JP5971472B2 - Hard material, manufacturing method of hard material, cutting tool and friction stir welding tool - Google Patents

Description

  The present invention relates to a hard material suitable for a constituent material such as a cutting tool or a friction stir welding tool, a manufacturing method thereof, and a cutting tool and a friction stir welding tool. In particular, the present invention relates to a hard material that is superior in plastic deformation resistance at high temperatures as compared to conventional cemented carbides and superior in hardness at low temperatures as compared to Co-based heat-resistant alloys.

  Conventionally, as a hard material for cutting steel, cast iron, and sintered alloy, a cemented carbide or a coated cemented carbide in which a ceramic hard coating is provided on the surface thereof is known (for example, Patent Document 1). Cemented carbide has excellent strength and fracture toughness, and also has excellent thermal conductivity. Therefore, it is used for friction stir welding used for joining flat plates, etc. in addition to cutting tools used for roughing and intermittent cutting of steel and cast iron. It is suitable for the constituent material of a tool (for example, patent document 2). On the other hand, the Co-base heat-resistant alloy is excellent in high-temperature strength, and is expected to be applied as an aircraft jet engine or industrial gas turbine material.

JP 2011-42830 JP 2001-314983 JP

  In recent years, hard materials that can withstand high-speed and high-efficiency machining have been demanded in the world of cutting in order to reduce machining costs. Moreover, the cutting temperature rises due to the difficulty of cutting the work material, and the need for a hard material having excellent heat resistance is also increasing. Also in the field of friction stir welding, in order to enable more efficient joining, development of a tool with even higher heat resistance is desired.

  Cemented carbide is a very hard material with excellent strength, toughness, and hardness. However, high-temperature hardness is insufficient in cutting environments where the cutting temperature exceeds 1000 ° C, resulting in plastic deformation during cutting and reduced wear resistance. Problems have occurred. Similarly, there is a concern that the friction stir welding tool lacks high-temperature hardness. On the other hand, Co-based heat-resistant alloys are excellent in high temperature hardness and excellent toughness, but are not utilized as a constituent material for cutting tools and friction stir welding tools because of low room temperature hardness.

  The present invention has been made in view of the above circumstances, and one of its purposes is to improve the plastic deformation resistance at high temperatures compared to conventional cemented carbide, and to provide a hard material having strength and toughness. It is in providing the manufacturing method. Another object of the present invention is to provide a cutting tool and a friction stir welding tool using the hard material.

  The present inventors diligently studied to devise the material of the hard phase on the assumption that WC constituting the hard phase of the conventional cemented carbide is used. As a result, we obtained knowledge that using a hard phase with WC as the core and Co-based heat-resistant alloy as the shell can improve the plastic deformation resistance of hard materials in particular while ensuring sufficient strength and toughness. . This invention was made | formed based on this knowledge, and has each structure of the hard material shown below, the manufacturing method of a hard material, a cutting tool, and the tool for friction stir welding.

[Hard material]
The hard material of the present invention is a hard material mainly composed of a hard phase, and this hard phase includes a first hard phase. The first hard phase has a core made of WC and a shell made of a Co-base heat-resistant alloy and covering the core.

  A hard material including the first hard phase having such a core-shell structure has high fracture toughness and rigidity because the core is made of WC.

  On the other hand, when the shell is made of a Co-base heat-resistant alloy, it is easy to form a Co-base heat-resistant alloy skeleton network having excellent plastic deformation resistance, and the plastic deformation resistance of hard materials can be improved. The low plastic deformation resistance in the temperature range near 1000 ° C, which is a defect of the alloy, can be improved. In addition, since the shell is a Co-based heat-resistant alloy, it has excellent wettability with the iron group metal. Therefore, when the iron group metal is used as the binder phase material, the sinterability is improved and a dense sintered body can be obtained. And a hard material with excellent fracture resistance.

  As one form of the hard material of the present invention, a form further containing a binder phase containing an iron group metal can be mentioned.

  According to this configuration, wear resistance and fracture resistance can be provided in a balanced manner as compared with a hard material having only a hard phase.

  As one form of the hard material of the present invention, a form in which the hard phase further contains a second hard phase can be mentioned. The second hard phase is composed of a compound of at least one metal element selected from Group 4, 5, 6 elements of the periodic table and at least one element of C and N. The content of the second hard phase with respect to the entire hard material is 5 to 70% by mass.

  According to this configuration, by containing a predetermined amount of the second hard phase, when the second hard phase having excellent thermal conductivity such as WC is appropriately interposed between the particles of the first hard phase of the core-shell structure, More heat conduction paths having high thermal conductivity can be formed in the hard material. Therefore, the heat dissipation of the hard material can be improved, and a material excellent in thermal shock resistance can be obtained. Similarly, when a second hard phase such as TiCN is appropriately interposed between the particles of the first hard phase, TiCN or the like having excellent wear resistance against steel can be present in the hard material. Therefore, it can be set as the material excellent in abrasion resistance.

  One form of the hard material of the present invention containing a binder phase is that the binder phase content is 3% by mass or less.

  The hard material having this configuration can be suitably used as a tool for applications that require particularly plastic deformation resistance, such as friction stir welding for steel.

