned above, it is possible to sinter in a relatively low humidity and short time, and furthermore, the diffusion rate is slower than in normal hot sintering, so it is possible to sinter in three phases with fine particles as shown in Figure 3. A sintered body consisting of
The tool performance is also very good.
また、Ti−W−C,Ti−Mo−Cの組成について考
えてみる。Also, consider the compositions of Ti-W-C and Ti-Mo-C.
前述した如くWあるいはMoなどの高融点金属相が存在
すると靭性に富み、WあるいはMOの増加に伴って靭性
は向上する。As described above, the presence of a high-melting point metal phase such as W or Mo provides high toughness, and as the amount of W or MO increases, the toughness improves.
しかし、これらの焼結体を工具材料として使用する場合
、焼結体の耐磨耗性が問題となる。However, when these sintered bodies are used as tool materials, the wear resistance of the sintered bodies becomes a problem.
耐磨耗特性から考えた場合、TiC の減少は、耐磨耗
性の低下を意味するものであり、工具材料として、本発
明焼結体を使用する場合WあるいはMoの量も耐磨耗性
と靭件の双方から制限される。Considering the wear resistance properties, a decrease in TiC means a decrease in wear resistance, and when the sintered body of the present invention is used as a tool material, the amount of W or Mo also affects the wear resistance. and restrictions.
WあるいはMoの量は焼結体の使用用途により異なるが
、原子比で40係、好ましくは25係以下5係以上であ
れば良い。The amount of W or Mo varies depending on the intended use of the sintered body, but it is sufficient that the atomic ratio is 40 parts, preferably 25 parts or less and 5 parts or more.
すなわちT i −W − C系のWの含有量は重量比
で80係以下24係以上、T i −Mo − C糸の
Moの含有量は重量比で68係以下14係以上が良い。That is, the W content in the Ti-W-C system is preferably 80 parts or less and 24 parts or more in weight ratio, and the Mo content in the Ti-Mo-C yarn is preferably 68 parts or less and 14 parts or more in weight ratio.
本発明のTi−WC−NOあるいはTi −Mo−C−
N−0の焼結体は更に良好な工具性能′を得るため、で
きる限り粒子を微細にしたことにも特徴がある。Ti-WC-NO or Ti-Mo-C- of the present invention
The N-0 sintered body is also characterized by making the particles as fine as possible in order to obtain even better tool performance.
超高圧焼結では前述した如く、短時間で焼結でき、粒成
長を抑制することができるが、拡散が伴った変形も生じ
少しではあるが粒成長する可能性がある。As mentioned above, ultra-high pressure sintering can perform sintering in a short time and suppress grain growth, but deformation accompanied by diffusion may also occur and grain growth may occur, albeit to a small extent.
この粒成長をさらに抑制するため、原料粉末にTiN粉
末を10重量係添加したところ、超高圧中の固相焼結に
おいて粒成長が抑制されることを発見した。In order to further suppress this grain growth, we added 10% TiN powder to the raw material powder, and found that grain growth was suppressed during solid-phase sintering under ultra-high pressure.
この原因については不明な点が多いが、TiNがTiC
粒子間に存在してTiC粒子の粒成長を抑制するものと
考えられる。Although there are many unknowns about the cause of this, TiN
It is thought that it exists between particles and suppresses the grain growth of TiC particles.
TiNの添加量としては1係未満であると、その効果は
見出せず、また20係を越えると工具としての耐磨耗性
が悪くなる。If the amount of TiN added is less than 1 part, no effect will be found, and if it exceeds 20 parts, the wear resistance of the tool will deteriorate.
TiNの添加量は1係〜20係が適当であり、この範囲
内であると良好な工具性能を有した焼結体が得られた。The appropriate amount of TiN added is 1 to 20 parts, and within this range a sintered body with good tool performance was obtained.
なおTiNを添加して焼結した場合TiNがTiC等の
粒子内に固溶する場合もあるがTiN量が重量比で20
係以下ならば工具性能は変わらない。Note that when TiN is added and sintered, TiN may form a solid solution in particles such as TiC, but if the TiN amount is 20% by weight,
If it is less than 100%, the tool performance will not change.
また、原料粉末としてTiCの代り[Ti(C,O)あ
るいはTi (C,N,O )の如き酸素を含有した粉
末を用いて、焼結体中に積極的に酸素を含ませることに
より焼結性が向上し、工具性能の良好な焼結体を得るこ
とができた。In addition, by using oxygen-containing powder such as Ti(C,O) or Ti(C,N,O) instead of TiC as the raw material powder, the sintered body can be sintered by actively incorporating oxygen into the sintered body. It was possible to obtain a sintered body with improved sinterability and good tool performance.
この理由は明確ではないが、TiCとTiOの特性を比
較すると、常温でのビツカース硬度がTic,TiOそ
れぞれ3 2 0 0kg/’am2、1 7 0 0
ky/turn2で常温ではTiC の硬度が高いが
、800℃になるとTiC,TiOそれぞれ5 0 0
kg/−朋2、660K9/朋2で高渦になるとTi
O の硬度が高くなる。The reason for this is not clear, but when comparing the properties of TiC and TiO, the Vickers hardness at room temperature is 3200 kg/'am2 and 1700 kg/'am2, respectively.
At ky/turn 2, TiC has high hardness at room temperature, but at 800°C, TiC and TiO each have a hardness of 500
kg/-Tomo 2, 660K9/Tomo 2 when it becomes a high vortex, Ti
The hardness of O increases.
またTiOはTiC より化学的に安全であり、合金に
酸素が含有すればTiOの特性を生かした合金が得られ
る。Furthermore, TiO is chemically safer than TiC, and if oxygen is contained in the alloy, an alloy that takes advantage of the properties of TiO can be obtained.
また、合金中に酸素が含有されていると切削時に合金表
面と酸素が反応し、表面にB e jag が形成さ
れ易くなり、合金を保護すると考えられる。Further, if oxygen is contained in the alloy, the alloy surface reacts with oxygen during cutting, and B e jag is likely to be formed on the surface, which is thought to protect the alloy.
同焼結体中の酸素の含有量としては、原子比で10係を
越えると工具性能が低下するため、原子比で10%以下
が適当である。The oxygen content in the sintered body is suitably 10% or less in terms of atomic ratio, since tool performance deteriorates if the content exceeds 10% in terms of atomic ratio.
Ti−Mo −C の各混度における3元状態図は、第
1図a−dの如くである。The ternary phase diagram for each mixture of Ti-Mo-C is as shown in FIGS. 1a-d.
Ti−W−C系でも略内様の状態図となる。The Ti-W-C system also has a substantially similar phase diagram.
温度の低いほどTiCに固溶するWまたはMoの量は少
なくなる。The lower the temperature, the smaller the amount of W or Mo dissolved in TiC.
金属状W又はMoが組織中に存在することにより合金全
体の靭性が甚しく向上するので、同一組成ならば、その
焼結温度の低いほど金属相の量が増え靭性に富むことに
なる。The presence of metallic W or Mo in the structure significantly improves the toughness of the entire alloy, so if the composition is the same, the lower the sintering temperature, the greater the amount of metallic phase and the richer the toughness.
