JPH0398766A - Manufacture of metal bonded tool - Google Patents

Abstract

PURPOSE:To disperse a micro deposit of carbon uniformly in alloy powder by heating iron base alloy powder forming a matrix up to its solid-solubilizing temperature or more so as to form solid solution and cooling the obtained solid solution rapidly at the cooling speed of over 5 deg.C per second, thus preparing the iron base alloy powder. CONSTITUTION:At the time of manufacturing a metal bonded tool provided with an abrasive grain layer formed of a sintered body of iron base alloy powder containing carbon and abrasive grain, the iron base alloy powder as raw material is heated up to the solid-solubilizing temperature or more so as to be formed into solid solution, and the obtained solid solution is cooled down to the temperature of 200 deg.C or less at the cooling speed of over 5 deg.C per second. The mixture of this obtained iron base alloy powder and abrasive grain is integrally sintered so as to form the abrasive grain layer, thus obtaining the desired metal bonded tool.

Description

[Detailed Description of the Invention] [Object of the Invention] (Industrial Application Field) The present invention provides a metal having an abrasive grain layer consisting of a sintered body of an iron-based alloy containing carbon and abrasive grains having high hardness. Regarding the manufacturing method of bond tools, in particular, it is possible to uniformly disperse microscopic carbon in the material, which improves lubricity during grinding, improves matrix strength, and extends life. It relates to a method for manufacturing tools.

(Conventional technology) Metal-bonded diamond tools that use diamond as abrasive grains are conventionally used as grinding tools for grinding and finishing high-hardness fine ceramics such as aluminum oxide, silicon nitride, aluminum nitride, and silicon carbide. more widely used.

In addition, cubic boron nitride (hereinafter referred to as rCBN) is used as an abrasive grain for grinding and finishing of difficult-to-cut alloy materials such as high-speed steel and martensitic stainless steel containing vanadium (V).
It is abbreviated as J. ) dispersed in a matrix have been used.

Among the above-mentioned metal bond tools, for example, metal bond diamond tools that use diamond powder as abrasive grains are generally made by mixing diamond powder abrasive grains with metal powder and metal powder containing a metal compound if necessary, and then sintering the abrasive grains. It is formed. This sintering operation improves the bonding force and mechanical strength between the matrix and the diamond powder abrasive grains, and the resulting metal bonded diamond tool is
It is used as a polishing and grinding tool while regenerating the surface of the whetstone by dressing it appropriately.

By the way, in the case of metal-bonded diamond tools that are suitable for heavy-duty grinding with large depths of cut, the raw material for the matrix is powder obtained by pulverizing chips of iron-based alloy casting material with a high carbon content using a ball mill or stamping method. is used. Diamond abrasive grains are uniformly mixed with this high carbon iron-based alloy powder, and the mixture is heated to a temperature of 800 to 900, for example, in a vacuum or in a protected atmosphere with an inert gas such as argon.
'C, under conditions of pressure 200~4QQkg/cnf,
Hot pressing is performed to form an abrasive layer. Carbon particles are fixed and dispersed around the abrasive grains.

The carbon particles act as a lubricant that reduces grinding resistance with the object to be ground, while the matrix acts as a holding material that supports and fixes the diamond abrasive grains.

(Problems to be Solved by the Invention) However, iron-based alloy powder obtained by crushing chips of alloy casting materials using conventional manufacturing methods has a low cooling rate during casting, so the size of carbon precipitates is small. is several tens of μm to several hundred μm
It is larger than the average particle size of the abrasive grains (several tens of μm to 100 μm), and is non-uniform in shape, and does not have a finely dispersed structure.

Therefore, the carbon particles held in the powder are likely to fall off during the crushing operation, resulting in uneven distribution and shape of carbon in the powder. In tool materials whose matrix is formed from iron-based alloy powder, the diameter of carbon precipitates is large, so carbon precipitates tend to fall off during grinding, and shavings and polishing debris can form in the depressions created by falling off. is deposited and causes clogging, which further causes damage to the matrix due to seizure and plastic deformation.

In addition, due to the formation of depressions near the abrasive grains, the retention strength of the abrasive grains rapidly decreases, and the diamond abrasive grains rapidly fall off, leading to a decrease in grinding and polishing efficiency, making it impossible to obtain higher finishing accuracy. There was a problem.