  As one form of the hard material of the present invention, the average particle diameter of the core may be 1 μm or more and 5 μm or less.

  According to this configuration, by specifying the average particle diameter of the core, it is possible to achieve a balance between improving the thermal conductivity of the hard material and improving the strength and fracture toughness.

  As one form of the hard material of the present invention, the average thickness of the shell may be less than 3% of the average particle diameter of the core.

  According to this configuration, it is possible to prevent the shell made of the highly plastic deformation-resistant Co-based heat-resistant alloy from peeling off or cracking the shell, and to strengthen the skeleton. As a result, the effect of improving the plastic deformation resistance of the hard material becomes remarkable.

[Method of manufacturing hard material]
The manufacturing method of the hard material of this invention is a manufacturing method of the hard material which produces the hard material containing a hard phase, Comprising: The following process is provided.
Preparation step: A raw material powder mainly composed of a hard phase is prepared.
Mixing step: The raw material powder is mixed to obtain a mixed powder.
Molding step: A compact is obtained by compressing the mixed powder at a predetermined pressure.
Sintering step: The molded body is sintered at a predetermined temperature.
In this manufacturing method, the hard phase in the preparation step includes a first hard phase, and the first hard phase includes a core made of WC and a shell made of a Co-based heat-resistant alloy formed on the outer periphery of the core. Have. And the said mixing process mixes the said raw material powder, without using a grinding | pulverization media.

  Using a first hard phase comprising a core made of WC and a shell of a Co-based heat-resistant alloy, and mixing the raw powder containing this hard phase, media-less mixing without using pulverizing media can damage the shell. And peeling can be minimized. Thereby, the hard material of the sintered compact whose core was more reliably covered with the shell can be obtained.

  As one form of the manufacturing method of the hard material of the present invention, in the preparation step, a binder phase raw material powder further containing an iron group metal is also prepared, and in the mixing step, the hard phase raw material powder and the binder phase raw material powder are mixed. To do.

  According to this manufacturing method, by including a binder phase, it is possible to obtain a hard material having a better balance of wear resistance and fracture resistance than a hard material having only a hard phase.

  As one form of the manufacturing method of the hard material of this invention, the said shell forms the method of forming into a film on the outer periphery of the said core by a physical vapor deposition method.

  By forming the shell by physical vapor deposition, a dense shell can be formed relatively easily.

  Moreover, in the manufacturing method of the hard material of the present invention in which the shell is formed by physical vapor deposition, the physical vapor deposition is a sputtering method, and a Co-based heat-resistant alloy is used as a target of the sputtering method.

〔Cutting tools〕
The cutting tool of the present invention is a cutting tool used for high-speed machining of steel, and at least a part thereof is composed of a base material made of the hard material according to the present invention described above. Furthermore, you may provide the hard coating | cover which covers this base material.

[Friction stir welding tool]
The friction stir welding tool of the present invention is a friction stir welding tool used for joining steel, and at least a part thereof is made of the hard material according to the present invention described above. Furthermore, you may provide the hard coating | cover which covers this hard material.

  According to the hard material of the present invention, a material having high strength, high fracture toughness, and excellent plastic deformation resistance in a temperature range near 1000 ° C. can be obtained.

  According to the method for producing a hard material of the present invention, when the hard material is produced using the raw material powder containing the hard phase powder having the core-shell structure, the damage to the shell can be effectively suppressed. As a result, it is possible to obtain a hard material having a hard phase with a core-shell structure with little cracking or peeling of the shell or substantially no cracking or peeling.

  According to the cutting tool of the present invention, by using the hard material of the present invention, it is possible to provide a tool having excellent fracture resistance and plastic deformation resistance while having sufficient wear resistance.

  According to the friction stir welding tool of the present invention, by using the hard material of the present invention, a tool excellent in fracture resistance and plastic deformation resistance while having sufficient wear resistance can be obtained.

(A) is a schematic diagram showing the structure of the hard material of the present invention according to the embodiment not including the second hard phase, (B) shows the structure of the hard material of the present invention according to the embodiment including the second hard phase. It is a schematic diagram. It is a schematic cross section which shows the cutting blade vicinity of the cutting tool of this invention which concerns on embodiment. It is a schematic cross section which shows the tool for friction stir welding of this invention which concerns on embodiment.

  Embodiments of the present invention will be described below.

〔Overview〕
The hard material of the present invention is composed of a sintered body in which a powder of a hard phase 10 is bonded with a bonding phase 20 as shown in FIG. 1 (A). The main feature of this hard material is the material and structure of the hard phase. Specifically, the first hard phase particles 10A having a core-shell structure in which the outer periphery of the core 11 is covered with a shell 12 are included in the hard phase 10, the material of the core 11 is WC, and the material of the shell 12 is a Co-based heat-resistant alloy. . In some cases, the hard material does not include the binder phase 20 and includes only the hard phase 10. Hereinafter, the hard material, a manufacturing method thereof, a cutting tool using the hard material, and a friction stir welding tool using the hard material will be described in detail.

[Hard material]
{Hard phase}
The hard phase includes a first hard phase having a core-shell structure, and optionally includes a second hard phase different from the first hard phase.

