WO2012053507A1 - 立方晶窒化硼素焼結体、及び立方晶窒化硼素焼結体工具 - Google Patents
立方晶窒化硼素焼結体、及び立方晶窒化硼素焼結体工具 Download PDFInfo
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- WO2012053507A1 WO2012053507A1 PCT/JP2011/073913 JP2011073913W WO2012053507A1 WO 2012053507 A1 WO2012053507 A1 WO 2012053507A1 JP 2011073913 W JP2011073913 W JP 2011073913W WO 2012053507 A1 WO2012053507 A1 WO 2012053507A1
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Definitions
- the present invention relates to a cBN sintered body mainly composed of cubic boron nitride (cBN).
- CBN is a high-hardness substance next to diamond
- cBN sintered bodies are used for various cutting tools, wear-resistant parts, impact-resistant parts and the like.
- a sintered body having a high content of cBN is generally used for cutting cast iron / sintered alloy, and the particle size of the cBN particles and the composition of the binder phase are optimized depending on the processing conditions.
- the toughness improves as the cBN particles contained in the sintered body become coarser, while the strength decreases as the binder phase becomes thicker.
- Patent Document 1 discloses the thickness and strength of the binder phase.
- Patent Document 2 an example in which defects and microcracks are eliminated is shown in Patent Document 2.
- the present invention is different from the conventional one, and even when coarse cBN is used, the toughness and strength can be increased at the same time, and excellent fracture resistance and wear resistance are achieved. It is an object to obtain a cubic boron nitride sintered body having a high content of cubic boron nitride. It is another object of the present invention to provide a cubic boron nitride sintered body tool suitable for continuous cutting and intermittent cutting of cast iron and sintered alloy under rough machining conditions.
- the present inventors diligently studied the improvement of the uniformity of the binder phase and the sintering conditions, and as a result, the shape of the interface between the cBN particles and the binder phase is a wedge type that has a high effect of suppressing dropping. It has been found that it is possible to make a convex portion having steps or more, and by using the above structure, the toughness and strength can be increased at the same time even when coarse-grained cBN is used. That is, the present invention has the following configuration.
- a cubic boron nitride sintered body composed of cubic boron nitride and a binder phase The content of cubic boron nitride is in the range of 82% by volume to 98% by volume,
- an isolated binder phase having an area of 0.05 ⁇ m 2 or more and 0.5 ⁇ m 2 or less has two or more protruding portions with respect to the cubic boron nitride.
- the side length perpendicular to the tip direction of the first step from the tip of the projection is A1
- the side length parallel to the tip is B1
- the side length perpendicular to the tip direction of the second step from the tip is When A2 and the parallel side length is B2, the area ratio of the isolated binder phase having a convex portion in which A1 / B1 is 1 to 10 times A2 / B2, the area is 0.05 ⁇ m 2 or more and 0.0.
- Cubic boron nitride sintered body characterized by being 25% or more of the entire isolated binder phase in the range of 5 ⁇ m 2 or less.
- a cubic boron nitride sintered body tool comprising the cubic boron nitride sintered body according to any one of (1) to (6) at least in a portion serving as a cutting edge.
- the above-mentioned problems can be solved, and a cubic boron nitride sintered body having a high content of cubic boron nitride having both excellent fracture resistance and wear resistance can be obtained. Further, by using the cubic boron nitride sintered body of the present invention, it is possible to provide a cubic boron nitride sintered body tool suitable for continuous cutting / intermittent cutting of cast iron / sintered alloy under roughing conditions. .
- FIG. 1 (a) is a schematic diagram of the shape of the interface between the binder phase and the cBN focused on in the present invention.
- FIG.1 (b) is an example of the sintered compact structure
- the present invention relates to a cubic boron nitride sintered body composed of cubic boron nitride and a binder phase, wherein the content of cubic boron nitride is in the range of 82% by volume to 98% by volume, and the cubic nitride
- an isolated binder phase having an area in the range of 0.05 ⁇ m 2 or more and 0.5 ⁇ m 2 or less has two or more protruding portions with respect to cubic boron nitride, and the protruding
- the side length perpendicular to the tip direction of the first convex part from the tip of the part is A1
- the side length parallel to the tip part is B1
- the side length perpendicular to the tip direction of the second stage convex part is A2.
