JPH0696751B2 - Cemented carbide - Google Patents
Cemented carbideInfo
- Publication number
- JPH0696751B2 JPH0696751B2 JP2091637A JP9163790A JPH0696751B2 JP H0696751 B2 JPH0696751 B2 JP H0696751B2 JP 2091637 A JP2091637 A JP 2091637A JP 9163790 A JP9163790 A JP 9163790A JP H0696751 B2 JPH0696751 B2 JP H0696751B2
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- solid solution
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- weight
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Description
【発明の詳細な説明】 〔産業上の利用分野〕 本発明は、WCおよびB1型固溶体を主体として、残部Co等
のFe族金属から構成される超硬合金に関するものであ
り、特に、その耐摩耗性および衝撃靱性の改善に関する
ものである。DETAILED DESCRIPTION OF THE INVENTION [Industrial field of use] The present invention relates to a cemented carbide mainly composed of a WC and B1 type solid solution and the balance being an Fe group metal such as Co. The present invention relates to improvement of wear resistance and impact toughness.
WCとB1型固溶体（但し、WCとB1型固溶体は、重量比でWC
/B1型固溶体＝97/3〜70/30の範囲）98〜70重量％と、Co
を主体とするFe族金属２〜30重量％とからなる超硬合金
は、良く知られているように、耐熱性・耐摩耗性・耐酸
化性等に富むため、鋼、鋳鋼、ステンレス鋼、高マンガ
ン鋼、ダクタイル鋳鋼等の切削工具用に広く用いられて
いる。WC and B1 type solid solution (however, WC and B1 type solid solution are
/ B1 type solid solution = 97 / 3-70 / 30) 98-70% by weight, Co
As is well known, cemented carbides containing 2 to 30% by weight of Fe group metal, which is mainly composed of, are rich in heat resistance, wear resistance, oxidation resistance, etc., so that steel, cast steel, stainless steel, Widely used for cutting tools such as high manganese steel and ductile cast steel.
従来、この種の超硬合金の硬質相におけるB1型固溶体
は、 出発原料として、TiCおよびTaCを使用し、焼結過程
中でWCの一部と固溶させて形成する。Conventionally, a B1-type solid solution in the hard phase of this kind of cemented carbide is formed by using TiC and TaC as starting materials and forming a solid solution with a part of WC during the sintering process.
出発原料として、D.Cと呼ばれるWCとTiCの固溶体お
よびTaCを使用し、焼結過程中にこれらを固溶させる。As a starting material, a solid solution of WC and TiC called DC and TaC are used, and these are dissolved during the sintering process.
出発原料として、WC−TiC−TaCの三元固溶炭化物を
用いる、等の方法が知られている。Methods such as using a WC-TiC-TaC ternary solid solution carbide as a starting material are known.
尚、上記D.Cまたは三元固溶炭化物としては、通常、そ
の中に含まれるWCとTiCが重量比でWC/TiC＝70/30〜97/3
のものが用いられる。これはTiCの耐酸化性、耐摩耗性
の特長と、TaCの高温での強靱性の双方の性質をバラン
スよく加味させるためである。As the DC or ternary solid solution carbide, WC and TiC contained therein are usually in a weight ratio of WC / TiC = 70/30 to 97/3.
What is used. This is because the characteristics of both TiC oxidation resistance and wear resistance and TaC toughness at high temperature are well balanced.
WCは状態図上必然的にTiC−TaCからなる固溶炭化物に吸
収され、３元固溶炭化物となる。また、TaCは非常に高
価であるために、その一部をNbCで置換することも提案
されているが、従来知られているNbC置換量は、高々30
重量％までであり、それ以上置換した場合には、合金の
諸性質が低下するとされている。WC is inevitably absorbed in the solid solution carbide composed of TiC-TaC in the phase diagram and becomes a ternary solid solution carbide. Since TaC is very expensive, it has been proposed to replace a part of it with NbC, but the amount of NbC replacement that has hitherto been known is 30 at most.
It is up to wt%, and it is said that when it is replaced more than that, various properties of the alloy deteriorate.
