Patent Application
20170297118
The present invention relates to a sintered material, a cutting tool using the sintered material, and a method of producing the sintered material.
As a material of a cutting tool used for cutting or the like, an aluminum oxide (Al2O3) sintered material has been known. Such an aluminum oxide sintered material is excellent in that it has low reactivity with an iron-based workpiece and can be produced inexpensively; however, the aluminum oxide sintered material tends to have a low toughness. Accordingly, the aluminum oxide sintered material tends to be likely damaged when used as a cutting tool. Furthermore, since reactivity between aluminum oxide and a metallic compound to serve as a binder is low, it is difficult to employ, as the binder, a nitride, carbonitride, or the like of each of metals of group 4A, group 5A, and group 6A in the periodic table.
To address this, as a ceramic sintered material having high hardness and toughness, Patent Document 1 (Japanese Patent Laying-Open No. 2013-216517) discloses a ceramic sintered material including: a cubic aluminum nitride; and at least one metallic compound selected from a group consisting of nitrides, carbides, oxides, and borides of metals of group 4A, group 5A, and group 6A in the periodic table as well as solid solutions thereof.
PTD 1: Japanese Patent Laying-Open No. 2013-216517
However, the technique of Patent Document 1 employs a cubic aluminum nitride having a low heat resistance. Accordingly, under a high speed cutting condition in the case of cutting a centrifugal cast iron or the like, the cubic aluminum nitride in the sintered material is converted into a hexagonal aluminum nitride having a low hardness. Thus, wear resistance of the sintered material is decreased under the high speed cutting condition, disadvantageously.
In view of this, it is an object to provide: a sintered material having an excellent wear resistance even under a high speed cutting condition; a tool using the sintered material; and a method of producing the sintered material.
A sintered material according to one embodiment of the present invention is a sintered material including:
a first particle group including a particle having a cubic rock-salt structure represented by Al(1-x)CrxN (formula (1)) (where x satisfies 0.2≦x≦0.8); and
a second particle group including a particle of at least one first compound selected from a group consisting of oxide and oxynitride of aluminum, zirconium, yttrium, magnesium, and hafnium.
A cutting tool according to one embodiment of the present invention is a cutting tool using the sintered material described above.
A method of producing a sintered material according to one embodiment of the present invention is a method of producing the above-described sintered material, the method including: obtaining a first mixed particle group including a hexagonal AlN particle and a hexagonal Cr2N particle; obtaining a second mixed particle group including a cubic CrN particle by thermally treating the first mixed particle group; obtaining, by treating the second mixed particle group through an isostatic synthesis method or an impulsive compression method, a first particle group including a particle having a cubic rock-salt structure represented by Al(1-x)CrxN (formula (1)) (where x satisfies 0.2≦x≦0.8); obtaining a third mixed particle group by mixing the first particle group with a second particle group including a particle of at least one first compound selected from a group consisting of oxide and oxynitride of aluminum, zirconium, yttrium, magnesium, and hafnium; and obtaining a sintered material by sintering the third mixed particle group.
A method of producing a sintered material according to one embodiment of the present invention is a method of producing the above-described sintered material, the method including: preparing a target including aluminum and chromium as component elements; and performing vapor phase synthesis of a thin film on a substrate by treating the target through a physical vapor deposition method in an argon and nitrogen atmosphere, the thin film including a first particle group including a particle having a cubic rock-salt structure represented by Al(1-x)CrxN (formula (1)) (where x satisfies 0.2≦x≦0.8).
According to the above embodiment, there can be provided: a sintered material having an excellent wear resistance even under a high speed cutting condition; a tool using the sintered material; and a method of producing the sintered material.
First, embodiments of the present invention are listed and described.
(1) A sintered material according to one embodiment of the present invention is a sintered material including:
a first particle group including a particle having a cubic rock-salt structure represented by Al(1-x)CrxN (formula (1)) (where x satisfies 0.2≦x≦0.8); and
a second particle group including a particle of at least one first compound selected from a group consisting of oxide and oxynitride of aluminum, zirconium, yttrium, magnesium, and hafnium.
In the particle (hereinafter, also referred to as “cubic AlCrN” or “cAlCrN”) represented by the formula (1), chromium is dissolved in the solid state in cubic aluminum nitride (hereinafter, also referred to as “cubic AlN” or “cAlN”) having a low heat resistance. Heat resistance is excellent in this particle. Therefore, the sintered material using this particle can have an excellent wear resistance even under a high speed cutting condition.
