WO2014126178A1 - 切削工具 - Google Patents
切削工具 Download PDFInfo
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- WO2014126178A1 WO2014126178A1 PCT/JP2014/053388 JP2014053388W WO2014126178A1 WO 2014126178 A1 WO2014126178 A1 WO 2014126178A1 JP 2014053388 W JP2014053388 W JP 2014053388W WO 2014126178 A1 WO2014126178 A1 WO 2014126178A1
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- silicon nitride
- melilite
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- B—PERFORMING OPERATIONS; TRANSPORTING
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- B23B—TURNING; BORING
- B23B27/00—Tools for turning or boring machines; Tools of a similar kind in general; Accessories therefor
- B23B27/14—Cutting tools of which the bits or tips or cutting inserts are of special material
- B23B27/148—Composition of the cutting inserts
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- C04B35/58—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides
- C04B35/584—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides based on silicon nitride
- C04B35/593—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides based on silicon nitride obtained by pressure sintering
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- B23B—TURNING; BORING
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- B23B—TURNING; BORING
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- B23B—TURNING; BORING
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Definitions
- the present invention relates to a cutting tool made of a silicon nitride sintered body.
- a silicon nitride-based sintered body containing either silicon nitride or sialon as a main component is lightweight and excellent in wear resistance, strength and high-temperature strength, and can be used under severe cutting conditions. Therefore, it is suitably used for high-speed rough cutting and the like.
- Patent Document 1 discloses a silicon nitride-based sintered body having an absolute value of residual stress of 42 to 55 MPa, and an absolute value of residual stress of 45 MPa or less. By doing so, it is described that high strength at room temperature and high temperature can be achieved.
- Patent Document 2 after grinding the surface of the silicon nitride-based sintered body, the compressive stress is increased on the surface of the sintered body by heat treatment in the atmosphere, and the strength reduced by the grinding process is recovered. It is disclosed that it can be achieved.
- the residual stress at the nose of the rake face is parallel to the rake face and the residual stress ⁇ 11 in the direction from the center of the rake face to the nose closest to the measurement point is 10 to 10 as compressive stress.
- an object of the present invention is to provide a cutting tool made of a silicon nitride-based sintered body having high fracture resistance, with the residual stresses on the rake face and flank face being in an appropriate range.
- the cutting tool of the present invention has a rake face, a flank face, and a cutting edge that is an intersecting ridge line portion of the rake face and the flank face, and has a silicon nitride phase of 50 volume% or more and a titanium nitride phase.
- the residual stress applied to the titanium nitride phase is tensile stress
- the tensile stress applied to the titanium nitride phase on the rake face is The tensile stress applied to the titanium nitride phase on the flank is larger.
- flank face when the tensile stress of the titanium nitride phase is smaller than that of the rake face, the progress of wear on the flank face is suppressed in cutting heat-resistant alloys such as Inconel, thereby extending the tool life. .
- the cutting tool 1 of this embodiment is composed of a silicon nitride-based sintered body containing a silicon nitride-based phase in a proportion of 50% by volume or more and a titanium nitride phase in a proportion of 10-30% by volume. As shown in the schematic perspective view of FIG. 1, the cutting tool 1 uses an intersecting ridge line portion between the rake face 2 and the flank face 3 as a cutting edge 4.
- the residual stress of the titanium nitride phase is a tensile stress
- the tensile stress of the titanium nitride phase on the rake face 2 is larger than the tensile stress of the titanium nitride phase on the flank face 3.
- the reason why the progress of wear on the flank 3 is suppressed in the cutting of the heat-resistant alloy such as Inconel is not clear.
- the residual stress on the flank 3 increases, the residual stress on the rake face 2 also increases. Therefore, the residual stress applied to the cutting edge 4 becomes too large, and the cutting tool 1 is produced. It is thought that the cause is that minute chipping is sometimes generated in the cutting edge 4 due to self-destruction.
- a measurement position is measured in the 1 mm or more inside (center side) position from the cutting edge 4 of the rake face 2 and the flank 3.
- the residual stress is measured using an X-ray diffraction method.
- the measurement is performed using the 2D method (multiaxial stress measurement method / full Debye fitting method), but a general X-ray diffraction apparatus may be used.