この点本発明の如き超高圧下焼結では焼結温度を低くす
ることが可能であるから更に有利である。In this respect, sintering under ultra-high pressure as in the present invention is more advantageous because the sintering temperature can be lowered.
本発明の焼結体を例えば切削工具として使用する場合、
耐磨耗性に優れたTi W Ct Tt−Mo−C,
Ti−W−C−N,Ti−Mo−C−N,Ti −W−
C −N−0, Ti −Mo−C −N−0焼結体は
、工具の切刃部のるに存在すればよい。When using the sintered body of the present invention as a cutting tool, for example,
Ti W Ct Tt-Mo-C with excellent wear resistance,
Ti-W-C-N, Ti-Mo-C-N, Ti-W-
The C-N-0, Ti-Mo-C-N-0 sintered body may be present on the cutting edge of the tool.
本発明の焼結体では、このTi W Cp TtMo
Cy Ti −W−C −1’L Ti −Mo
−C −N,Ti−W C N−0,Ti−Mo−
C−N−O焼結体層が0. 1 mmJJ,上の厚さで
超硬合金母材上に直接結合した状態で製造することがで
きる。In the sintered body of the present invention, this Ti W Cp TtMo
Cy Ti -WC -1'L Ti -Mo
-C -N, Ti-W C N-0, Ti-Mo-
The C-N-O sintered body layer is 0. It can be manufactured directly bonded onto a cemented carbide matrix with a thickness of over 1 mm JJ.
WC基を代表とする超硬合金は剛性が高く、靭性に富ん
でいる為このような複合体とすることによって工具に強
靭性が付与される。Cemented carbide, typically WC-based, has high rigidity and is rich in toughness, so by forming such a composite, toughness is imparted to the tool.
このような複合工具としては、例えばWC基超硬合金母
材に、化学蒸着法によってTic−lPTiNの薄層を
約5ミクロンの厚みに被覆した工具が市販されている。As such a composite tool, for example, a tool in which a WC-based cemented carbide base material is coated with a thin layer of Tic-lPTiN to a thickness of about 5 microns by chemical vapor deposition is commercially available.
しかしこのような工具では被覆層の厚みが薄く、この約
5ミクロンの層が磨耗すると、母材が磨耗面に現れて急
激に進行する。However, in such a tool, the coating layer is thin, and when this approximately 5 micron layer is worn away, the base material appears on the worn surface and progresses rapidly.
化学蒸着法等の手段で本発明の焼結体の如く厚い層を形
成することは非常に長時間を要し実際上困難である。Forming a thick layer like the sintered body of the present invention by means such as chemical vapor deposition takes a very long time and is practically difficult.
またこの方法では、母材との結合強度が、本発明の超高
圧下における接着のものより弱く、工具として使用した
場合接合界面より剥離することがある。In addition, in this method, the bonding strength with the base material is weaker than that of the bonding under ultra-high pressure of the present invention, and when used as a tool, it may peel off from the bonded interface.
本発明において、このような複合焼結体を製造する場合
には、超高圧下ホットプレス時に、原料粉末と母材とな
る超硬合金もしくは超硬合金を形成するW C JPC
oの混合粉末を直接接触せしめて、焼結と同時に焼結
体層と超硬合金母材を接合させることができる。In the present invention, when manufacturing such a composite sintered body, W C JPC is used to form a cemented carbide or a cemented carbide as a base material with the raw material powder during hot pressing under ultra-high pressure.
The sintered body layer and the cemented carbide base material can be bonded together at the same time as sintering by directly contacting the mixed powder of o.
WC−COよりなる超硬合金母材は1320℃以上で液
相を生じるが、このとき、前述した如く本発明の焼結体
のホットプンス圧力が高い為、硬質層を形成する粉末は
、加圧時に既に高密度となっており、超硬合金母材に生
じた液相は、硬質焼結体層形成粉末中には侵入し難い。The cemented carbide base material made of WC-CO generates a liquid phase at temperatures above 1320°C, but at this time, as mentioned above, since the hot punching pressure of the sintered body of the present invention is high, the powder forming the hard layer is not pressurized. At times, the density is already high, and the liquid phase generated in the cemented carbide base material is difficult to penetrate into the hard sintered body layer forming powder.
このことによって、本発明の目的とする鉄族金属の結合
金属相を含まない硬質焼結体層が超硬合金母材に直接結
合した焼結体が得られる。As a result, it is possible to obtain a sintered body in which a hard sintered body layer that does not contain a binding metal phase of an iron group metal is directly bonded to a cemented carbide base material, which is the object of the present invention.
このように複合焼結体とした場合の硬質焼結体部の厚み
は、用途によって適当に選択することができる。The thickness of the hard sintered body portion in the case of forming a composite sintered body as described above can be appropriately selected depending on the application.
一般に本発明の焼結体を切削工具として使用する場合は
、工具の切刃部逃げ面の磨耗巾が微小切削では0。Generally, when the sintered body of the present invention is used as a cutting tool, the wear width of the flank surface of the cutting edge of the tool is 0 for micro-cutting.
■記位で0. 5 mrnを越えることは稀であるため
、硬質焼結体部の厚みは0.1朋以上、望ましくは0.
5 rtrrnJJ,上あれば良い。■0 in the notation. Since it is rare that the thickness exceeds 5 mrn, the thickness of the hard sintered body part should be 0.1 mrn or more, preferably 0.1 mrn or more.
5 rtrrnJJ, above is fine.
また切り込み量の大きい重切削等においては、肉厚の大
きい焼結体を製造し使用することも可能である。In addition, for heavy cutting with a large depth of cut, it is also possible to manufacture and use a sintered body with a large wall thickness.
本発明の焼結体の製造に当っては、原料となる硬質化合
物粉末に微細粉末を使用する為粉末に吸着したガス成分
の除去に特に留意する必要がある。In producing the sintered body of the present invention, since fine powder is used as the hard compound powder serving as the raw material, special attention must be paid to the removal of gas components adsorbed to the powder.
このような微粉末を原料として、高圧下でポットプレス
することによって焼結体を製造する場合に、粉末の有す
るガス成分を有効に除去し、またホットプレス焼結時に
も、気密を保った状態で外部からのガス成分の侵入をも
防止する手段を講じなければならない。When producing a sintered body using such fine powder as a raw material by pot pressing under high pressure, gas components contained in the powder are effectively removed, and an airtight state is maintained even during hot press sintering. Measures must also be taken to prevent gas components from entering from outside.
特に本発明の焼結体の製造に当って、固体圧力媒体を用
いて高圧下でホットプレスする場合、先ず加熱に先立っ
て高圧力を試料に加えた段階で圧粉体の緻密化が起るの
で、粉末が吸着ガスを有したり、粉末粒子間にガス成分
が存在すると、引続いて行われる加熱段階で、ガス成分
の逃げ道がなく圧粉体粒子間に閉じ込められ、焼結体中
に気孔が残留することになる。In particular, in the production of the sintered body of the present invention, when hot pressing is performed under high pressure using a solid pressure medium, densification of the green compact occurs at the stage where high pressure is first applied to the sample prior to heating. Therefore, if the powder has an adsorbed gas or a gas component exists between the powder particles, during the subsequent heating step, the gas component will have no escape route and will be trapped between the green compact particles, causing it to form in the sintered body. Pores will remain.