In addition, in the conventional manufacturing process for metal-bonded diamond tools, carbon particles such as graphite are added, compression molded, and then sintered to disperse carbon particles in the sintered body. However, it has been difficult to uniformly disperse fine carbon grains throughout the abrasive grain layer. As a result, many carbon precipitates and abrasive grains fall off, which reduces the efficiency of grinding and polishing processes, making it impossible to obtain high finishing accuracy, and posing the fundamental problem that the life of the grinding wheel itself is short.

The present invention was made to solve the above-mentioned problems, and by uniformly dispersing fine carbon particles in the material, it improves lubricity during grinding, increases the strength of the matrix, and improves the abrasive grains and lubricant. The purpose of the present invention is to provide a method for manufacturing a metal bond tool that can produce an economical metal bond tool that has a long lifespan, has less carbon particles falling off, and can perform grinding and polishing processes with high efficiency. shall be.

[Structure of the invention]

(Means and effects for solving the problem) The inventors of the present application discovered that the conventional problem was caused by the form of carbon in the matrix. With the aim of obtaining metal-bonded tools, we investigated the method of dispersing fine carbon particles in the matrix material, and also investigated the effects of the particle size of the alloy powder, type of grinding wheel, and particle size on the polishing properties of the abrasive layer. researched.

As a result, the raw material iron-based alloy powder is heated above its solid solution temperature to form a solid solution, and the resulting solid solution is
When the mixture of iron-based alloy powder and abrasive grains obtained after cooling to a temperature of 200°C or less at a cooling rate of 100°C or more is sintered to form an abrasive grain layer, compared to the conventional method, hand,
We were able to obtain a long-life metal bond tool with significantly superior grinding properties.

Furthermore, when the average particle size of the iron-based alloy powder that forms the matrix before sintering is set to 1/3 or less of the average particle size of the abrasive grains, a strong matrix is formed and the shedding of the abrasive grains and carbon grains is effectively prevented. It was possible to obtain an abrasive grain layer with a long life and a long service life.

The present invention has been made based on the above findings. The iron-based alloy powder used in the method of the present invention is made of Fe as a base material, with addition of carbon to serve as a lubricant, silicon to promote carbon precipitation, and elements such as Ni and Go to improve sinterability. The alloy material is used. The composition of the alloy material is determined by taking into consideration the required strength of the matrix, heat conductivity, etc., but in general, alloy materials are made by combining two or more metals in order to increase the retention strength of the abrasive grains. is used.

Examples of means for pulverizing the alloy material include a method of pulverizing an ingot of the alloy material using a ball mill or a stamp mill, and a method of pulverizing the alloy material using a normal rapid cooling method such as a molten metal spraying method.

The above-mentioned molten metal spraying method is a method in which the molten metal of the raw material alloy material is pulverized by gas spraying, water spraying, centrifugal spraying, etc., and the cooling rate and powder particle size are adjusted to be appropriate according to the spraying conditions. This is a method for obtaining desired raw material powder.

In the method of the present invention, iron-based alloy powder prepared to have a predetermined composition and particle size is heated to a temperature higher than its solid solution temperature to form a solid solution, and the resulting solid solution is cooled at a cooling rate of 5°C per second or higher. Cool rapidly to a temperature below 200°C.

By heating above the solid solution temperature, all of the carbon contained in the alloy powder is once dissolved in the iron matrix to form a homogeneous solid solution. When this solid solution is cooled, carbon having a particle size depending on the cooling rate is precipitated into the matrix.

If the cooling rate is slower than 5°C per second, the carbon precipitates will become coarser and the function as a lubricant will decrease when used as a tool, while abrasive grains will frequently fall off and reduce grinding and polishing efficiency. In addition, high finishing accuracy cannot be obtained.

On the other hand, rapid cooling at 5°C or more per second prevents the coarsening of precipitates and disperses fine carbon precipitates uniformly within the alloy powder, so there is no decrease in the retention strength of the abrasive grains and the grinding ratio is It is possible to form a tool with an extremely large size and a long life.

Further, in the cooling treatment, the alloy powder needs to be sufficiently cooled to a temperature of 200° C. or lower.

This is because, in a high temperature state where the powder is cooled to a temperature exceeding 200° C., diffusion and movement of elements within the powder is still active, and coarsening of carbon precipitates progresses.