(First hard phase)
The core-shell structure of the first hard phase in the present invention uses core-shell composite particles in which a WC core is coated with a Co-based heat-resistant alloy shell at the raw material powder stage.

<Core>
The core constitutes the center of the hard phase of the core-shell structure and has a function that contributes mainly to the improvement of the wear resistance of the hard material by having sufficient hardness.

<Material>
The core material is WC. By configuring the core with WC, in addition to ensuring sufficient hardness as a hard material, it also contributes to ensuring the thermal conductivity of the hard material.

"size"
The average particle diameter of the core is preferably 1 μm or more and 5 μm or less. If the particle size of the hard phase is small, the grain boundaries increase, and the thermal conductivity of the hard material decreases. Therefore, if the average particle diameter of the core is 1 μm or more, the effect of improving the thermal conductivity of the hard material can be easily obtained. Moreover, the core particle of such a size is easy to manufacture. In particular, considering the high thermal conductivity of the hard material, the average particle size is preferably 1.5 μm or more, more preferably 2 μm or more. On the other hand, the upper limit of the average particle diameter of the core is about 5 μm. This is because if the average particle size of the core is 5 μm or less, a high-strength hard material can be easily obtained. This average particle size is a value calculated by using the Fullman equation after the cut surface of the sintered hard material is mirror-polished after surface grinding and photographed with a scanning electron microscope (SEM). . The average particle size of the other particles in this specification is measured similarly. In addition, since the average particle diameter (average particle diameter after sintering) in the hard material of the present invention is manufactured through a mixing method that does not use a pulverizing medium as described later, the average particle diameter of the core particles in the raw material powder The diameter is almost maintained.

<Shell>
The shell mainly covers the outer periphery of the core, ensures the toughness of the hard material, and forms a highly plastic deformation-resistant skeleton in the hard material.

<Material>
When the shell is made of a Co-base heat-resistant alloy, it is easy to form a network of a Co-base heat-resistant alloy skeleton having excellent plastic deformation resistance in the hard material, and the plastic deformation resistance of the hard material can be improved. It can improve the low plastic deformation resistance in the temperature range around 1000 ℃, which is a defect of cemented carbide. In addition, since the shell is a Co-based heat-resistant alloy, it has excellent wettability with the iron group metal. Therefore, when the iron group metal is used as the binder phase material, the sinterability is improved and a dense sintered body can be obtained. And a hard material with excellent fracture resistance. In the case of using an iron group metal binder phase, a shell made of a Co-base heat-resistant alloy can be distinguished from a binder phase based on the density of constituent elements by EDX mapping of the structure of the hard material. Even when no binder phase raw material is used, a dense sintered body can be obtained due to the excellent sinterability of the Co-base heat-resistant alloy constituting the shell.

  The composition of the Co-based heat-resistant alloy may include Co as a main component and at least one of Cr: 2 to 30% by mass, Ni: 2 to 35% by mass, and W: 3 to 45% by mass. “Co as a main component” means that Co is contained in the element having the highest content among the constituent elements of the Co-base heat-resistant alloy. As other additive elements, Fe: 1 to 20% by mass, Mn: 0.1 to 2.0% by mass, Mo: 4 to 10% by mass, Al: 0.1 to 13% by mass, Ta: 0.1 to 10% by mass, Nb: 2 -4% by mass, Ti: 0.2-2.0% by mass, C: 0.1-1.0% by mass and B: 0.001-1% by mass are optionally contained. More specific compositions include HS-based Co-based heat-resistant alloys such as HS6, HS25, HS31, HS152, HS188 and the like, as well as MP35N, UMCo50, S816 and the like, and HS25 and S816 are particularly suitable.

"thickness"
The average thickness of the shell composed of the Co-base heat resistant alloy is preferably about 0.01 to 1 μm. This is because if the average thickness is 0.01 μm or more, it is easy to obtain the effect of making the shell highly resistant to plastic deformation with a shell having excellent plastic deformation resistance, and if it is 1 μm or less, the shell is hard to crack and hard. This is because it is easy to maintain the effect of improving the plastic deformation resistance of the material. In particular, the average thickness of the shell is preferably set to 0.01 μm or more and 0.1 μm or less in order to make the effect of highly plastic deformation of a hard material remarkable, and in order to more reliably suppress cracks in the shell, The average thickness is preferably 1 μm or less, more preferably 0.3 μm or less. This average thickness is measured by processing a focused ion beam (FIB) on a cut surface of a hard material, taking a photograph with a transmission electron microscope (TEM), and measuring 10 points on multiple first hard phase particles. This is done by averaging the shell thickness at the above measurement points.

  Further, when the average thickness of the shell composed of the Co-base heat resistant alloy is expressed as a ratio to the average particle diameter of the core, it is preferably less than 3% of the average particle diameter of the core. This is because, by setting the ratio to less than 3%, the effect of high plastic deformation resistance of the hard material is increased for the reasons described above.

  That is, a preferable condition for suppressing cracks in the shell is to make the volume content of the core in the composite particles having the core-shell structure larger than the volume content of the shell. If a shell having a thickness less than a certain ratio is formed according to the size of the core, it is easy to suppress the occurrence of cracks in the shell.