(2) Preferably, x satisfies 0.3≦x≦0.7. According to this configuration, the wear resistance of the sintered material is further improved.
(3) Preferably, the sintered material includes not less than 0.5 volume % and not more than 90 volume % of the second particle group, and the first compound includes at least one selected from a group consisting of Al2O3, ZrO2, AlON, Y2O3, MgO, and HfO2. By using, as the first compound, the above-described range of amount of Al2O3, ZrO2, AlON, Y2O3, MgO, or HfO2, sinterability of the sintered material is improved, thus resulting in further improved wear resistance of the sintered material.
(4) Preferably, the sintered material further includes a third particle group including a cubic boron nitride. The cubic boron nitride is a hard particle having more excellent toughness and strength than those of the particle having the cubic rock-salt structure represented by the formula (1). Hence, when the sintered material includes such particles, the toughness of the sintered material is improved, thus resulting in improved chipping resistance.
(5) Preferably, the sintered material includes not less than 20 volume % and not more than 70 volume % of the third particle group. Accordingly, the chipping resistance of the sintered material is further improved.
(6) A tool according to one embodiment of the present invention is a cutting tool using the sintered material recited in any one of (1) to (5).
Since the sintered material is excellent in wear resistance, the tool using this sintered material is also excellent in wear resistance. Hence, the tool according to one embodiment of the present invention can have a longer life than that of the conventional tool.
(7) A method of producing a sintered material according to one embodiment of the present invention is a method of producing the sintered material recited in any one of (1) to (5), the method including: obtaining a first mixed particle group including a hexagonal AlN particle and a hexagonal Cr2N particle; obtaining a second mixed particle group including a cubic CrN particle by thermally treating the first mixed particle group; obtaining, by treating the second mixed particle group through an isostatic synthesis method or an impulsive compression method, a first particle group including a particle having a cubic rock-salt structure represented by Al(1-x)CrxN (formula (1)) (where x satisfies 0.2≦x≦0.8); obtaining a third mixed particle group by mixing the first particle group with a second particle group including a particle of at least one first compound selected from a group consisting of oxide and oxynitride of aluminum, zirconium, yttrium, magnesium, and hafnium; and obtaining a sintered material by sintering the third mixed particle group.
According to the method of producing the sintered material, the sintered material recited in any one of (1) to (5) can be obtained.
(8) A method of producing a sintered material according to one embodiment of the present invention is a method of producing the sintered material recited in any one of (1) to (5), the method including: preparing a target including aluminum and chromium as component elements; and performing vapor phase synthesis of a thin film on a substrate by treating the target through a physical vapor deposition method in an argon and nitrogen atmosphere, the thin film including a first particle group including a particle having a cubic rock-salt structure represented by Al(1-x)CrxN (formula (1)) (where x satisfies 0.2≦x≦0.8).
According to the method of producing the sintered material, the sintered material recited in any one of (1) to (5) can be obtained.
With reference to FIGURES, the following describes specific examples of a sintered material, a tool, and a method of producing the sintered material according to an embodiment of the present invention. It should be noted that the present invention is defined by the terms of the claims, rather than these examples, and is intended to include any modifications within the scope and meaning equivalent to the terms of the claims.
When an atomic ratio is not particularly defined in a chemical formula described in the present specification, respective elements are not necessarily contained at an equal atomic ratio. It is intended to include all the conventionally known atomic ratios.
In the present specification, the term “average particle size” refers to a value measured with a particle size distribution measurement device such as Microtrac.
A sintered material according to a first embodiment is a sintered material including:
a first particle group including a particle having a cubic rock-salt structure represented by Al(1-x)CrxN (formula (1)) (where x satisfies 0.2≦x≦0.8); and
a second particle group including a particle of at least one first compound selected from a group consisting of oxide and oxynitride of aluminum, zirconium, yttrium, magnesium, and hafnium.
The cubic rock-salt crystal structure, which is a crystal structure representative of a rock salt (sodium chloride), is such a structure that two different types of face centered cubic lattices are combined to be displaced from each other in the direction of ridge of a unit cubic lattice by half the ridge length. The particle (cAlCrN) having the cubic rock-salt structure represented by the above formula (1) has a structure having chromium dissolved in the solid state in the crystal structure of cubic aluminum nitride (cAlN). Accordingly, cAlCrN has a heat-resistant temperature higher than that of cAlN. Hence, the sintered material including cAlCrN can have an excellent wear resistance in high speed cutting.
