JPH10310839A - Super hard composite member with high toughness, and its production - Google Patents

Abstract

PROBLEM TO BE SOLVED: To combine high toughness with high hardness in a diamond(CBN) dispersed composite member. SOLUTION: This composite member has a hard phase composed essentially of at least one compound selected from WC, TiC, TiN, and TiCN and diamond(CBN) grains and a binding phase composed essentially of iron group metal and also has a cross section containing binding-phase structures having a shape where aspect ratio is 5-20. Further, the composite material has density of >=95% theoretical density ratio. Because these binding-phase structures are flat, cracks necessarily cross the binding phases at the time of crack propagation and the crack propagation energy is dissipated by the plastic deformation of the binding phases at this time, by which high toughness can be attained.

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a high-toughness super-hard composite member and a method for producing the same.

[Prior art]

[0002] A diamond dispersed cemented carbide material obtained by mixing diamond particles and a WC-based cemented carbide and integrally sintering the same is disclosed in JP-B-61-56067, JP-B-61-58432, and US Pat. No. 5,158,148. It is described in. Since these materials are manufactured using an ultrahigh-pressure generating container, a dense sintered body can be manufactured, but there is a problem that the cost is high. Further, in terms of performance, there is also a problem that toughness is reduced by adding diamond particles to the cemented carbide.

On the other hand, there has been proposed an attempt to produce such a material by hot pressing. Although the production cost could be reduced by this method, sintering was carried out in a temperature range where a liquid phase was not formed in the cemented carbide, so that a sufficiently dense sintered body could not be produced, and the sintered body strength was low. It was not enough. Attempts have been made to produce such materials at the liquid phase appearance temperature and to densify them (Japanese Patent Application Laid-Open No. 50-146614), but since sintering took a long time, diamond Had a problem that part of the material was transformed into graphite. Further, US Pat. No. 5,096,655 proposes a technique for producing a composite member holding metal-coated superhard particles in a binder phase by an infiltration method. In this method, the binder phase metal is infiltrated into the gap between the diamond particles at a temperature lower than 1300 ° C. However, it is difficult to produce a dense composite member by the infiltration method, and the strength of the sintered body is insufficient. Was something.

In general, a hard alloy in which the hard phase is mainly WC and the binder phase is an iron group metal such as Co or Ni is called a WC-based cemented carbide, and the hard phase is mainly composed of TiC (N) and the binder phase is mainly composed of TiC (N). Is a TiC (N) -based cermet. These hard alloys are generally above 1350 ° C
The sintering is carried out at a temperature of not more than 00 ° C. and in a vacuum for about one hour without pressure. In some cases, thereafter, HIP (hot isostatic pressing) may be performed at a temperature lower than the sintering temperature.

FIG. 3 shows a photograph of a cross-sectional structure of the hard alloy produced by these methods. The white spots in the figure are the binder phases, but these binder phases are present only at the grain boundaries of the hard phase and at the gaps between the grains on any cut surface. There are few distinct shapes that can be called binder phase particles, and even if present, they have a shape with an aspect ratio smaller than 3. The reason for such a structure is that when the binder phase is dissolved during sintering and a liquid phase is generated, the wettability between the hard phase and the binder phase is high in a WC-based cemented carbide or TiC (N) -based cermet (contact This is because the liquid phase flows to the hard phase grain boundaries and gaps due to the small angle.

[0006] Even when an ultrahigh-pressure generating vessel is used, the binder phase has such a structure. A cemented carbide having such a structure does not have sufficient toughness. In particular, in the case of a hard composite member containing hard brittle particles such as diamond, it is necessary to increase the amount of the binder phase in order to suppress a decrease in the toughness of the material, resulting in a reduction in wear resistance and heat resistance. I was

[0007]

SUMMARY OF THE INVENTION Accordingly, an object of the present invention is to provide an ultra-hard composite member which can be manufactured without using an ultra-high pressure generating vessel, has high toughness, and is excellent in hardness and strength, and a method of manufacturing the same. Is to do.