(Second hard phase)
The second hard phase is a hard phase other than the first hard phase, and has a function of improving characteristics such as wear resistance, thermal shock resistance, and fracture resistance of the hard material according to the material and blending amount thereof. . For example, as shown in FIG. 1 (B), the hard material including the second hard phase has a structure in which the first hard phase particles 10A and the second hard phase particles 10B are mixed and bonded by the binder phase 20.

<Material>
As the material of the second hard phase, a compound of at least one metal element selected from Group 4, 5, 6 elements of the periodic table and at least one element of C and N, that is, carbide, nitride of the above metal element, And at least one of carbonitrides can be used. In particular, at least one of WC and TiCN can be suitably used. When at least one of WC and TiCN is included as the second hard phase, the thermal shock resistance and wear resistance of the hard material can be further improved. In addition, when at least one of TaC and NbC is included as the second hard phase, the resistance to steel can be improved, and when at least one of ZrC, ZrCN, and ZrN is included, the strength of the hard material at high temperature can be improved. . In addition, when at least one of Cr ₃ C ₂ and Mo ₂ C is contained as the second hard phase, the sinterability can be improved. When materials other than WC and WC are included, the content of WC in the entire second hard phase is preferably 50% by mass or more from the viewpoint of improving thermal shock resistance (breakage resistance).

"Construction"
The structure of the second hard phase is generally a single-phase structure, but may be a cored structure included in a conventional cermet. As a specific example, the inner core portion is substantially made of Ti (C, N), and the peripheral portion is (Ti, W, Mo) (C, N), (Ti, W, Nb) (C, N ), (Ti, W, Mo, Nb) (C, N), (Ti, W, Mo, Nb, Zr) (C, N) and the like.

"size"
The average particle size of the second hard phase is preferably about 0.1 to 4 μm. This is because, by setting the average particle size to 0.1 μm or more, the raw material powder is easy to handle and is industrially available. Further, by setting the average particle size to 4 μm or less, it is easy to ensure the strength and wear resistance of the hard material. In particular, when the particle size of the second hard phase is smaller than the particle size of the first hard phase, the second hard phase is easily interposed between the particles of the first hard phase, and the filling rate of the hard phase is increased. This is because it is easy to improve wear resistance and plastic deformation resistance.

(Content)
The content of the hard phase (including the second hard phase when there is a second hard phase) is preferably 90% by mass or more and 100% by mass or less with respect to the entire hard material. By containing the hard phase in an amount of 90% by mass or more, particularly 95% by mass or more, more preferably 97% by mass or more, it is easy to ensure the strength and wear resistance of the hard material. The hard phase content may be 100% by mass. Even if it is a hard material which consists only of a hard phase and does not contain a binder phase, since a 1st hard phase is equipped with the shell of a Co-base heat-resistant alloy, it can be set as a sintered compact. A hard material having a hard phase content of 100 mass% is particularly excellent in plastic deformation resistance.

  The content of the first hard phase with respect to the entire hard material is preferably 10% by mass or more. The content of the first hard phase is more preferably 15% by mass or more, 20% by mass or more, or 30% by mass or more, further preferably 50% by mass or more, and particularly preferably 65% by mass or more. By containing 10 mass% or more of the first hard phase, an effect of improving plastic deformation resistance is particularly easily obtained, and by increasing this content, the plastic deformation resistance tends to be more excellent. There is no particular upper limit for the content of the first hard phase. All of the hard phases may consist of the first hard phase.

  When a 2nd hard phase is included, it is preferable that content of the 2nd hard phase with respect to the whole hard material shall be 5-70 mass%. This is because if it is less than 5% by mass, the effect of containing the second hard phase is small, and if it exceeds 70% by mass, the presence effect of the core-shell structure particles may be small. The upper limit is more preferably 60% by mass or less.

  In addition, when WC is contained in the second hard phase, when the volume content of the first hard phase is larger than the volume content of the second hard phase (WC), the resistance to the conventional cemented carbide of similar composition. Greatly improves plastic deformation and wear resistance. Conversely, even when the volume content of the first hard phase is smaller than the volume content of the WC (second hard phase), the hard material of the present invention is inferior in wear resistance compared to conventional cemented carbide. , Thermal shock resistance, and fracture resistance.

{Bond phase}
<Material>
The binder phase is a material that binds the particles of the hard phase by being contained as necessary, and an iron group metal is preferable. In particular, at least one of Co and Ni is preferable because of its high hard phase and wettability. When the binder phase is mainly composed of Co, the sinterability is particularly improved, the sintered body can be easily densified, and the strength and fracture toughness can be improved. On the other hand, Ni is excellent in corrosion resistance. Further, the constituent elements of the hard phase such as W, Cr, Ru, and C may be dissolved in the binder phase. In particular, a large amount of at least one of W, Cr, and Ru is preferable because the binder phase is strengthened by solid solution and the toughness of the hard material can be improved.

"Content"
The binder phase is preferably contained in an amount of 0.5% by mass to 10% by mass with respect to the entire hard material. The higher the binder phase content, the higher the toughness and sinterability of the hard material. However, the binder phase is 3 masses in applications that require plastic deformation resistance, specifically steel friction stir welding applications. % Or less is preferable.