上述したように、従来は硬質相におけるB1型固溶体とし
て、WC−TiC−TaC固溶体が主として用いられてきたが、
最近B1型固溶体としてHfC、VC、あるいはZrCなどの優れ
た性質を利用しようとの試みもなされている。しかしな
がら、これらの炭化物を実際に超硬合金に多量に含有さ
せ、実用に供している例はあまり見当らない。その理由
は必ずしも明かでないが、これらの炭化物を多量に含有
するほど機械的靱性あるいは熱的靱性が劣化することが
主な原因と考えられる。すなわち、元来、B1型固溶体と
Fe族金属とのぬれ性はWCとFe族金属との濡れ性ほど良好
ではない。しかるに、B1型固溶体中に更にHf、Zr、また
はＶの炭化物や窒化物を含有させた場合には、より一層
ぬれ性が劣化し靱性をおとすことが経験上知られてお
り、このことが実用合金として多量に含有できない原因
とおもわれる。As described above, conventionally, as the B1 type solid solution in the hard phase, WC-TiC-TaC solid solution has been mainly used,
Recently, attempts have been made to utilize the excellent properties of HfC, VC, or ZrC as a B1 type solid solution. However, there are not many examples in which a large amount of these carbides are actually contained in a cemented carbide and are put to practical use. Although the reason is not always clear, it is considered that the main cause is that the mechanical toughness or the thermal toughness deteriorates as the content of these carbides increases. That is, originally, B1 type solid solution and
The wettability with Fe group metals is not as good as the wettability with WC and Fe group metals. However, it is known from experience that if a B1 type solid solution further contains Hf, Zr, or V carbides or nitrides, the wettability further deteriorates and the toughness deteriorates. This is probably the reason why it cannot be contained in a large amount as an alloy.
本発明は、上記欠点すなわちB1型固溶体とFe族金属のぬ
れ性を改良し、耐撃靱性、熱的靱性、および耐摩耗性を
改善した新規な超硬合金を提供することを目的とする。It is an object of the present invention to provide a novel cemented carbide which has the above-mentioned drawbacks, that is, the wettability of a B1 type solid solution and a Fe group metal, and has improved impact toughness, thermal toughness, and wear resistance.
上記目的を達成するために、本発明は、重量％で、WCお
よびB1型固溶体を合計で98〜70重量％（但し、WCとB1型
固溶体の含有量は、重量比で、WC/B1型固溶体の重量比
は、97/3〜70/30の範囲内）と、Coを主体とする２〜30
重量％のFe族金属とから構成されるWC基超硬合金におい
て、上記B1型固溶体が、WCおよびTiCならび第３の硬質
物質（但し、該第３の硬質物質ＭはHfC、ZrC、またはVC
のうち１種または２種以上からなり、その５〜30重量％
がHfN,ZrN,またはVNで置換されたもの）Ｍから構成さ
れ、かつWC−TiC−Ｍの重量比率を表す第１図における
点Ａ（63.8WC−34.4TiC−1.8M）、点Ｂ（38.8WC−58.1T
iC−3.1M）、点Ｃ（21.1WC−31.5TiC−47.4M）、点Ｄ
（42.6WC−23.0TiC−34.4M）の４点を結ぶ線で囲まれた
領域内の固溶体であることを特徴とするものである。In order to achieve the above object, the present invention provides a total of 98 to 70% by weight of WC and B1 type solid solution (however, the content of WC and B1 type solid solution is WC / B1 type by weight ratio). The solid solution weight ratio is within the range of 97/3 to 70/30) and 2 to 30 mainly containing Co.
In a WC-based cemented carbide composed of wt% Fe group metal, the B1-type solid solution comprises WC and TiC and a third hard substance (provided that the third hard substance M is HfC, ZrC, or VC).
5 to 30% by weight of one or more of the above
Is substituted with HfN, ZrN, or VN) M, and represents the weight ratio of WC-TiC-M in FIG. 1 at point A (63.8WC-34.4TiC-1.8M) and point B (38.8WC-34.4TiC-1.8M). WC-58.1T
iC-3.1M), point C (21.1WC-31.5TiC-47.4M), point D
(42.6WC-23.0TiC-34.4M) is a solid solution in a region surrounded by a line connecting four points.
