WO2014065131A1 - 立方晶窒化ホウ素焼結体およびその製造方法 - Google Patents
立方晶窒化ホウ素焼結体およびその製造方法 Download PDFInfo
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Definitions
- the present invention relates to a cubic boron nitride sintered body and a method for producing the same, and more particularly to a cubic boron nitride sintered body containing a binder and a catalyst and a method for producing the same.
- Cubic boron nitride (hereinafter referred to as “cBN”) sintered body has the characteristics that it has the hardness next to diamond and does not react with iron-based materials. Therefore, it has been conventionally used as a cutting tool for iron-based materials. Yes.
- cBN sintered bodies generally used as cutting tools are made of cBN powder using ceramics such as TiC and TiN as a binder. Manufactured by sintering under ultra high pressure.
- At least one selected from the group consisting of cobalt (Co), chromium (Cr), nickel (Ni) and molybdenum (Mo) is a catalyst for the purpose of improving fracture resistance. It may be included as an element.
- the catalyst element is added for the purpose of improving the toughness of the cBN sintered body and improving the fracture resistance, but since it is a metal element, it has ductility. However, due to its ductility, it was difficult to pulverize and mix the catalyst element with the cBN powder.
- the conventional cBN sintered body uses a catalyst element in the state of a compound such as carbide or nitride to prepare a powdery catalyst element and sinter a mixture of the catalyst element powder and the cBN powder. It is produced by.
- the catalytic element is mixed with the cBN powder as a powder (hereinafter also referred to as “powder mixing”), so that the catalytic element is uniformly distributed in the obtained cBN sintered body. In some cases, it was not distributed. Further, it is known that the catalyst element has a lower hardness than cBN, and if used in a large amount, it causes deterioration in wear resistance. Therefore, from the viewpoint of wear resistance and the like, when it is necessary to keep the addition amount of the catalytic element low, the effect of improving the fracture resistance of the cBN sintered body by the catalytic element cannot be sufficiently obtained.
- the present invention has been made to solve the above-described problems.
- the main object of the present invention is to provide a cubic boron nitride sintered body capable of improving the fracture resistance while keeping the addition amount of the catalyst element low and a method for producing the same.
- the cubic boron nitride sintered body of the present invention is a cubic boron nitride sintered body comprising cubic boron nitride, a binder, and a metal catalytic element, and the content of cubic boron nitride is 50% by volume or more. 85% by volume or less, and the catalyst element content is 0.5% by mass or more and 5% by mass or less.
- the binder is at least one selected from the group consisting of nitrides, carbides, borides, oxides, and solid solutions of Group 4a elements, Group 5a elements, Group 6a elements of the Periodic Table And an aluminum compound.
- the catalytic element can be dispersed in the binder in the cubic boron nitride sintered body, the fracture resistance of the cubic boron nitride sintered body can be improved.
- the catalyst element may be composed of at least one element selected from the group consisting of cobalt (Co), chromium (Cr), nickel (Ni), and molybdenum (Mo).
- Composition analysis on a line segment dividing an image obtained by observing an 8 ⁇ m ⁇ 8 ⁇ m region of the structure of the cubic boron nitride sintered body of the present invention with a scanning transmission electron microscope into partial regions of 4 rows and 4 columns To calculate the total value of the detection peak value of nitrogen (N) and the detection peak value of boron (B) at any measurement point on the line segment, and the total value is calculated at all measurement points of the total value.
- the measurement point that is less than half of the maximum value is determined as the joint measurement point, and the ratio of the number of measurement points where no catalytic element is detected among the joint measurement points to the total number of joint measurement points is 30% or less. Can do.
- the bending strength of the cubic boron nitride sintered body can exceed 125 kgf / mm 2 when the content of the cubic boron nitride is 70 volume% or more and 80 volume% or less.
- the method for producing a cubic boron nitride sintered body according to the present invention includes a step of preparing cubic boron nitride powder, a step of attaching a catalytic element of metal to the surface of the powder, and producing a powder with catalyst, A step of mixing the powder with catalyst and the binder, and a step of sintering the mixture of the powder with catalyst and the binder.
- a catalytic element is dispersed in the binder, and a cubic boron nitride sintered body having excellent fracture resistance can be produced.
- the step of producing the powder with catalyst may include a step of coating the surface of the powder with a film containing a catalytic element by a physical vapor deposition method.
