WO1999021806A1 - Agglomere ceramique a base d'alumine et procede de production dudit agglomere - Google Patents

Agglomere ceramique a base d'alumine et procede de production dudit agglomere Download PDF

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WO1999021806A1
WO1999021806A1 PCT/JP1998/004727 JP9804727W WO9921806A1 WO 1999021806 A1 WO1999021806 A1 WO 1999021806A1 JP 9804727 W JP9804727 W JP 9804727W WO 9921806 A1 WO9921806 A1 WO 9921806A1
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Prior art keywords
alumina
volume
sintered body
cutting
wear
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PCT/JP1998/004727
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English (en)
French (fr)
Inventor
Toyoshige Sasaki
Mitsuyoshi Nagano
Eiji Okuma
Shinzou Mitomi
Tetsuo Uchiyama
Shigeo Inoue
Haruka Tamura
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Nippon Tungsten Co., Ltd.
Riken Corporation
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Application filed by Nippon Tungsten Co., Ltd., Riken Corporation filed Critical Nippon Tungsten Co., Ltd.
Priority to EP98947943A priority Critical patent/EP0963962A4/en
Priority to CA002275468A priority patent/CA2275468A1/en
Priority to US09/319,618 priority patent/US6133182A/en
Publication of WO1999021806A1 publication Critical patent/WO1999021806A1/ja