[Method of manufacturing hard material]
The hard material of the present invention is typically produced through the steps of preparation of raw material powder → mixing → molding → sintering / cooling. If necessary, a separate heat treatment may be performed after sintering.

{Preparation process}
In the preparation step, a hard phase powder mainly comprising a hard phase is prepared. The hard phase powder includes a first hard phase powder. At that time, if necessary, at least one raw material powder of the second hard phase powder and the binder phase powder is prepared. Since many of the raw material powders other than the first hard phase powder can use, for example, commercially available products, the following description mainly describes a method for obtaining the first hard phase powder.

  In order to obtain the first hard phase powder having a core-shell structure, first, a powder (core powder) made of core particles is prepared. That is, a core powder made of WC is prepared. Next, each particle of the prepared core powder is coated with a Co-based heat-resistant alloy serving as a shell. In addition to physical vapor deposition, a liquid phase method such as a sol-gel method can be used for forming the shell. By forming the shell by physical vapor deposition, a dense shell can be formed relatively easily.

  For example, in the case of physical vapor deposition, the core powder is put into a container, and after the container is evacuated, the surface of each particle of the core powder is sputtered using a Co-base heat-resistant alloy target while rotating the container. A Co-base heat-resistant alloy shell is formed. By rotating the container, a shell can be uniformly formed on each particle of the core powder.

{Mixing process}
Each raw material powder mentioned above is mixed as uniformly as possible by an appropriate mixing means to obtain a mixed powder. In this mixing step, it is important to mix the raw material powder so as not to damage the core-shell structure of the first hard phase, particularly the shell. That is, in this mixing step, a mixing means is selected that does not cause cracks or peeling in the shell. Specifically, for example, the raw material powder is mixed with an organic solvent such as ethanol or acetone to form a slurry, and the slurry is mixed without pulverizing media while being irradiated with ultrasonic waves. According to this mixing method, the raw material powder can be mixed without substantially pulverizing the raw material powder and without damaging the shell.

  When the raw material powder is mixed to obtain a mixed powder, usually, a binder is added to the mixed powder, and the mixture is spray-dried using a drying means such as a spray dryer and granulated. Examples of the binder include paraffin wax and polyethylene glycol. The content of the binder is preferably about 1 to 4% by mass with respect to the total of the raw material powder and the binder.

{Molding process}
Molding of the mixed powder obtained in the mixing step is performed by filling the mold with the mixed powder and molding it into a predetermined shape with a predetermined pressure. Examples of the molding method include a dry pressure molding method, a cold isostatic pressing method, an injection molding method, and an extrusion molding method. The molding pressure is preferably about 50 to 200 MPa. Moreover, the shape of a molded object selects the appropriate shape which does not become an excessively complicated shape according to the shape of the product calculated | required. The final product shape may be appropriately machined after calcination or sintering as necessary.

{Sintering process}
It is preferable to perform the sintering of the compact by holding the compact for a predetermined time in a temperature range where a liquid phase is generated. The sintering temperature is preferably about 1300 ° C to 1600 ° C. If the sintering temperature is too high, particles constituting the hard phase tend to grow. The holding time is preferably about 0.5 to 2.0 hours, particularly preferably about 1.0 to 1.5 hours. The atmosphere during heating is preferably an inert gas atmosphere such as nitrogen or argon or a vacuum (about 0.1 to 0.5 Pa). Further, in the sintering step, when cooling the heated compact while maintaining the sintering temperature for a predetermined time, it is preferable to cool in a vacuum or an inert gas atmosphere such as argon (Ar).

  In order to densify the sintered body, hot isostatic pressing may be performed after sintering in a temperature range of 1300 ° C. to 1500 ° C. in an argon atmosphere under a pressure of 10 to 200 MPa. In addition, a method of obtaining a denser sintered body by pressing the raw material powder at a high pressure of 1 to 10 GPa may be employed. The sintering temperature during ultra-high pressure pressing is preferably about 1200 to 1600 ° C. This method using an ultrahigh pressure press can be suitably used for producing a sintered body having only a hard phase having no binder phase.

{Heat treatment process}
You may perform a solution treatment and an age hardening process with respect to the sintered compact after sintering. The solution treatment is performed at 800 to 1500 ° C. for 5 minutes to 2 hours, and the age hardening treatment is performed at 500 to 1000 ° C. for 1 hour to 50 hours. By performing this heat treatment, the structure of the hard material can be controlled, and the strength and hardness can be improved.

〔Cutting tools〕
The cutting tool using the hard material of the present invention includes, for example, a base 110 and a hard coating 120 that covers the base 110 as shown in FIG. In FIG. 2, the upper surface of the cutting tool is a rake face, the left slope is a flank face, and the ridge lines on both sides are cutting edges.

{Cutting edge area}
In this cutting tool, the entire substrate is made of the hard material of the present invention described above, and the entire surface of the substrate 110 is covered with the hard coating 120. However, the portion formed of the hard material of the present invention may be at least a region involved in cutting, that is, a cutting blade peripheral region including the cutting blade and its vicinity. The peripheral region of the cutting edge includes a region where flank wear and crater wear are likely to occur, and a region where chips come into contact.