- FIG. 5 is a characteristic diagram when a composition analysis is performed on a line V in FIG. 4. It is a structure
- FIG. 7 is a characteristic diagram when a composition analysis is performed on the line VII in FIG. 6.
- the cBN sintered body according to the present embodiment includes cBN, a binder, and a catalytic element made of Co and Cr.
- the content of cBN in the cBN sintered body is 80% by volume.
- the binder is at least one selected from the group consisting of nitrides, carbides, borides, oxides, and solid solutions of Group 4a elements, Group 5a elements, Group 6a elements of the Periodic Table And an aluminum compound.
- the binder is made of Ti, N, and Al.
- the content of the binder in the cBN sintered body according to the present embodiment is 20% by volume, and the content of the catalytic elements composed of Co and Cr is 3% by mass in total.
- the cBN sintered body according to the present embodiment Co and Cr are dispersed in the binder.
- the cBN crystal grains are bonded to each other through a bonding material made of Ti, N, and Al, and Co and Cr are dispersed and exist in the bonding material without being localized.
- the region where the total value of the detection peak value of N and the detection peak value of B is more than half of the maximum value among all the measurement points is determined as the cBN measurement point where cBN exists, and all the measurements are performed.
- a region that is less than half of the maximum value among the points is determined as a joint measurement point where a binder composed of Ti, N, and Al is disposed.
- the ratio of the number of measurement points where neither Co nor Cr was detected to the total number of measurement points determined as the joint measurement points was 30%. It is as follows. In examples described later, cBN content obtained by mixing and sintering cBN powder coated with CoCr by RF sputtering PVD method and binder powder (powder in which TiN and Al are mixed) and 80% by volume and Co The ratio of the cBN sintered body having a total content of 3% by mass of Cr and Cr was 23.6%.
- cBN powder, binder powder and catalyst element powder are mixed and sintered to obtain a cBN content of 80% by volume and a total content of Co and Cr of 3% by mass.
- the ratio of the sintered body was 38.4%.
- the catalyst element in the cBN sintered body of the example is more uniformly dispersed in the binder as compared with the comparative example.
- the cBN in the cBN sintered body is in contact with Co and Cr in a wider area. can do.
- a conventional cBN sintered body is produced by adding a catalytic element as powder to cBN by powder mixing, the catalytic element is unevenly distributed in the binder of the cBN sintered body. Therefore, in the conventional cBN sintered body, unless the content of the catalytic element is increased, cBN and the catalytic element cannot be sufficiently brought into contact with each other.
- the cBN sintered body according to the present embodiment can uniformly contact cBN and the catalytic element in a wide region, the amount of addition of the catalytic element is not suppressed to 5% by mass or less. Fracture resistance can be improved as an effect of the element.
- the content ratio of the catalytic element is 1.5 from the examples described later. It was confirmed that the bending strength was 115 kgf / mm 2 or more when the content was 5% by mass and 5% by mass.
- the cBN sintered body having a cBN content of 70% by volume to 80% by volume has a bending strength when the catalyst element content is 0.5% by mass and 5% by mass. Was found to exceed 125 kgf / mm 2 .
- the cBN sintered body according to the present embodiment is excellent in toughness in addition to the above bending strength.
- the inventor of the present application uses a tool using a cBN sintered body as an evaluation of toughness, steel grade SKD11-6V specified in JIS G4404, hardness HRC64, diameter 100 mm ⁇ length 300 mm, and six V grooves in the axial direction on the surface.
- the provided work material was intermittently cut under the conditions of a cutting speed of 100 m / min, a feed rate of 0.2 mm / rev, and a cutting depth of 0.15 mm, the time until the cBN sintered body was lost was evaluated.
- the cBN sintered body according to the present embodiment has a time until loss of 5% or more as compared with a conventional cBN sintered body containing the same amount of catalyst element. That is, the cBN sintered body according to the present embodiment is superior in bending strength and toughness and superior in fracture resistance as compared with the conventional cBN sintered body.
- the method for producing a cBN sintered body according to the present embodiment includes a step of preparing cBN powder (S01), a step of attaching a catalytic element to the surface of the cBN powder, and producing a powder with catalyst (S02).
- the step of mixing the cBN powder with catalyst and the binder (S03) and the step of sintering the mixture of the cBN powder with catalyst and the binder (S04) are provided.