このことから、本発明の焼結体の製造に当っては、ホッ
トプレス前に、粉末の有するガス成分を充分除去し、気
密を保った容器に封入することが必要である。For this reason, in producing the sintered body of the present invention, it is necessary to sufficiently remove the gas components contained in the powder before hot pressing, and then seal the powder in an airtight container.
その具体的方法としては、開口を有する容器に原料粉末
またはその型押体を収納し、前記開口に多孔質の蓋とろ
う材を置くか、あるいは通気を許す形状のろう材を介し
て蓋を置き、この全体を好ましくは500℃以上の温度
で加熱しながら真空引きして、脱ガスを行うと同時にろ
う材を多孔質の蓋に溶浸させるか、あるいはろう材で蓋
を容器に接着せしめて、容器を密閉する方法がある。Specifically, the raw material powder or its embossed body is stored in a container with an opening, and a porous lid and brazing material are placed in the opening, or a lid is placed through a brazing material shaped to allow ventilation. Then, the whole is heated preferably at a temperature of 500° C. or higher while being evacuated to degas it, and at the same time the porous lid is infiltrated with the brazing material, or the lid is bonded to the container with the brazing material. There is a way to seal the container.
このような方法をとることにより、粉末に吸着している
ガスを取除くことができ、焼結体に気孔が残留して焼結
体の強度が低下することを防止できる。By adopting such a method, the gas adsorbed to the powder can be removed, and it is possible to prevent pores from remaining in the sintered body and the strength of the sintered body from decreasing.
さらにTi (C,O),Ti (C,N,O )の酸
素を含有している粉末を焼結する場合、容器中に閉じ込
めてあるため焼結中に脱酸素現象を起すことなく、強度
の高い焼結体を得ることが可能である。Furthermore, when sintering powders containing oxygen such as Ti (C, O) and Ti (C, N, O), since they are confined in a container, there is no deoxidation phenomenon during sintering, and the strength is increased. It is possible to obtain a sintered body with a high
同、TiCやZrCを1 0 0 kg/mrn2程度
の圧力を加えてホットプンスすることは、今までも試験
的に行われているが、本発明の如く原料粉末を1ミクロ
ン以下の微粉体として、焼結前に加熱脱ガスすると同時
に気密な容器に封入し、粒成長を殆んど起さない状態で
、大部分が1ミクロン以下の粒子よりなる微細な組織を
有する焼結体を得ることは試みられていない。Similarly, hot-punching TiC or ZrC under a pressure of about 100 kg/mrn2 has been carried out experimentally, but as in the present invention, when the raw material powder is made into a fine powder of 1 micron or less, It is possible to obtain a sintered body with a fine structure consisting mostly of particles of 1 micron or less without causing almost any grain growth by heating and degassing before sintering and simultaneously sealing it in an airtight container. Not tried.
本発明の焼結体は、鉄族金属等の結合金属を焼結体中に
実質的に含んでいないことを特徴とするものであるが、
原料粉末の製造時や、粉砕過程でFe p Ni t
Co等の金属が混入してくることがある。The sintered body of the present invention is characterized in that it does not substantially contain a binding metal such as an iron group metal,
Fe p Ni t is produced during the production of raw material powder and during the grinding process.
Metals such as Co may be mixed in.
しかし、例えばTiC中にはNiが約0.5重量係まで
は固溶し得るとされており、焼結中に硬質化合物中ある
いは高融点金属相中にこのように固溶する量以下であれ
ば問題でない。However, for example, it is said that up to about 0.5% by weight of Ni can be dissolved as a solid solution in TiC, and even if the amount is less than this amount dissolved in a hard compound or high melting point metal phase during sintering. It's not a problem.
それ以上にこれ等の金属が混入した場合は、原料粉末を
酸洗して除去する等の手段が必要となる。If more of these metals are mixed in, it will be necessary to remove them by pickling the raw material powder.
本発明の焼結体は、特に一般の鋼、鋳鉄の切削加工用工
具に適したものである。The sintered body of the present invention is particularly suitable for cutting tools for general steel and cast iron.
鋼の仕上げ加工用工具としては従来のどの工具材料より
も格段に優れた特性を有するものである。As a tool for finishing steel, it has properties far superior to any conventional tool material.
発明者等は、本発明の焼結体で切削加工用のチップを作
成し、谷種の被削材について広範囲な条件下で切削性能
の評価を行った。The inventors created a cutting tip using the sintered body of the present invention, and evaluated the cutting performance of Tani-type work materials under a wide range of conditions.
詳細な結果については後述するが、従来、WC基超硬合
金やTiC基サーメットが使用されていた炭素鋼や合金
鋼の切削加工においては、本発明の工具刃先の逃げ而磨
耗、すくい面磨耗共に従来主具よりも著しく少ない。The detailed results will be described later, but in cutting of carbon steel and alloy steel, where WC-based cemented carbide and TiC-based cermet were conventionally used, the tool cutting edge of the present invention has both relief wear and rake face wear. Significantly less than conventional main tools.
また、耐熱疲労強度の高い切削工具が要求される鋼、鋳
鉄の重切削においては、従来WC基超硬合金が用いられ
ているが、これらは鉄族金属結合相が用いられているた
め、高温で結合金属相が軟化し高温での耐塑性変形性、
あるいは耐熱疲労靭性に限界がある。In addition, WC-based cemented carbide has conventionally been used for heavy cutting of steel and cast iron, which requires cutting tools with high thermal fatigue resistance, but since these use an iron group metal binder phase, high temperature The bonded metal phase softens and the plastic deformation resistance at high temperatures increases.
Or there is a limit to thermal fatigue toughness.
本発明の焼結体は、鉄族金属結合相の代りにWe Mo
の高融点金属相を用いている為、高温での耐塑性変形性
、耐熱疲労靭性共従来のWC基超合金よりも非常に優れ
ている。The sintered body of the present invention contains We Mo instead of the iron group metal binder phase.
Because it uses a high melting point metal phase, it has much better plastic deformation resistance and thermal fatigue toughness at high temperatures than conventional WC-based superalloys.
さらに、切削速度が250m/分〜500m/分といっ
た高速切削条件では、刃先温度が高くなって鉄族金属結
合相を含有する工具では、短時間で寿命となる為、従来
はA l 2 0 3系セラミックは使用されていたが
、本発明の焼結体は、このような条件下でもAl203
系セラミック工具よりも大変驚くべきことであるが、耐
磨耗性が優れており、充分実用に供し得ることが判明し
た。Furthermore, under high-speed cutting conditions such as a cutting speed of 250 m/min to 500 m/min, the cutting edge temperature becomes high and the tool life of a tool containing an iron group metal binder phase is shortened. Although Al203-based ceramics have been used, the sintered body of the present invention can maintain Al203 even under such conditions.
Surprisingly, it has been found that this tool has better wear resistance than other ceramic tools, and can be put to practical use.