- the cubic boron nitride sintered body of the present invention is characterized in that the content of cubic boron nitride is 82 volume% or more and 98 volume% or less. This means that the higher the cBN content, the smaller the average area of the isolated binder phase becomes, and it is difficult to become a starting point of falling off. This is because it cannot be sintered. For this reason, it is more preferable that the content of the cubic boron nitride is in the range of 86 volume% to 95 volume%.
- an isolated bonded phase having an area in the range of 0.05 ⁇ m 2 or more and 0.5 ⁇ m 2 or less has two in comparison with the cubic boron nitride. It has the convex part more than a step, It is characterized by the above-mentioned. Thereby, the shape of the interface between the cubic boron nitride and the binder phase becomes a wedge shape, and the effect of suppressing the falling of the cubic boron nitride is exhibited.
- the side length perpendicular to the tip direction of the first step convex portion from the tip of the convex portion is A1
- the side length parallel to the tip direction is B1
- the side length perpendicular to the tip direction of the second step convex portion is A2.
- the parallel side length is B2
- the area is 0.05 ⁇ m 2 to 0.5 ⁇ m It is characterized by being 25% or more of the entire isolated binder phase in the range of 2 or less.
- the isolated binder phase in which the area ratio of the isolated binder phase having a convex portion in which A1 / B1 is 1 to 10 times that of A2 / B2 is in the range of 0.05 ⁇ m 2 to 0.5 ⁇ m 2 It is more preferable that it is 40% or more of the whole. More preferably, the area ratio of the binder phase region is 50% or more.
- the binder phase is a simple substance of at least one element selected from the group consisting of W, Co, Al, Zr, Ni, Cr, and Mo, a mutual solid solution, It is preferable to contain any one or more of carbide, nitride, carbonitride, boride and oxide.
- the particle diameter of the cubic boron nitride after sintering is 1.5 ⁇ m or more and 10 ⁇ m or less is 50% by volume or more of the entire cubic boron nitride. This is for maintaining high toughness in cutting under roughing conditions.
- the area ratio of the isolated binder phase having an area exceeding 0.5 ⁇ m 2 is preferably 20% or less of the total binder phase. This is to reduce the binder phase having a large area that is the starting point of dropout.
- the present inventors succeeded in forming two or more convex portions that act as wedges at the interface between the binder phase and cBN.
- the raw material powder constituting the binder phase is blended at a certain mass ratio, and after heat treatment, mixed using a ball mill comprising a cemented carbide pot and a ⁇ 3.5 mm cemented carbide ball.
- a ball mill comprising a cemented carbide pot and a ⁇ 3.5 mm cemented carbide ball.
- mixing using the above ball mill is performed before the heat treatment. Grinding and mixing were performed using a high apparatus.
- the sintering pressure range is preferably 6.5 to 7.5 GPa, and the maximum temperature during sintering is preferably 1700 to 1900 ° C.
- the cBN sintered body tool of the present invention is composed only of a cBN sintered body tool having the cBN sintered body of the present invention at least at a portion that becomes a cutting edge of a base material such as cemented carbide or cermet, or a cBN sintered body.
- CBN sintered body tool can be produced according to a known method.
- a hard ceramic coating layer may be provided on the surface of the cBN sintered body.
- Specific examples of the cBN sintered body tool include a cutting tool.
- Examples and Comparative Examples ⁇ Sintered body preparation ⁇ (Samples 1 to 4) After selecting WC powder, Co powder and Al powder and Zr, Ni, Cr and Mo as shown in Table 1 and blending them in a mass ratio of 60: 25: 10: 5, a cemented carbide pot and After mixing using a ball mill consisting of ⁇ 3.5 mm balls, the mixed powder was kept at 1000 ° C. for 30 minutes in a vacuum and subjected to heat treatment. Thereafter, the heat-treated mixed powder was pulverized with an apparatus having a high pulverization capability comprising a zirconia pot and a silicon nitride ball having a diameter of 0.3 mm to obtain a binder powder.
- these binder powders and cubic boron nitride powder having a particle size in the range of 0.5 ⁇ m or more and 3.0 ⁇ m or less are uniformly mixed at a blending ratio of 90% by volume using the above ball mill.