[0008]

According to the present invention, there is provided a hard phase mainly composed of at least one compound selected from WC, TiC, TiN and TiCN, diamond particles, and an iron group. In a composite member containing a binder phase metal mainly composed of metal, the aspect ratio is 5 to 20.
And a dense structure having a theoretical density ratio of 95% or more. In particular, the binder phase structure having a shape having an aspect ratio of 5 to 20 is
Preferably, the maximum length is at least three times the average crystal grain size of the hard phase.

Here, the aspect ratio refers to the ratio between the maximum length and the average thickness of the binder phase structure. As will be described later, the hard alloy of the present invention is obtained by current pressure sintering, and the bonding phase structure is crushed by the pressing at that time. As a result, a structure having the above aspect ratio is formed. Since such a binder phase structure is formed by pressurization at the time of sintering, the structure has directionality and has a flat shape. Further, in the super-hard composite member of the present invention, the metal constituting the binder phase is formed into a flat shape using a stamp mill or the like, or the binder phase is formed by a hot extrusion method or an injection molding process in addition to current pressure sintering. It can also be obtained by sintering at a low temperature for a short time after elongation. Needless to say, the alloy of the present invention may contain unavoidable impurities. Inevitable impurities include:
For example, Al, Ba, Ca, Cu, Fe, Mg, Mn, N
i, Si, Sr, S, O, N, Mo, Sn, Cr and the like.

Heretofore, it has been considered that a hard alloy having such a non-uniform binder phase structure exhibits low bending strength and is not preferable as a liquid phase sintered material. However, as will be shown in Examples later, the fracture toughness of the composite member of the present invention shows a higher value than that of the conventional alloy. This is presumably because the crack always crosses the flat binder phase during crack propagation, and the crack growth energy is expended in the plastic deformation of the binder phase at this time. Moreover, the bending strength of the composite member of the present invention is at the same level as that of the conventional alloy, and does not show low bending strength. It is considered that this is because the binder phase grains have a large aspect ratio and thus do not easily act as a stress concentration source. In addition, by adopting a structure having a denseness with a theoretical density ratio of 95% or more, a composite member having high diamond holding power, excellent wear resistance and strength can be obtained.

It is preferable that such a rigid composite member further includes the following requirements alone or in combination. (1) ISO standards A00 to A04 and B00 to B04
It has a density satisfying the range up to. Whether or not the material is dense can be evaluated by mirror-processing the cross section of this material and then observing the structure with an optical microscope.

(2) Diamond particles are lr, Os, P
It is coated with at least one metal selected from t, Re, Rh, Cr, Mo and W. In order to obtain a dense sintered body of a WC-based cemented carbide or a TiC (N) -based cermet, a sintering temperature exceeding 1300 ° C is preferable. Under such conditions, diamond and CBN are easily attacked from the generated liquid phase. To prevent this, the above metal coating is very effective. Diamond and C
When the BN is completely covered, it is particularly effective in preventing the deterioration of diamond.

(3) The content of diamond changes continuously or stepwise in the thickness direction such that the amount of diamond particles is larger on one surface side and smaller on the other surface side in the super-hard composite member. In the present super-hard composite member, the inclusion of diamond causes problems such as a decrease in toughness, an increase in cost, and a decrease in workability. Therefore, such a problem can be solved by increasing the content of diamond only in necessary portions and by reducing or eliminating the content of diamond in unnecessary portions. Note that the change in the diamond content includes a stepwise change and a substantially continuous change.

(4) Joined on a substrate made of any of a WC-based cemented carbide, a TiC (N) -based cermet, and a metal material. For the same reason as in the above item (3), it is preferable that the super-hard composite member is joined to a substrate made of any of a WC-based cemented carbide, a TiC (N) -based cermet, and a metal material. In particular, when sintering is performed on a metal material such as steel, the bonding strength, which has conventionally been insufficient by brazing the sintered body and the metal base, is improved, and the brazing step can be omitted. In addition, the use of steel as the base makes it possible to perform a brazing operation between other steel products and steel, so that the joining strength and workability are greatly improved.