特に断続的な切削で衝撃応力の加わる場合にはセラミッ
ク工具は欠損することが多いが、本発明の焼結体は、A
l203系セラミック工具よりもこのような条件下では
欠損し難い。In particular, ceramic tools often break when impact stress is applied during intermittent cutting, but the sintered body of the present invention
It is less likely to break under such conditions than the l203 series ceramic tool.
これは、切刃となる硬質焼結体の成分がAl203より
も靭性が高いこと、また粒子が微細で粒界に高融点金属
相があること、及び硬質焼結体が高剛性で靭性に優れた
超硬合金母材に強固に接合されていることによると考え
られる。This is because the components of the hard sintered body that forms the cutting edge are higher in toughness than Al203, the grains are fine and there is a high melting point metal phase at the grain boundary, and the hard sintered body has high rigidity and excellent toughness. This is thought to be due to the fact that it is firmly bonded to the cemented carbide base material.
更に、本発明の焼結体では切削油を使用する湿式切削等
の工具刃先に熱衝撃が加わる切削条件下で使用・[ると
、他の現用工具材料よりもサーマルクラックが生じ難い
特徴を有している。Furthermore, the sintered body of the present invention has the characteristic that it is less likely to cause thermal cracks than other currently used tool materials when used under cutting conditions that apply thermal shock to the tool edge, such as wet cutting using cutting oil. are doing.
これは超硬合金やサーメットが熱伝導度や熱膨脹係数の
差が大きい炭化物相と鉄族金族等の結合金属相の2相混
合組織であるのに対して、本発明の焼結体は、鉄族金属
等の結合金属相を含まないものであり、Ti+ Wg
Moの炭化物、窒化物とWp Moの3相あるいは4相
の混合組織で、これ等の熱的性質が類似しているため、
焼結体結晶粒子間に熱応力が生じ難いためと思われる。This is because cemented carbide and cermet have a two-phase mixed structure of a carbide phase with a large difference in thermal conductivity and thermal expansion coefficient and a binder metal phase such as iron group metal, whereas the sintered body of the present invention It does not contain a binding metal phase such as iron group metals, and Ti+ Wg
It is a mixed structure of 3 or 4 phases of Mo carbides and nitrides and WpMo, and their thermal properties are similar.
This seems to be because thermal stress is less likely to occur between the crystal grains of the sintered body.
本発明の焼結体の耐磨耗性の特徴が最も発揮される用途
は、鋼の仕上げ切削である。The application in which the wear-resistant characteristics of the sintered body of the present invention are most exhibited is finish cutting of steel.
鋼の仕上げ切削加工には、従来超硬合金やサーメソトが
用いられてきたが、被加工物の寸法精度や仕上げ面粗度
を良くする為に、通常の切削条件よりも工具の切込み量
、送り量共に小さくして切削する場合が多い。Conventionally, cemented carbide and therme-soto have been used for finish cutting of steel, but in order to improve the dimensional accuracy and finished surface roughness of the workpiece, the depth of cut and feed of the tool have been changed from normal cutting conditions. In many cases, cutting is done by reducing both the amount and the amount.
このような条件で、本発明の焼結体を用いて切削すると
、従来の工具に比較して格段に優れた耐磨耗性を有する
ごとが判明した。It has been found that when the sintered body of the present invention is cut under these conditions, it has much better wear resistance than conventional tools.
本発明の焼結体は、鉄族金属等の結合金属相を含有しな
い為に、切屑の工具刃先への溶着が少なく、また微粒の
焼結体である為工具刃先の刃立性か良く被加工物の加工
向粗度が良い。Since the sintered body of the present invention does not contain a binding metal phase such as an iron group metal, there is less adhesion of chips to the tool cutting edge, and since the sintered body is a fine-grained sintered body, the sharpness of the tool cutting edge is improved. The roughness of the workpiece is good for machining.
特に本発明の焼結体は、炭素鋼、合金鋼の精密中ぐり加
工等の一般にJIS規格で加工而粗度か6−S以下が要
求される場合や、寸法精度を重視する仕上げ切削に適し
ており、従来の工具よりもはるかに長寿命である。In particular, the sintered body of the present invention is suitable for precision boring of carbon steel and alloy steel, which generally requires machining roughness of 6-S or less according to JIS standards, and for finish cutting where dimensional accuracy is important. and has a much longer lifespan than traditional tools.
以下実施例により更に具体的に説明する。This will be explained in more detail below with reference to Examples.
実施例 1
平均粒度1ミクロンのTiC 粉末80重量係と平均粒
度1ミクロンのMo粉末20重量係を超硬合金製のボー
ルを使用して、アトライターで10時間湿式混合した。Example 1 80 parts by weight of TiC powder with an average particle size of 1 micron and 20 parts by weight of Mo powder with an average particle size of 1 micron were wet mixed in an attritor for 10 hours using a cemented carbide ball.
混合された粉末を走査型電子顕微鏡を用いて観察したと
ころ、大部分は1ミクロン以下の微粒となっていた。When the mixed powder was observed using a scanning electron microscope, most of the powder was found to be fine particles of 1 micron or less.
この粉末をステンレス製の内径1o.om,fi径14
M771の底付き容器に充填し、外径9.9朋で厚さ3
1rL1rLのWC−6%Coの合金の円板をその上に
置いた。This powder was applied to a stainless steel plate with an inner diameter of 1 o. om, fi diameter 14
Filled in an M771 container with a bottom, outer diameter 9.9 mm and thickness 3.
A disk of 1rL1rL WC-6%Co alloy was placed on top of it.
更にその上に−100メッシュ+200メッシュの鉄粉
を型押した外径10.Ornmで厚さ2朋の通気性を有
する型押体を置き、ステンVス製円筒に栓をした。Furthermore, on top of that, -100 mesh + 200 mesh iron powder was embossed with an outer diameter of 10. An embossed body with air permeability of 2 mm thick was placed with Ornm, and the stainless steel cylinder was plugged.
この上に純銅の板をのせ、全体を真空炉に入れて1 0
’ mmHgの真空下で1000℃に加熱し1時間
保持して脱ガスせしめた後、湿度を1100℃に昇湿し
10分間保持した。Place a pure copper plate on top of this and put the whole thing in a vacuum furnace.
' After heating to 1000°C under a vacuum of mmHg and holding for 1 hour to degas, the humidity was increased to 1100°C and held for 10 minutes.
冷却後取出してみると、銅が鉄圧粉体中に含浸されてお
り、またこれとステンレス製円筒の界面にも銅が侵入し
て完全に気密な状態に保たれていた。When taken out after cooling, it was found that copper had been impregnated into the iron compact, and that copper had also penetrated the interface between this and the stainless steel cylinder, maintaining a completely airtight state.
この粉末を充填した容器をダイヤモンド合成に用いられ
るガードル型超高圧装置に装入した。The container filled with this powder was placed in a girdle-type ultra-high pressure device used for diamond synthesis.
圧力媒体にはパイロフイライトを用い、ヒーターには黒
鉛の円筒を用いた。Pyrofilite was used as the pressure medium, and a graphite cylinder was used as the heater.