- the mixed powder was kept at 1000 ° C. for 20 minutes in a vacuum furnace and degassed.
- the pressure was increased to 7.0 GPa using an ultrahigh pressure apparatus, and then the temperature was raised to 1300 ° C. and kept at this pressure temperature condition for 10 minutes. Subsequently, the temperature was raised to 1800 ° C. while maintaining the pressure with the same apparatus, held for about 5 minutes, and then sintered at 1500 ° C. for 20 minutes to produce a cubic boron nitride sintered body containing cubic boron nitride and a binder phase. did.
- binder powders were produced in the same manner as Samples 1 to 4.
- binder powders and cubic boron nitride powder having a particle size of 0.5 ⁇ m or more and 3.0 ⁇ m or less were converted into 98, 95, 85, 82 as shown in Table 1 using the above-mentioned ball mill.
- Cubic boron nitride sintered bodies were produced in the same manner as in Samples 1 to 4 by mixing uniformly at a blending ratio of 78% by volume.
- Example 10 WC powder, Co powder, and Al powder were blended at a mass ratio of 60:25:15, and then a binder powder was produced in the same manner as in samples 1 to 4.
- these binder powders and a cubic boron nitride powder having a particle diameter of 0.5 ⁇ m or more and 3.0 ⁇ m or less are uniformly mixed using the above ball mill at a blending ratio such that the cubic boron nitride is 90% by volume.
- a cubic boron nitride sintered body was produced in the same manner as Samples 1 to 4.
- Example 11 and 12 As shown in Table 1, TiN powder or Al 2 B 3 powder and cubic boron nitride powder having a particle size of 0.5 ⁇ m or more and 3.0 ⁇ m or less are adjusted to 90 volume% of cubic boron nitride using the above ball mill. Cubic boron nitride sintered bodies were produced in the same manner as in Samples 1 to 4 by mixing uniformly at various blending ratios.
- binder powders were produced in the same manner as Samples 1 to 4.
- binder powders and cubic boron nitride powder having a particle size of 0.5 ⁇ m or more and 3.0 ⁇ m or less as shown in Table 1 are adjusted to 90% by volume using the above-mentioned ball mill.
- Cubic boron nitride sintered bodies were produced in the same manner as Samples 1 to 4 except that they were uniformly mixed at a blending ratio and the sintering pressure and sintering temperature were as shown in Table 1.
- binder powders were produced in the same manner as Samples 1 to 4. Next, these binder powders and a cubic boron nitride powder having a particle size of 0.1 ⁇ m or more and 1.0 ⁇ m or less are uniformly mixed at a blending ratio such that the cubic boron nitride is 90% by volume using the above ball mill. did. Thereafter, the mixed powder was kept at 1000 ° C. for 20 minutes in a vacuum furnace and degassed.
- the pressure was increased to 7.0 GPa using an ultrahigh pressure apparatus, and then the temperature was raised to 1300 ° C. and kept at this pressure temperature condition for 10 minutes. Subsequently, the temperature was raised to 1800 ° C. while maintaining the pressure with the same apparatus, and the mixture was held and sintered for about 30 minutes to produce a cubic boron nitride sintered body containing cubic boron nitride and a binder phase.
- the isolated binder phase having an area in the range of 0.05 ⁇ m 2 or more and 0.5 ⁇ m 2 or less has two or more protrusions with respect to cubic boron nitride, and the protrusions
- the side length perpendicular to the tip direction of the first convex portion from the tip of A1 is A1
- the side length parallel to the tip direction is B1
- the side length perpendicular to the tip direction of the second convex portion is A2
- B2 is B2
- an isolated bonded phase having a convex portion in which A1 / B1 is 1 to 10 times that of A2 / B2 is a bonded phase having an area in the range of 0.05 ⁇ m 2 to 0.5 ⁇ m 2
- Table 1 The area ratio of the entire area was determined by image processing and shown in Table 1.