Thus, the super-hard composite member and the super-hard alloy,
By joining with a cermet, a member having both hardness and toughness can be obtained. In addition, it is advantageous because a compressive residual stress can be generated on the surface due to the coefficient of thermal expansion. It is preferable to sinter the super-hard composite member, the super-hard alloy, and the metal material in this order. When connecting the metal material and the cemented carbide, a thin insert material (for example, Ni foil) may be inserted between the two to suppress the voids by the Kirkendall effect of the metal material.

(5) At least a part of the diamond particles is replaced with at least one of cubic boron nitride and wurtzite boron nitride. Since cubic boron nitride and wurtzite boron nitride are harder than diamond and have better stability to iron group metals than diamond, they can be expected to have better performance than diamond in terms of wear resistance against iron group metals. In addition, since the present super-hard composite material is mainly composed of an iron group metal in the binder phase, the surface of the CBN is hardly eroded during liquid phase sintering, and it is possible to produce a sintered body that is dense and has excellent mechanical properties. it can.

The method for manufacturing the super-hard composite member is described in WC,
A hard phase powder mainly composed of diamond particles and at least one compound selected from TiC, TiN and TiCN; and a binder phase powder mainly composed of an iron group metal having a particle diameter three times or more as large as the hard phase powder. And a step of arranging a raw material member composed of the mixed powder in an electric heating device, and the raw material member is heated to 1100 ° C to 1350 ° C and 5 to 200 MPa.
And sintering under electric pressure.
The particle size of the binder phase powder is preferably at least 5 times.

Here, the raw material member includes the powder itself of each raw material, a green compact pressed in advance, an intermediate sintered body, a laminate thereof, and the like. Further, a grain growth inhibitor such as a high melting point compound may be added when mixing the raw material powders as necessary. Examples of the high melting point compound include carbides, nitrides, and carbonitrides of elements belonging to the group IVa, Va, and VIa. Most preferably, no grain growth inhibitor is added. When adding, minimize it.

In the electric pressure sintering, heating, pressurizing and cooling can be performed rapidly by direct energization to the material to be sintered without using an external heater, so that sintering can be completed in a short time within 10 minutes. Therefore, the time during which the material to be sintered is exposed to a high temperature can be shortened as compared with the case where the maximum temperature holding time is simply shortened by conventional pressure sintering, and the sintering can be completed without transforming the diamond into graphite. Moreover, the bonding process between diamond and the matrix can be increased by the energization process. Also,
A plasma may be generated between the particles through a pulsed current to further improve the sintering and bonding force between the diamond and the matrix. As described above, in the current pressure sintering, the performance merit unique to the present super-hard composite member, which cannot be obtained by the conventional pressure sintering method, can be obtained. Furthermore, since production can be performed in a short time, cost reduction can be expected by improving the operation rate of equipment.

If sintering is carried out for a short time at a low temperature by rapidly raising the temperature by this method, the time required for the binder phase to move is not sufficient, so that the binder phase particles have a flat shape crushed in the direction of the pressure axis. It is formed.

The sintering is desirably performed in the presence of a liquid phase. When sintering is performed by solid-phase sintering, a flat bonded phase structure is easily generated, but sintering with the appearance of a liquid phase promotes densification. Thereby, the strength of the sintered body is improved. Therefore, by forming a liquid phase at a temperature at which the flat binder phase structure does not disappear and sintering it in a short time, a dense alloy having excellent strength, toughness, and hardness can be produced.

The reasons for limiting the above sintering conditions are as follows. If the sintering temperature is lower than 1100 ° C., the densification hardly proceeds, and if it exceeds 1350 ° C., the liquid phase tends to be stained. The sintering temperature here refers to the temperature of the graphite mold surface when controlling the sintering furnace. It is considered that the actual sample temperature is about 150 to 300 ° C. higher than this temperature.