本発明の特長は、特に出発原料としてのB1型固溶体にお
けるWCとTiCの重量比を調整することによって、B1型固
溶体のぬれ性を改善したことにある。すなわち、本発明
者等は硬質相におけるB1型固溶体を構成する成分につい
て、その原料粉末の組成と諸物性との関係、および原料
粉末組成と焼結体の組織の相関等に関して詳細な検討を
加えたところ、次のような驚くべき事実を見出した。
原料粉末として、D.Cと他の硬質物質を用いて焼結過程
中で固溶させB1型固溶体を構成するよりも、あらかじめ
所定成分組成のB1型固溶体を作成し、これを出発原料と
して用いる方が、得られる焼結体の硬さが高く耐摩耗性
に優れている。この場合靱性は同等である。B1型固溶
体出発原料中のWCとTiCの含有比によって靱性は大きく
変化し、靱性を最も向上させる最適範囲が存在する。The feature of the present invention is that the wettability of the B1 type solid solution is improved by adjusting the weight ratio of WC and TiC in the B1 type solid solution as a starting material. That is, the present inventors, for the components constituting the B 1 type solid solution in the hard phase, the relationship between the composition of the raw material powder and various physical properties, and a detailed study on the correlation between the raw material powder composition and the structure of the sintered body, etc. In addition, I found the following surprising facts.
As a raw material powder, it is better to prepare a B1 type solid solution having a predetermined component composition in advance and use this as a starting material than to form a B1 type solid solution by solid solution using DC and other hard substances in the sintering process. The obtained sintered body has high hardness and excellent wear resistance. In this case, the toughness is the same. The toughness changes greatly depending on the content ratio of WC and TiC in the B1 type solid solution starting material, and there is an optimum range for improving the toughness most.
上記のの理由については詳細不明であるが、おそらく
D.Cを用いた場合、焼結過程中で他の硬質物質がD.Cに固
溶して粒成長が生ずることに一因があるものと思われ
る。I'm not sure about the reasons above, but maybe
When DC is used, it is thought that this is partly because other hard substances form a solid solution with DC during the sintering process to cause grain growth.
上記の理由については第２図を用いて満足のいく説明
が出来る。すなわち、通常の超硬合金の焼結温度範囲は
1350℃〜1500℃であるが、この範囲での相境界は、良く
知られているように、WC/TiC＝70/30の線上と考えて良
い。そして、B1型固溶体出発原料のWC/TiCの比がこの相
境界とずれている場合、例えば、第２図上のａ点やｃ点
の組成である場合、焼結過程でａ点からｂ点へ、あるい
はｃ点からｂ点へとB1型固溶体の組成が変化するような
駆動力（driving force）が働く。しかしながら注目す
べきことは、B1型固溶体中でのＷの拡散速度は1350℃〜
1500℃において非常に遅く、このためB1型固溶体が有芯
構造となる点である。すなわち、ａ点の組成を有するB1
型固溶体を出発原料として用いた場合には、焼結過程で
WCを放出してWC poor側に移行するため、内部に比べて
表層部はWCがpoorになる。一方、ｃ点の組成から成るB1
型固溶体を出発原料として用いた場合には、焼結過程に
周辺にあるWC原料粉末粒子との相境界からB1型固溶体原
料粒子中にWCを取り込んでWC rich側に移行するため、
内部に比べて表層部がWC richな固溶体が形成される。
第３図はこのようにして形成される有芯構造を模式的に
示したものである。相境界よりWCがpoorなB1型固溶体を
出発原料として用いた場合は、表層部におけるWCが非常
に高濃度と成るためFe族金属との濡れ性は著しく改善さ
れる。本発明の最も特長とする点は、まさにこの点にあ
る。すなわち、本発明は、B1型固溶体の表面にWCを析出
させることによって、非常に焼結性は悪るいが工具材料
としては優れた性質を有するZrC、VC、HfC等の炭化物、
あるいはZrN、VN、HfN等の窒化物をB1型固溶体成分とし
て超硬合金に多量に含有させることを可能ならしめたも
のである。The above reason can be explained satisfactorily with reference to FIG. That is, the sintering temperature range of ordinary cemented carbide is
Although it is 1350 ° C to 1500 ° C, the phase boundary in this range can be considered to be on the line of WC / TiC = 70/30, as is well known. When the WC / TiC ratio of the B1 type solid solution starting material is deviated from this phase boundary, for example, when the composition is the point a or the point c in FIG. 2, the point a to the point b in the sintering process. , Or a driving force that changes the composition of the B1-type solid solution from point c to point b. However, it should be noted that the diffusion rate of W in the B1-type solid solution is 1350 ° C-