- a cBN powder having an average particle size of about 0.5 ⁇ m to 5.0 ⁇ m is prepared.
- Co and Cr which are catalytic elements, are attached to the surface of the cBN powder prepared in the previous step (S01) by the RF sputtering PVD method.
- a cBN powder coated with CoCr (50:50) is prepared using a solid metal material (target) in which Co and Cr are alloyed at a composition ratio of 1: 1.
- Film formation conditions by sputtering PVD may be determined based on a calibration curve between the sputtering time and the coating amount so as to be a predetermined coating amount.
- Co and Cr are deposited on the surface of the cBN powder under the condition that the Co and Cr content in the cBN sintered body is 3 mass%.
- the cBN powder produced in the previous step (S02) and coated with CoCr (50:50) is mixed with the binder.
- the binder is prepared as a powder obtained by pulverizing and mixing a compound obtained by heat-treating a mixed powder of TiN and Al in a vacuum at a temperature of 1200 ° C. for 30 minutes using a planetary ball mill.
- the blending ratio of the catalyst-attached cBN powder and the binder powder is determined so as to have a predetermined cBN content in the produced cBN sintered body, but in this embodiment, the cBN content is 80% by volume. Blend as follows.
- the inner walls are uniformly mixed by a planetary ball mill using a pot made of Teflon (registered trademark) and balls made of Si 3 N 4 . Further, the mixed cBN powder with catalyst and the binder powder are degassed by being held at a temperature of 900 ° C. for 20 minutes in a vacuum furnace.
- step (S04) the mixed powder of the cBN powder and the binder powder coated with CoCr (50:50) obtained in the previous step (S03) is filled into a Mo capsule, and then the ultra high pressure Using an apparatus, it is sintered at a pressure of 5.8 GPa and a temperature of 1400 ° C. for 20 minutes. Thereby, the cBN sintered compact concerning this embodiment is producible.
- the cBN sintered body according to the present embodiment is produced by mixing and sintering a cBN powder whose surface is coated with a catalytic element and a binder. Accordingly, in the cBN sintered body, the catalyst element can be dispersed and included in the binder. As a result, the cBN sintered body according to the present embodiment has a high ratio of the catalytic element in contact with cBN among the added catalytic elements, so that the content of the catalytic element is as low as 5% by mass or less. , Can have excellent fracture resistance.
- the cBN sintered body of the present embodiment has a cBN content of 80% by volume, but is not limited to this, and can be arbitrarily determined in the range of 50% by volume to 85% by volume. From the examples described later, the cBN sintered body having a cBN content of 60% by volume or more and 90% by volume or less was superior to the conventional cBN sintered body produced by powder mixing in both bending strength and toughness. . However, it is considered that a cBN sintered body having similar characteristics can be obtained even when the cBN content is 50% by volume or more.
- the cBN sintered body according to the present embodiment includes Co and Cr as catalyst elements, but is not limited thereto.
- the catalyst element may be composed of at least one element selected from the group consisting of Co, Cr, Ni, and Mo. Even in this case, the cBN sintered body to which the catalyst element is added can have excellent fracture resistance.
- the present invention is not limited to this.
- the catalytic element contained in the cBN sintered body may be arbitrarily added as long as it is 0.5 mass% or more and 5 mass% or less. From the examples described later, the cBN sintered body to which Co and Cr are added in a total of 1.5% by mass and the cBN sintered body to which 5% by mass are added have a toughness and a bending strength of a conventional cBN sintered body. We were able to confirm that it was superior. If the addition amount of the catalyst element is 0.5% by mass or more and 5% by mass or less, it is considered that a cubic boron nitride composite polycrystal having similar characteristics can be obtained.
- the binder is prepared from a mixed powder of TiN and Al, but is not limited thereto.
- the binder was selected from the group consisting of Group 4a elements, Group 5a elements, Group 6a nitrides, carbides, borides, oxides, and solid solutions thereof of the Periodic Table.
- Any ceramic-based binder containing at least one kind and an aluminum compound can be used.
- it may be prepared from a mixed powder of Ti (CN) and Al.
- the method of coating the catalytic element on the surface of the cBN powder in the step (S02) uses the sputtering PVD method, but is not limited thereto. .
- a plating method or the like may be used. Even in this case, the catalytic element can be coated on the surface of the cBN powder.
- the sintering conditions using the ultrahigh pressure apparatus in the step (S04) are not limited to the above-described conditions. Any condition can be selected as long as cBN can be sintered.