Further, the average particle size of the alloy powder to be prepared is preferably 150 μm or less and 1/3 or less of the average particle size of the abrasive grains.

The average particle size exceeds 150 μm, and the average particle size of the abrasive grains exceeds 150 μm.
This is because if it exceeds /3, the distribution of abrasive grains in the matrix becomes non-uniform, the retention strength of the abrasive grains also decreases, and the grinding and polishing ability of the tool tends to decrease.

Further, the carbon content in the iron-based alloy powder forming the matrix is 1.5% by weight or more, preferably 2.5% by weight or more; 4.
The content is adjusted to 5% by weight or less. This is because if the carbon content is less than 1.5%, self-lubricating properties will be reduced, the strength as a matrix metal will be reduced, and diamond, which is an abrasive grain, will be eluted into the iron base material.

On the other hand, if the carbon content exceeds 4.5% by weight, the matrix becomes brittle and the strength as a tool decreases, so the carbon content is set in the range of 1.5 to 4.5% by weight.

As described above, the iron-based alloy used in the present invention may contain carbon in the range described above, and in the heating and cooling process, the cooling rate is set to a predetermined value or higher, and the size of the carbon precipitates is reduced. The effects of the present invention can be obtained by controlling is not asked.

However, when silicon is added to this alloy composition, silicon destabilizes the cementite matrix, making it easier to generate carbon (graphite), forming finer carbon precipitates, and increasing the strength and lubricity of the matrix. can.

This amount of silicon is 1. Owl%~3. 5 wt% is preferred. If the amount of silicon is less than 1.0%, carbon precipitation and grain size become non-uniform, and at the same time, it is difficult to obtain sufficient strength as a tool. On the other hand, when the amount of silicon exceeds 3.5%, the ferrite phase that occupies the main part of the matrix metal undergoes transformation.
This is because hardening tends to reduce sinterability and strength.

Further, as the abrasive grains, CBN may be mixed in addition to diamond powder. diamond and cb
The Knoop hardness of N is 850 0. 5 1
All have extremely high values of 0.0 kg/7 or more, and are useful as abrasive grains for processing difficult-to-grind materials. In particular, CBN abrasive grains have excellent heat resistance, so their use as abrasive grains for dry machining without using a coolant is rapidly expanding.

As described above, an abrasive grain layer is formed by sintering a mixture of an iron-based alloy powder in which fine carbon is uniformly precipitated, and diamond and/or CBN used as abrasive grains, and A metal bond tool is manufactured by joining the abrasive grain layer and the alloy part.

The sintering operation is preferably carried out at about 1000 to 1180°C in a non-oxidizing atmosphere. F when the sintering temperature is less than 1000℃
It takes a long time to diffuse Si and C in e, making it difficult to obtain an abrasive grain layer with sufficient strength. On the other hand, if the temperature exceeds 1180°C, a liquid phase is generated, which causes an interfacial reaction with the abrasive grains, which tends to cause a decrease in the strength of the abrasive grain layer.

When pressure sintering is used, compared to the above-mentioned pressureless sintering, 850
Low-temperature sintering at temperatures above ℃ is possible, and interfacial reactions are less likely to occur. Furthermore, dimensional changes in the sintered body are small, and truing can be simplified.

The pressing force is set to 50 kg/cm or more in order to promote formability and mutual diffusion during sintering. However, even when pressure sintering is performed, if the sintering temperature is lower than 850°C, it takes a long time to diffuse silicon and carbon into the iron base material, making it difficult to obtain sufficient strength. Therefore, the pressure sintering temperature is set in the range of 850 to 1180°C.

As described above, according to the method for manufacturing a metal bond tool according to the present invention, the iron-based alloy powder forming the matrix is once heated to a temperature higher than its solid solution temperature to form a solid solution, and the obtained solid solution is Iron-based alloy powder is prepared by rapid cooling at a cooling rate of ℃ or higher. Therefore, fine carbon precipitates can be uniformly dispersed within the alloy powder. Therefore, there is no reduction in the retention strength of the abrasive grains by the matrix, and it is possible to maintain sufficient lubricity, and the life of the tool can be significantly extended.

Further, since the temperature of the alloy powder after rapid cooling is set to 200° C. or less, the diffusion of alloy constituent elements after cooling is small, and coarsening of carbon precipitates can be prevented.