- the X-ray diffraction peak used for measurement of residual stress is a TiN (511) plane peak that appears when the value of 2 ⁇ is between 130 ° and 140 °.
- the residual stress is positive, it becomes tensile stress, and when it is negative, it becomes compressive stress.
- the residual stress applied to the titanium nitride phase of the rake face 2 is 200 to 400 MPa, preferably 250 to 350 MPa in terms of tensile stress, and the residual stress applied to the titanium nitride phase of the flank 3 is 100 to 100% of tensile stress. It is 300 MPa, preferably in the range of 150 to 250 MPa.
- the difference in tensile stress between the rake face 2 and the flank face 3 of the titanium nitride phase is in the range of 20 to 150 MPa, preferably 50 to 100 MPa.
- the peak intensity ratio of the (111) plane peak to the total titanium nitride peak of the titanium nitride phase on the surface is the total titanium nitride of the titanium nitride phase inside. It is desirable to make it larger than the peak intensity ratio of the (111) plane peak to the peak.
- the ratio of the peak intensity of the (111) plane peak to the total titanium nitride peak of the titanium nitride phase on the surface is the ratio of the peak intensity ratio of the (111) plane peak to the total titanium nitride peak of the titanium nitride phase inside. Is in the range of 1.1 to 1.4.
- the inside of the sintered body has a high toughness and strength structure, and suppresses sudden defects and stable cutting performance. It can be set as the cutting tool which exhibits.
- the inside in the present invention is defined as a depth region of 1000 ⁇ m or more from the surface of the sintered body.
- the arithmetic average roughness (Ra) on the rake face 2 of the cutting tool 1 is 0.2 to 0.6 ⁇ m.
- the overall composition of the sintered body is 50% by volume or more of the silicon nitride phase, 10 to 30% by volume of the titanium nitride phase, preferably 15 to 25% by volume, and the balance is the grain boundary phase.
- the grain boundary phase includes silica (SiO 2 ) in which a silicon nitride-based phase is decomposed, an aluminum compound such as aluminum oxide powder or aluminum oxide (Al 2 O 3 ) in which the aluminum nitride powder is changed as a raw material, and an RE element compound It contains RE element compounds such as RE element oxides in which the powder has changed.
- the grain boundary phase exists as an amorphous phase, a part thereof may be crystallized.
- the phases other than the silicon nitride phase and the titanium nitride phase are regarded as grain boundary phases.
- the RE element in the present invention refers to yttrium (Y) and rare earth metals.
- the content of the RE element component in this embodiment is added so as to be 0.5 to 10% by mass in terms of RE 2 O 3 with respect to the entire sintered body for densification of the sintered body.
- a desirable range of the content of the RE element component is 1 to 8% by mass.
- the content of the aluminum component in this embodiment is Al 2 in order to suppress a decrease in wear resistance due to a decrease in the liquid phase generation temperature of the sintering aid, a densification of the sintered body, and a decrease in oxidation resistance. It is 0 to 15% by mass in terms of O 3 , and a particularly desirable range is 3 to 10% by mass.
- the RE element component is yttrium, yttrium and aluminum are divided into a part that exists at the grain boundary as a glass phase, a part that constitutes a melilite phase, a part that constitutes a YAG phase, and a part that constitutes sialon.
- Titanium nitride is present as a dispersed phase in a proportion of 10 to 45% by mass, particularly 10 to 30% by mass in terms of TiN, based on the entire sintered body, and enhances the toughness of the sintered body.
- the silicon nitride phase exists as a main crystal, specifically, it exists mainly as a ⁇ -sialon phase or as a ⁇ -silicon nitride phase.
- the Z value of the ⁇ -sialon phase (value representing the amount of Al and O elements present in the ⁇ -sialon phase: when the sialon phase is represented by Si 6-Z Al Z O Z N Z value) is in the range of 0.01 to 0.3.
- a heat-resistant alloy such as Inconel 718.
- a part of the ⁇ -silicon nitride phase may be an ⁇ -silicon nitride phase
- a part of the ⁇ -sialon phase may be an ⁇ -sialon phase.
- the ratio of the ⁇ -silicon nitride phase to the entire silicon nitride phase ( ⁇ ratio) is in the range of 0 to 0.3.