先ず圧力を5 0 kbまで加え、次いで電気を通じて
1300℃に加熱して、20分間保持したのち冷却した
。First, pressure was applied to 50 kb, and then electricity was heated to 1300° C., held for 20 minutes, and then cooled.
圧力を徐々に下げて容器を取出した。The pressure was gradually lowered and the container was removed.
この容器のステンレス部分を除去したところ、T i
−Mo − Cの約1朋厚みの焼結体がWC−15%C
o合金に強固に接着したものが得られた。When the stainless steel part of this container was removed, T i
-Mo-C sintered body with a thickness of about 1 mm is WC-15%C
A product that firmly adhered to the o alloy was obtained.
焼結体の部分をダイヤモンドペーストを用いて研磨し、
顕微鏡で組織観祭したところ、焼結体は第3図や第4図
aK示すようKT iC − ( T i y Mo
) C−Moの3相より成っており、殆んど気孔を有し
ておらず、大部分は1ミクロン以下の微細粒子からなる
ものであった,一方、同一原料粉末を50kbで型押し
た後、1300゜G,10k97朋2の圧力を加え20
分間保持して焼結体を作成した。Polish the sintered body part using diamond paste,
When the structure was observed under a microscope, the sintered body was found to be KT iC − (T i y Mo ) as shown in Figures 3 and 4.
) It was composed of three phases of C-Mo, had almost no pores, and mostly consisted of fine particles of 1 micron or less.On the other hand, the same raw material powder was embossed with 50 kb. After that, apply a pressure of 1300°G and 10k97 to 20
A sintered body was created by holding for a minute.
このホットプレス焼結体■の組織写真を第4図bに示す
。A photograph of the structure of this hot-pressed sintered body (2) is shown in FIG. 4b.
第4図aの超高圧焼結体は殆んど粒成長していないが、
bのホットフレス焼結体■は、かなり粒成長しており、
気孔も存在して焼結体としては不児全なものであった。The ultra-high pressure sintered body shown in Figure 4a has almost no grain growth, but
Hotless sintered body ■ of b has considerable grain growth,
Pores were also present, and the sintered body was defective.
また、同一原料粉末を使用して黒鉛型を用いた通常のホ
ットプレスにより真空中で、18oO℃に加熱し、2
kg/ mm2(7)圧力ヲ加エ、10分間保持して焼
結体を作成した。In addition, the same raw material powder was heated to 18oO℃ in vacuum using a normal hot press using a graphite mold, and
kg/mm2 (7) pressure was applied and held for 10 minutes to create a sintered body.
このホットプンス焼結体Hの比重は5.41であり、1
.5%の気孔率を有するものであった。The specific gravity of this hot punch sintered body H is 5.41, and 1
.. It had a porosity of 5%.
組織観察の結果粒子は粗大化しており、平均粒度は約1
5ミクロンであった。As a result of microstructural observation, the particles have become coarser, with an average particle size of approximately 1
It was 5 microns.
前記焼結体を、ダイヤモンド切断刃によって切断し、こ
れを超硬合金製の通常のスローアウェイチップの一角に
ロウ付けした。The sintered body was cut with a diamond cutting blade, and this was brazed to one corner of an ordinary indexable tip made of cemented carbide.
このチップを用いて切削試験を行った。A cutting test was conducted using this chip.
被剛材は炭素鋼S55C調質材である。The material to be stiffened is carbon steel S55C tempered material.
切削条件は切削速度を170m/分と400m/分の2
種、切込み0.2mm,送り0.1mm/回転とした。The cutting conditions are cutting speeds of 170 m/min and 400 m/min.
The cutting depth was 0.2 mm, and the feed rate was 0.1 mm/rotation.
比較の為に前述のホットプレス体と市販のTi(C=N
)糸サーメット及びAl203−TiC系のホットプレ
ス焼結によるセラミックを用いて、同一条件で切削した
。For comparison, the hot-pressed body and the commercially available Ti (C=N
) Cutting was carried out under the same conditions using thread cermet and Al203-TiC based hot press sintered ceramic.
第5図及び第6図は各工具の磨耗曲線を示したものであ
る。5 and 6 show the wear curves of each tool.
すなわち本発明の焼結体は、比較工具に対して切削速度
1 7 0n/分の条件では工具逃げ面磨耗量が約1/
3〜1/4である。In other words, in the sintered body of the present invention, the amount of tool flank wear is approximately 1/1 compared to the comparative tool at a cutting speed of 170 n/min.
It is 3 to 1/4.
特に同一原料を用いて通常のホットプレスによって作成
した焼結体と比較しても磨耗量は1/3〜1/4で格段
に優れた耐磨耗性を有している。In particular, compared to a sintered body made from the same raw material by ordinary hot pressing, the amount of wear is 1/3 to 1/4, and it has extremely excellent wear resistance.
同第6図に示したように切削速度400m/分といった
高速切削でも、本発明の焼結体は、大変驚くべきことに
セラミック工具より優れた耐磨耗性を有している。As shown in FIG. 6, even during high-speed cutting at a cutting speed of 400 m/min, the sintered body of the present invention surprisingly has superior wear resistance to ceramic tools.
実施例 2 次表の粉末を準備した。Example 2 The powders shown in the table below were prepared.
この粉末を実施例1と同様にして、10時間湿式でアト
ライター混合した。This powder was wet mixed with an attritor for 10 hours in the same manner as in Example 1.
得られた粉末を走査型電子顕微鏡により観察した結果、
大部分の粒子は1ミクロン以下の微粉であった。As a result of observing the obtained powder with a scanning electron microscope,
Most of the particles were fine particles of 1 micron or less.
この粉末を、超硬合金母材を用いず他は実施例1と同様
にしてステンレス製容器に充填し、真空中で加熱脱ガス
し、気密に保たれた状態でピストンシリンダー型の超高
圧装置を用いて次表の条件でホットプレスした。This powder was filled into a stainless steel container in the same manner as in Example 1 except that the cemented carbide base material was not used, and the powder was heated and degassed in a vacuum. Hot pressing was carried out under the conditions shown in the table below.
得られた焼結体をダイヤモンド砥石で、研磨後、ダイヤ
モンドペーストでラツピングして組織観察を行ったとこ
ろ、入〜Cの焼結体はT iC ( T t +W)
Cまたは( Ti , Mo ) C−WまたはMoの
3相の緻密な焼結体となっており、焼結体の結晶粒は、
大部分が1ミクロン以下の微細粒子より成っていて、著
しい粒成長は認められなかった。After polishing the obtained sintered body with a diamond grindstone, the structure was observed by wrapping it with diamond paste and found that the sintered body of I-C was TiC (T t +W).
It is a dense sintered body with three phases of C, (Ti, Mo) C-W, or Mo, and the crystal grains of the sintered body are
The majority consisted of fine particles of 1 micron or less, and no significant grain growth was observed.
一方Dの焼結体は緻密ではあったが、(Ti,Mo)C
−Moの2相より成り、焼結体の結晶粒は平均5ミクロ
ンと粒成長していた。On the other hand, although the sintered body D was dense, (Ti,Mo)C
The sintered body consisted of two phases of -Mo, and the crystal grains of the sintered body had grown to an average size of 5 microns.