- the ratio of the area of the isolated binder phase with an area exceeding 0.5 ⁇ m 2 to the whole binder phase was determined and shown in Table 1. Further, the ratio of the area occupied by the cBN particles having a particle diameter of 1.5 ⁇ m or more and 10 ⁇ m or less to the entire cBN is obtained by image processing, and is assumed to be distributed in the same direction in the depth direction. It was shown to. In image processing, binarization based on color depth was carried out. Elemental analysis specified in advance that black was a compound of cBN, gray was a compound of Al and Co, and white was a compound of W. Based on this, The cBN content, binder phase region and shape were determined.
- the image processing as described above should increase the number of fields of view and be discussed with asymptotic values. This time, five 10000 times SEM images taken in an arbitrary vertical range of 9 ⁇ m and horizontal 12 ⁇ m were measured, and the average of the measured values was obtained. Moreover, when the convex part was not a combination of rectangles, the calculation was performed from the average value of the two sides.
- one of the side lengths perpendicular to the tip direction of the first convex portion from the tip is A1a
- the other is A1b
- the average value (A1a + A1b) / 2 is A1
- one of the side lengths parallel to the tip direction is also the same.
- B1a was set as B1b
- the average value (B1a + B1b) / 2 was set as B1.
- a cutting tool was created using the sintered body.
- the cutting tool was created by brazing the sintered body manufactured by the above manufacturing method onto a base material made of cemented carbide and molding the sintered body into a predetermined shape (ISO model number: CNGA120408). Using this cutting tool, wear resistance was evaluated by continuous cutting of a sintered alloy under the following conditions.
- An isolated binder phase having a convex portion in which the area is in the range of 0.05 ⁇ m 2 to 0.5 ⁇ m 2 and A1 / B1 is 1 to 10 times A2 / B2 has an area of 0.05 ⁇ m 2.
- Samples 1 to 8 in which the area ratio of the entire binder phase in the range of 0.5 ⁇ m 2 or less is 25% or more have high wear resistance and achieved a long life.
- Sample 9 is considered to have a short life because the area ratio of the binder phase is high, but the cBN content is low and the wear resistance is reduced.
- the area ratio occupied by the region of the binder phase is less than 25%, and it is considered that the lifetime of the sample 10 was short due to the loss of the binder phase.
- Samples 11, 12, and 13 did not have the above binder phase region, and had a particularly short life.
- Sample 14 although the area ratio occupied by the region of the binder phase is as large as 40%, it is considered that the cBN is fine and the toughness is insufficient and the life is short.
- Sample 10 has a high cBN content of 90% by volume, the area ratio occupied by the region of the binder phase is less than 25%, which is considered to have a short life due to the loss of the binder phase.
- Samples 11, 12, and 13 also had a high cBN content of 90% by volume, but the region of the binder phase did not exist and the lifetime was particularly short.
- the area ratio occupied by the region of the binder phase is as large as 40%, and cBN is fine, so that the strength is high and the lifetime is long.
- Samples 11 and 12 have a high cBN content of 90% by volume, but have a short life because ceramics with low thermal conductivity are used for the binder phase. Since the sample 13 has a high cBN content of 90% by volume and uses a cemented carbide with high thermal conductivity for the binder phase, it has a relatively long life. It is considered that Sample 14 has low toughness due to fine cBN particles, thermal cracks progress, and has a short life due to defects.