- the cBN content in the cBN sintered body is 60% by volume to 90% by volume, and the content of the catalytic element (CrCo) is 1.5% by mass.
- the cBN sintered bodies of 5% by mass were prepared, and their bending strength and toughness were evaluated.
- a cBN powder having an average particle size of about 1.2 ⁇ m is prepared in step (S01), and the surface of the cBN powder is sputtered PVD in step (S02).
- CoCr (50:50) was coated by the method. At this time, film formation was performed under two kinds of sputtering conditions so that CoCr was 1.5% by mass and 5% by mass in total in the cBN sintered body, and two types of cBN powder with catalyst were prepared.
- step (S03) the compound obtained by heat-treating the mixture of TiN and Al as described above is pulverized and mixed to produce a binder powder, and the binder powder and two types of catalyst-cBN powder are mixed. To prepare a mixture. At this time, it mix
- a cBN powder having an average particle size of about 1.2 ⁇ m and a Co / Cr carbide powder having an average particle size of 0.5 ⁇ m as a catalyst element were prepared at a weight ratio of 1: 1.
- the binder is prepared as a powder obtained by pulverizing and mixing a compound obtained by heat-treating a mixture of TiN and Al, and the mixture of cBN powder, catalytic element powder and binder powder is the same as the example sample.
- 14 were prepared and held at a pressure of 5.8 GPa and a temperature of 1400 ° C. for 20 minutes to sinter, thereby preparing 14 cBN sintered bodies.
- the present invention uses a coating method in which the above-described cBN powder is coated with a metal catalytic element. If the metal element can be finely pulverized, the same effect as that of the present invention can be obtained by adding and mixing the obtained fine metal to the cBN powder.
- the content rate of the catalytic element in the cBN sintered bodies of the example samples and the comparative example samples was measured by an ICP method.
- Example 1 With reference to FIG. 3, as experiment 1, the bending strength of the example evaluation sample and the comparative example evaluation sample was evaluated. Specifically, the cBN sintered body is formed into a square test piece 10 having a length of 6 mm, a width of 3 mm, and a thickness of 0.5 mm, and the test piece 10 is arranged on two struts 11 arranged with an interval L of 4 mm. did. A load N was applied to a central point between the columns 11, and the load N when the cBN sintered specimen 10 was broken was measured as a bending strength. In addition, the support
- the example samples had a bending strength of 115 kgf / mm 2 or more when the cBN content was in the range of 60 volume% to 90 volume%.
- the example sample had the same cBN content and showed a higher bending strength than the comparative example sample to which the catalyst element was added to the same degree.
- the example sample to which 1.5% by mass of the additive element was added had the same cBN content, and the bending strength was higher than that of the comparative example sample to which 5% by mass of the catalyst element was added.
- the bending strength exceeds 125 kgf / mm 2 , and it can be confirmed that the bending strength is particularly high compared with the comparative sample. It was.
- Example 2 As Experiment 2, the toughness of the example evaluation sample and the comparative example evaluation sample was evaluated. Specifically, using a tool using a cBN sintered body, a work material having a steel type SKD11-6V, a hardness HRC64, a diameter of 100 mm ⁇ a length of 300 mm, and six V grooves in the axial direction on the surface is prepared. Then, intermittent cutting was performed under the conditions of a cutting speed of 100 m / min, a feed amount of 0.2 mm / rev, and a cutting depth of 0.15 mm, and the time until the cBN sintered body was lost was evaluated. The measurement results are shown in Table 2.
- the time taken for the example samples to be lost was 1.5 minutes or longer.
- the example sample has the same cBN content and has a toughness of 5% or more longer than that of the comparative example sample to which the catalyst element is added to the same extent, and has excellent toughness. It could be confirmed.
- the example sample to which 1.5% by mass of the additive element was added had the same cBN content, and the time to reach a defect was longer than that of the comparative example sample to which 5% by mass of the catalyst element was added. It was confirmed that the toughness was excellent.
- the example sample according to the present invention is excellent even when the catalyst element content is as low as 5% by mass or less compared to the comparative sample having the same cBN content. It was confirmed that they had bending strength and toughness.