In the above formula (1), x satisfies 0.2≦x≦0.8, x preferably satisfies 0.3≦x≦0.7, and x more preferably satisfies 0.4≦x≦0.6. If x is less than 0.2, the sintered material cannot exhibit excellent wear resistance in high speed cutting. This is presumably because the heat resistance of cAlCrN is not sufficiently improved if x is less than 0.2. On the other hand, if x is more than 0.8, the sintered material cannot exhibit excellent wear resistance in high speed cutting. This is presumably due to the following reason: if x is more than 0.8, the hardness of cAlCrN is decreased, so that the hardness of the sintered material is also decreased.
The sintered material according to the first embodiment preferably includes not less than 20 volume % and not more than 99.5 volume % of the first particle group, more preferably includes not less than 35 volume % and not more than 99.5 volume % of the first particle group, and further preferably includes not less than 40 volume % and not more than 80 volume % of the first particle group. When the sintered material includes not less than 20 volume % of the first particle group, the sintered material can have an excellent wear resistance in high speed cutting.
The sintered material according to the first embodiment includes a second particle group including a particle of at least one first compound selected from a group consisting of oxide and oxynitride of aluminum, zirconium, yttrium, magnesium, and hafnium. The second particle group in the sintered material exists in an interface between adjacent hard particles, and serves as a binder phase. Since the binder phase can bind the hard particles to each other strongly, the sintered material can have a more excellent wear resistance.
Examples of the first compound included in the second particle group include aluminum oxide (Al2O3), zirconium oxide (ZrO2), yttrium oxide (Y2O3), magnesium oxide (MgO), hafnium oxide (HfO2), and the like. Among these, the use of aluminum oxide (Al2O3), yttrium oxide (Y2O3), magnesium oxide (MgO), and hafnium oxide (HfO2) leads to significant improvement of the wear resistance of the sintered material.
The sintered material according to the first embodiment preferably includes not less than 0.5 volume % and not more than 90 volume % of the second particle group, and more preferably includes not less than 10 volume % and not more than 50 volume % of the second particle group. When the sintered material includes not less than 0.5 volume % and not more than 90 volume % of the second particle group, the wear resistance and chipping resistance of the sintered material are improved further. Moreover, when the second particle group includes Al2O3 and ZrO2, the chipping resistance of the sintered material is significantly improved. This is presumably because Al2O3 is dispersion-strengthened by ZrO2 to provide strong toughness.
The sintered material according to the first embodiment preferably further includes a third particle group including a cubic boron nitride. The cubic boron nitride is a hard particle having more excellent toughness and strength than those of cAlCrN. Hence, when the sintered material includes such particles, the toughness of the sintered material is improved, thus resulting in improved chipping resistance. Particularly, when the third particle group includes cubic boron nitride, the chipping resistance of the sintered material is significantly improved. This is presumably because boron and cAlCrN are bonded to each other strongly.
The sintered material further preferably includes not less than 20 volume % and not more than 70 volume % of the third particle group. When the sintered material includes not less than 20 volume % of the third particle group, the chipping resistance of the sintered material is significantly improved. On the other hand, if the amount of the third particle group in the sintered material is more than 70 volume %, the wear resistance is decreased.
A tool according to a second embodiment is a tool using the sintered material according to the first embodiment. Since the sintered material of the first embodiment is excellent in wear resistance in high speed cutting as described above, the tool using this sintered material is also excellent in wear resistance.
Examples of the cutting tool according to the second embodiment include a drill, an end mill, an indexable cutting insert for milling, an indexable cutting insert for turning, a metal saw, a gear cutting tool, a reamer, or a tap. Moreover, the cutting tool may be entirely or partially (for example, an edge portion) composed of the above sintered material.
When the cutting tool is entirely composed of the above sintered material, the cutting tool can be produced by processing the sintered material into a desired shape. The sintered material can be processed by a laser, for example. On the other hand, when the cutting tool is partially composed of the above sintered material, the cutting tool can be produced by joining the sintered material to a desired position of a base body included in the tool. It should be noted that a method of joining the sintered material is not particularly limited; however, in order to suppress the sintered material from being separated from the base body, it is preferable to provide a joining layer between the base body and the sintered material to strongly couple the base body and the sintered material to each other.