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Abstract
Description
立方晶窒化硼素の含有率が82体積%以上98体積%以下の範囲にあり、
かつ当該立方晶窒化硼素焼結体の断面において、面積が0.05μm2以上0.5μm2以下の範囲にある孤立した結合相が、立方晶窒化硼素に対して二段以上の凸部を有し、
かつ該凸部の先端から一段目の凸部の、先端方向に垂直な辺長をA1、平行な辺長をB1とし、また先端から二段目の凸部の先端方向に垂直な辺長をA2、平行な辺長をB2とした場合、A1/B1がA2/B2の1倍以上10倍以下である凸部を有する孤立した結合相の面積割合が、面積が0.05μm2以上0.5μm2以下の範囲にある孤立した結合相全体の25%以上であることを特徴とする立方晶窒化硼素焼結体。
(2)前記結合相がWと、Coと、Alと、Zr、Ni、Cr、Moからなる群より少なくとも1つ選択される元素の単体、相互固溶体、炭化物、窒化物、炭窒化物、硼化物及び酸化物のいずれか一つ以上とを含むことを特徴とする前記(1)に記載の立方晶窒化硼素焼結体。
(3)前記立方晶窒化硼素の焼結後の粒径が1.5μm以上10μm以下である粒子が、立方晶窒化硼素全体の50体積%以上であることを特徴とする前記(1)又は(2)に記載の立方晶窒化硼素焼結体。
(4)前記A1/B1がA2/B2の1倍以上10倍以下である凸部を有する孤立した結合相の面積割合が、面積が0.05μm2以上0.5μm2以下の範囲にある結合相全体の40%以上であることを特徴とする前記(1)~(3)のいずれかに記載の立方晶窒化硼素焼結体。
(5)前記立方晶窒化硼素焼結体の断面において、面積が0.5μm2を超える孤立した結合相の面積割合が、結合相全体の20%以下であることを特徴とする前記(1)~(4)のいずれかに記載の立方晶窒化硼素焼結体。
(6)前記立方晶窒化硼素の含有率が86体積%以上95体積%以下の範囲にあることを特徴とする前記(1)~(5)のいずれかに記載の立方晶窒化硼素焼結体。
(7)少なくとも刃先となる部分に前記(1)~(6)のいずれかに記載の立方晶窒化硼素焼結体を有することを特徴とする立方晶窒化硼素焼結体工具。
これにより結合相のくさびによる立方晶窒化硼素粒子の脱落抑制効果がさらに強くなる。前記A1/B1がA2/B2の1倍以上10倍以下である凸部を有する孤立した結合相の面積割合が、面積が0.05μm2以上0.5μm2以下の範囲にある孤立した結合相全体の40%以上であると、より好ましい。当該結合相の領域の面積割合が50%以上であると更に好ましい。
このとき焼結圧力範囲は6.5~7.5GPa、焼結時の最高温度は1700~1900℃とすることが好ましい。
cBN焼結体工具としては、具体的には切削工具等が挙げられる。
≪焼結体の作製≫
(試料1~4)
WC粉末、Co粉末及びAl粉末と、表1に示す通りZr、Ni、Cr、Moから1種類を選択し、60:25:10:5の質量比で配合した後、超硬合金製ポット及びφ3.5mmのボールとからなるボールミルを用いて混合した後、この混合粉末を真空中で1000℃に30分間保ち熱処理を施した。その後、ジルコニア製ポット及びφ0.3mmの窒化シリコン製ボールとからなる粉砕能力の高い装置で、上記の熱処理済み混合粉末を粉砕して結合材粉末を得た。
次にこれら結合材粉末と粒径が0.5μm以上3.0μm以下の範囲にある立方晶窒化硼素粉末を上記のボールミルを用いて立方晶窒化硼素が90体積%となるような配合比で均一に混合した。その後、この混合粉末を真空炉にて1000℃に20分間保持し、脱ガスした。
さらに、この脱ガス済みの混合粉末をMo製カプセルに充填後、超高圧装置を用いて7.0GPaまで加圧した後、1300℃まで昇温してこの圧力温度条件に10分間保持した。続いて同装置により圧力を保ったまま1800℃まで昇温し、約5分間保持した後1500℃で20分間焼結させ、立方晶窒化硼素と結合相を含む立方晶窒化硼素焼結体を製造した。
WC粉末、Co粉末、Al粉末及びZr粉末を60:25:10:5の質量比で配合した後、試料1~4と同様の方法で結合材粉末を製作した。
次にこれら結合材粉末と粒径が0.5μm以上3.0μm以下である立方晶窒化硼素粉末を上記のボールミルを用いて立方晶窒化硼素が表1に示す通り98、95、85、82、78体積%となるような配合比で均一に混合し、試料1~4と同様の方法で立方晶窒化硼素焼結体を製造した。
WC粉末、Co粉末及びAl粉末を60:25:15の質量比で配合した後、試料1~4と同様の方法で結合材粉末を製作した。