- the degree of variation of the binder and the catalytic element in the cBN sintered body according to the embodiment of the present invention was observed. Further, an image of an 8 ⁇ m ⁇ 8 ⁇ m region of the cBN sintered body is acquired, and composition analysis is performed on a line segment that divides the image into partial regions of 4 rows and 4 columns, and the degree of dispersion of the catalytic element in the binder Evaluated.
- STEM scanning transmission electron microscope
- Example sample a cBN sintered body having a cBN content of 80% by volume and a catalyst element (Co, Cr) of 1.5% by mass was used as an example sample of Example 2.
- a cBN powder having an average particle size of about 1.2 ⁇ m and a Ni / Mo carbide powder having an average particle size of 0.5 ⁇ m as a catalyst element were prepared at a weight ratio of 1: 1.
- the binder was prepared as a powder obtained by grinding and mixing a compound obtained by heat-treating a mixture of TiN and Al.
- a mixture of cBN powder, catalyst element powder, and binder powder was prepared so that the cBN content in the cBN sintered body was 80% by volume and the Ni and Mo contents were 1.5% by mass.
- the mixture was sintered while being held at a pressure of 5.8 GPa and a temperature of 1400 ° C. for 20 minutes to prepare a cBN sintered body.
- the maximum value of the total value of the detection peak value of B (peak intensity) and the detection peak value of N at all measurement points is obtained, and the total value of the detection peak of B and the detection peak of N is less than half of the maximum value.
- the total value of the detection peak of B and the detection peak of N is less than half of the maximum value.
- the total number of measurement points at which the detection peak value of the catalyst element was 0 at the joint measurement point and no catalyst element was detected was calculated, and the ratio to the total number of joint measurement points was calculated. That is, the smaller the ratio, the more dispersed the catalytic element in the binder.
- two types of catalyst elements, Co and Cr were added to each of the example sample and the comparative example sample, but the catalyst element was detected at the measurement point where the two catalyst elements were not detected simultaneously.
- the total number was determined as the measurement points that did not exist. This is because Co and Cr (or Ni and Mo) have different effects on cBN, and Co and Cr (or Ni and Mo) can act at the same time to obtain excellent fracture resistance. Because. Specifically, Co acts on B in cBN, and Cr acts on N in cBN.
