JPS5997579A - Composite sintered body and manufacture - Google Patents

Abstract

(57) [Summary] This bulletin contains application data before electronic filing, so abstract data is not recorded.

Description

DETAILED DESCRIPTION OF THE INVENTION The present invention applies to hardened alloy steels, carburized materials, stainless steels, and high nickel steels, which are difficult-to-cut materials that have high hardness, wear resistance, toughness, heat resistance, and corrosion resistance. The present invention relates to a composite sintered body suitable for cutting tools such as alloys, and wear-resistant tools such as bearings, work rests, and dies, and a method for manufacturing the same.

A conventional Enoji body in which a high-density phase boron nitride sintered body containing CB1~ and/or rt, W BiN f and a cemented carbide or cermet is circularly bonded is a high-density phase boron nitride sintered body. When judged as a sintered body consisting of CBN and/or WBN in the body part and a binder phase, it can be broadly classified by phase: first, those in which the binder phase is made of metal or alloy;
Second, the binder phase is composed of a single compound, rt, or composite compound; and third, the binder phase is composed of a metal or alloy and a single compound or a composite compound. . This sintered body consisting of a binder phase with an internal temperature of 1 has a low hardness and is easily softened at high temperatures. The disadvantage is that the wear resistance is extremely poor, and the sintered body made of the second binder phase has a high hardness of the binder phase and little decrease in hardness at high temperatures, but has low toughness and cannot be used under intermittent cutting conditions. It has the disadvantage that chipping or chipping is likely to occur when used, and the sintered body made of the third binder phase has a low hardness and becomes even softer in the Shima vortex when the amount of gold or alloy in the binder phase increases. It is easy to say that when the amount of a single compound or a composite compound in the binder phase increases, the hardness increases and the toughness decreases, and the properties are simply in the middle between the first (/:) binder phase and the second binder phase. -iJ There is a problem.

In addition, when rotary bonding a high-density phase A #metallic sintered body and a cemented carbide base metal or cermet, there are two methods: bonding with an intervening abrasion at normal pressure, and rotary bonding at a Mi-related pressing temperature F. There is a way. A 7"c piece joined with this inner vein material is made of both the densified boron sintered body and the super-alloy or C-met (
There is a problem that the frequency of joining is low because there is no solder material that is in demand, or that the solder material softens at high temperatures and becomes thicker when plastic deformation occurs. This poses a problem in that the reactivity between the Umada phase boron nitride sintered base and the cemented carbide base metal or cermet is poor, resulting in the formation of pores in the bonded joint, resulting in a decrease in the strength of the same layer.

The present invention completely eliminates the above-mentioned conventional drawbacks and problems, and provides a high-density phase nitrided (DL) composite material that has excellent hardness, heat resistance, corrosion resistance, and high-temperature strength, as well as improved wear resistance and toughness. The composite sintered body of the present invention is a temporary sintered body that has a high bonding strength with cemented carbide or cermet, and a method for manufacturing the same. Or with or without WBN and a bonding phase of 20-60 hours:
If the sintered insert consisting of avoided impurities and the sintered body of the CBNB and/or Wi3 are strongly solidified with hard alumina or cermet, The bonded phase is 141 ratio C2~40% of Jj!8 aggregate ('
l'i, W, Ta) CN or ('l'i, W, 'I
"a, Nb) Bl type solid solution of CN and 6 to 40
%'■゛1,'lr, kif%Ta, Nb, V
One or more nitrides, carbonitrides, or mutual solid solution of these and 1 to 20% of A4. , S i, T i.

Intermetallic compound consisting of two or more of Zr, 1-1f, k”e, Ni, Co and/or At, Si,
Ti, Zr.

13 or more borides of Hf, i”e, Ni, Co,
0.1 to boronitride or their mutual solid solution compound
This is a composite sintered body containing 20% of WC4 precipitated at grain boundaries, and this sintered body is firmly M bonded to a cemented carbide or cermet. In such composite 9'h compacts, WC precipitated at grain boundaries during the sintering process is mixed with CBN and/or WBN and other compounds in the binder phase. On the surface of each particle, there is a fine amount of Nll W C
It is thought that because it is precipitated as particles, it improves the bonding strength between c 13 N and/or WBN and the binder phase, and also increases the bond strength between each particle in the binder phase. The imitatively rigid WC grains precipitated at the grain boundaries in this way form the crystal-dense phase boron nitride g!
The toughness and strength of the high-finess phase boron nitride sintered body are significantly improved due to the bond-mediated effect between each particle in the 8-crystal, and the WC precipitated at the grain boundary is fine and hard. The Bl-type solid solution in the binder phase and the high hardness of fine compounds contribute to the At wear resistance, and the At, Si, '1'' i, Zr, Mf,
Fe, Ni.