- the peak intensity ratio of the silicon nitride-based phase to the entire peak on the surface is set to the peak intensity ratio of the silicon nitride-based phase relative to all the internal peaks. It is made smaller than the peak intensity ratio of the peak.
- the peak intensity ratio of the silicon nitride phase peak to the total peak on the surface is in the range of 0.05 to 0.5 as a ratio to the peak intensity ratio of the silicon nitride phase peak to the total internal peak. .
- the peak intensity of all peaks on the surface is the sum of the peak intensities of all peaks detected by the X-ray diffraction pattern measured on the surface of the silicon nitride sintered body, and the silicon nitride phase on the surface
- the peak intensity of the peak is the sum of the peak intensities of all the peaks of the silicon nitride phase detected by the X-ray diffraction pattern measured on the surface.
- the peak intensity of all the peaks inside is the sum of the peak intensities of all peaks detected by the X-ray diffraction pattern measured inside the silicon nitride sintered body, and the peak peak of the silicon nitride phase inside.
- the intensity is the sum of the peak intensities of all the peaks of the silicon nitride phase detected by the X-ray diffraction pattern measured inside.
- the peak intensity ratio of the peak of the melilite phase relative to all the peaks on the surface is larger than the peak intensity ratio of the peak of the melilite phase relative to all the peaks inside.
- the peak intensity ratio of the peak of the melilite phase with respect to all the peaks on the surface is within a range of 3.0 to 6.0 as a ratio to the peak intensity ratio of the peak of the melilite phase with respect to all the peaks inside.
- the peak intensity of the peak of the melilite phase on the surface is the sum of the peak intensities of all the peaks of the melilite phase detected by the X-ray diffraction pattern measured on the surface of the silicon nitride-based sintered body.
- the peak intensity of the peak of the melilite phase inside is the sum of the peak intensity of all the peaks of the melilite phase detected by the X-ray diffraction pattern measured inside the silicon nitride sintered body.
- the peak intensity ratio of the (201) plane peak to the total melilite peak of the melilite phase on the surface is made larger than the peak intensity ratio of the (201) plane peak to the total melilite peak of the inner melilite phase.
- the peak intensity ratio of the (201) plane peak to the total melilite peak of the melilite phase on the surface is 1. It is within the range of 1 to 2.0.
- the peak intensity ratio of the peak of the (201) plane with respect to the total melilite peak of the melilite phase on the surface is the peak intensity ratio of the melilite phase relative to the sum of the peak intensity of the melilite phase, which is the peak intensity of the melilite phase on the surface.
- the 201) is the ratio of the peak intensity of the surface peak.
- the peak intensity ratio of the peak of the (201) plane to the total melilite peak of the melilite phase inside is the (201) plane of the melilite phase relative to the sum of the peak intensity of the peak of the melilite phase which is the peak intensity of the melilite phase inside. It is the ratio of the peak intensity of the peak.
- the temperature of the cutting blade provided on the surface of the sintered body becomes high as in the high-speed wet rough cutting process condition, and the inside of the sintered body Under cutting conditions where the temperature is not so high, tool damage such as crater wear and flaking on the cutting edge and abnormal wear from minute chipping is suppressed. Moreover, the fracture resistance inside the sintered body is also improved.
- the silicon nitride-based sintered body contains a YAG (3Y 2 O 3 ⁇ 5Al 2 O 3 ) phase as a grain boundary phase, and the peak intensity ratio of the peak of the (420) plane of the YAG phase to the entire peak on the surface.
- the ratio of the peak of the YAG phase to the peak intensity ratio with respect to all the peaks inside is 0.8 to 1.1, particularly 0.85 to 0.97.
- the hardness of the sintered body at high temperature can be improved, and the difference in thermal expansion between the surface and the inside can be reduced to improve the fracture resistance of the sintered body.
- the peak intensity ratio of the peak on the (420) plane of the YAG phase with respect to all the peaks inside is 0.010 to 0.0150.
- a periodic table group 6 element silicide can be contained in a sintered compact.
- a decrease in high-temperature strength can be suppressed, and the color of the sintered body can be blackened.
- Examples of periodic table group 6 element silicides include chromium silicide, molybdenum silicide, and tungsten silicide.