- FIGS. 4 and 6 show images obtained by observing an 8 ⁇ m ⁇ 8 ⁇ m region of the example sample and the comparative example sample by the STEM high angle scattering dark field (HAADF) method, respectively.
- HAADF STEM high angle scattering dark field
- spectra obtained by composition analysis on one line segment shown in FIGS. 4 and 6 are shown in FIGS. 5 and 7, respectively.
- 4 and 6 are HAADF images, B and C constituting cBN are dark, and Co, Cr, Ti and the like constituting a catalytic element and a binder are observed brightly. This was consistent with the spectra shown in FIGS. Thereby, it was confirmed that the binder and the catalytic element were more uniformly dispersed around the cBN in the example sample than in the comparative example sample.
Abstract
Description
cBN粒子(粉末)を単独で直接焼結することは非常に困難であるため、一般に切削工具として用いられているcBN焼結体は、TiCやTiNなどのセラミックスをバインダとして用いてcBNの粉末を超高圧下で焼結して製造されている。
本実施の形態に係るcBN焼結体は、cBNと、結合材と、CoおよびCrからなる触媒元素とを備える。cBN焼結体におけるcBNの含有率は、80体積%である。また、結合材は、周期律表第4a族元素、第5a族元素、第6a族元素の窒化物、炭化物、ホウ化物、酸化物およびこれらの固溶体からなる群の中から選択された少なくとも1種と、アルミニウム化合物とを含む。本実施の形態に係るcBN焼結体において、結合材はTi、NおよびAlからなる。本実施の形態に係るcBN焼結体における結合材の含有率は、20体積%であり、CoおよびCrからなる触媒元素の含有率は、合計で3質量%である。
まず、本実施の形態に係るcBN焼結体の製造方法に従って、工程(S01)で平均粒径が1.2μm程度のcBN粉末を準備し、工程(S02)において該cBN粉末の表面をスパッタリングPVD法によりCoCr(50:50)で被覆した。このとき、cBN焼結体においてCoCrが合計で1.5質量%および5質量%となるように2通りのスパッタリング条件で成膜を行い、2通りの触媒付cBN粉末を作製した。工程(S03)において、上述のようにTiNとAlとの混合物を熱処理して得られた化合物を粉砕混合し結合材粉末を作製し、該結合材粉末と2通りの触媒付cBN粉末とを混合し、混合物を作製した。このとき、cBN焼結体においてcBN含有率が60体積%、65体積%、70体積%、75体積%、80体積%、85体積%、90体積%となるように配合した。つまり、工程(S03)では14通りの混合物を作製した。該14通りの混合物を工程(S04)において、圧力5.8GPa、温度1400℃で20分間保持して焼結し、14通りのcBN焼結体を作製した。
まず、平均粒径が1.2μm程度のcBN粉末と、触媒元素として、平均粒径が0.5μmのCoとCrの炭化物粉末を1:1の重量比で準備した。結合材はTiNとAlとの混合物を熱処理して得られた化合物を粉砕混合して得られた粉末として準備し、cBN粉末と触媒元素粉末と結合材粉末との混合物を、実施例試料と同様の配合率で14通り作製し、これらを圧力5.8GPa、温度1400℃で20分間保持して焼結し、14通りのcBN焼結体を作製した。金属元素は、延性や展性を有するため、現在の技術ではナノレベルに粉砕することは非常に困難である。そのため、炭化物、窒化物、炭窒化物、酸化物などの化合物にすることで延性や展性をなくし、微粉砕することによって、結合材中に添加する方法が用いられている。しかし、化合物では触媒機能を有しない。そのため、本発明は、上述のようなcBN粉末を金属の触媒元素で被覆する被覆法を用いている。金属元素を微粉砕することができれば、得られた微粒金属をcBN粉末に添加し、混合することで本発明と同等の効果を得ることができる。
図3を参照して、実験1として、実施例評価試料と比較例評価試料の抗折力を評価した。具体的には、cBN焼結体を長さ6mm、幅3mm、厚み0.5mmの四角形状の試験片10とし、該試験片10を、間隔Lを4mmとして配置された2支柱11上に配置した。この支柱11間の中央の一点に負荷Nを加え、cBN焼結体の試験片10が折損したときの負荷Nを抗折力として測定した。なお、支柱11は直径2mmとした。測定結果を表1に示す。
実験2として、実施例評価試料と比較例評価試料の靭性を評価した。具体的には、cBN焼結体を用いた工具を用いて、鋼種SKD11-6V、硬度HRC64、直径100mm×長さ300mm、表面上において軸方向にV溝が6本設けられた被削材を、切削速度100m/min、送り量0.2mm/rev、切り込み0.15mmという条件で断続切削し、cBN焼結体が欠損するまでの時間を評価した。測定結果を表2に示す。
上述した実施例1における実施例試料のうち、cBN含有率80体積%、触媒元素(Co、Cr)1.5質量%のcBN焼結体を、実施例2の実施例試料とした。
まず、平均粒径が1.2μm程度のcBN粉末と、触媒元素として、平均粒径が0.5μmのNiとMoの炭化物粉末を1:1の重量比で準備した。結合材はTiNとAlとの混合物を熱処理して得られた化合物を粉砕混合して得られた粉末として準備した。cBN焼結体におけるcBN含有率が80体積%、NiおよびMoの含有率が1.5質量%となるように、cBN粉末と触媒元素粉末と結合材粉末との混合物を作製した。該混合物を圧力5.8GPa、温度1400℃で20分間保持して焼結し、cBN焼結体を作製した。