Intermetallic compound consisting of two or more buildings of Co and/or Az, Si, Ti, Zr, 1-1f, Fe
, Ni, C.

One or more +jl oxides, boronitrides, or mutual solid solution compounds thereof promote the densification of the sintered body and improve wear resistance at high temperatures.
This is a high-density phase nitrided axonal sintered body in which the +/III compound of +/III provides excellent wear resistance at high temperatures.

Moreover, the WC particles precipitated in such a high-density phase boron nitride sintered body have good wettability with iron group metals contained in the cemented carbide or cermet, and Due to the fact that the recured compound is mainly gold inside and the surface diffusion of fc and other compounds is easy, it is a composite sintered body in which the unglazed shaft, cemented carbide or cermet, and gold are densely bonded and firmly bonded. .

The method for producing a composite sintered body of the present invention uses 40% as a starting material.
~80 units of CBN and/or WBN and 2-40
Bll type compound solid solution on the lines A, B, C, D and within each point shown in Figure 1 of the volume. A is good because it does not change 40 mol% TiC-50 mol%
WC-10 mol% TaC B is 55 mol% TiC-35 mol% IL/%we-to mol%'1' a C is 40 mol% 1c-20 mol% WC-40 mol% 'ra C J Ha, 25 mol % TiC-35 mo) and % WC-40 mol % TaC and 6 to 40 bodies O1j% '1' i, Z r, H
f, T a, tN b.

One or more nitrides of V or their mutual 1ml solution nitridation: Of course, 1 to 20 units of At, 8i, 'f
A powder compact formed by mixing and crushing one or more metal balls or alloys of i, Zr, and Hf with gold is brought into contact with one side of the arm body of an 'AAW lump made of cemented carbide or cermet. Fe contained in a sintered arm made of cemented carbide or cermet is produced by sintering in a stable region of tensic phase boron nitride at a pressure of 40 to 60 Kb and a temperature of 1200 to 1500°C.
, Ni, and Co can also be diffused into the dense phase boron nitride sintered body. In addition, 'e, 1' is used to permeate and diffuse into the cylindrical density phase boron nitride sintered body.
Ji, amount of metal or alloy of Co01 or more? In order to increase the starting material, 40 to 80 samples of CBN and/or WBN and 2 to 40 samples of A as shown in Figure 1,
B.

Place the Bl type back on the C and D lines and within the trough point.
d-form (however, less than 30% ri Nb compared to rac)
Even if it is replaced with C), 6-40 performance chi ri, Zr,
) if, 'l'a, Nb, nitride with one or more of V, or a mutually fused nitride of these? Aj, Sl...
1.1, A plate-shaped object consisting of a complete set or combination of one or more of Hl, V, i'e, Ni, Co [touch the other side of this plate-shaped object] Place a carbide base metal or cermet (I-shaped arm) in contact with the other side and apply a pressure of 40 to 60
K b , 77, , i1 rule 1200~1500℃ ultra-pressure knitting temperature to sinter the plate-like object to still @
Degree phase visualization 1jffll lA= m fE+'i (A ts Sx% Hf% V%shile in G,
It is also possible to permeate and diffuse the metals or alloys of N 15Co and I'ljf. As described above, the starting materials for the viscous material in the high-sodium-phase boron nitride system 7 in the method for producing a composite sintered body of the present invention are At, S i, T i, j
(f, V, Fe, Ni, C.

When one or more metals or alloys are added in whole powder form or permeated and diffused through a plate-like object, it is possible to combine powdered hemp and permeate-diffused from a plate-like object. The powder of the base metal becomes a fine powder, but it is easy to form a layer of carbon and moisture, and if this adsorbed porium and moisture become like a scum in a sealed crystal temperature and pressure chamber, the sintered body will become denser. I paid so much money to be done! ) or alloys are susceptible to seepage and diffusion from plate-like objects. The plate-shaped object used here may be a whole sheet or a thin plate of an alloy, and furthermore, methods such as plating and vapor deposition can also be used. Among the other starting materials, the Bl-type carbonized solid solution may be cooled in the form of ('I'i,'vV)C and T a C, but the temperature is raised during the sintering process.
As the rearrangement of each compound element progresses and the precipitation of WC progresses, a large amount of gas is generated, and the contact between each particle decreases, making it difficult for interdiffusion to occur, making it difficult to precipitate WC. Bll type 1+! l solid solution (D output %a3j
na, (4' i, W, T a ) C or 1ti (
Ti, W, Ta, Nb) Form of C5
It is preferable to add

In the method for producing a composite sintered body of the present invention, the starting materials of the high-density phase boron nitride sintered body are CBN and/or WBN and WBN.
It is a raw material for Cf precipitation (Ti.