This is very slow at 1500 ° C, which is why the B1-type solid solution has a core structure. That is, B1 having a composition of point a
When the mold solid solution is used as the starting material,
Since WC is released and moves to the WC poor side, WC becomes poorer in the surface layer compared to the inside. On the other hand, B1 consisting of the composition of point c
When a type solid solution is used as a starting material, since WC is incorporated into the B1 type solid solution material particles from the phase boundary with the WC material powder particles in the periphery of the sintering process, the WC rich side is transferred,
A solid solution with a WC rich surface layer is formed compared to the inside.
FIG. 3 schematically shows the cored structure thus formed. When a B1-type solid solution in which WC is poor from the phase boundary is used as the starting material, the WC concentration in the surface layer is extremely high, and the wettability with the Fe group metal is significantly improved. This is the most important point of the present invention. That is, the present invention, by precipitating WC on the surface of the B1 type solid solution, ZrC, VC, carbide such as HfC, which has excellent properties as a tool material, although the sinterability is very poor,
Alternatively, it is possible to add a large amount of a nitride such as ZrN, VN, HfN to the cemented carbide as a B1 type solid solution component.
本発明において、好ましい効果を得るためには、WCとTi
Cの含有量に留意することが望ましく、重量比で65/35≧
WC/TiC≧40/60の範囲とするのが良い。また、更に良い
性質を得るためには60/40≧WC/TiC≧50/50の範囲とする
ことが望ましい。WC/TiC＞65/35ではB1型固溶体の表面
にあまりWCが析出せず靱性が改善されず、一方、WC/TiC
＜40/60では、WC析出層の厚みがありすぎてB1型固溶体
の性質が失われるので望ましくないためである。In the present invention, in order to obtain a preferable effect, WC and Ti
It is desirable to pay attention to the C content, and the weight ratio is 65/35 ≧
WC / TiC ≧ 40/60 is recommended. Further, in order to obtain better properties, it is desirable that the range is 60/40 ≧ WC / TiC ≧ 50/50. When WC / TiC> 65/35, WC does not precipitate much on the surface of B1-type solid solution and the toughness is not improved, while WC / TiC
This is because when <40/60, the WC precipitate layer is too thick and the properties of the B 1 type solid solution are lost, which is not desirable.
また、本発明において、第３の硬質物質Ｍとして、Zr
C、HfC、VCを選んだ理由は、これらの炭化物はTiCおよ
びWCとの固溶体を形成した場合、耐フランク摩耗性、お
よび耐クレーター摩耗性が著しく向上するためである。
ZrN、HfN、VN等についても同様の理由による。特に窒化
物の場合には、焼結性が炭化物よりもちらに悪いため、
本発明によってはじめて多量に含有することが可能とな
ったものである。Further, in the present invention, as the third hard material M, Zr
The reason why C, HfC, and VC are selected is that these carbides significantly improve flank wear resistance and crater wear resistance when forming a solid solution with TiC and WC.
The same reason applies to ZrN, HfN, VN, etc. Especially in the case of nitrides, because the sintering property is much worse than that of carbides,
The present invention makes it possible for the first time to contain a large amount.