{Hard coating}
This cutting tool is preferably provided with a hard coating 120 at least in the peripheral region of the cutting edge of the substrate 110. By providing the hard coating, higher wear resistance can be obtained.

The material of the hard coating 120 is selected from the group consisting of one or more elements selected from the group consisting of metals of Groups 4, 5, 6 of the periodic table, Al, Si and B, and carbon, nitrogen, oxygen and boron. It is preferable to use a compound with one or more elements. Specific examples include TiCN, Al ₂ O ₃ , TiAlN, TiN, and AlCrN. The film structure of the hard coating 120 may be a single layer or multiple layers. The total thickness of the hard coating 120 is preferably about 1 to 20 μm. As a method for forming the hard coating 120, any of a CVD method such as a thermal CVD method and a PVD method such as a cathode arc ion plating method can be used.

  Specific examples of the cutting tool include a tool used as a blade-tip-exchangeable tip, particularly a cutting tool, an end mill, and the like. The cutting tool using the hard material of the present invention can be suitably used for high-speed cutting of steel. Generally, high speed cutting is cutting performed at a speed of 150 m / min or more. Although FIG. 2 shows a cutting tool having the hard coating 120, it may be a cutting tool having only this base material 110 without this coating.

[Friction stir welding tool]
As illustrated in FIG. 3, the friction stir welding tool 30 using the hard material of the present invention includes a shaft portion 30S and a probe 30P protruding from the tip of the shaft portion 30S. The shaft portion 30S is a rod-shaped member supported by a rotation mechanism (not shown), and rotates by driving the rotation mechanism. On the other hand, the probe 30P is a rod-like member having a diameter smaller than that of the shaft portion 30S, and is a portion that is pressed against the joining interface to be joined when performing friction stir welding. The probe 30P may be provided integrally with the shaft portion 30S, but may be formed detachably with respect to the shaft portion 30S. In the latter case, for example, a screwing method in which the probe 30P is fixed to the shaft portion 30S by screw fitting, or a self-grip method in which the probe 30P is pushed into the concave portion of the shaft portion 30S and fixed. In this example, the shaft portion 30S and the probe 30P are made of the hard material of the present invention as an integral base material 31, and the hard coating 32 is formed on the entire outer periphery of the base material 31. As the material and thickness of the hard coating 32, the same material and thickness as the hard coating 120 of the cutting tool described above can be used.

  When performing friction stir welding with the friction stir welding tool 30 shown in FIG. 3, first, a pair of objects to be joined are butted in parallel. A steel plate is mentioned as a joining object. When the joining target is abutted, the friction stir welding tool 30 is pressed against the joining portion while rotating the friction stir welding tool 30, and the friction stir welding tool 30 is moved along the abutting interface of the joining target. As the friction stir welding tool 30 is rotated and moved, the objects to be joined in the vicinity of the butted portion are plastically flowed, and both objects to be joined are joined. In addition, spot welding such as spot welding can be performed by friction stir welding using the tool 30 for friction stir welding.

  Looking at the process of friction stir welding as described above, in particular, the probe 30P portion of the friction stir welding tool 30 is required to have both wear resistance, fracture resistance, and plastic deformation resistance. I understand. Therefore, in order to improve the hardness that affects the wear resistance and the toughness that affects the fracture resistance, the hard material of the present invention is used in at least the probe 30P portion of the friction stir welding tool 30. Needless to say, the shaft 30S may be made of the hard material of the present invention.

<Test Example 1>
Prepare a WC powder with an average particle size of 3 μm as the core powder, put the powder in a stainless steel container and evacuate it, then flow the Ar gas while rotating the container, and the composition is Co-20Cr- Using a target of 15W-10Ni-0.1C Co-based heat-resistant alloy (HS25 equivalent material), each particle (core) of WC powder is coated with a Co-based heat-resistant alloy (shell) with an average thickness of 0.08μm under a pressure of 3Pa. Composite powder (WC with heat-resistant shell) is obtained. The average thickness of the shell of this coating powder is about 2.7% of the average particle size of the core. The average thickness of the shell can be measured by TEM. Raw material powders such as Co, WC, TiCN, TaC, NbC, TaNbC, Cr ₃ C ₂ , and ZrC are added to the prepared composite powder having a core-shell structure and mixed so as not to break the shell of the composite powder. Specifically, the raw material powder is mixed in ethanol using ultrasonic waves without using a grinding medium, and the inventive products 1-1 to 1-8 using the core-shell structure particles and the core-shell structure particles are used. Make a mixed powder of non-comparative products 1-1 to 1-4 (see Table 1). In addition, alloy powder having an average particle diameter of 100 μm prepared by an atomizing method is used as a raw material powder of a comparative Co-based heat-resistant alloy that does not use core-shell structured particles. The mixed powder of the invention is granulated using camphor and ethanol. The comparative mixed powder is pulverized and mixed in ethanol using a ball mill for 48 hours, and the obtained mixed powder is granulated using camphor and ethanol. Each granulated mixed powder of the invention product and the comparative product is press-molded at a pressure of 1 ton / cm ² (about 98 MPa) to obtain a molded body. Thereafter, hydrogen gas of 25 Torr (about 3.3 kPa) was introduced in the temperature range from room temperature to 1200 ° C, and the compact was sintered under vacuum at a maximum temperature of 1410 ° C and held for 1 hour. obtain. Further, the sintered body was densified by holding it at 1380 ° C. for 1 hour under a pressure of 100 MPa in an argon atmosphere by using a hot isostatic press. It can be confirmed by EPMA (Electron Probe Micro Analyzer) that the composition of the sintered body almost matches the composition of the raw material powder.