If the pressing force is 5 MPa or less, the effect of pressure sintering is not seen, and it is difficult to increase the pressing force beyond 200 MPa in terms of equipment, which causes a cost increase. A particularly preferred pressure is between 10 and 50 MPa. The reason is that an inexpensive graphite type can be used.

Further, the sintering time is preferably within 3 minutes. By shortening the sintering time, grain growth of the hard phase and movement of the liquid phase during sintering can be suppressed, and a hard alloy having a different bonding layer amount in the thickness direction can be produced. More preferably, it is within one minute. The sintering atmosphere is preferably a vacuum of 0.1 Torr or less.

In order to manufacture a composite member in which the amount of diamond particles changes in the thickness direction, a plurality of mixed powders having different diamond particle contents may be prepared. Then, in the step of arranging the raw material members in the electric heating device, these plural kinds of mixed powders are laminated and arranged in the order of the content of the diamond particles. If the type of the prepared powder mixture is small, it is possible to obtain an ultra-hard composite member (the minimum is two stages—with or without diamond particles) having a different diamond particle content stepwise in the thickness direction. If the thickness of each layer to be laminated is reduced by increasing the number of layers, an ultra-hard composite member in which the content of diamond particles changes substantially continuously can be obtained. According to the method of the present invention, the grain growth of the hard phase and the movement of the liquid phase during sintering are small, so that a sintered body having such a configuration can be stably manufactured. In the same manner, an ultra-hard composite member in which the amount of the binder phase changes in the thickness direction can be manufactured.

In order to join such a hard alloy having a tilted structure to a substrate made of a cemented carbide, a cermet or a metal material, the raw material member together with the substrate may be arranged in an electric heating device. For example, raw material powder for ultra-hard composite members,
A cemented carbide substrate and a metal material substrate can be sequentially laminated and joined in an electric heating device.

Further, among the raw material powders, when diamond is previously coated with at least one metal selected from lr, Os, Pt, Re, Rh, Cr, Mo and W, a known plating method, CVD method, The PVD method may be used.

Hereinafter, embodiments of the present invention will be described. (Example 1) Diamond powder having an average particle diameter of 0.5 μm, WC powder having an average particle diameter of 1 μm, Co powder having an average particle diameter of 1 μm, TiCN powder having an average particle diameter of 1.5 μm, TiC powder having an average particle diameter of 2 μm, and an average particle diameter of 1 μm Was prepared, blended with the composition shown in Table 1, and mixed and pulverized with a ball mill for 20 hours to prepare raw material powders (Nos. 1-1 to 1-7). In addition, Co powder and N
Raw material powders Nos. 2-2 to 2-7 in which the i-powder was changed to coarse raw materials having an average particle size of 3 µm and 5 µm, respectively, were similarly prepared.

[0029]

[Table 1]

Next, these powders were charged into a graphite mold, and were heated under a vacuum of about 0.01 Torr or less using an electric heating and sintering apparatus.
Heating speed 2 while applying MPa pressure from top to bottom
Pass a current through the graphite mold at 50 ° C / min, keep it for 1 minute when it reaches 1100 ° C, and cool at a rate of about 100 ° C / min to obtain a 25 × 8 × 5 mm sintered body. (Sample Nos. 1 to 14) were obtained.

There are no cracks in the obtained sintered body,
It had a dense structure with a theoretical density ratio of 95 to 100%. Furthermore, these sintered bodies are cut along a plane parallel to the pressure axis, the cross section is ground, and after mirror polishing, a photograph of the structure in any three visual fields is taken with an optical microscope at a magnification of 1500 times. Was used to calculate the aspect ratio of the binder phase metal. here,
The aspect ratio was calculated by dividing the maximum length of the three bonded phase grains having the largest aspect ratio by the average thickness. The aspect ratio of the largest value among the total of six aspect ratio values is shown in Table 2. Described. The hardness and fracture toughness were measured by a indentation method using a diamond Vickers indenter under a load of 50 kg. Further, the bending strength was measured by a three-point bending test. Table 2 shows the measurement results.