まず、上述のように、STEMによりcBN焼結体中の結合材および触媒元素のばらつきの程度を観察した。さらに、STEMにより、cBN焼結体の8μm×8μmの領域の画像を取得し、当該画像を4行4列の部分領域に分割する各線分上でEDXによる組成分析を行い、結合材中における添加元素の分散の程度を評価した。なお、組成分析は、日本電子製 JEM-2100Fを用いて、ビームスポットサイズを0.4nmとして行った。組成分析の結果に基づいた結合材中における添加元素の分散評価は、以下の方法で行った。
図4と図6に、それぞれ実施例試料と比較例試料の8μm×8μmの領域をSTEM高角度散乱暗視野(HAADF)法で観察したときの像を示す。また、図4と図6中に示す一の線分上で組成分析して得られたスペクトルを、それぞれ図5と図7に示す。図4および図6はHAADF像のため、cBNを構成するBやCは暗く、触媒元素や結合材を構成するCo、Cr、Ti等は明るく観察されている。これは図5と図7に示すスペクトルとも一致していた。これにより、実施例試料は、比較例試料と比べて結合材および触媒元素がcBNの周囲により均一に分散していることが確認できた。
Claims (6)
- 立方晶窒化ホウ素と結合材と金属の触媒元素とを備える立方晶窒化ホウ素焼結体であって、
前記立方晶窒化ホウ素の含有率が50体積%以上85体積%以下であり、
前記触媒元素の含有率が0.5質量%以上5質量%以下であり、
前記結合材は、周期律表第4a族元素、第5a族元素、第6a族元素の窒化物、炭化物、ホウ化物、酸化物およびこれらの固溶体からなる群の中から選択された少なくとも1種と、アルミニウム化合物とを含む、立方晶窒化ホウ素焼結体。 - 前記触媒元素は、コバルト、クロム、ニッケル、およびモリブデンからなる群から選択される少なくとも1つの元素を含む、請求項1に記載の立方晶窒化ホウ素焼結体。
- 前記立方晶窒化ホウ素焼結体の組織の8μm×8μmの領域を走査型透過電子顕微鏡で観察して得られた画像を4行4列の部分領域に分割する線分上で組成分析を行って、前記線分上の任意の測定点における窒素の検出ピーク値とホウ素の検出ピーク値との合計値を算出し、
前記合計値が、前記合計値の全測定点における最大値の半分以下である測定点を結合部測定点と決定し、
前記結合部測定点の総数に対する、前記結合部測定点のうち前記触媒元素が検出されなかった測定点数の比率が30%以下である、請求項1または請求項2に記載の立方晶窒化ホウ素焼結体。 - 前記立方晶窒化ホウ素の含有率が70体積%以上80体積%以下であって、抗折力が125kgf/mm2越えである、請求項1~請求項3のいずれか1項に記載の立方晶窒化ホウ素焼結体。
- 立方晶窒化ホウ素の粉末を準備する工程と、
前記粉末の表面に金属の触媒元素を付着させて、触媒付粉末を作製する工程と、
前記触媒付粉末と結合材とを混合する工程と、
前記触媒付粉末と前記結合材との混合物を焼結する工程とを備える、立方晶窒化ホウ素焼結体の製造方法。 - 前記触媒付粉末を作製する工程は、前記粉末の表面を物理蒸着法によって前記触媒元素を含む膜で被覆する工程を含む、請求項5に記載の立方晶窒化ホウ素焼結体の製造方法。
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Citations (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS61168569A (ja) * | 1985-01-17 | 1986-07-30 | 昭和電工株式会社 | 立方晶窒化硼素焼結体の製造方法 |
JPH10182242A (ja) * | 1996-10-31 | 1998-07-07 | Sumitomo Electric Ind Ltd | 高硬度高靱性焼結体 |
WO2005066381A1 (ja) * | 2004-01-08 | 2005-07-21 | Sumitomo Electric Hardmetal Corp. | 立方晶型窒化硼素焼結体 |
JP2010513037A (ja) * | 2006-12-13 | 2010-04-30 | ダイヤモンド イノベイションズ インコーポレーテッド | 改善された機械加工性を有する研磨成形体 |
WO2011111261A1 (ja) * | 2010-03-12 | 2011-09-15 | 住友電工ハードメタル株式会社 | 立方晶窒化硼素焼結体工具 |
JP2011207690A (ja) | 2010-03-30 | 2011-10-20 | Sumitomo Electric Hardmetal Corp | 複合焼結体 |
WO2012053507A1 (ja) * | 2010-10-18 | 2012-04-26 | 住友電工ハードメタル株式会社 | 立方晶窒化硼素焼結体、及び立方晶窒化硼素焼結体工具 |
Family Cites Families (14)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS601390B2 (ja) * | 1981-06-29 | 1985-01-14 | 三菱マテリアル株式会社 | 切削工具用立方晶窒化硼素基超高圧焼結材料 |
JPS6020457B2 (ja) * | 1981-10-06 | 1985-05-22 | 三菱マテリアル株式会社 | 切削および耐摩耗工具用高靭性窒化硼素基超高圧焼結材料 |
US5697994A (en) | 1995-05-15 | 1997-12-16 | Smith International, Inc. | PCD or PCBN cutting tools for woodworking applications |
US5639285A (en) * | 1995-05-15 | 1997-06-17 | Smith International, Inc. | Polycrystallline cubic boron nitride cutting tool |