- tungsten silicide is used because it can be present as fine particles in a sintered body using a fine oxide raw material. It is desirable to use The periodic table Group 6 element silicide particles exist as a dispersed phase in the silicon nitride sintered body.
- the cutting tool 1 may be provided with a hard coating layer such as TiN, Al 2 O 3 , or TiAlN on the surface of the sintered body.
- silicon nitride (AlN) and titanium nitride (TiN) are prepared.
- silicon nitride raw material either ⁇ -silicon nitride powder, ⁇ -silicon nitride powder, or a mixture thereof can be used.
- the average particle diameter of these silicon nitride raw materials is preferably 1 ⁇ m or less, particularly preferably 0.5 ⁇ m or less.
- an oxide powder having an average particle size of 0.5 to 5 ⁇ m is used as a raw material for the RE element.
- Titanium nitride (TiN) is a powder having an average particle size of 0.5 to 5 ⁇ m.
- the amount of RE element oxide added is 0.5 to 10% by volume, preferably 1 to 8% by volume, in terms of RE 2 O 3 . This promotes densification of the sintered body.
- the amount of aluminum nitride added is 0 to 10% by mass, especially 3 to 8% by mass in terms of AlN.
- the amount of aluminum oxide added is 0 to 10% by mass, particularly 1 to 5% by mass in terms of Al 2 O 3 .
- the raw material for forming the periodic table group 6 element silicide may be any of the oxides, carbides, silicides, nitrides, etc. of the periodic table group 6 element, but it is oxidized because it is inexpensive and easily obtains a fine powder. It is desirable to use a product.
- raw materials such as aluminum nitride, aluminum oxide, Group 6 element oxide, carbide, silicide, and nitride, powder having an average particle size of 0.5 to 5 ⁇ m is used.
- magnesium oxide may be added in the range of 0 to 10% by mass and silica (SiO 2 ) in the range of 0 to 10% by mass.
- silica SiO 2
- any raw material powder such as an oxide, carbide, silicide, or nitride of a periodic table group 6 element can be added. It is desirable to use an oxide because it is inexpensive and easily obtains a fine powder. These raw materials are powders having an average particle size of 0.5 to 5 ⁇ m.
- a binder and a solvent are appropriately added to the mixed powder obtained by weighing these raw materials, mixed and pulverized, and dried and granulated by a spray drying method or the like. Then, this granulated powder is formed into a predetermined cutting tool shape by press molding.
- molding it is important to change the molding density on the main surface of the molded body that becomes the rake face and the side surface of the molded body that becomes the flank surface.
- a method for changing the molding density on the main surface and the side surface of the molded body it is possible to increase the moving speed of the upper and lower punches of the mold during press molding and shorten the time for applying the load.
- Other methods of changing the molding density on the main and side surfaces of the molded body include adjusting the particle size and hardness of the granules used during molding, the ease of flow of the granules, the hardness of the binder, the amount of binder added, etc. Is also possible.
- the mass ratio of MnO 2 powder and Si 3 N 4 powder is 1: 5 to 1:50 in the firing pot.
- the paste containing the mixed powder mixed in the ratio can be applied and dried in a dried state.
- the MnO 2 powder adheres to the surface of the compact and acts as a catalyst to advance the firing of the surface of the sintered body.
- the surface and the inside of the sintered body are in different states, and the surface state of the sintered body can be adjusted to a predetermined range.
- MnO 2 adheres to the surface of the sintered body and acts as a catalyst to advance the firing of the surface of the sintered body.
- the surface and the inside of the sintered body are in different states, and the surface state of the sintered body can be adjusted to a predetermined range.
- the MnO 2 powder volatilizes from the surface of the sintered body during firing and does not remain in the sintered body after firing.
- firing is performed under the following conditions.
- the specific conditions for firing are as follows.
- the molded body is put in a firing furnace, and the inside of the firing furnace is made into a nitrogen atmosphere of 101 Pa to 1011 Pa (1 to 10 atm), and then the temperature is raised at 1 to 10 ° C./minute to 1650. Hold at a firing temperature of ⁇ 1800 ° C. for 1-5 hours.
- the holding temperature is held for 1 to 4 hours, and then the room temperature is raised to 10 to 50 ° C. Cool at a second rate of temperature decrease per minute.