[0032]

[Table 2]

From Table 2, it can be seen that raw material Nos. 2-1 to 2-
The aspect ratio of the binder phase of the sintered body of No. 7 is larger than that of the alloy obtained by sintering the raw materials No. 1-1 to 1-7 having no difference in the particle diameter of the hard phase and the binder phase, and about 5 to 15 Value. The fracture toughness of Sample Nos. 2, 4, 6, 8, 10, 12, and 14 was
It was confirmed that the fracture toughness was significantly superior to the fracture toughness of 3,5,7,9,11,13. Furthermore, the flexural strength of Sample Nos. 2, 4, 6, 8, 10, 12, and 14 was almost the same as the flexural strength of Samples No. 1, 3, 5, 7, 9, 11, and 13. Was not reduced.

FIG. 1 shows an optical microscope photograph of a cross section of the sintered body cut along a plane parallel to the pressing axis and subjected to surface grinding and mirror polishing. The white part of the photograph is the binder phase. As is clear from this photograph, a part of the binder phase has a shape elongated in a direction perpendicular to the pressing axis, that is, a shape having an aspect ratio of 5 to 20. In addition, the binder phase metals identified in the structure photograph are arranged so as to extend in a direction perpendicular to the pressure axis of the sintering apparatus, and have directionality. The black dots in the photograph are diamonds.

Next, FIG. 2 shows an optical microscope photograph of a cross section of the sintered body cut along a plane perpendicular to the pressing axis and subjected to surface grinding and mirror polishing. Again, the white portion represents the binding phase. Some of the binder phase grains in the photograph are spread and observed in a circular or irregular shape, indicating that the binder phase metal has a flat shape.

(Example 2) Raw material powder produced in Example 1
Using powder of the same raw material and composition as No.2-5, 900,100
At a sintering temperature of 0, 1100, 1200, 1300, 1400 ° C., a sintered body was produced in the same manner as in Example 1. Then, this sintered body is
After surface grinding with a grinding wheel No. 0, mirror polishing was performed, and the presence or absence of pores in the WC-Co phase was observed using an optical microscope at a magnification of × 200. The observation results were classified into A00 to B08 based on ISO, and are described in Table 3. Table 3 shows the results of measurement of the actual sample temperature during sintering with a thermocouple. The aspect ratio of the binder phase metal, the theoretical density ratio, and the bending strength of each sintered body are also described. The theoretical density ratio is 15.6 g / cm ³ for WC specific gravity,
Calculate the theoretical density of this composition by setting the specific gravity of o to 8.9 g / cm ³ , the specific gravity of VC to 5.5 g / cm ³ , and the specific gravity of diamond to 3.5 g / cm ³ , and measure the density of the sintered body by the Archimedes method It was done by doing.

[0037]

[Table 3]

From Table 3, it can be seen that No. 2-1 when the actual sample temperature was 1050 ° C.
The sample No. has a low theoretical density ratio of 90% and has many nests compared to B08, so that the bending strength is low. Samples No. 2-3, 4, 5 of A type and B type having less than 04 pores are dense, It was confirmed that excellent characteristics were obtained. In Sample No. 2-6, the liquid phase oozed out of the graphite mold during sintering, and the flexural strength also showed a low value.

The sintering temperature is 1100-1300 ° C.
It was also found that the range described above was preferable from the viewpoint of bending strength. Furthermore, it was confirmed that the difference between the sintering temperature for temperature control and the actual sample temperature was about 200 ° C.