The following describes a method of producing the sintered material according to a third embodiment with reference to
The method of producing the sintered material recited in the first embodiment includes: a step (indicated as S1 in
(Step of Obtaining First Mixed Particle Group)
With reference to
(Step of Obtaining Second Mixed Particle Group)
Next, in the step (S2) of obtaining the second mixed particle group, the first mixed particle group is thermally treated to obtain the second mixed particle group including a cubic CrN particle.
The thermal treatment can be performed by heating the first mixed particle group in a nitrogen atmosphere at not less than 800° C. and not more than 1100° C., for example. Accordingly, hexagonal Cr2N included in the first mixed particle group is changed into cubic CrN.
(Step of Obtaining First Particle Group)
Next, in the step (S3) of obtaining the first particle group, the second mixed particle group is treated by the isostatic synthesis method or the impulsive compression method to obtain the first particle group including the cubic AlCrN particle.
The impulsive compression method can be performed, for example, by: mixing the second mixed particle group with copper powder serving as a heat sink and pressure medium; introducing them into a steel container; and momentarily applying a pressure of not less than 15 GPa by way of an impulse wave for a pressure application time of not more than 50 microseconds. Accordingly, the hexagonal AlN included in the second mixed particle group is changed into cubic AlN, and Cr is dissolved in the cubic AlN in the solid state, thus synthesizing cubic AlCrN. For the impulsive application of pressure, a pressure of not less than 15 GPa and not more than 50 GPa is preferable and a pressure of not less than 35 GPa and not more than 50 GPa is more preferable. A temperature during the impulsive application of pressure is preferably not less than 1200° C. and not more than 3000° C., and is more preferably not less than 1800° C. and not more than 2200° C.
The obtained first particle group is preferably pulverized using a ball mill device, a bead mill device, or the like into an average particle size of not less than 0.1 m and not more than 0.5 m. The first particle group can be used as a source material of the sintered material.
(Step of Obtaining Third Mixed Particle Group)
Next, in the step (S4) of obtaining the third mixed particle group, the third mixed particle group is obtained by mixing the first particle group with a second particle group including a particle of at least one first compound selected from a group consisting of oxide and oxynitride of aluminum, zirconium, yttrium, magnesium, and hafnium.
The third particle group can further include a cubic boron nitride.
The third mixed particle group is preferably mixed using a ball mill device, a bead mill device, or the like, and is preferably pulverized to have an average particle size of not more than 0.5 m.
(Step of Obtaining Sintered Material)
Next, in the step (S5) of obtaining the sintered material, the third mixed particle group is sintered to obtain the sintered material.
Specifically, for example, the third mixed particle group can be treated at a pressure of not less than 10 kPa and not more than 15 GPa and at a temperature of not less than 800° C. and not more than 1900° C., thereby obtaining the sintered material. The step of obtaining the sintered material is preferably performed under a non-oxidizing atmosphere, particularly, in vacuum or under a nitrogen atmosphere. Although a sintering method is not particularly limited, spark plasma sintering (SPS), hot press, ultra-high pressure press, or the like can be used.
A method of producing a sintered material according to a fourth embodiment includes:
a step of preparing a target including aluminum and chromium as component elements; and
a step of performing vapor phase synthesis of a thin film on a substrate by treating the target through a physical vapor deposition method in an argon and nitrogen atmosphere, the thin film including a first particle group including a particle having a cubic rock-salt structure represented by Al(1-x)CrxN (formula (1)) (where x satisfies 0.2≦x≦0.8).
The step of performing the vapor phase synthesis of the thin film including the first particle group can be performed, for example, by treating the target by an arc ion plating method to form the thin film on the substrate. In this case, for example, treatment conditions can be set as follows: an Ar flow rate of 20 sccm; a N2 flow rate of 80 sccm; a pressure of 2 Pa; a bias of 110 V; an arc current of 91 Å; and a substrate temperature of 400° C.
The following describes the present invention more specifically by way of examples. However, the present invention is not limited by these examples.
[Samples 1 to 42]
(Step of Obtaining First Mixed Particle Group)
Hexagonal AlN particles (provided by Tokuyama Corporation) and hexagonal Cr2N particles (provided by Shin Nippon Kinzoku Co., Ltd.) were mixed at a ratio of 10:90 to 90:10, thereby obtaining a first mixed particle group. It should be noted that the first mixed particle group was pulverized by a bead mill to have an average particle size of not more than 0.5 m.