Furthermore, by adding silicon, which destabilizes cementite and facilitates the formation of graphite precipitates, it becomes possible to uniformly form more stable and fine carbon precipitates in the alloy powder, improving the strength of the bond material. The interfacial bonding force with the abrasive grains can be improved.

In addition, the metal powder that forms the matrix and the highly hard abrasive grains made of at least one of diamond and CBN are firmly bonded by sintering to form the abrasive grain layer, so the retention force of the abrasive grains is large. , it is possible to obtain a good ground surface and extend the life of the tool. Note that by using diamond and CBN together as abrasive grains, the range to be ground can be widened.

In addition, since fine carbon precipitates are uniformly dispersed in advance inside the iron-based alloy powder that forms the matrix, even after sintering, the carbon grains as a lubricant are uniformly distributed around the abrasive grains. be able to.

In addition, the average particle size of the iron-based alloy powder is adjusted to 1/3 or less of the average particle size of the abrasive grains. , it can be uniformly dispersed around the abrasive grains.

Therefore, the lubrication function during grinding is fully demonstrated, the strength of the matrix as a supporting material is ensured sufficiently, and abrasive grains are prevented from falling off. As a result, it is possible to maintain high grinding efficiency at all times, and the abrasive grain layer The lifespan of can be significantly extended.

(Examples) Next, the present invention will be described in more detail with reference to the following examples.

Examples 1 to 3 and Comparative Examples 4 to 6 First, as Examples 1 to 3, carbon 3.0% and silicon 1.5%
An iron-based alloy powder consisting of , balance iron and having an average particle size of 30 μm was prepared by a conventional stamp mill method.

Next, the iron-based alloy powder was heated to 1180° C., which is higher than the solid solution temperature, to form a solid solution in which additional elements such as carbon and silicon were completely dissolved in the iron matrix.

Next, compressed air for cooling is applied to the iron-based alloy powder that has formed a solid solution, and the cooling rate is 5 and 1.0.2 per second, respectively.
The temperature was adjusted to 0°C, and the temperature was cooled to 200°C.

Here, the cooling rate was adjusted by controlling the temperature and flow rate of the cooling compressed air fed to the alloy powder layer, as in a normal cooling operation.

Next, 20% by weight of diamond abrasive grains having an average particle size of 100 μm were uniformly mixed with 80% by weight of the iron-based alloy powder obtained by the above heat treatment and cooling treatment. Furthermore, the mixture having the above composition was filled into a mold space having an outer diameter of 80 mm and an inner diameter of 15 mm, and sintering was performed by hot pressing in a vacuum. In the sintering operation, the temperature was raised to 900° C. while applying a pressure of 400 kg/caf, held for 30 minutes, and then processed to form a diamond tool with a width of 10 mm.

Also, Comparative Examples 4 and 5. 6, raw materials having the same alloy composition as those in Examples 1 to 3 were used, and after heating to the same temperature, the cooling rate was 1° C./sec. 3℃/s
EC and rapidly cooled to a temperature of 200°C (Comparative Example 4)
．． 5) and the one rapidly cooled to a temperature of 300°C at a cooling rate of 10°C/see (Comparative Example 6) was mixed with diamond abrasive grains, sintered, and processed to obtain an outer diameter of 80 lIII + 1 inner diameter of 15
A diamond tool with a width of 10 mm was used.

Using the thus obtained diamond tools of Examples 1 to 3 and Comparative Examples 4 to 6, S with a Vickers hardness of 1700 was used.
Grinding of i3N4 was performed.

Grinding conditions are rotation speed 3000 rpm, feed speed 5 m.
/min, grinding width 10mm, cutting depth 0.25m
It was set to m.

The grinding test results obtained in this way are shown in Examples 1 to 3 in Table 1.
, shown in the right column corresponding to Comparative Examples 4 to 6.

Here, the ground surface roughness shown in Table 1 refers to the S
The measured value of the surface roughness of iaN4 is shown, and the grinding ratio is expressed as the ratio of the amount of material to be ground removed to the amount of wear on the grinding wheel.

As can be seen from the results in Table 1, the average particle size of the precipitated carbon in the iron-based alloy powder prepared by setting the cooling rate to 5°C/sec or more in the cooling process is extremely fine; It can be seen that the diamond grindstones used in Examples 1 to 3 have higher grinding ratios and longer life than Comparative Examples 4 and 5, which were processed at a cooling rate of less than 5°C/sec.