  The obtained sintered body is subjected to surface grinding of the bearing surface with a # 200 diamond grindstone and then subjected to cutting edge processing to obtain a base material having a shape of SNMG120408 (the flank and rake face are not ground). Furthermore, the surface of this base material was coated with an AlTiSiN film (hard coating) with an average thickness of 5 μm by a known PVD method to obtain a cutting tool.

  Using this tool, turning test was performed on SCM435 work material at a cutting speed of 300m / min, a feed rate of 0.3mm / rev, a cutting depth of 1.5mm, and a wet condition for 5 minutes to measure the average flank wear of the tool. And wear resistance test.

  Also, using a tool with the same shape, a cutting test was performed on a SK5 workpiece under the conditions of a cutting speed of 180 m / min, a feed rate of 0.35 mm / rev, a cutting depth of 1.5 mm, and a dry type, and the plastic deformation amount of the tool (mm ) To measure the plastic deformation resistance.

  Furthermore, using a tool with the same shape, a turning test was performed on a SCM435 slit workpiece with a cutting speed of 150 m / min, a feed rate of 0.4 mm / rev, a cutting depth of 2 mm, and wet conditions, and four corners were cut. Investigate the breakage rate of corners and conduct a fracture resistance test.

  The results of the three tests are shown in Table 2. From Table 2, invention products 1-1 to 1-8 having a core-shell structure hard phase with a core of WC and a shell of Co-based heat-resistant alloy are comparative products 1-1 to 1-4 having no core-shell structure hard phase. It can be seen that it has excellent wear resistance and plastic deformation resistance as compared with. Inventive products 1-2 to 1-4 and 1-6, which contain WC as the second hard phase in addition to the first hard phase, are particularly excellent in fracture resistance. Inventions 1-6 containing TiCN are particularly excellent in wear resistance.

<Test Example 2>
In the same manner as in Test Example 1, a composite powder having a core-shell structure in which the average particle diameter of the core powder and the average thickness of the shell are different is prepared. The composition of the shell is Co-20Cr-15W-10Ni-0.1C Co-based heat-resistant alloy (HS25 equivalent material) by mass%. Table 3 shows the average particle diameter (d) of the core of the composite powder, the average thickness (t) of the shell, and the ratio of the thickness t to the average particle diameter d (thickness / diameter). A mixed powder was prepared in the same manner as in Test Example 1 so that these composite powders had a composition of 87.85% by mass, WC 10% by mass, Cr ₃ C ₂ 0.15% by mass, and Co 2% by mass. Similarly, press molding, sintering, and machining are performed to produce the base material 31 of the friction stir tool. As shown in FIG. 3, the base member has a substantially cylindrical shaft portion 30S, and a substantially cylindrical probe 30P projecting concentrically with the shaft portion 30S at the center of the tip of the shaft portion 30S. . The shaft portion has a diameter of 10 mm and a height of 20 mm, and the probe 30P has a diameter of 4 mm and a height of 0.7 mm. Further, in the same manner as in Test Example 1, the base material 31 is coated with an AlTiSiN film (hard coating 32) with a PVD method to an average thickness of 5 μm to form a friction stir welding tool, and a fracture resistance test and a plastic deformation resistance test are performed. Do. The test is a 980 MPa class ultra-high strength steel with a thickness of 2 mm as a steel plate, and the point joining conditions are a rotation speed of 1000 rpm, a push load of 1.3 tons, and a push time of 3 seconds. The fracture resistance test is evaluated by the life until failure, and the plastic deformation resistance test is evaluated by the decrease in probe length at the 250-point machining point. Perform measurement every 50 points.

  The results are shown in Table 4. From the results in Table 4, invention products 2-1, 2-2, 2-3, 2-4, 2-6, and 2-7, whose average shell thickness is less than 3% of the average particle diameter of the core, are plastic resistant. Deformability is better than Invention 2-5. Furthermore, invention products 2-2 to 2-6 having an average particle diameter of the core in the range of 1 to 5 μm are invention products 2-1 having an average particle diameter of the core of 0.5 μm, and an average particle diameter of the core of 7.5 μm. The balance between fracture resistance and plastic deformation resistance is superior to the inventive products 2-7.