次に、第2表の条件で焼結したAについて、実施例1と
同様にしてスローアウエイチップを作成し、切削試験し
た。Next, a throw-away tip was prepared in the same manner as in Example 1 using A sintered under the conditions shown in Table 2, and a cutting test was conducted.
被削材はS45C相当の鋼の丸棒で、切削速度300m
/分、切込み11ft1ft、送り0.25r/Li/
回転の条件で、10分間切削した。The work material is a round bar of steel equivalent to S45C, and the cutting speed is 300 m.
/min, depth of cut 11ft1ft, feed 0.25r/Li/
Cutting was performed for 10 minutes under rotating conditions.
比較の為、実施例1でテストし1こAl203−TiC
系セラミック工具を同時に試験した。For comparison, one Al203-TiC was tested in Example 1.
A series of ceramic tools were tested at the same time.
その結果、?発明の焼結体Aは、工具逃げ面磨耗巾が0
.08rnmですくい面磨耗深さが6ミクロンであった
のに対してA103−{′iC系セラミックでは、それ
ぞれ0.1 5mm、1 0ミクロンであった。the result,? The sintered body A of the invention has a tool flank wear width of 0.
.. The rake face wear depth was 6 microns at 0.08 rpm, whereas it was 0.15 mm and 10 microns for the A103-{'iC series ceramic, respectively.
この切削条件はAl203を主成分とするセラミック工
具が最も特徴を発揮する領域にあり、特に工具すくい面
は高温となり、鋼に対して高温で化学的に安定なAl2
03が他の炭化物や窒化物を主体とする工具材料よりも
耐磨耗性において優れていると考えられてきた。These cutting conditions are in the region where ceramic tools whose main component is Al203 exhibit the most characteristics, and the rake face of the tool is particularly hot, and Al2, which is chemically stable at high temperatures with respect to steel,
It has been thought that 03 has better wear resistance than other carbide- and nitride-based tool materials.
しかし本発明の焼結体はこのような領域においてもA1
03を主体とするセラミックより優れた性能を有してい
ることが判明した。However, the sintered body of the present invention has A1 even in such a region.
It was found that the ceramic had better performance than ceramics mainly composed of 03.
実施例 3 次表の組成に各粉末を配合した。Example 3 Each powder was blended into the composition shown in the table below.
以下実施例1と同様にしてWC−1 5 % Co超硬
合金母材に厚さ1朋の硬質焼結体層が直接接合した焼結
体を作成した。Thereafter, in the same manner as in Example 1, a sintered body was prepared in which a hard sintered body layer having a thickness of 1 mm was directly bonded to a WC-1 5% Co cemented carbide base material.
同焼結時の圧力は55kbとし温度は1350°Cで行
った。The pressure during the sintering was 55 kb and the temperature was 1350°C.
焼結体の組織観察の結果、E,FはTic − ( T
i , Mo ) C 一TiN−Moの4相より、G
はTic−(Ti,Mo)C−Moの3相より、H,I
はT iC 一( Ti, W)( C , N )
−TiN−Wの4相より、KはTi(C,O) (T
i,Mo)(C,O)TiN−Moの4相より、LはT
r ( C t O ) ( Tt yW)(C,O
) 一TiN−Wの4相より、MはTi (CI N
t O )−(Ti j Mo ) (C# NlO)
−TiN−Moの4相より、NはTi(C,N,0 )
−(Ti,W)( C,N,O )−TiN−Wの0
4相より成り、且つこれらの焼結体はTiN添加の効果
により、すべて平均粒度が0.5ミクロン以下の微細で
緻密な組織を有していた。As a result of microstructural observation of the sintered body, E and F are Tic − (T
i, Mo) C - From the four phases of TiN-Mo, G
is from the three phases of Tic-(Ti, Mo)C-Mo, H, I
is TiC (Ti, W) (C, N)
- From the four phases of TiN-W, K is Ti(C,O) (T
i,Mo)(C,O)TiN-Mo, L is T
r (CtO) (TtyW)(C,O
) From the four-phase TiN-W, M is Ti (CI N
tO)-(TijMo)(C#NlO)
-From the four-phase TiN-Mo, N is Ti(C,N,0)
-(Ti,W)(C,N,O)-TiN-W 0
These sintered bodies were composed of four phases, and all had a fine and dense structure with an average grain size of 0.5 microns or less due to the effect of TiN addition.
一方、高融点金属の含有量が3重量係のJ焼結体は平均
粒度が0.5ミクロン以下の微細で緻密ではあったが、
組織を観祭するとTic (Ti,Mo )(C,N
)−TiNの3相より成り、Mo相が存在しなかった。On the other hand, the J sintered body with a high melting point metal content of 3% by weight was fine and dense with an average grain size of 0.5 microns or less;
When observing the organization, Tic (Ti, Mo) (C, N
)-TiN, and no Mo phase was present.
またOも微細で緻密な焼結体であり、組織もTi (C
, O )−(Ti , Mo )(C,N,O)−T
iN−Mo の4相から成り立っていた。O is also a fine and dense sintered body, and its structure is Ti (C
, O)-(Ti, Mo)(C,N,O)-T
It consisted of four phases of iN-Mo.
こへでK〜0の焼結体について含有酸素量を調べデー結
果を旭4表に示オー
表から明らかなように、焼結中における脱酸素はほとん
ど認められない。Here, the amount of oxygen contained in the sintered bodies of K~0 was investigated and the results are shown in Table 4 of Asahi.As is clear from the table, almost no deoxidation of oxygen was observed during sintering.
これらの焼結体の切削性能と靭性を調べた。The cutting performance and toughness of these sintered bodies were investigated.
比較のために、市販のTi(CN)系サーメット、JI
S分類PIO相当のWC基超硬合金も同時にテストした
。For comparison, a commercially available Ti(CN)-based cermet, JI
A WC-based cemented carbide equivalent to S-class PIO was also tested at the same time.
まず耐磨耗テストとしてS55C相当の鋼調質処理材を
、切削速度1’70m/分、切り込み0. 2 an、
送り0.1朋/回転の条件で中ぐり加工を行い逃げ面磨
耗巾と共に面粗度の測定も行った。First, as a wear resistance test, heat-treated steel material equivalent to S55C was cut at a cutting speed of 1'70 m/min and a depth of cut of 0. 2 an,
Boring was performed at a feed rate of 0.1 mm/rotation, and the flank wear width and surface roughness were also measured.
また靭性試験としてJISSCM3種調質材の丸棒に■
形溝を180°間隔で2ケ所長手方向に設け、切削速度
100TrL/分、切込み1 turn,送り0.5r
ILm/回転で切削した。In addition, as a toughness test, a round bar of JISSCM Class 3 tempered material was tested.
Shape grooves are provided in two locations at 180° intervals in the longitudinal direction, cutting speed is 100TrL/min, depth of cut is 1 turn, and feed rate is 0.5r.
Cutting was performed at ILm/rotation.