- the thermal expansion coefficient of silicon nitride (the linear thermal expansion coefficient from room temperature to 1420 ° C. is 3.5 ⁇ 10 ⁇ 6 ) by holding at 1250 to 1600 ° C. in the cooling process after the firing, and Thermal expansion coefficient of sialon (linear thermal expansion coefficient from room temperature to 1000 ° C. is 3.2 ⁇ 10 ⁇ 6 ) and thermal expansion coefficient of titanium nitride (linear thermal expansion coefficient from room temperature to 1000 ° C. is 9.4 ⁇ 10 Due to the difference from ⁇ 6 ), volume expansion occurs between silicon nitride and sialon and titanium nitride.
- the volume expansion of silicon nitride, sialon, and titanium nitride on the rake face and flank face is also different.
- the residual stress of silicon nitride, sialon, and titanium nitride on the rake face and the flank face is set to a predetermined level by cooling from the holding temperature to room temperature at a temperature lowering rate of 10 to 50 ° C./min. It can be a range. Further, the temperature is lowered at a rate of 1 to 10 ° C./min from the firing temperature to the range of 1450 to 1600 ° C.
- the surface melilite phase is within the holding time. It can be crystallized with an orientation within the range. At this time, the titanium nitride phase is also oriented in a specific direction as the melilite phase is generated.
- the above-mentioned sintered body is subjected to grinding.
- the rake face is processed by double-head grinding, and the flank face is processed by outer peripheral grinding.
- the cutting blade is polished using an elastic grindstone or wheel brush polishing, and the cutting blade is provided with chamfer honing or R-plane honing.
- a hard coating layer such as TiN, Al 2 O 3 , or TiAlN may be formed on the surface of the sintered body by a vapor phase synthesis method such as CVD or PVD.
- TiN powder having an average particle diameter of 2.5 ⁇ m in the ratio of Table 1 After preparing powder, aluminum nitride (AlN) powder having an average particle diameter of 0.7 ⁇ m, and titanium nitride (TiN) powder having an average particle diameter of 2.5 ⁇ m in the ratio of Table 1, and adding a binder and a solvent Then, it was pulverized and mixed in an attritor mill for 72 hours.
- the molded body was set in a firing pot, and after degreasing, the inside of the firing furnace was set to nitrogen 911 Pa (9 atm) and sintered under the firing conditions shown in Table 1 to obtain a sintered body.
- the firing temperature was maintained for 2 hours.
- the first temperature drop rate from the firing temperature to the holding temperature of 1250 to 1600 ° C. is the temperature drop rate 1
- the holding time at the holding temperature is the holding time
- the second temperature falling rate from the holding temperature to the room temperature is lowered.
- the speed was described as 2.
- the surface of the sintered body is subjected to double-head grinding for the rake face, outer peripheral grinding for the flank face, and chamfer honing process so that the cutting edge has a shape of 0.10 mm ⁇ 20 ° using an elastic grindstone. A cutting tool was obtained.
- the rake face and the flank face are mirrored, and then the 2D method (apparatus: X-ray diffraction D8 DISCOVER with GADDS Super Speed manufactured by BrukerAXS, radiation source: CuK ⁇ , output 45 kV,
- the residual stress of titanium nitride on the rake face and flank face was measured using 110 mA, detector distance 15 cm, collimator diameter: 0.8 mm ⁇ , and measurement diffraction line: 140 ° (TiN (511) face).
- the polished cross-sectional structure of the sintered body is observed using a scanning electron microscope (SEM), and element mapping of Si and Ti elements is performed by energy dispersive spectroscopy (EPMA) analysis, and a silicon nitride phase and a titanium nitride phase are obtained. Identified. Then, from the Luzex image analysis method, the abundance ratio between the silicon nitride phase and the titanium nitride phase was determined as area%, and this was determined as volume%. The results are as shown in Table 2.
- cutting performance was evaluated under the following conditions using the obtained cutting tool having the RNGN 1204 shape.
- Machining method Turning work material: Inconel 718 50 ⁇ round bar
- Cutting speed 200 m / min
- Feed amount 0.15 mm / rev
- Cutting depth 1.0mm
- wet cutting evaluation item The amount of boundary wear after cutting for 5 minutes was measured and the state of the cutting edge was observed. The results are shown in Table 2.