V, Ta) C or (', I' i, W, Ta,
Nb) Bl-type carbide solid solution of C penetrates and diffuses into this Bl-type carbide solid dispersion and contributes to the precipitation of W('Ti,
Zr, Hf.

'Pa51N+), one or more nitrides of V or their mutually solid f-body silting and sintering aid action in the sintering process and VVC, B1 promotion trace action k t 6 A t,
8 i, 'I''i.

When one or more of Zr, If, Fe, Ni, and Co are placed under high temperature and pressure, Al, S j, '
f i, Zr.

1 (f, i'e, Ni, Co (7) IIFJ or more permeates into the grain boundaries of each particle and forms a BL-type carbide solid solution and '1' i, Zr, 14f, Ta,
By promoting the surface diffusion sound of each particle with one or more nitrides of Nb, V or their mutual solid solution deposition, W, Ti, Zr,
Along with the diffusion movement with one or more of Hf, Ta, Nb, and V, the diffusion movement of nitrogen and carbon, which are interstitial elements, becomes stagnant, and the nitrogen element mainly enters and diffuses into the Bl type carbide solid solution, causing Bl It is thought that WC in the type carbide precipitates at grain boundaries as fine particles. In addition, At, which acts as a sintering aid and promotes WC grain boundary precipitation, 8
i, Ti, Zr, Hf, F'e, Ni, C
Since o has good wettability with other particles, it penetrates uniformly into the grain boundaries of each particle and suppresses the grain growth of each particle, and as sintering progresses, CBN and /'i dWf
It is thought that it also reacts with 3N and remains as a boride and/or +4 nitride after sintering, and that some unreacted or excessively present gold lj4 intercompounds exist. Furthermore, WC grains and At which precipitated at the grain boundaries within the dense phase nitrided I/l accumulated sintered body.

Sl, lpj, Zr, Hf, Fe, Ni, Co
(7) If more than one structure contains all of Fe, Ni, and Co, the adhesion bond strength of the joint surface will be significantly impaired when a composite sintered body is formed with cemented carbide or cermet.

Here, we will discuss the reasons for limiting the numerical values for the composite baked octopus body of the present invention.

(a) Amount of CBN and/or WBN CBN and/or
If the WBN is less than 40 volume, the effect of high hardness CBN and/or WBN is weak and the wear resistance becomes too low, and if it exceeds 80 volume, the strength becomes too low and the wear resistance becomes too low. CBN and/or W in the madder density phase nitrided Y8 structure is difficult to use under intermittent cutting conditions.
The amount of BN was 40 to 80 bodies.

(b) Amount of Bl-type solid solution If the amount of Bl-type solid solution is less than 2 volumes, grain boundary ejection of WC will not occur, but if it exceeds 40% by volume, the amount of other components will be relatively small. especially CBN and/or W
BNi and ′■゛1, Zr, Hf.

The abrasion resistance is reduced because the nitrides or mutual solid solution nitrides of one or more of Ta, Nb, and V are less sensitive. For this purpose, the amount of Bl-type solid solution in the 16-density sintered body was set to 2 to 40 bodies.

In addition, the amount of Bl type carbide solid bath in the starting material is indicated by A in Figure 1.
, B, C, and D and the areas surrounding each point are because the amount of WC precipitated is too large on the side with a lot of WC away from the A and D lines, and because it is used as a starting material. This is because sometimes it is difficult to form a complete solid solution, and on the side with less TaC outside the A and B lines, the heat resistance of the sintered body and the strength at the sieve temperature decrease.5. B, C On the side where there are many TICs that have come loose, W.
C is discharged and becomes black, and C, i) On the side where there is a large amount of TaC outside the peak, the price is high and the hardness of the sintered body becomes low F1, so the Bl type carbonization solid bath of the starting material is Body V Yu, 1st
It was placed on the lines A, B, c4 L) and within the trough points in the figure.