切削性能の試験結果を第7図に、また靭性試験の結果を
第5表に示す。The cutting performance test results are shown in FIG. 7, and the toughness test results are shown in Table 5.
本発明による焼結体は、耐磨耗性而粗度靭性ともTi(
C,N)系サーメットより優れている。The sintered body according to the present invention has excellent wear resistance, roughness and toughness as well as Ti(
Superior to C,N) based cermets.
さらに本発明焼結体は耐磨耗性向粗度はWC基超硬合金
と比較にならないほど良好である。Furthermore, the sintered body of the present invention has better wear resistance and roughness than WC-based cemented carbide.
また本発明による焼結体は高融点結合金属であるWやM
oの量が減少するほど耐磨耗性は向上し、逆に靭性はM
oが粒界に存在しないJ焼結体は低く、粒界にWあるい
はMoが存在し始める領域からは急に上昇し、あとはW
あるいはMoの増加に伴い除々に良好となる傾好がある
。Furthermore, the sintered body according to the present invention is made of high melting point bonding metals such as W and M.
The wear resistance improves as the amount of o decreases, and conversely, the toughness increases as the amount of M
The J sintered body in which o does not exist at the grain boundaries has a low value, but it rises suddenly from the region where W or Mo begins to exist at the grain boundaries, and then W
Alternatively, as Mo increases, there is a tendency to gradually become better.
また、酸素を含有した焼結体は、高融点結合金属である
WやMOの量を酸素を実質的に含有しない焼結体と同一
にした場合、耐磨耗性能、靭性共良好となる。Further, the sintered body containing oxygen has good wear resistance and toughness when the amount of W and MO, which are high melting point bonding metals, is the same as that of the sintered body that does not substantially contain oxygen.
しかし含有酸素量が10原子係以上であるO焼結体は、
耐磨耗性能、靭性共本発明による焼結体より劣っている
。However, O sintered bodies with an oxygen content of 10 atoms or more,
Both wear resistance and toughness are inferior to the sintered body according to the present invention.
実施例 4
実施例3で作成したG,IおよびNについて切削試験を
行った。Example 4 A cutting test was conducted on G, I and N prepared in Example 3.
被削材はSCM3、切削条件としては、切削速度150
m/分、送り0.50朋/回転、切り込み2xmで10
分間切削した。The workpiece material is SCM3, and the cutting conditions are cutting speed 150.
m/min, feed rate 0.50 h/rev, depth of cut 2xm 10
Cut for a minute.
比較のため市販のTiC コーティングチップも同時に
テストした。For comparison, a commercially available TiC coated chip was also tested at the same time.
その結果を次表に示す。本発明品は市販のTiC コ
ーティングチップやTi(C,N)糸はサーメットより
優れた性能を持っている。The results are shown in the table below. The product of the present invention has better performance than commercially available TiC coated chips and Ti(C,N) threads than cermets.
実施例 5 次表の如く谷粉末を配合した。Example 5 Tani powder was blended as shown in the following table.
以下実施例1と同様にしてWC−1 5 % Co超硬
合金母材に厚さ1.2朋の硬質焼結体層が直接接合した
焼結体を作成した。Thereafter, in the same manner as in Example 1, a sintered body was prepared in which a hard sintered body layer having a thickness of 1.2 mm was directly bonded to a WC-1 5% Co cemented carbide base material.
なお、焼結時の圧力は50kbX?M度は1400℃で
15分間保持した。In addition, the pressure during sintering is 50kbX? The M degree was maintained at 1400° C. for 15 minutes.
焼結体の組織観察の結果、P,Q,R,S,T,U焼結
体はそれぞれ、Ti (C,O)−(Ti,Mo )(
C,O)−Mo,Ti (C,0)−(Ti,W)(C
,0)−W,Ti (C,N) (Ti,W)(C,
N)−W,Ti (C,N) (Ti,Mo )<C
I N)−MOj Ti (CI Nj O )−(T
i ,W)(C,N,O)−W,Ti (C,N,0)
−(Ti j Mo ) ( CI Nj O )
−Mo の3相よりなる焼結体で緻密な組織を有して
いた。As a result of microstructural observation of the sintered bodies, it was found that the P, Q, R, S, T, and U sintered bodies had Ti(C,O)-(Ti,Mo)(
C,O)-Mo,Ti (C,0)-(Ti,W)(C
,0)-W,Ti (C,N) (Ti,W)(C,
N) - W, Ti (C, N) (Ti, Mo) < C
I N)-MOj Ti (CI Nj O)-(T
i, W) (C, N, O) - W, Ti (C, N, 0)
-(Tij Mo) (CI Nj O)
The sintered body was composed of three phases of -Mo and had a dense structure.
これらの焼結体を用いて切削用のバイトを作成し、炭素
鋼S55Cを速度200m/分、切込み0. 5 va
n、送り0. 3 am/ revで切削した。A cutting tool was made using these sintered bodies, and carbon steel S55C was cut at a speed of 200 m/min and a depth of cut of 0. 5 va
n, feed 0. Cut at 3 am/rev.
比較のためTi(C,N)糸サーメットも同時にテスト
した。For comparison, a Ti(C,N) thread cermet was also tested at the same time.
30分切削後の逃げ面磨耗巾を第7表に示す。実施例
6
次表の各粉末を配合した。Table 7 shows the flank wear width after 30 minutes of cutting. Example
6 Each powder in the following table was blended.
第8表
工具材質 Ti(Co.aNo.2)o.gg Ti
N Mo WV 65 5 30
W 70 1020
実施例1と同様にして、圧力50kb,淵度1450℃
で15分間焼結した。Table 8 Tool material Ti (Co.aNo.2) o. gg Ti
N Mo WV 65 5 30 W 70 1020 In the same manner as in Example 1, the pressure was 50 kb and the depth was 1450°C.
It was sintered for 15 minutes.
焼結体の組織観察の結果V,WはそれぞレTi ( C
, N ) (Ti,W)(C,N) 一TiN’
−W及びTi(C,N)一( Ti , Mo )
( C , N ) −TiN−Moの4相よりなる緻
密な組織であった。As a result of microstructural observation of the sintered body, V and W are Ti ( C
, N) (Ti, W) (C, N) -TiN'
-W and Ti(C,N) (Ti, Mo)
It had a dense structure consisting of four phases of (C,N)-TiN-Mo.
これらの焼結体を用いて切削工具用のバイトを作成し、
845C炭素鋼を速度250m/分、切込み1 #!m
、送り0. 3 IIL1IL/回転で10時間切削し
た。These sintered bodies are used to create bits for cutting tools,
845C carbon steel at a speed of 250 m/min, depth of cut 1 #! m
, Feed 0. Cutting was performed for 10 hours at 3 IIL1IL/rotation.
V,Wの逃げ面磨耗巾はそれぞれ0.06と0.07で
あった。The flank wear widths of V and W were 0.06 and 0.07, respectively.