また、TiCに対する第３の硬質物質Ｍの重量比を95/5≦T
iC/第３の硬質物質Ｍ≦40/60とした理由は、第３の硬質
物質Ｍの含有量が95/5未満と少ない場合には当該第３の
硬質物質含有による良い性質が引き出せないためであ
り、一方、40/60を超えて含有させた場合には、Fe族金
属とのぬれ性が悪くなるためである。尚、本発明者等の
実験結果によれば、80/20≦第３の硬質物質Ｍ≦50/50で
は、さらに靱性、耐摩耗性、耐熱性において望ましい改
善効果が得られた。Further, the weight ratio of the third hard material M to TiC is 95/5 ≦ T
The reason for setting iC / third hard substance M ≤ 40/60 is that if the content of the third hard substance M is as low as less than 95/5, good properties due to the inclusion of the third hard substance cannot be derived. On the other hand, when it is contained in excess of 40/60, the wettability with the Fe group metal deteriorates. According to the results of experiments conducted by the present inventors, 80/20 ≦ third hard material M ≦ 50/50 further provided desirable improvements in toughness, wear resistance, and heat resistance.
本発明において、第３の硬質物質Ｍにおける窒化物の置
換量を30％以下としたのも上記と同様の理由による。ま
た、本発明において、TiN置換量をTiCの50％以内にした
理由は、それ以上置換した場合には機械的性質が低下し
望ましくないためである。In the present invention, the reason why the substitution amount of the nitride in the third hard material M is set to 30% or less is the same as the above. Further, in the present invention, the reason why the TiN substitution amount is set within 50% of TiC is that the mechanical properties are deteriorated when it is further substituted, which is not desirable.
さらに、上記第３の硬質物質ＭとしてTaCとNbCの固溶体
を用いる場合には、TaCとNbCの重量比が0.3≦NbC/（TaC
＋NbC）≦0.5の範囲にあることが望ましい。その理由
は、0.3未満の添加含有では経済的効果が薄く、一方、
0.5を超える含有では耐熱衝撃性が悪くなり実用に供し
得ないためである。Further, when a solid solution of TaC and NbC is used as the third hard material M, the weight ratio of TaC and NbC is 0.3 ≦ NbC / (TaC
+ NbC) ≦ 0.5 is desirable. The reason is that if the content of addition is less than 0.3, the economic effect is small, while
This is because if the content exceeds 0.5, the thermal shock resistance deteriorates and it cannot be put to practical use.
以下、本発明を実施例により詳述する。 Hereinafter, the present invention will be described in detail with reference to examples.
実施例１ 重量比で、76WC−5TiC−3TiN−4TaC−8Coの組成になる
ように、第６表に示す原料粉末を用いて配合した。Example 1 The raw material powders shown in Table 6 were blended to give a composition of 76WC-5TiC-3TiN-4TaC-8Co in a weight ratio.
次に、この配合粉末にプレス助剤としてパラフインを２
重量％加え有機溶剤中アトライターで６時間混合した。
これを乾燥後、1t/cm2の圧力にプレス成形した後1425℃
で真空焼結し、試験片を得た。得られた超硬合金は第２
表に示すごとく、SSを使用した本発明による試料２は比
較材試料１に比べて靱性がはるかに優れ、また硬さも高
いことがわかる。 Next, 2 parts of paraffin as a press aid was added to this compounded powder.
% By weight was added and mixed in an organic solvent with an attritor for 6 hours.
After drying it, press molding it to a pressure of 1 t / cm 2 and then 1425 ° C.
Vacuum sintering was carried out to obtain a test piece. The cemented carbide obtained is the second
As shown in the table, it is understood that the sample 2 according to the present invention using SS has much higher toughness and higher hardness than the comparative material sample 1.
実施例２ 重量比で、71WC−12TiC−7HfC−1HfN−9Coの組成になる
ように、第３表に示す原料粉末を用いて配合した。 Example 2 The raw material powders shown in Table 3 were blended so that the composition would be 71WC-12TiC-7HfC-1HfN-9Co in a weight ratio.