次にこれら結合材粉末と粒径が0.5μm以上3.0μm以下である立方晶窒化硼素粉末を上記のボールミルを用いて立方晶窒化硼素が90体積%となるような配合比で均一に混合し、試料1~4と同様の方法で立方晶窒化硼素焼結体を製造した。
表1に示す通りTiN粉末またはAl2B3粉末と粒径が0.5μm以上3.0μm以下である立方晶窒化硼素粉末を上記のボールミルを用いて立方晶窒化硼素が90体積%となるような配合比で均一に混合し、試料1~4と同様の方法で立方晶窒化硼素焼結体を製造した。
WC粉末、Co粉末、Al粉末及びZr粉末を60:25:10:5の質量比で配合した後、試料1~4と同様の方法で結合材粉末を製作した。
次にこれら結合材粉末と、表1に示す通り粒径が0.5μm以上3.0μm以下である立方晶窒化硼素粉末を上記のボールミルを用いて立方晶窒化硼素が90体積%となるような配合比で均一に混合し、焼結圧力、焼結温度を表1に示す通りにした以外は試料1~4と同様の方法で立方晶窒化硼素焼結体を製造した。
WC粉末、Co粉末、Al粉末及びZr粉末を60:25:10:5の質量比で配合した後、試料1~4と同様の方法で結合材粉末を製作した。
次にこれら結合材粉末と粒径が0.1μm以上1.0μm以下である立方晶窒化硼素粉末を上記のボールミルを用いて立方晶窒化硼素が90体積%となるような配合比で均一に混合した。その後、この混合粉末を真空炉にて1000℃に20分間保持し、脱ガスした。
さらに、この脱ガス済みの混合粉末をMo製カプセルに充填後、超高圧装置を用いて7.0GPaまで加圧した後、1300℃まで昇温してこの圧力温度条件に10分間保持した。続いて同装置により圧力を保ったまま1800℃まで昇温し、約30分間保持して焼結させ、立方晶窒化硼素と結合相を含む立方晶窒化硼素焼結体を製造した。
上記、製造方法により得られた14種の焼結体に対して、面出し加工により平滑な観察面を作成して立方晶窒化硼素の組織を走査型電子顕微鏡(以下SEMと記す)により観察した。SEMによる組織観察は10nmの粒径が識別可能な10000倍の視野で行った。図1(b)に試料1の観察結果を示す。
得られたSEM画像から、面積が0.05μm2以上0.5μm2以下の範囲にある孤立した結合相が、立方晶窒化硼素に対して二段以上の凸部を有し、かつ該凸部の先端から一段目の凸部の、先端方向に垂直な辺長をA1、平行な辺長をB1とし、また二段目の凸部の先端方向に垂直な辺長をA2、平行な辺長をB2とした場合、A1/B1がA2/B2の1倍以上10倍以下である凸部を有する孤立した結合相が、面積が0.05μm2以上0.5μm2以下の範囲にある結合相全体に占める面積割合を画像処理より求め、表1に示した。また焼結体断面において、面積が0.5μm2を超える孤立した結合相の結合相全体に占める面積の割合を求め、表1に示した。また、粒径が1.5μm以上10μm以下であるcBN粒子のcBN全体に占める面積の割合を画像処理より求め、深さ方向にも同様の割合で分布していると見なし、体積%として表1に示した。
画像処理では色の濃さによる二値化を実施したが、予め元素分析により黒色がcBN、灰色がAl及びCoの化合物、白色がWの化合物であることを特定しており、これに基づいてcBN含有率、結合相の領域及び形状の判定を行なった。
また凸部が長方形の組み合わせでない場合、それぞれの2辺の平均値から算出を行った。例えば先端から一段目の凸部の、先端方向に垂直な辺長の一方をA1a、他方をA1bとしてそれらの平均値(A1a+A1b)/2をA1とし、同じく先端方向に平行な辺長の一方をB1a、他方をB1bとしてそれらの平均値(B1a+B1b)/2をB1としとした。
被削材 :0.8C-2.0Cu-残Fe
(JPMA記号:SMF4040)
硬度HRB78 φ100丸棒
切削条件:切削速度Vc=200m/min.、
送り量f=0.2mm/rev.、
切り込み量ap=0.3mm、
湿式切削
寿命判定:逃げ面からの観察で刃先の稜線が、切削前の刃先稜線より200μm以上摩耗した状態を寿命と定め、寿命に到達するまでの時間を計測し、表1に示した。
試料9は、上記結合相の領域の占める面積割合は高いが、cBN含有率が低く、耐摩耗性が低下したため短寿命となったと考えられる。試料10は上記結合相の領域の占める面積割合が25%より小さく、結合相の脱落のため短寿命となったと考えられる。試料11、12、13は上記結合相の領域が存在せず、特に短寿命となった。試料14は上記結合相の領域の占める面積割合が40%と大きいものの、cBNが微粒のため、靱性が不足して短寿命となったと考えられる。
続いて、評価1と同様の切削工具を用いて下記条件で焼結合金の断続切削より、耐欠損性評価を行なった。
<切削試験条件>
被削材 :0.8C-2.0Cu-残Fe