(c) Ti, Zr, Hf, Ta, Nb,
If the weight of one or more nitrides, charcoal compounds, or their mutual co-bath combination of V is less than 6 vol. If the amount exceeds that amount, other components will be relatively reduced, but At and S are thought to play a role as a sintering aid and a promoting effect on the production of WC41, especially in the Bl-type solid solution and sintering process. i, 'I'
j, Zr, , Hf, Fe%Ni, C.

Since the number of jits in buildings 01 and above decreases, the densification of the sintered body and the precipitation of WC are supported by Kffi, so the above amount is 6.
~40 pieces were accumulated.

(d) At, S i, 'ri, Zr, Hf,
li'e, Ni, C.

Intermetallicization consisting of two or more atoms @proboscis and/or Aty
Six Ti, Z5 Hf, Fe, Ni, C
The amount of shelving or boronitride of more than 1 volume of IW is less than 1 volume. The hardness decreases due to too much Kanasugi doubling, resulting in poor M tag resistance and bending.
In addition, the amount of self-sufficiency was set at 1 to 20.

(c) When the grain boundary discharge amount of WC is 0.1 volume, 0.1μi
Even if the WC is extremely mechanical, the number of WC particles is too small, resulting in a decrease in toughness and strength, and if the number exceeds 20% by volume, it becomes difficult to precipitate all the WC particles. The amount of WC grain boundary precipitation was 0.1 to 20 vol.

In the present invention, sintering can be performed using an ultra-high pressure device such as a girdle type or a belt type.

Next, the composite sintered body of the present invention and its manufacturing method will be described in detail according to all embodiments.

Example 1 CBNf60% with average grain e3μm and (with average grain size 3μm)
40%'jl''1-40%W-15%'f'a=5%N
b) (T'o, 9-Tao, □)N'ik 15% and 9 with a total of 20% CD carbide solid solution and an average particle size of 1.5 μm
79% kl 3 below 15 μm heat treated at 00℃
The entire mixture was mixed with 0%'l'1m gold powder ff15% and molded into an outer diameter of 16i+i and a height of 1.5gm. This powder compact was placed in a Mo container with a CO thin plate clamping the same amount as 3% of the powder compact between cemented carbide with an outer diameter of 16U, After degassing at a temperature of 1,000°C, it was charged into a belt m high-pressure device and maintained at a pressure of 50 Kb and a temperature of 1,450°C for 20 minutes to obtain a fractured sintered body. This composite sintered body was completely electrically discharged and soldered to the tip of the cemented carbide to give a 5NP432 tip. 5NP432 to which the composite sintered body of the present invention was brazed and commercially available CB
In comparison, 5NP432 to which the N^ pressure sintered body was brazed was cut under the following continuous turning conditions, and the cutting time until chipping or chipping was compared four times. The results were 45 minutes, 43 minutes, and 47 minutes, whereas the commercial products were 13 minutes, 16 minutes, 20 minutes, and 10 minutes, and the product of the present invention was behind in fracture resistance in the interrupted rotation 8υ test. It was confirmed that the present invention tends to be superior even in terms of variations in the results of all the repeated tests.

Intermittent turning condition plate r: J1j material SCM-3 (MRC58-62 inch 8mxrll 2 slotted 50ψ intermittent turning cutting JL 100m/min Depth of cut 0.15XIl Feed rate 0.25111111/rev Composite firing of the present invention As a result of X-ray analysis of the part of the high-strength phase violetized 7/lit elemental sintered body, CBN, (Ti, Ta) NC, TiB2, (Ti, w, Ta, Nb) CN, and Az3 were analyzed.
The peak thought to be TtCo and the peak of WC thought to be precipitated could not be confirmed. Furthermore, precipitated fcWC was confirmed by microscopic structure observation.

Example 2 65% CBNi with an average particle size of 3 μm and an average particle size of 1.5 μm
A carbide solid solution of (40%゛r i -50%W -10%Ta)C with 15% and an average particle size of 1.5μm (',I
' t O,7Z r o, 3) 20% Nf and gold mixed powder were pressed and molded to have an outer diameter of 16 mm and a height of 1.5 mm. Like this powder bed compact, a Zr2 vapor layer with an amount equivalent to 3% of the compact is formed on the surface of this natural layer by ion grating on a piece of cemented carbide with an outer diameter of 16 mm. A corresponding amount of N1 thin plate was placed, a green compact was placed in contact with the Ni thin plate, and the compact was placed in a container made of rAo, which was then charged into a belt-type high-pressure device at a pressure of 5 kb.