On the other hand, since the alloy powders shown in Comparative Examples 4 and 5 have a slow cooling rate, the carbon precipitates become coarser and the average particle size becomes larger. Therefore, a tendency is observed that the roughness of the ground surface increases during grinding and the grinding ratio also decreases.

In addition, as shown in Comparative Example 6, the cooling rate was set to 10°C/se.
Even if it is set to a large value c, if the temperature after cooling is set to a high value of 300℃, the diffusion of elements inside the powder will proceed even after cooling, the average particle size of the precipitated carbon will become coarser, and the grinding characteristics will deteriorate slightly. I understand that.

Examples 7 to 9 and Comparative Examples 10 to 12 Next, as Examples 7 to 9, iron-based alloys having the structures shown in Table 1 and obtained by crushing iron-based alloys obtained by a casting method with a stamp mill were used. The alloy powder is heated to a temperature higher than its solid solution temperature 11
A solid solution was formed by heating to 60-1200°C, and then the resulting solid solution was rapidly cooled to a temperature of 180°C at a cooling rate of 10°C per second.

Through this heating and cooling treatment, an iron-based alloy powder having an average particle size of 30 μm in which fine precipitated carbon was uniformly dispersed was obtained.

Next, 20% by weight of CBN with an average particle size of 100 μm was added to 80% by weight of the obtained iron-based alloy powder, and the uniformly mixed mixture was sintered under the same conditions as in Examples 1 to 3. Sintered, C with an outer diameter of 80 mm, an inner diameter of 15 mm, and a width of 10 mm.
A BN grindstone was formed.

Further, as Comparative Example 10-t2, iron-based alloy powder having the same composition as Examples 7, 8, and 9 was heated to a temperature lower than its solid solution temperature (800 to 900°C), and then
It was cooled under the same conditions as in No. 9, and further mixed with CBN abrasive grains and sintered to form a CBN grindstone of the same shape.

And the above-mentioned Examples 7-. Using the CBN grinding wheels obtained in Comparative Examples 10 to 12, grinding of cemented carbide was performed under the same processing conditions as in Examples 1 to 3, and the grinding ratio was measured. The influence on the grinding properties was investigated. The grinding test results are shown in the corresponding right column of Table 1.

As can be understood from the results in Table 1, even when using CBN abrasive grains, Example 7 used an iron-based alloy powder that was heated to a temperature higher than its solid solution temperature and then rapidly cooled. -9 have better grinding ratios than Comparative Examples 10-12, which were heated below the solid solution temperature. Comparative example lO~1
In No. 2, since the heating temperature is below the solid solution temperature, there is little carbon dissolved in the solid solution, and it is difficult to make the precipitated carbon in the alloy powder fine even if it is cooled at a high rate. As a result, the strength of the tool matrix decreases, which suggests a tendency for the grinding ratio to decrease.

Examples 13.14 and Comparative Examples 15-18 Next, Example 1
3.14 is an iron-based alloy powder obtained by crushing a cast iron-based alloy consisting of 3.0% carbon, 1.0% silicon, and the balance iron using a stamp mill method, and adjusting the average particle size to 10.15 μm. And so. Next, the obtained iron-based alloy powder was heated to 1150°C, which is higher than its solid solution temperature, and the cooling rate was further increased to 20°C.
It was rapidly cooled to 150°C at a rate of °C/sec.

Diamond abrasive grains (average particle size 55 μm) and CBN abrasive grains (average particle size 55 μm) were used as abrasive grains at a weight ratio of 9:1, that is, 22% by weight of each of the thus obtained iron-based alloy powders. .5% by weight and 2.5% by weight were mixed, and the obtained mixed powder was subjected to the same sintering process as in Examples 1 to 3 to form a diamond CBN composite grindstone.

In addition, as Comparative Examples 15 to 17, cast materials having the same composition as the iron-based alloys obtained in Examples 13 to 14 were crushed by a stamping method, and the average particle size was varied in the range of 25 to 90 μm.
The particle size ratio to the average particle size (55 μm) of the abrasive grains is 0.45.
~1.64, and a diamond CBN composite grindstone was further formed using the same sintered body composition and sintering conditions as in Examples 13-14.