試料３は固溶体を使用しないものであり、試料４はD.C
を使用したもの、試料５はSSを用いた本発明ののもので
ある。但し、本実施例におけるSSはWC−TiC−HfC−HfN
の４元固溶体である。Sample 3 does not use solid solution, Sample 4 is DC
Is used, and sample 5 is that of the present invention using SS. However, SS in this example is WC-TiC-HfC-HfN.
It is a quaternary solid solution.
この配合粉末から実施例１と同様の方法を用いて試料を
作成し、諸物性を調査した。その結果を第４表に示す。
第４表から明らかなごとくSSを使用した本発明による試
料５は硬さ、抗析力ともに従来材より優れていることが
わかる。 A sample was prepared from this blended powder by the same method as in Example 1, and various physical properties were investigated. The results are shown in Table 4.
As is apparent from Table 4, Sample 5 according to the present invention, which uses SS, is superior to the conventional material in both hardness and segregation force.
実施例３ 重量％で、第５表に示す組成の合金となるよう原料を配
合し、実施例１と同様な方法により試料を作成した。 Example 3 A sample was prepared in the same manner as in Example 1 except that the raw materials were blended so as to give an alloy having the composition shown in Table 5 at a weight percentage.
ただし、試料No.6,8,10,及び12は第６表に示す組成の固
溶炭窒化物を用いて配合した。但し、6,8,10,及び12に
用いた固溶体炭窒化物は、いずれもWC/TiC＝55/45,TiC/
M＝60/40のものである。また、第６表中の数値はいずれ
も重量％であるが、重量比は100％に換算していない。
また第７表に抗析力と硬さを示す。However, sample Nos. 6, 8, 10, and 12 were compounded using solid solution carbonitrides having the compositions shown in Table 6. However, the solid solution carbonitrides used for 6, 8, 10, and 12 are all WC / TiC = 55/45, TiC /
M = 60/40. Further, all the numerical values in Table 6 are% by weight, but the weight ratio is not converted to 100%.
Table 7 shows the anti-segregation force and hardness.
この表から、本発明による試料6,8,10,12のものは、他
の従来の試料に比べて優れた抗析力を有する事がわか
る。このように本発明材は優れた靱性を示すことがわか
る。 From this table, it can be seen that the samples 6, 8, 10 and 12 according to the present invention have superior anti-sedimentation force as compared with other conventional samples. Thus, it can be seen that the material of the present invention exhibits excellent toughness.
実施例４ 重量％で、第８表に示す組成の合金となるよう原料を配
合し、実施例１と同様な方法により試料を作成した。但
し、試料No.14,16,18,20及び22は第９表に示す固溶体炭
窒化物を用いて配合したものである。Example 4 A sample was prepared in the same manner as in Example 1 except that the raw materials were mixed so as to give an alloy having the composition shown in Table 8 at a weight percentage. However, sample Nos. 14, 16, 18, 20 and 22 were compounded using solid solution carbonitrides shown in Table 9.
但し、14,16,18,20及び22に用いた固溶体炭窒化物は、
いずれもWC/TiC＝50/50、TiC/M＝60/40のものである。
また、第11表中の数値はいずれも重量％であるが、重量
比は100％に換算していない。 However, the solid solution carbonitrides used for 14, 16, 18, 20 and 22 are
Both have WC / TiC = 50/50 and TiC / M = 60/40.
In addition, all the numerical values in Table 11 are% by weight, but the weight ratio is not converted to 100%.
これらの試料の抗析力と硬さを第15表に示す。Table 15 shows the anti-sedimentation force and hardness of these samples.
この表から、本発明による試料22,24,26,28および30の
ものは、他の従来の試料に比べて優れた抗析力を有する
事がわかる。From this table, it can be seen that the samples 22, 24, 26, 28 and 30 according to the present invention have a superior anti-sedimentation force as compared with other conventional samples.