A temporary sintered body was obtained by holding at a temperature of 1400'C for 20 minutes. This was all done with Example 1 and 8NP 432.The finish was 5NP with commercially available C"BNN positive pressure sintered body brazed.
432' (r Comparatively, cutting was performed under the following turning conditions, and the average flank wear amount was added up. The product of the present invention has an average of V!l = 0.13 range, whereas the product of the wide market has an average of VB = 0. ．．
It was confirmed that 18 items and the unexploded J items were wear resistant and dredged. Moreover, even if the variation in the results of repeated identical tests is suppressed, the product of the present invention has a narrow variation range and is inexpensive.
I was able to confirm that it was.

Turning conditions Work material 5KI)-11HRC59~62 Cutting speed
9Qm/min Depth of cut 0.5mm Feed 0.1mm/rev Cutting time 2
0 minute cutting oil Emulcut (Ti, W, '1''a) A peak thought to be CN and a peak of WC thought to be precipitated were confirmed. Also, precipitated vvC was confirmed from microscopic structure observation.

Example 3 - Total 68% CBN with an average particle size of 3 μm and an average particle size of 1.
5 μm (55%', 1'1-35%W-10%Ta
) with a carbide solid solution of 10% and an average particle size of 145 μm (T
i o9-Nb, □) N'c 15% and 70% Ti-30%8i alloy powder heat-treated at 900°C and having an i of 15 μm or less were mixed and ground to form an outer diameter of 16 mm and a height of 1.
It was molded into 5 pieces. This was placed in contact with one surface of the wc-1ow% colsi & alloy with an outer diameter of 16mm and a height of 3B in an MO container, and the vacuum level was 10-4mmHg and the temperature was 1.
After removing the scum at 1,400°C, it was charged into a belt-type high-pressure device, held for 20 minutes near the eutectic point of WC-Co during heating, and then further heated to 1,400°C for 20 minutes to obtain the present invention. I got a bosom @ 戊supply body. This is 5NP432 as a co-worker with Kinyoshi Sakukoshi.
Finished with commercially available CBN high pressure sintered body 8
Comparing NP432 (-), the composite sintered body was cut under the following 7 rice cutting conditions, and the durability and tilting sound of the composite sintered body and # hard alloy, including the strength of the strong bond between them, were investigated.The test results showed that the composite sintered body of the present invention showed Masatomi wear even after 5 minutes of cutting, whereas the commercially available sintered compacts used for comparison showed chipping at the cutting edge after 3 minutes of cutting, and chipping at the bonded joint with the Mi hard alloy. there were.

Milling cutting conditions Work material 5KDII HRC59~6250X10
Cutting 0 surface Cutting speed 200m/mln Depth of cut 1.0 feed Re 0.3/rev Cutting Cutting test line It was confirmed that CO permeated and diffused in the hm bisque fired part, and as a result of X-ray analysis and microscope microscopic examination, it was confirmed that precipitated C was present.Example 4 Average particle size of 3μ WB with Cf31 ~ and average particle size of 5 μm
The composite of the present invention was prepared by blending N, a carbide solid solution with an average particle size of 1 to 3 μm shown in Table 1, and a spirit compound compound in the composition shown in Table 1, and sintered by the same manufacturing method as in Example 2. As a result of examination using X-ray analysis and an X-powder microanalyzer, it was found that each sample contained a Bl-type carbonitride solid solution in addition to a high-order phase, a Bl-type carbonitride solid solution. i, zr, i (f, Ta, Nb, one or more nitrides or mutually homopolymer compounds, aluminum nitride, borides or borides of group 4a transition metals, and intermetallic compounds) In addition, the VVC peak was confirmed in all samples.The WC precipitated in each sample was also confirmed by microscopic structure observation.The male permeation diffusion elements from the plate-like object were confirmed using an X-gland microscopic microscope. This was also confirmed using an analyzer.

Among the contained sintered bodies of the present invention shown in Table 1, sample '4
+ Among the sintered bodies shown in No. 1.3.4.8.10 and No. 2, which were removed from the present invention, sample No. 11.12 was finished into a 5NP432 chip and further commercialized. In addition to comparison, the CBN yarn sintered body was also subjected to a cutting f9υ test in the same manner as in Example 1, and as a result, it was found to be 3C.