In addition, as Comparative Example 18, the iron-based alloy of the cast material obtained in Examples 13 to 14 was pulverized by a stamping method, and the average particle size was 60.
μm iron-based alloy powder was prepared, mixed with abrasive grains without heating and cooling treatment, sintered with the same sintered body composition and sintering conditions as in Examples 13 and 14, and then processed to produce diamond CBN. A composite grindstone was formed.

Using the diamond CBN composite grindstones obtained in Examples 13 to 14 and Comparative Examples 15 to 18, a grinding test of Si3N4 was conducted under the same processing conditions as in Examples 1 to 3. The results shown in the column were obtained.

[Margin below]

As can be seen from the results in Table 1, diamond abrasive grains and CB
In Examples 13 and 14, in which mixed abrasive grains with N abrasive grains were used and the grain size of the alloy powder was set to 1/3 or less of the average grain size of the abrasive grains, it was possible to perform good machining and finishing. can be,
Furthermore, a high grinding ratio can be ensured.

However, as shown in Comparative Examples 15 to 17, when the average particle size of the metal powder serving as the matrix exceeds 1/3 of the average particle size of the abrasive grains, the shedding of the abrasive grains increases and the grinding ratio is reversed. descend. Therefore, it is necessary to set the average particle size of the metal powder constituting the matrix to 1/3 or less of the average particle size of the abrasive grains.

On the other hand, as shown in Comparative Example 18, when the iron-based alloy powder prepared by crushing the cast material according to the conventional method is used as the raw material for the sintered body without heating and cooling, the precipitated carbon in the alloy powder is Due to the large particle size, the strength of the matrix decreases,
It can be seen that sufficient grinding characteristics cannot be obtained.

〔Effect of the invention〕

As explained above, according to the method for manufacturing a metal punching tool according to the present invention, the iron-based alloy powder forming the matrix is
An iron-based alloy powder is prepared by once heating above the solid solution temperature to form a solid solution, and then rapidly cooling the obtained solid solution at a cooling rate of 5° C. per second or more. Therefore, fine carbon precipitates can be uniformly dispersed within the alloy powder.

Therefore, there is no reduction in the retention strength of the abrasive grains by the matrix, and it is possible to maintain sufficient lubricity, and the life of the tool can be significantly extended.

Further, since the temperature of the alloy powder after rapid cooling is set to 200° C. or lower, diffusion of alloy constituent elements after cooling is small, and coarsening of carbon precipitates can be prevented.

In addition, since the average particle size of the iron-based alloy powder is adjusted to 1/3 or less of the average particle size of the abrasive grains, the iron-based alloy powder that serves as the support material for the carbon grains as a lubricant and the abrasive grains can be reduced. It can be uniformly dispersed around the abrasive grains.

In addition, the metal powder that forms the matrix and high-hardness abrasive grains made of at least one of diamond and CBN are firmly bonded by sintering to form an abrasive grain layer, which increases the retention force of the abrasive grains. A large and good ground surface can be obtained, and the life of the tool can be extended. Note that by using diamond and CBN together as abrasive grains, the range to be ground can be widened.

In addition, since fine carbon precipitates are uniformly dispersed in advance in the iron-based alloy powder that forms the matrix, even after sintering, the carbon grains as a lubricant can be uniformly distributed around the abrasive grains. I can do it.

Therefore, the lubrication function during grinding is fully demonstrated, the strength of the matrix as a supporting material is ensured sufficiently, and abrasive grains are prevented from falling off. As a result, it is possible to maintain high grinding efficiency at all times, and the abrasive grain layer The lifespan of can be significantly extended.

Claims (1)

[Scope of Claims] 1. In a method for manufacturing a metal bond tool having an abrasive grain layer made of a sintered body of carbon-containing iron-based alloy powder and abrasive grains, iron-based alloy powder as a raw material is hardened. A solid solution is formed by heating above the melting temperature, the obtained solid solution is cooled to a temperature of 200°C or less at a cooling rate of 5°C or more per second, and the obtained mixture of iron-based alloy powder and abrasive grains is integrated. A method for manufacturing a metal bond tool, characterized by forming an abrasive layer by sintering. 2. The average particle size of the iron-based alloy powder is 1/3 of the average particle size of the abrasive grains.
A method for manufacturing a metal bond tool according to claim 1, set as follows. 3. The method for manufacturing a metal bond tool according to claim 1, wherein at least one of diamond and cubic boron nitride is used as the abrasive grain.