KR100263594B1 (ko) | 1996-10-31 | 2000-08-01 | 오카야마 노리오 | 고경도 고인성 소결체 |
JP4160898B2 (ja) | 2003-12-25 | 2008-10-08 | 住友電工ハードメタル株式会社 | 高強度高熱伝導性立方晶窒化硼素焼結体 |
JP5093160B2 (ja) * | 2009-03-11 | 2012-12-05 | 富士通株式会社 | 通信装置 |
JP5045953B2 (ja) * | 2009-03-31 | 2012-10-10 | 三菱マテリアル株式会社 | 立方晶窒化ホウ素の合成方法および立方晶窒化ホウ素焼結体の製造方法 |
WO2012053375A1 (ja) * | 2010-10-19 | 2012-04-26 | 住友電工ハードメタル株式会社 | 立方晶窒化硼素焼結体工具 |
WO2012056758A1 (ja) * | 2010-10-28 | 2012-05-03 | 住友電工ハードメタル株式会社 | 表面被覆焼結体 |
WO2012105710A1 (ja) * | 2011-02-04 | 2012-08-09 | 株式会社タンガロイ | cBN焼結体工具および被覆cBN焼結体工具 |
JP5613970B2 (ja) * | 2011-03-30 | 2014-10-29 | 三菱マテリアル株式会社 | 立方晶窒化ホウ素の合成方法および立方晶窒化ホウ素焼結体の製造方法 |
JP2014131819A (ja) * | 2011-04-18 | 2014-07-17 | Tungaloy Corp | 複合体 |
CN104321154B (zh) * | 2012-05-31 | 2017-02-22 | 山特维克知识产权股份有限公司 | 制造cbn材料的方法 |
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Patent Citations (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS61168569A (ja) * | 1985-01-17 | 1986-07-30 | 昭和電工株式会社 | 立方晶窒化硼素焼結体の製造方法 |
JPH10182242A (ja) * | 1996-10-31 | 1998-07-07 | Sumitomo Electric Ind Ltd | 高硬度高靱性焼結体 |
WO2005066381A1 (ja) * | 2004-01-08 | 2005-07-21 | Sumitomo Electric Hardmetal Corp. | 立方晶型窒化硼素焼結体 |
JP2010513037A (ja) * | 2006-12-13 | 2010-04-30 | ダイヤモンド イノベイションズ インコーポレーテッド | 改善された機械加工性を有する研磨成形体 |
WO2011111261A1 (ja) * | 2010-03-12 | 2011-09-15 | 住友電工ハードメタル株式会社 | 立方晶窒化硼素焼結体工具 |
JP2011207690A (ja) | 2010-03-30 | 2011-10-20 | Sumitomo Electric Hardmetal Corp | 複合焼結体 |
WO2012053507A1 (ja) * | 2010-10-18 | 2012-04-26 | 住友電工ハードメタル株式会社 | 立方晶窒化硼素焼結体、及び立方晶窒化硼素焼結体工具 |
Non-Patent Citations (1)
Title |
---|
See also references of EP2913317A4 |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2014156625A1 (ja) * | 2013-03-29 | 2014-10-02 | 住友電工ハードメタル株式会社 | 立方晶窒化ホウ素焼結体の製造方法および立方晶窒化ホウ素焼結体 |
US9522850B2 (en) | 2013-03-29 | 2016-12-20 | Sumitomo Electric Hardmetal Corp. | Method for manufacturing cubic boron nitride sintered body, and cubic boron nitride sintered body |
EP2980046A4 (en) * | 2013-03-29 | 2017-02-22 | Sumitomo Electric Hardmetal Corp. | Method for manufacturing cubic boron nitride sintered body, and cubic boron nitride sintered body |
Also Published As
Publication number | Publication date |
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KR101766985B1 (ko) | 2017-08-09 |
US20150291478A1 (en) | 2015-10-15 |
US9487449B2 (en) | 2016-11-08 |
KR20150060970A (ko) | 2015-06-03 |
EP2913317B1 (en) | 2020-08-26 |
JP2014084268A (ja) | 2014-05-12 |
JP5988430B2 (ja) | 2016-09-07 |
CN104768898B (zh) | 2017-03-15 |
CN104768898A (zh) | 2015-07-08 |
EP2913317A1 (en) | 2015-09-02 |
EP2913317A4 (en) | 2016-07-06 |
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