Table 3 The results shown in Table 3 confirm that the composite sintered body of the present invention is significantly inferior in fracture resistance in the interrupted turning test compared to conventional commercially available composite sintered bodies. did it.

Example 5 Composite sintered body of the present invention with sample number 5.6.70 shown in Table 1 of Example 4 and composite sintered body of the present invention with sample number 13.14 shown in Table 2 In addition to comparing all commercially available CBN yarn sintered bodies, an Okoshi type abrasion test was conducted under the following conditions. As a result, the amount of wear of samples 5 and 6.7, which are composite sintered bodies of the present invention, is different from that of sample number 13, which is a composite sintered body of the present invention.
．． It was about 1/2 compared to No. 14 and commercially available CBN-based sintered bodies.

Taisho type wear test Rotor friction speed 195 m/min Initial pressure 4 edges 4 history Final force] January 2 19.5
Kf haigen time 1 hour

[Brief explanation of drawings]

FIG. 1 shows a 3X phase diagram of WC, Ill i C, and TaC.

Claims (1)

[Claims] (1140 to 80 volumes of CBN and/or WBN
The sintered body consisting of 20~600~60 molten metal and unavoidable impurities and the cemented carbide or cermet are strongly fi! In the II layered bale combination, the binder phase of the sintered body has a volume ratio of 2 to 40% ('1' i, W, 'l' a
) CN or ('l' i, W, T a, N b
) Bl-type solid solution of CI'lJ and 6-40% Ti,
One or more nitrides, carbonitrides, or mutual solid solution compounds of Zr, Hf, 'i'a, Nb, V and 1 to 20% of AL, Si, Ti, 'l! r. Intermetallic compound consisting of 2a or more of Hf, k'e, Ni, Co and/or At, Si, ', I'
i, Zr, Hf. A composite containing one or more borides, borides, or mutual solid solution compounds of 1''e, Ni, and Co, and 0.1 to 20% of WC-f precipitated at grain boundaries. Sintered body. (2) 40 to 800 to 80 pieces as starting material
and/or WBN and Bl-type carbide solid solution on the lines A, B, C, and D shown in Figure 1 and within each point of the 2 to 40 strips.However, 30% or less of TaC is NbC.
6 to 40 volume % of Ti5Z r, Hf,
Ta, Nb%V (7) 1 to 20 compounds or their mutual solid solution combination and 1 to 20% of NbAz
, S i, f1, Zr, Hf, 1i or more metals or alloys are mixed and pulverized and then compacted)"e, Nj,
Containing a metal or alloy of 1 or more Co, 7'C, in contact with a carbide base metal or cermet, and heated under ultra-simple pressure at high temperature to 21
12i, CBN and/or WBN negative 4! In the sintered body, 0.1 to 20 g of WC is precipitated from the BI type carbide solid bath at the grain boundaries, and all metals or alloys of 18i or more of upper 'e, Nj, and Co are precipitated from the cemented carbide or cermet. A method for manufacturing a composite sintered body, which is characterized in that it is firmly fixed to a cemented carbide or cermet by permeation diffusion. (3) A shown in Figure 1 with 40 to 80 volumes of BN and/or WBN and 2 to 40 volumes as starting materials,
B1 type carbide solid solution placed above and within the valleys of B, C, and D (however, 30% or less of TaC is replaced with NbC)
and 6~40 volume-〇″r!, Zr, Hf, Ta,
One or more nitrides of Nb, V or their mutual solid solution nitrides and a powder compact formed after pulverization, and At, Sl, Tj, Zr, , Hf on one side of the powder compact.
, Fe, Ni, Co, all of which are made of a plate-like object made of one or more metals or alloys, and the other surface of the plate-like object or the other surface of the powder compact is completely covered with cemented carbide or cermet.
! ! i and sintered under ultra-high pressure and high temperature to form CBN and/or
Alternatively, 0.1 to 20 volumes of WC2 grain boundaries are precipitated from the Bl type carbide solid solution in the WBN-containing M sintered body, and A t of 1 to 20 volumes is permeated from the plate-like object.
, S s, 'l'i, Zr, Hf, Fe, N
i, an intermetallic compound consisting of two or more of Co, and/or kt, S i, Ti. A composite characterized by the presence of one or more borides of Zr, Hf, Fe, Ni, Co, #l oxides, or mutual solid solution compounds thereof, which are strongly bonded to cemented carbide or cermet. A method for producing a sintered body.