(JPMA記号:SMF4040)
焼入硬度HRA69 φ100焼入ギア
切削条件:切削速度Vc=120m/min.、
送り量f=0.1mm/rev.、
切り込み量ap=0.25mm、
乾式切削
寿命判定:逃げ面からの観察で刃先の稜線が、切削前の刃先稜線より200μm以上摩耗するか若しくは、刃先の急激な欠損により切削を継続できなくなった状態を寿命と定め、寿命に到達するまでの時間を計測し、表1に示した。
同じcBN含有率の試料1~4で比較した場合には、上記結合相の領域の占める面積割合の高い順に長寿命となった。cBN含有率が異なる試料1、5~9で比較した場合、cBN含有率が90体積%以上の試料1、5、6では長寿命を達成したが、含有率が85体積%以下では欠損が発生し、寿命が低下した。
試料10はcBN含有率が90体積%と高いものの、上記結合相の領域の占める面積割合が25%より小さく、結合相の脱落のため短寿命となったと考えられる。試料11、12、13もcBN含有率は90体積%と高いが、上記結合相の領域が存在せず、特に短寿命となった。試料14は上記結合相の領域が占める面積割合が40%と大きく、cBNが微粒のため、強度が高く、長寿命となったと考えられる。
続いて、評価1、2と同様の切削工具を用いて下記条件で鋳鉄のフライス加工より、耐摩耗性評価を行なった。
<切削試験条件>
被削材 :FC250
切削条件:切削速度Vc=1700m/min.、
送り量f=0.15mm/rev.、
切り込み量ap=0.5mm、
乾式切削
寿命判定:逃げ面からの観察で刃先の稜線が、切削前の刃先稜線より200μm以上摩耗した状態を寿命と定め、寿命に到達するまでの時間を計測し、表1に示した。
同じcBN含有率の試料1~4で比較した場合には、上記結合相の領域の占める割合の高い順に長寿命となった。cBN含有率が異なる試料1、5~9で比較した場合、含有率90体積%以上の試料1、5、6では長寿命を達成したが、含有率が85体積%以下では熱亀裂を起点に欠損が発生し、寿命が低下した。試料10はcBN含有率が90体積%と高いため、長寿命を達成した。
試料11、12はcBN含有率が90体積%と高いものの、結合相に熱伝導率の低いセラミックスを使用しているため、短寿命となった。試料13はcBN含有率が90体積%と高く、結合相に熱伝導率の高い超硬合金を使用しているため、比較的長寿命となっている。試料14はcBNが微粒のため靱性が低く、熱亀裂が進展し、欠損による短寿命となったと考えられる。
Claims (7)
- 立方晶窒化硼素及び結合相からなる立方晶窒化硼素焼結体であって、
立方晶窒化硼素の含有率が82体積%以上98体積%以下の範囲にあり、
かつ当該立方晶窒化硼素焼結体の断面において、面積が0.05μm2以上0.5μm2以下の範囲にある孤立した結合相が、立方晶窒化硼素に対して二段以上の凸部を有し、
かつ該凸部の先端から一段目の凸部の、先端方向に垂直な辺長をA1、平行な辺長をB1とし、また先端から二段目の凸部の先端方向に垂直な辺長をA2、平行な辺長をB2とした場合、A1/B1がA2/B2の1倍以上10倍以下である凸部を有する孤立した結合相の面積割合が、面積が0.05μm2以上0.5μm2以下の範囲にある孤立した結合相全体の25%以上であることを特徴とする立方晶窒化硼素焼結体。 - 前記結合相がWと、Coと、Alと、Zr、Ni、Cr、Moからなる群より少なくとも1つ選択される元素の単体、相互固溶体、炭化物、窒化物、炭窒化物、硼化物及び酸化物のいずれか一つ以上とを含むことを特徴とする請求項1に記載の立方晶窒化硼素焼結体。
- 前記立方晶窒化硼素の焼結後の粒径が1.5μm以上10μm以下である粒子が、立方晶窒化硼素全体の50体積%以上であることを特徴とする請求項1又は2に記載の立方晶窒化硼素焼結体。
- 前記A1/B1がA2/B2の1倍以上10倍以下である凸部を有する孤立した結合相の面積割合が、面積が0.05μm2以上0.5μm2以下の範囲にある結合相全体の40%以上であることを特徴とする請求項1~3のいずれかに記載の立方晶窒化硼素焼結体。
- 前記立方晶窒化硼素焼結体の断面において、面積が0.5μm2を超える孤立した結合相の面積割合が、結合相全体の20%以下であることを特徴とする請求項1~4のいずれかに記載の立方晶窒化硼素焼結体。
- 前記立方晶窒化硼素の含有率が86体積%以上95体積%以下の範囲にあることを特徴とする請求項1~5のいずれかに記載の立方晶窒化硼素焼結体。
- 少なくとも刃先となる部分に請求項1~6のいずれかに記載の立方晶窒化硼素焼結体を有することを特徴とする立方晶窒化硼素焼結体工具。