以上詳述したように、本発明は出発原料としてB1型固溶
体を使用し、特に固溶体中のWCとTiCの比を調整するこ
とにより、焼結過程中においてB1型固溶体表面上にFe族
金属との濡れ性の良いWCを析出させ、それによって、従
来、添加量が限られていたZr,Hf,Vの炭化物あるいは炭
窒化物を多量に添加することを可能ならしめて著しい靱
性、耐摩耗性の向上をみたものである。 As described in detail above, the present invention uses a B1 type solid solution as a starting material, and particularly by adjusting the ratio of WC and TiC in the solid solution, an Fe group metal on the B1 type solid solution surface during the sintering process. Of WC, which has a good wettability, is added, which makes it possible to add a large amount of Zr, Hf, V carbides or carbonitrides, which had been limited in the past, to achieve remarkable toughness and wear resistance. This is an improvement.
第１図はWC−TiC−第３硬質物質Ｍの重量比率を表す
図、第２図はB1型固溶体の焼結過程中での組成の変化を
示した図、第３図はB1型固溶体の有芯組織を示す図、第
４図は出発原料のWC/TiC比の変化を示す図である。FIG. 1 is a diagram showing the weight ratio of WC-TiC-third hard material M, FIG. 2 is a diagram showing the compositional change of the B1 type solid solution during the sintering process, and FIG. 3 is a diagram showing the B1 type solid solution. FIG. 4 is a diagram showing a cored structure, and FIG. 4 is a diagram showing changes in the WC / TiC ratio of the starting material.
Claims (3)
体の重量比は、97/3〜70/30）98〜70重量％と、Coを主
体とするFe族金属２〜30重量％から構成されるWC基超硬
合金において、上記B1型固溶体が、WC,TiC,および第３
の硬質物質Ｍ（但し、該第３の硬質物質ＭはHfC,ZrC,ま
たはVCのうちの１種または２種以上からなり、その５〜
30重量％がHfN,ZrN,またはVNで置換されたもの）から構
成され、かつWC−TiC−Ｍの重量比率を表す第１図にお
ける点Ａ（63.8WC−34.4TiC−1.8M）、点Ｂ（38.8WC−5
8.1TiC−3.1M）、点Ｃ（21.1WC−31.5TiC−47.4M）、点
Ｄ（42.6WC−23.0TiC−34.4M）の４点を結ぶ線で囲まれ
た領域内の固溶体であることを特徴とするWC基超硬合
金。1. WC and B1 type solid solution (however, the weight ratio of WC / B1 type solid solution is 97/3 to 70/30) 98 to 70% by weight, and Fe group metal mainly composed of Co 2 to 30% by weight % Of WC-based cemented carbide, the B1-type solid solution is WC, TiC, and
Hard substance M (provided that the third hard substance M is composed of one or more of HfC, ZrC, or VC;
30% by weight of HfN, ZrN, or VN) and represents the weight ratio of WC-TiC-M, point A (63.8WC-34.4TiC-1.8M), point B in FIG. (38.8WC-5
8.1TiC-3.1M), point C (21.1WC-31.5TiC-47.4M), and point D (42.6WC-23.0TiC-34.4M) are solid solutions in the area surrounded by the line connecting them. Characteristic WC-based cemented carbide.
体の重量比は、97/3〜70/30）98〜70重量％と、Coを主
体とするFe族金属２〜30重量％から構成されるWC基超硬
合金において、上記B1型固溶体が、WC,TiC,および第３
の硬質物質Ｍ（但し、該第３の硬質物質ＭはHfC,ZrC,ま
たはVCのうちの１種または２種以上からなり、その５〜
30重量％がHfN,ZrN,またはVNで置換されたもの）から構
成され、かつWC−TiC−Ｍの重量比率を表す第１図にお
ける点Ａ（63.8WC−34.4TiC−1.8M）、点Ｂ（38.8WC−5
8.1TiC−3.1M）、点Ｃ（21.1WC−31.5TiC−47.4M）、点
Ｄ（42.6WC−23.0TiC−34.4M）の４点を結ぶ線で囲まれ
た領域内の固溶体であるWC基超硬合金において、前記B1
型固溶体を構成するTiCの５〜50％をTiNで置換したこと
を特徴とするWC基超硬合金。2. WC and B1 type solid solution (however, the weight ratio of WC / B1 type solid solution is 97/3 to 70/30) 98 to 70% by weight, and Fe group metal mainly composed of Co 2 to 30% by weight % Of WC-based cemented carbide, the B1-type solid solution is WC, TiC, and
Hard substance M (provided that the third hard substance M is composed of one or more of HfC, ZrC, or VC;
30% by weight of HfN, ZrN, or VN) and represents the weight ratio of WC-TiC-M, point A (63.8WC-34.4TiC-1.8M), point B in FIG. (38.8WC-5
8.1TiC-3.1M), point C (21.1WC-31.5TiC-47.4M), point D (42.6WC-23.0TiC-34.4M), which is a solid solution in the area surrounded by the line connecting the four points. In cemented carbide, the B1
A WC-based cemented carbide, characterized in that 5 to 50% of TiC constituting the mold solid solution is replaced with TiN.