- Si 3 N 4 silicon nitride
- Al 2 O 3 aluminum oxide
- AlN aluminum nitride
- Example 1 The raw density ratio of Example 1 was 1.035. Then, Si 3 N 4 powder having an average particle diameter of 3 ⁇ m and MnO 2 powder having an average particle diameter of 3 ⁇ m are mixed at a ratio of 1:20, and an Mn paste is prepared by adding an organic resin thereto. Then, the Mn paste was applied to the surface of the molded body and dried. Table 3 shows the presence / absence of application of Mn paste.
- the molded body was set in a firing pot, and after degreasing, the inside of the firing furnace was set to nitrogen 909 kPa (9 atm) and fired at the firing temperature and firing time shown in Table 3. From the firing temperature, 1450 to 1600 ° C. The temperature lowering rate to the holding temperature of 5 ° C./min was held at the holding temperature and holding time shown in Table 3, and the temperature lowering rate from the holding temperature to room temperature was lowered at 50 ° C./min to obtain a sintered body. .
- the surface of the sintered body is subjected to double-head grinding for the rake face, outer peripheral grinding for the flank face, and chamfer honing process so that the cutting edge has a shape of 0.10 mm ⁇ 20 ° using an elastic grindstone. And sample no. 20 to 36 cutting tools were obtained.
- the X-ray diffraction measurement was performed to measure the X-ray diffraction peaks in the unpolished state (surface) of the rake face and the polished state (inside) of 1000 ⁇ m.
- Intensity ratio between the sum of the peaks and the peak of the silicon nitride phase, the peak intensity ratio between the sum of all measured peaks and the peak of the melilite phase, the sum of all peaks showing the melilite phase and the melilite phase The peak intensity ratio with the peak indicating the (201) plane, and the peak intensity ratio between the total sum of all measured peaks and the peak sum indicating the YAG phase were determined.
- Their surface / internal ratio was determined. In the table, it was described as a ratio. The results are shown in Tables 4 and 5. Note that it was confirmed by scanning electron microscope (SEM) that the silicon nitride phase was present in 50% by volume or more in any sample.
- Example 2 the residual stress of titanium nitride on the rake face and flank face was measured. Furthermore, the cutting performance was evaluated under the following conditions using the obtained SNGN120212-shaped cutting tool. The results are shown in Table 6. Machining method: Turning work material: Inconel 718 200 ⁇ round bar Cutting speed: 400 m / min Feed amount: 0.10 mm / rev Cutting depth: 1.0mm Cutting conditions: Wet cutting evaluation items: The cutting time when the amount of wear was 0.3 mm was measured to determine the tool life. Moreover, the state of the cutting edge at the time of reaching the tool life was observed.
- the titanium nitride phase is contained at a ratio of 10 to 30% by volume, and the tensile stress applied to the titanium nitride phase on the rake face is the tensile stress applied to the titanium nitride phase on the flank face.
- Sample No. larger than In Nos. 20 to 33 the cutting blade was hardly damaged, and the cutting tool was stable and had a long life.
- 34 to 36 the cutting blade was damaged early, and the wear progressed from there, resulting in a short tool life.