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CA 2785696 CA2785696C (en) | 2010-10-18 | 2011-10-18 | Cubic boron nitride sintered body and cubic boron nitride sintered body tool |
CN201180005244.3A CN102712047B (zh) | 2010-10-18 | 2011-10-18 | 立方氮化硼烧结体和立方氮化硼烧结体工具 |
KR1020127014616A KR101363178B1 (ko) | 2010-10-18 | 2011-10-18 | 입방정 질화붕소 소결체, 및 입방정 질화붕소 소결체 공구 |
US13/510,429 US9120707B2 (en) | 2010-10-18 | 2011-10-18 | Cubic boron nitride sintered body and cubic boron nitride sintered body tool |
JP2012502361A JP5568827B2 (ja) | 2010-10-18 | 2011-10-18 | 立方晶窒化硼素焼結体、及び立方晶窒化硼素焼結体工具 |
EP11834346.6A EP2631027B1 (en) | 2010-10-18 | 2011-10-18 | Cubic boron nitride sintered body and cubic boron nitride sintered body tool |
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WO2014065131A1 (ja) * | 2012-10-26 | 2014-05-01 | 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およびその製造方法 |
JP2019515864A (ja) * | 2016-04-11 | 2019-06-13 | イルジン ダイアモンド カンパニー リミテッド | 多結晶立方晶窒化ホウ素及びその製造方法 |
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JP6095162B2 (ja) * | 2013-03-29 | 2017-03-15 | 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 |
JP6291995B2 (ja) * | 2014-04-18 | 2018-03-14 | 住友電気工業株式会社 | 立方晶窒化ホウ素多結晶体、切削工具、耐摩工具、研削工具、および立方晶窒化ホウ素多結晶体の製造方法 |
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JP6607470B2 (ja) * | 2016-11-17 | 2019-11-20 | 住友電工ハードメタル株式会社 | 焼結体およびそれを含む切削工具 |
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Also Published As
Publication number | Publication date |
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CA2785696A1 (en) | 2012-04-26 |
EP2631027A1 (en) | 2013-08-28 |
EP2631027A4 (en) | 2014-09-24 |
US20120230786A1 (en) | 2012-09-13 |
CA2785696C (en) | 2014-08-12 |
US9120707B2 (en) | 2015-09-01 |
KR20120099249A (ko) | 2012-09-07 |
JPWO2012053507A1 (ja) | 2014-02-24 |
JP5568827B2 (ja) | 2014-08-13 |
KR101363178B1 (ko) | 2014-02-13 |
CN102712047A (zh) | 2012-10-03 |
EP2631027B1 (en) | 2015-09-30 |
CN102712047B (zh) | 2015-01-14 |
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