体の重量比は、97/3〜70/30）98〜70重量％と、Coを主
体とするFe族金属２〜30重量％から構成されるWC基超硬
合金において、上記B1型固溶体が、WC,TiC,および第３
の硬質物質Ｍ（但し、該第３の硬質物質Ｍは、TaCとNbC
の固溶炭化物であり、かつTaCとNbCの重量比が0.3≦NbC
/（TaC＋NbC）≦0.5である）から構成され、かつWC−Ti
C−Ｍの重量比率を表す第１図における点Ａ（63.8WC−3
4.4TiC−1.8M）、点Ｂ（38.8WC−58.1TiC−3.1M）、点
Ｃ（21.1WC−31.5TiC−47.4M）、点Ｄ（42.6WC−23.0Ti
C−34.4M）の４点を結ぶ線で囲まれた領域内の固溶体で
あることを特徴とするWC基超硬合金。3. WC and B1 type solid solution (however, the weight ratio of WC / B1 type solid solution is 97/3 to 70/30) 98 to 70% by weight, and Fe group metal mainly composed of Co 2 to 30% by weight % Of WC-based cemented carbide, the B1-type solid solution is WC, TiC, and
Hard material M (however, the third hard material M is TaC and NbC
Solid solution carbide and the weight ratio of TaC and NbC is 0.3 ≦ NbC.
/ (TaC + NbC) ≤ 0.5) and WC-Ti
Point A (63.8WC-3
4.4TiC-1.8M), Point B (38.8WC-58.1TiC-3.1M), Point C (21.1WC-31.5TiC-47.4M), Point D (42.6WC-23.0Ti)
C-34.4M) WC-based cemented carbide characterized by being a solid solution in the region surrounded by the line connecting the four points.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2091637A JPH0696751B2 (en) | 1990-04-06 | 1990-04-06 | Cemented carbide |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2091637A JPH0696751B2 (en) | 1990-04-06 | 1990-04-06 | Cemented carbide |
Related Parent Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP9706181A Division JPS57210950A (en) | 1981-06-23 | 1981-06-23 | Sintered hard alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH04263038A JPH04263038A (en) | 1992-09-18 |
| JPH0696751B2 true JPH0696751B2 (en) | 1994-11-30 |
Family
ID=14032048
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2091637A Expired - Lifetime JPH0696751B2 (en) | 1990-04-06 | 1990-04-06 | Cemented carbide |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0696751B2 (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6797369B2 (en) | 2001-09-26 | 2004-09-28 | Kyocera Corporation | Cemented carbide and cutting tool |
| JP4126451B2 (en) * | 2002-03-22 | 2008-07-30 | 京セラ株式会社 | Cemented carbide |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5942067B2 (en) * | 1975-04-25 | 1984-10-12 | 三菱マテリアル株式会社 | Tough tungsten carbide-based cemented carbide for cutting tools |
| JPS6214025A (en) * | 1985-07-11 | 1987-01-22 | Komatsu Ltd | Vehicle load measuring device |
-
1990
- 1990-04-06 JP JP2091637A patent/JPH0696751B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPH04263038A (en) | 1992-09-18 |
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