Example 3 WC powder having an average particle size of 0.5 μm, Co powder having an average particle size of 2 μm, and Cr _{3 having} an average particle size of 1 μm
A C ₂ powder was prepared and these were weight% WC: Co: Cr.
_The mixture was blended so that ₃ C ₂ = 89: 10: 1 to prepare a superhard powder. Further, a diamond powder having an average particle size of 50 μm was prepared, and the surface of this powder was coated with 2 μm of various metals shown in Table 4 by the PVD method. These diamond powders were 30% by volume with respect to the previously prepared carbide powder. And mixed with a ball mill for 5 hours to prepare a raw material powder. These raw material powders are charged into a graphite mold, and a current is passed through the graphite mold using an electric heating sintering apparatus at a heating rate of 200 ° C./min while applying a pressure of 50 MPa from above and below.
When the temperature reached 00 ° C., the sample was kept for 30 seconds and cooled at a rate of about 100 ° C./min to produce hard alloys of Sample Nos. 3-1 to 3-13.

Samples Nos. 3-1 to 3-13 thus obtained
Was subjected to a disk-type abrasive friction test (a method of evaluating abrasion resistance by pressing a test piece at a pressure of 10 kg against the circumference of a 10-mm-wide circular disk rotating in SiC slurry). Table 4 shows the results. The evaluation results are shown by standardizing the wear test results of the other samples, with the wear amount of sample No. 3-1 made of diamond powder without metal coating being taken as 1.

[0042]

[Table 4]

As shown in Table 4, compared with Sample No. 3-1 in which diamond was not coated at all and Sample No. 3-13 containing no diamond (only cemented carbide), lr and Os were added to the diamond particles. , Pt, Re, Rh, Cr, Mo, W
It was found that the samples No. 3-2 to No. 3-9 coated with No. 3 can realize extremely excellent wear resistance.

(Example 4) Powder and steel having the composition (% by weight) shown in Table 5 were pressed in layers and filled in a graphite mold, and the temperature was raised at a rate of 200 ° C / 200 ° C. while applying a pressure of 10 MPa from above and below. current through the graphite mold so that
When the temperature reached 50 ° C., it was kept for 1 minute to perform rapid cooling. Observation of the obtained disc-shaped sintered body having a diameter of 50 mm and a thickness of 20 mm revealed that no cracks occurred between the layers and the layers were well joined. The cross section in the thickness direction of this sintered body is mirror-polished, and the EPM
A composition analysis was performed at A. As a result, the movement of elements was relatively small even between the respective layers, and diffusion of components between the layers, which had a problem in the conventional sintered body, was suppressed.

[0045]

[Table 5]

The sintered body of this structure can obtain high wear resistance due to the surface layer containing diamond, and high strength and high toughness due to the use of a super hard and steel layer as the inner layer.
Usually, it is a material that can achieve both contradictory characteristics. In addition, the use of a steel layer has a great advantage in use, such as enabling welding, and the advantage that such an excellent material can be manufactured at low cost without using an ultrahigh-pressure vessel is very significant.

(Example 5) Raw material powder described in Example 1
No. 2-1 to 2-7 diamond with average particle size of 1μm CBN
Or sample No.4-1 with WBN partially or completely replaced
4-7 were sintered under the same conditions as in Example 1 to produce a sintered body having a diameter of 20 mm and a thickness of 5 mm. Table 6 shows the compositions of Sample Nos. 4-1 to 4-7.

[0048]

[Table 6]

These sintered bodies were surface ground with a # 250 diamond grindstone, mirror-polished, and observed with an optical microscope. As a result, it was found that the aspect ratio of the binder phase metal was in the range of 5 to 15 at the maximum for each sample, and the theoretical density ratio of each sample showed a value of 95% or more. In addition, no cracks were generated and no CBN (WBN) particles were dropped off in any of the samples, and it was confirmed by X-ray qualitative analysis that CBN (WBN) was sintered without being transformed into hexagonal BN. Was.

[0050]

As described above, the composite member of the present invention is capable of firmly dispersing and holding diamond (CBN) particles having excellent hardness and abrasion resistance in a high-toughness cemented carbide or cermet. By forming a structure, both extremely high hardness and strength can be achieved.