Abstract
Description
まず、出発原料として、例えば、窒化珪素(Si3N4)粉末と、RE元素の水酸化物(RE(OH)2)または酸化物(RE2O3)、酸化アルミニウム(Al2O3)、窒化アルミニウム(AlN)、窒化チタン(TiN)を準備する。
加工方法:旋削加工
被削材:インコネル718 50φ丸棒
切削速度:200m/分
送り量:0.15mm/rev
切り込み量:1.0mm
切削条件:湿式切削
評価項目:5分切削後の境界摩耗量を測定するとともに刃先状態を観察した。
結果は表2に示した。
加工方法:旋削加工
被削材:インコネル718 200φ丸棒
切削速度:400m/分
送り量:0.10mm/rev
切り込み量:1.0mm
切削条件:湿式切削
評価項目:摩耗量が0.3mmとなった切削時間を測定して工具寿命とした。また、工具寿命となった時点での切刃の状態を観察した。
2 すくい面
3 逃げ面
4 切刃
Claims (9)
- すくい面と、逃げ面と、前記すくい面と前記逃げ面との交差稜線部である切刃とを有し、窒化珪素系相を50体積%以上、窒化チタン相を10~30体積%の割合で含有する窒化珪素系焼結体からなり、前記窒化チタン相にかかる残留応力が引張応力であり、かつ前記すくい面における前記窒化チタン相にかかる引張応力が、前記逃げ面における前記窒化チタン相にかかる引張応力よりも大きい切削工具。
- 前記窒化珪素系焼結体が、さらにメリライト(Y2Si3O3N4)相を含み、前記窒化珪素系焼結体のX線回折測定において、表面における全ピークに対する前記窒化珪素系相のピークのピーク強度比が、内部における全ピークに対する前記窒化珪素系相のピークのピーク強度比よりも小さく、前記表面における全ピークに対する前記メリライト相のピークのピーク強度比が、前記内部における全ピークに対する前記メリライト相のピークのピーク強度比よりも大きく、かつ前記表面における前記メリライト相の全メリライトピークに対する(201)面のピークのピーク強度比が前記内部における前記メリライト相の前記全メリライトピークに対する(201)面のピークのピーク強度比よりも大きい請求項1に記載の切削工具。
- 前記表面における全ピークに対する窒化珪素系相のピークのピーク強度比が、前記内部における全ピークに対する窒化珪素系相のピークのピーク強度比に対する比率で0.05~0.5の範囲内である請求項2に記載の切削工具。
- 前記表面における全ピークに対するメリライト相のピークのピーク強度比が、前記内部における全ピークに対するメリライト相のピークのピーク強度比に対する比率で3.0~6.0の範囲内である請求項2または3に記載の切削工具。
- 前記表面におけるメリライト相の全メリライトピークに対する(201)面のピークのピーク強度比が、前記内部におけるメリライト相の全メリライトピークに対する(201)面のピークのピーク強度比に対する比率で1.1~2.0の範囲である請求項2乃至4のいずれかに記載の切削工具。
- 前記表面における前記窒化チタン相の全窒化チタンピークに対する(111)面のピークのピーク強度比が、前記内部における前記窒化チタン相の全窒化チタンピークに対する(111)面のピークのピーク強度比よりも大きい請求項2乃至5のいずれかに記載の切削工具。
- 前記表面における窒化チタン相の全窒化チタンピークに対する(111)面のピークのピーク強度比が、前記内部における窒化チタン相の全窒化チタンピークに対する(111)面のピークのピーク強度比に対する比率で1.1~1.4の範囲内である請求項6に記載の切削工具。
- さらに、窒化珪素系焼結体は、YAG(3Y2O3・5Al2O3)相を含有するとともに、前記表面における全ピークに対する前記YAG相の(420)面のピークのピーク強度比が、前記内部における全ピークに対する前記YAG相の(420)面のピークのピーク強度比に対する比率で0.9~1.1である請求項2乃至7のいずれかに記載の切削工具。
- 前記窒化珪素系焼結体の表面に、さらに硬質被覆層が設けられている請求項1乃至8のいずれかに記載の切削工具。
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US14/766,915 US10086437B2 (en) | 2013-02-13 | 2014-02-13 | Cutting tool |
CN201480007415.XA CN105073310B (zh) | 2013-02-13 | 2014-02-13 | 切削工具 |
EP14751959.9A EP2957368B1 (en) | 2013-02-13 | 2014-02-13 | Cutting tool |
JP2014531795A JP5677638B1 (ja) | 2013-02-13 | 2014-02-13 | 切削工具 |
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WO2021124690A1 (ja) * | 2019-12-20 | 2021-06-24 | 日本特殊陶業株式会社 | 切削工具 |
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Also Published As
Publication number | Publication date |
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US20150367421A1 (en) | 2015-12-24 |
JPWO2014126178A1 (ja) | 2017-02-02 |
CN105073310B (zh) | 2017-03-08 |
CN105073310A (zh) | 2015-11-18 |
JP5677638B1 (ja) | 2015-02-25 |
EP2957368B1 (en) | 2020-04-22 |
EP2957368A1 (en) | 2015-12-23 |
EP2957368A4 (en) | 2016-10-19 |
US10086437B2 (en) | 2018-10-02 |
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