【図面の簡単な説明】
第1図a,by cp dはTi−Mo−C系の各湿度
における状態図、第2図はTi−W−C系の状態図、第
3図はTiC−(Ti ,Mto) C−Moの組織写
真、第4図a,bはそれぞれTiC−(Ti ,Mo
)C−Moの超高圧およびホットプレス焼結体の組織写
真、第5図、第6図及び第7図は本発明の焼結体を切削
工具として使用したときの性能を他の公知工具材料と比
較したグラフである。[Brief explanation of the drawings] Fig. 1 a, by cp d is a state diagram of the Ti-Mo-C system at each humidity, Fig. 2 is a state diagram of the Ti-W-C system, and Fig. 3 is a state diagram of the Ti-Mo-C system. Figures 4a and b are photographs of the structure of TiC-(Ti, Mo) C-Mo, respectively.
) Structure photographs of C-Mo ultra-high pressure and hot pressed sintered bodies, Figures 5, 6 and 7 show the performance when the sintered body of the present invention is used as a cutting tool compared to other known tool materials. This is a comparison graph.
Claims (1)
焼結体のWまたはMoの高融点金属の焼結体中の含有量
が、原子比で5チ以上40係以下であるTic−( T
i* W)C−Ws TiC−(Ti+Mo )C
Mo,Ti (Cy N) (Tt tW)( C,
N)−W,Ti ( C,N)−(Ti,Mo )(
C,N)−Mo,Ti (C,N )−(Ti,W)(
C,N) TiN−W,Ti (C,N)−(Ti,
Mo )(C,N)−TiN−Mo,Ti ( C,O
)−(Ti,W)(C,O) −W,Ti (C,0)
−(Tij Mo )( Cj O)−Mop ’r
i (Cj N,0) 一( Ti,W)(C,N,0
) −W,Ti(C,N,0 )−(Ti,Mo )
(C,N,O)−Mo,Ti ( C,N,0 ) −
( Ti,W)(C,N,O )−TiN−W,Ti
( C,N,0 ) −( Tit Mo )( Ct
Np O ) TiN MopTiC−( Ti
s Mo )C−TiN−Moe TiC −(Ti
,W)C−TiN−W,Ti ( C,O )−( T
i s Mo ) ( Ct O ) −TiN−M
o,あるいはTi ( C, 0 )−(Ti , W
) ( C, O ) −TiN−Wの組織を有する硬
質焼結体であって鉄族金属の結合金属相を実質的に含有
せず、焼結体中の結晶粒の大部分が1ミクロン以下の微
細粒子より成ることを特徴とする工具用焼結体。 2 特許請求の範囲第1項において、(Ti・W)(C
,N)または(Ti,Mo )(C,N)の形で固溶し
ていないTiNの含有量が重量比で20係以下、1係以
上であることを特徴とする工具用焼結体。 3 特許請求の範囲第1項において、焼結体中の酸素の
含有量が原子比で0.1%以上、10係以下であること
を特徴とする工具用焼結体。[Claims] A high melting point metal such as IW or Mo is present at the grain boundaries,
Tic-(T
i*W)C-Ws TiC-(Ti+Mo)C
Mo, Ti (Cy N) (Tt tW) (C,
N)-W,Ti (C,N)-(Ti,Mo)(
C,N)-Mo,Ti (C,N)-(Ti,W)(
C,N) TiN-W,Ti (C,N)-(Ti,
Mo)(C,N)-TiN-Mo,Ti(C,O
) - (Ti, W) (C, O) - W, Ti (C, 0)
-(Tij Mo)(Cj O)-Mop'r
i (Cj N, 0) one (Ti, W) (C, N, 0
) -W,Ti(C,N,0)-(Ti,Mo)
(C,N,O)-Mo,Ti (C,N,0)-
(Ti,W)(C,N,O)-TiN-W,Ti
(C,N,0) −(TitMo)(Ct
NpO) TiN MopTiC-(Ti
sMo)C-TiN-MoeTiC-(Ti
,W)C-TiN-W,Ti(C,O)-(T
isMo)(CtO)-TiN-M
o, or Ti (C, 0)-(Ti, W
) (C, O) - A hard sintered body having a structure of -TiN-W, which does not substantially contain a binding metal phase of iron group metal, and most of the crystal grains in the sintered body are 1 micron or less. A sintered body for tools characterized by comprising fine particles of. 2 In claim 1, (Ti・W)(C
. 3. A sintered body for a tool according to claim 1, wherein the content of oxygen in the sintered body is 0.1% or more and 10% or less in terms of atomic ratio.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP54042177A JPS596906B2 (en) | 1979-04-07 | 1979-04-07 | Sintered body for tools |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP54042177A JPS596906B2 (en) | 1979-04-07 | 1979-04-07 | Sintered body for tools |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS55134152A JPS55134152A (en) | 1980-10-18 |
JPS596906B2 true JPS596906B2 (en) | 1984-02-15 |
Family
ID=12628695
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP54042177A Expired JPS596906B2 (en) | 1979-04-07 | 1979-04-07 | Sintered body for tools |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS596906B2 (en) |
Families Citing this family (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE102004046320A1 (en) * | 2004-09-17 | 2006-05-11 | Bundesanstalt für Materialforschung und -Prüfung (BAM) | Friction materials / tribological materials for radial and axial foil bearings |
JP7429432B2 (en) * | 2019-03-29 | 2024-02-08 | 国立研究開発法人産業技術総合研究所 | Pressure sintered body and its manufacturing method |
-
1979
- 1979-04-07 JP JP54042177A patent/JPS596906B2/en not_active Expired
Also Published As
Publication number | Publication date |
---|---|
JPS55134152A (en) | 1980-10-18 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP2907315B2 (en) | Production of polycrystalline cubic boron nitride | |
JP6257896B2 (en) | Consolidated high toughness coated hard particles in high toughness matrix materials. | |
JP4965047B2 (en) | Cemented carbide tool and method for producing the same | |
US20050226691A1 (en) | Sintered body with high hardness for cutting cast iron and the method for producing same | |
WO2005056495A1 (en) | Cubic boron nitride sintered body and method for making the same | |
JPS627149B2 (en) | ||
JP2000234136A (en) | Cemented carbide, coated cemented carbide and production thereof | |
JPS596906B2 (en) | Sintered body for tools | |
JPS5946907B2 (en) | Sintered cermets for wear-resistant materials and tools | |
JPS5857502B2 (en) | Sintered material with toughness and wear resistance | |
JPS6213311B2 (en) | ||
JPS5818988B2 (en) | Sintered body for tools and its manufacturing method | |
JPS6246510B2 (en) | ||
JP2002194474A (en) | Tungsten carbide matrix super hard composite sintered body | |
JPS644989B2 (en) | ||
JPS5836045B2 (en) | Sintered body for tools and its manufacturing method | |
JPS6059085B2 (en) | coated ceramic tools | |
JP3146803B2 (en) | Method for producing cubic boron nitride based ultra-high pressure sintered material with excellent wear resistance | |
CN112251658B (en) | Ultrafine grain gradient hard alloy and preparation method and application method thereof | |
JPH0551267A (en) | Sintering material for tool | |
JPS6335591B2 (en) | ||
JPS6242988B2 (en) | ||
JPS638072B2 (en) | ||
JPH0149667B2 (en) | ||
JPH10310839A (en) | Super hard composite member with high toughness, and its production |