(Step of Obtaining Second Mixed Particle Group)
Next, the first mixed particle group was thermally treated in a nitrogen treatment furnace at 900° C., thereby obtaining a second mixed particle group including cubic CrN particles. A ratio of a content (mol %) of hAlN to a content (mol %) of cCrN in the second mixed particle group of each sample is shown in Table 1 at the column “Second Mixed Particle Group”.
(Step of Obtaining First Particle Group)
Next, the second mixed particle group was mixed with a heat sink and copper powder, and was introduced into a steel container. Then, by explosion of an explosive, the second mixed particle group was treated at a pressure of 40 GPa and a temperature of 2000° C., thereby obtaining the first particle group. The obtained first particle group was subjected to XRD analysis, and cAlCrN was identified. It should be noted that the first particle group was pulverized by a bead mill to have an average particle size of not more than 0.5 μm.
(Step of Obtaining Third Mixed Particle Group)
Next, the first particle group, the second particle group, and the third particle group were mixed to obtain a third mixed particle group. It should be noted that respective blending amounts thereof and types of compounds included in each particle group are shown in Table 1. It should be noted that the third mixed particle group was pulverized by a bead mill to have an average particle size of not more than 0.5 m.
(Step of Obtaining Sintered Material)
Next, the third mixed particle group was introduced into a capsule composed of tantalum, and was sintered for 15 minutes at a pressure of 7 GPa and a temperature of 1350° C. using a pressing machine, thereby obtaining a sintered material.
(Measurement of Sintered Material)
The sintered material was subjected to XRD analysis and a lattice constant was refined by a Rietveld method, thereby obtaining a lattice constant of cAl(1-x)CrxN and a value of x. Here, the value of x was obtained by determining an amount of solid solution of Cr through proportion calculation based on a cAlN lattice constant of 4.12 Å and a cCrN lattice constant of 4.15 Å. The result is shown in Table 1.
When the CP-treated surface of the sintered material was observed with SEM-EDX, it was confirmed that an area ratio of AlCrN to the second particle group in the CP-treated surface of the sintered material was substantially the same as a volume ratio of the first particle group to the second particle group in the third mixed particle group (employed software: WinROOF by Mitani Corporation).
(Evaluation)
The obtained sintered material was cut by a laser and was finished to produce a cutting tool with a tool shape of CNMA120408 and a negative land of 15°×0.1 to 0.15 mm. The obtained cutting tool was used for a test of cutting a centrifugal cast iron under below-described cutting conditions to measure an amount (m) of flank wear after cutting for 1.5 km. Moreover, wear type and chipping state of the cutting tool after cutting for 2.0 km were observed.
Cutting speed: 900 m/minute
Depth of cut: 0.1 mm
Feed rate: 0.28 mm/rev
Coolant: emulsion
Lathe: OKUMA LB400; Holder: EWN68-150CKB6
Workpiece: centrifugal cast iron having a structure of dense perlite and having a chemical composition of gray cast iron
Shape of workpiece: cylindrical shape; inner diameter φ of 85 mm
The result is shown in Table 1.
(Evaluation Result)
In comparison among sample 1 to sample 7, when the value of x in the formula (1) above was not less than 0.2 and not more than 0.8 (samples 2 to 6), the wear resistance of each of the sintered materials was excellent.
In comparison among sample 8 to sample 14, as the amount of the first particle group in the third mixed particle group was larger, the wear resistance of each of the sintered materials was more excellent.
In comparison among sample 4 and samples 15 to 20, the wear resistances of the sintered materials were equally excellent when Al2O3, ZrO2, Y2O3, MgO, or HfO2 was used as the second particle group.
In comparison among sample 4 and samples 21 to 29, the chipping resistance was excellent when particles of two or more compounds were used as a second particle group. Moreover, the chipping resistance was also excellent when cBN was used as the third particle group.
In comparison among samples 30 to 37, each of the samples was excellent in chipping resistance, and the wear resistance was more excellent as the amount of the third particle group in the third mixed particle group was smaller.