<Test Example 3>
As shown in Table 5, invention products 3-1, 3-2, 3-4 and comparative product 3-1, which differ only in the composition and thickness of the shell under the same production conditions as invention product 1-1 of test example 1, 3-2, and the composition of the shell is the same as that of Invention Product 1-1, but an Invention Product 3-3 having a shell thickness different from that of Invention Product 1-1 is produced. Particles having different shell compositions can be obtained by changing the composition of the target used when coating the shell. Inventive products 3-1 to 3-4 used Co-base heat-resistant alloy targets, and Comparative products 3-1 and 3-2 used alloy targets that were not heat-resistant alloys. Invention 3-1 is MP35N equivalent material, Invention 3-2 is HS152 equivalent material, Invention 3-3 is HS25 equivalent material, and Invention 3-4 is S816 equivalent material. For these friction stir welding tools 3-1 to 3-4 and comparative products 3-1 and 3-2, a fracture resistance test and a plastic deformation resistance test are performed in the same manner as in Test Example 2. .

  The results are shown in Table 6. From the results of Table 6, it can be seen that Inventions 3-2 to 3-4 containing W in the shell have better fracture resistance and plastic deformation resistance than Invention 3-1 containing no W in the shell. .

  The embodiments and test examples disclosed this time should be considered as illustrative in all points and not restrictive. The scope of the present invention is defined by the terms of the claims, rather than the description above, and is intended to include any modifications within the scope and meaning equivalent to the terms of the claims.

  Since the hard material of the present invention has high fracture resistance as well as wear resistance and plastic deformation resistance, it is expected to be used in applications that require higher heat resistance than conventional cemented carbide. In particular, since this hard material is excellent in plastic deformation resistance, it can be suitably used as a cutting tool for high-speed machining of steel or as a tool for friction stir welding of steel. Furthermore, the manufacturing method of the hard material of this invention can be utilized for the manufacturing field etc. of the tool for cutting tools and a friction stir welding.

10 Hard phase 10A First hard phase particle 10B Second hard phase particle
11 core 12 shell
20 bonded phase
30 Friction stir welding tool 30S Shaft 30P Probe
31 Base material 32 Hard coating
110 Base material 120 Hard coating

Claims (13)

A hard material mainly composed of a hard phase,
The hard phase contains a first hard phase;
The first hard phase,
A core made of WC;
Co is the main component, Cr: 2-30 mass% is essential, Ni: 2-35 mass%, W: 3-45 mass%, Fe: 1-20 mass%, Mo: 4-10 mass%, Nb A hard material comprising: a Co-based heat-resistant alloy containing at least one of C: 0.1 to 1.0% by mass and C: 0.1 to 1.0% by mass, and a shell covering the core.   Furthermore, the hard material of Claim 1 containing the binder phase containing an iron group metal. Furthermore, the hard phase contains a second hard phase,
Wherein the second hard phase consists of a compound of at least one element of at least one metal element and C and N are selected from the Periodic Table 4,5,6 group elements,
Hard material as claimed in claim 1 or claim 2 content of the second hard phase is 5 to 70 wt% with respect to the entire hard material.   The hard material according to claim 2, wherein the content of the binder phase is 3% by mass or less. The hard material according to any one of claims 1 to 4, wherein an average particle size of the core is 1 µm or more and 5 µm or less. The hard material according to claim 1, wherein an average thickness of the shell is less than 3% of an average particle diameter of the core. A method for producing a hard material for producing a hard material containing a hard phase,
Preparing a raw material powder of the first hard phase as the hard phase ;
A mixing step of mixing the raw material powder to obtain a mixed powder;
A molding step of compressing the mixed powder at a predetermined pressure to obtain a molded body;
A sintering step of sintering the molded body at a predetermined temperature,
The first hard phase that put on the preparation process, and a core consisting WC, the main component Co, Cr: the essential 2 to 30 mass%, Ni: 2 to 35 wt%, W: 3 to 45 wt% , Fe: 1 to 20 wt%, Mo: 4 to 10 mass%, Nb: 2 to 4 mass%, and C: is composed of Co-base heat-resistant alloy containing at least one 0.1 to 1.0 wt% And a shell formed on the outer periphery of the core ,
The said mixing process is a manufacturing method of the hard material which mixes the said raw material powder, without using a grinding medium. In the preparation step, a raw material powder of a second hard phase is also prepared as the hard phase, and the second hard phase is composed of at least one metal element selected from Group 4, 5, and 6 elements of the periodic table and C and N. Consisting of a compound with at least one element,
  The said mixing process is a manufacturing method of the hard material of Claim 7 which mixes the raw material powder of a 1st hard phase, and the raw material powder of a 2nd hard phase. In the preparation step, a raw material powder of a binder phase further containing an iron group metal is prepared,
The mixing step method for producing a rigid material according to claim 7 or claim 8 for mixing the raw material powder of the binder phase and material powders of the hard phase. The said shell is a manufacturing method of the hard material as described in any one of Claims 7-9 formed in the outer periphery of the said core by the physical vapor deposition method in the said preparation process . The physical vapor deposition method is a sputtering method,
The method for producing a hard material according to claim 10 , wherein a Co-base heat-resistant alloy is used as a target of this method. A cutting tool used for high-speed processing of steel,
The cutting tool which at least one part consists of the hard material as described in any one of Claims 1-6. A friction stir welding tool used for joining steel,
A friction stir welding tool comprising at least a part of the hard material according to any one of claims 1 to 6.

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