Accordingly, the composite member of the present invention can be used for cutting tools such as casing bits, earth auger bits, shield cutter bits, etc., cutting tools such as woodworking, metalworking, and resin processing chips, and machine tools. It can be used for wear-resistant materials such as bearings, centerless blades and nozzles, plastic working tools such as drawing dies, and tools for grinding.

Further, in the production method of the present invention, the raw material powder containing the binder phase powder having a coarse particle size of at least three times the hard phase particle size is sintered in a short time by current pressure sintering, so that the toughness is improved. It is possible to obtain a dense super-hard composite member having excellent hardness, abrasion resistance and excellent hardness. In particular, since the heating time, the keeping time, and the cooling time can be shortened, further cost reduction can be expected as compared with the conventional manufacturing method (including the method using the ultrahigh pressure generating vessel).

[Brief description of the drawings]

FIG. 1 is a micrograph showing the structure of a cross section of the hard alloy of the present invention cut along a plane parallel to a pressure axis.

FIG. 2 is a micrograph showing a structure of a cross section of the hard alloy of the present invention cut along a plane perpendicular to a pressing axis.

FIG. 3 is a micrograph showing a cross-sectional structure of a conventional hard alloy.

──────────────────────────────────────────────────の Continued on the front page (51) Int.Cl. ⁶ Identification code FI C22C 29/02 B22F 3/14 101B

Claims (11)

[Claims] 1. A composite member having a hard phase and a binder phase metal, wherein the hard phase is composed of diamond particles, WC, TiC, and TiN.
And at least one compound selected from the group consisting of TiCN and TiCN, wherein the binder phase metal is mainly composed of an iron group metal and has a cross section including a binder phase structure having an aspect ratio of 5 to 20; A high-toughness super-hard composite member having a dense structure with a ratio of 95% or more. 2. ISO standards A00 to A04 and B0
The high-toughness super-hard composite member according to claim 1, having a denseness satisfying a range of 0 to B04. 3. The high-toughness super-hard composite member according to claim 1, wherein the arrangement of the binder phase structure having an aspect ratio of 5 to 20 has directionality. 4. The high-toughness super-hard composite member according to claim 1, wherein the binder phase structure having an aspect ratio of 5 to 20 has a flat shape. 5. The diamond particles are lr, Os, Pt,
The high-toughness super-hard composite member according to claim 1, wherein at least one metal selected from the group consisting of Re, Rh, Cr, Mo and W is coated. 6. The method according to claim 1, wherein the diamond content is changed continuously or stepwise in the thickness direction such that the amount of diamond particles is larger on one surface side of the high toughness super hard member and is smaller on the other surface side. The high-toughness super-hard composite member according to claim 1, wherein: 7. The high-toughness super-hard composite member according to claim 1, wherein the high-toughness super-hard composite member is bonded to a substrate made of one of a WC-based cemented carbide, a TiC (N) -based cermet, and a metal material. 8. The high-toughness super-hard composite member according to claim 1, wherein at least a part of the diamond particles is replaced with at least one of cubic boron nitride and wurtzite boron nitride. 9. A hard phase powder composed of diamond particles and at least one compound selected from WC, TiC, TiN and TiCN, and a bonded phase of an iron group metal having a particle size three times or more the size of the hard phase powder. A step of mixing a raw material member composed of the mixed powder with an electric heating device; and a step of performing electric pressure sintering of the raw material member at 1100 ° C. to 1350 ° C. and 5 to 200 MPa. A method for producing a high-toughness super-hard composite member, comprising: 10. The raw material powder, wherein diamond particles are previously coated with at least one metal selected from lr, Os, Pt, Re, Rh, Cr, Mo and W. The method for producing a high-toughness super-hard composite member of the present invention. 11. The method according to claim 9, wherein at least a part of the diamond particles is replaced with at least one of cubic boron nitride and wurtzite boron nitride.