[Samples 43 to 84]
(Step of Obtaining First Mixed Particle Group)
Hexagonal AlN particles (provided by Tokuyama Corporation) and hexagonal Cr2N particles (provided by Shin Nippon Kinzoku Co., Ltd.) were mixed to attain an atomic ratio of Al to Cr as shown in Table 2 at the column “Blending Ratio”, thereby obtaining a first mixed particle group. It should be noted that the first mixed particle group was pulverized by a bead mill to have an average particle size of not more than 0.5 μm.
(Step of Obtaining First Particle Group)
Next, the first mixed particle group was treated in a nitrogen furnace at a nitrogen pressure of 8 MPa and a temperature of 2000° C., thereby producing a first particle group (isostatic synthesis method). The particle hard material was subjected to XRD analysis, and cAlCrN was identified.
(Step of Obtaining Third Mixed Particle Group)
Next, the first particle group, the second particle group, and the third particle group were mixed to obtain a third mixed particle group. It should be noted that respective blending amounts thereof and types of compounds included in each particle group are shown in Table 2. It should be noted that the third mixed particle group was pulverized by a bead mill to have an average particle size of not more than 0.5 m.
(Step of Obtaining Sintered Material)
Next, the third mixed particle group was introduced into a capsule composed of tantalum, and was sintered for 15 minutes at a pressure of 7 GPa and a temperature of 1350° C. using a pressing machine, thereby obtaining a sintered material.
(Measurement of Sintered Material)
The sintered material was subjected to XRD analysis and a lattice constant was refined by a Rietveld method, thereby obtaining a lattice constant of cAl(1-x)CrxN and a value of x. Here, the value of x was obtained by determining an amount of solid solution of Cr through proportion calculation based on a cAlN lattice constant of 4.12 Å and a cCrN lattice constant of 4.15 Å. The result is shown in Table 2.
When the CP-treated surface of the sintered material was observed with SEM-EDX, it was confirmed that an area ratio of AlCrN to the second particle group in the CP-treated surface of the sintered material was substantially the same as a volume ratio of the first particle group to the second particle group in the third mixed particle group (employed software: WinROOF by Mitani Corporation).
(Evaluation)
The obtained sintered material was cut by a laser and was finished to produce a cutting tool with a tool shape of CNMA120408 and a negative land of 15°×0.1 to 0.15 mm. The obtained cutting tool was used for a test of cutting a centrifugal cast iron under below-described cutting conditions to measure an amount (m) of flank wear after cutting for 1.5 km. Moreover, wear type and chipping state of the cutting tool after cutting for 2.0 km were observed.
Cutting speed: 900 m/minute
Depth of cut: 0.1 mm
Feed rate: 0.28 mm/rev
Coolant: emulsion
Lathe: OKUMA LB400; Holder: EWN68-150CKB6
Workpiece: centrifugal cast iron having a structure of dense perlite and having a chemical composition of gray cast iron
Shape of workpiece: cylindrical shape; inner diameter φ of 85 mm
The result is shown in Table 2.
(Evaluation Result)
In comparison among sample 43 to sample 49, when the value of x in the formula (1) above was not less than 0.2 and not more than 0.8 (samples 44 to 48), the wear resistance of each of the sintered materials was excellent.
In comparison among sample 50 to sample 56, as the amount of the first particle group in the third mixed particle group was larger, the wear resistance of each of the sintered materials was more excellent.
In comparison among sample 46 and samples 57 to 62, the wear resistances of the sintered materials were equally excellent when Al2O3, ZrO2, Y2O3, MgO, or HfO2 was used as the second particle group.
In comparison among sample 46 and samples 63 to 71, the chipping resistance was excellent when particles of two or more compounds were used as a second particle group. Moreover, the chipping resistance was also excellent when cBN was used as the third particle group.
In comparison among samples 72 to 79, each of the samples was excellent in chipping resistance, and the wear resistance was more excellent as the amount of the third particle group in the third mixed particle group was smaller.
From above, it was confirmed that the sintered material produced using the isostatic synthesis method exhibits a result similar to that of the sintered material produced using the impulsive compression method.
[Samples 85 to 126]
(Target Preparing Step)
A target was prepared such that a blending ratio (atomic ratio) of Al to Cr in the target was as described in Table 3 at the column “Target Composition”.
(Step of Obtaining First Particle Group)
Next, the target was treated by an arc ion plating method, thereby forming a thin film on a high-speed steel substrate. The treatment conditions were as follows: an Ar flow rate of 20 sccm; a N2 flow rate of 80 sccm; a pressure of 2 Pa; a bias of 110 V; an arc current of 91 Å; and a substrate temperature of 400° C. Next, the thin film formed on the high-speed steel substrate was collected by detaching it from the substrate, and was pulverized by a bead mill into a particle size of 0.5 m to 3 m to produce a slurry. Then, the slurry is dried to obtain a first particle group. This first particle group was subjected to XRD analysis, and cAlCrN was identified.
(Step of Obtaining Third Mixed Particle Group)
Next, the first particle group, the second particle group, and the third particle group were mixed to obtain a third mixed particle group. It should be noted that respective blending amounts thereof and types of compounds included in each particle group are shown in Table 3. It should be noted that the third mixed particle group was pulverized by a bead mill to have an average particle size of not more than 0.5 m.
(Step of Obtaining Sintered Material)
Next, the third mixed particle group was introduced into a capsule composed of tantalum, and was sintered for 15 minutes at a pressure of 7 GPa and a temperature of 1350° C. using a pressing machine, thereby obtaining a sintered material.
(Measurement of Sintered Material)
The sintered material was subjected to XRD analysis and a lattice constant was refined by a Rietveld method, thereby obtaining a lattice constant of cAl(1-x)CrxN and a value of x. Here, the value of x was obtained by determining an amount of solid solution of Cr through proportion calculation based on a cAlN lattice constant of 4.12 Å and a cCrN lattice constant of 4.15 Å. The result is shown in Table 3.
When the CP-treated surface of the sintered material was observed with SEM-EDX, it was confirmed that an area ratio of AlCrN to the second particle group in the CP-treated surface of the sintered material was substantially the same as a volume ratio of the first particle group to the second particle group in the third mixed particle group (employed software: WinROOF by Mitani Corporation).
(Evaluation)
The obtained sintered material was cut by a laser and was finished to produce a cutting tool with a tool shape of CNMA120408 and a negative land of 15°×0.1 to 0.15 mm. The obtained cutting tool was used for a test of cutting a centrifugal cast iron under below-described cutting conditions to measure an amount (m) of flank wear after cutting for 1.5 km. Moreover, wear type and chipping state of the cutting tool after cutting for 2.0 km were observed.
Cutting speed: 900 m/minute
Depth of cut: 0.1 mm
Feed rate: 0.28 mm/rev
Coolant: emulsion
Lathe: OKUMA LB400; Holder: EWN68-150CKB6
Workpiece: centrifugal cast iron having a structure of dense perlite and having a chemical composition of gray cast iron
Shape of workpiece: cylindrical shape; inner diameter φ of 85 mm
The result is shown in Table 3.
(Evaluation Result)
In comparison among sample 85 to sample 91, when the value of x in the formula (1) above was not less than 0.2 and not more than 0.8 (samples 2 to 6), the wear resistance of each of the sintered materials was excellent.
In comparison among sample 92 to sample 98, as the amount of the first particle group in the third mixed particle group was larger, the wear resistance of each of the sintered materials was more excellent.
In comparison among sample 88 and samples 99 to 104, the wear resistances of the sintered materials were equally excellent when Al2O3, ZrO2, Y2O3, MgO, or HfO2 was used as the second particle group.
In comparison among sample 88 and samples 105 to 113, the chipping resistance was excellent when particles of two or more compounds were used as a second particle group. Moreover, the chipping resistance was also excellent when cBN was used as the third particle group.
In comparison among samples 114 to 121, each of the samples was excellent in chipping resistance, and the wear resistance was more excellent as the amount of the third particle group in the third mixed particle group was smaller.
From above, it was confirmed that the sintered material produced using the physical vapor deposition method exhibits a result similar to that of the sintered material produced using the impulsive compression method.
The embodiments and examples disclosed herein are illustrative and non-restrictive in any respect. The scope of the present invention is defined by the terms of the claims, rather than the embodiments described above, and is intended to include any modifications within the scope and meaning equivalent to the terms of the claims.
The sintered material including cubic AlCrN according to one embodiment of the present invention can be widely used for cutting tools. For example, the sintered material can be used for a drill, an end mill, an indexable cutting insert for milling, an indexable cutting insert for turning, a metal saw, a gear cutting tool, a reamer, or a tap.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2014-204706 | Oct 2014 | JP | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/JP2015/077494 | 9/29/2015 | WO | 00 |