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Definitions

  • the present invention relates to an alumina-based ceramic having high hardness, excellent wear resistance, high strength and high whip properties, and particularly suitable for cutting-cutting tools and wear-resistant members.
  • a 1 2 ⁇ 3 ceramics is excellent in wear resistance at high hardness, is in the ceramic material 0 fee is easy densification relatively sintering, conventional tool steels, high speed - steel, It is used as a cutting tool for high-speed machining and high-temperature machining where it is difficult to use tool materials such as cemented carbide, and as wear-resistant members.
  • the sintered body obtained by adding WC to A 1 2 ⁇ 3 strength, toughness is greatly improved, since it is 0 and a high hardness, has been attempted application to wear-resistant member.
  • the purpose of this invention is excellent while maintaining the oxidation resistance and wear resistance, strength and toughness - is to provide an A 1 2 0 3 based ceramic which is remarkably improved.
  • the invention includes a 5-7 0% by volume WC, T i (C, N ) solid solution containing 5-7 0 volume%, a dense sintered body and the balance of A 1 2 ⁇ 3
  • This sintered body has high strength and toughness, and exhibits excellent wear resistance even at high temperatures.
  • the content of WC is specified in the range of 5 to 70% by volume. This is because when the content of WC is less than 5% by volume, the WC phase is reduced and the strength and the toughness of the sintered body are not improved. On the other hand, if the content exceeds 70% by volume, it becomes difficult to obtain a dense and dense sintered body, and the oxidation resistance at high temperatures tends to decrease. However, by applying HIP (Hot Isostatic Pressing Sintering) to the sintered body with a relative density of 95% or more by hot pressing etc., WC addition up to 70%-% A dense sintered body can be obtained even in the amount.
  • HIP Hot Isostatic Pressing Sintering
  • the effect of improving strength and toughness depends on the added amount of W-C, but the amount of WC, which has poor self-sintering properties, is 70% by volume or more. In the case of-, the sinterability is reduced and a dense sintered body cannot be obtained.
  • the molar ratio of C: -N in Ti (C, N) is effective in the range of 1: 9 to 9: 1.
  • a 1 2 ⁇ 3 based ceramic material sintered body of the present invention by containing WC and T i (C, N) 0 predetermined amount both at the same time, has excellent wear resistance, yet high - have It has both strength and toughness.
  • phase walking • becomes the composite compound phase between the a 1 2 ⁇ 3 occurs, these exist, strength and • hardness, thereby deteriorating the abrasion resistance.
  • the sintering - a big feature that aid does not lead to deterioration of the characteristics occurring due this yo 0 UNA auxiliaries that improve only sinterability is not used at all, a 1 2 0 3, WC and
  • the free carbon contained in the raw material powder will be present as foreign matter having a size of several m to several + m-m in the sintered body, resulting in a decrease in bending strength and, consequently, during cutting. May cause loss.
  • this free carbon 1.
  • Metals up to 250% by volume easily form compounds with carbon such as W and Ti, and the addition of metals that do not adversely affect the characteristics of the sintered body is permissible.
  • the carbon is removed by combining this C with W or Ti during sintering to form WC or TiC. -Both lead to improved reliability.
  • the A12 ⁇ 3-based ceramic sintered body of the present invention is blended to have a predetermined composition.
  • the powder is manufactured by thoroughly mixing the powders and hot pressing at 1600-1900 ° C for 0.5-5 hours in an inert gas atmosphere at a pressure of 50-300 kgf Zcm 2 .
  • a slight amount of binder is added to the powder, and molding is performed using mold molding, cold isostatic pressing, or both, and then at 1600 to 1900 in an inert gas atmosphere-0.5 to 5 hours. It may be manufactured by sintering and, in some cases, hot isostatic sintering at 1400 to 1700 ° C, an inert atmosphere, and a pressure of 500 to 2000 atm.
  • -Table 1 shows the relationship between the composition subjected to the test and various characteristics.
  • No. 1 to No. 14 fall within the composition range of the present invention
  • No. 15 to N5 o.25 fall outside the composition range
  • No. 26 to No. 29 Here is an example of a ceramic tool.
  • a predetermined amount of raw material powder with an average particle size of 2 / im or less is weighed, put into a ball mill, mixed with a methanol solvent for 20 hours, and the dried and granulated prepared powder is put into It was then sintered at a temperature of 1700 ° C and a press pressure of 20 to 25 MPa for 600 minutes.
  • the sintered body was cut and ground to form a 3 ⁇ 4 ⁇ 40 mm bent test piece and a cutting tip of JIS SNGN432, which were subjected to various tests.
  • the abrasion resistance test was carried out as follows: FCD450 ⁇ 250 ⁇ -500 mm, cutting speed 20 OmZmin, depth of cut 1.5 mm, feed 0.2
  • the fracture resistance test is used to check the resistance of the tool to chipping. Using a work material ( ⁇ 250 x 500 mm) that has four cutouts and is subjected to impact, -The cutting speed is 20 OmZmin, the cutting depth is 1.5 mm, and the feed rate is changed.
  • a chilled steel cutting test was performed using a work material of ⁇ 400-500 mm, a cutting speed of ⁇ 7 Om / min, a cutting depth of 1.5 mm, and a feed rate of 2 mmZr ev.
  • the flank wear becomes 1.
  • Omm and cutting becomes impossible-the time is defined as the cutting time and the cutting time is compared with the conventional tool. • From the results, the following became clear.
  • C has low oxidation resistance, so its wear resistance decreases.
  • the rate of decrease in wear resistance is proportional to the added amount of WC, and the performance as a tool is exhibited at 40 vo 1% or less, preferably 30 vo 1% or less.
  • oxidation of WC is suppressed and wear does not progress because there is no increase in the temperature of the cutting edge during cutting.
  • 0 WC and Ti (C, N) are effective when the total amount of addition is 40% by volume or more. However, a remarkable effect is exhibited at 50 to 80% by volume. If it is less than 50% by volume, the ratio of alumina is high, and the toughness is reduced. If it is more than 80% by volume,-the sinterability is reduced, and the pores are present in the sintered body. As a result, the strength and the toughness are reduced. As a result, the performance as a tool is reduced.
  • WC is 5 to 70% by volume and Ti (C, N) is 5 to 70%.
  • the bonding force between crystal grains is strengthened by the effect of WC, and further, wear resistance is improved by Ti (C, N), adhesive wear is reduced, and chilled- ⁇ ⁇ As seen in the example of steel cutting, high-efficiency cutting of difficult-to-cut materials has become possible.
  • T i C T i N ratio of T i (C, N) between 1: 9 and 9: 1, but T i N as in No. 15
  • the content was too large, the effect of adding TiN was exhibited, and early fracture was recognized at low hardness.
  • the number of dents 1 is too large in the range of No. 16, the effect of adding TiC appears, the sinterability is slightly reduced, and pores are likely to remain. Premature wear occurred.
  • conventional ceramic tools shown in No. 26 to No. 29 in Table 1 have low toughness and are used for metal materials called difficult-to-cut materials such as chilled steel and forged steel.
  • -Alumina cutting tools are excellent in wear resistance, but they cannot be used in applications that require tool toughness such as interrupted cutting and difficult-to-cut materials due to low material strength.
  • Carbide tools have high fracture strength due to high strength and toughness, but tend to wear out early due to cutting heat5 during cutting. This is particularly noticeable in high-speed cutting.
  • S i 3 N 4 -tools are ceramics that do not contain metal components, so high-speed cutting is possible.. High strength among ceramics Z
  • High fracture toughness due to high toughness Work material-Medium Reaction with the iron component of the steel causes cohesion Z
  • the black ceramic, the super hard coating 0, and the like had a short life as a result of abrasion and micro chipping as a result of the loss of crystal particles in addition to the chipped chipping.
  • the A 1 -based ceramic sintered body according to the present invention can be used for a wide range of members where toughness and wear resistance are required.

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Description

- 明 細 書
* アルミナ基セラミックス焼結体とその製造方法
- 技術分野
5 本発明は、 高い硬度を有し、 耐摩耗性に優れ、 高強度、 高鞭性で、 とくに切 - 削工具ゃ耐摩耗部材に適したアルミナ基セラミックスに関する。
• 背景技術
* A 1 2〇3セラミックスは、 高硬度で耐摩耗性に優れており、 セラミックス材0 料の中では比較的焼結による緻密化も容易であるため、 従来の工具鋼、 高速度 - 鋼、 超硬合金などの工具用材料の使用が困難な高速加工、 高温加工用の切削ェ - 具ゃ耐摩耗部材として用いられている。
- しかしながら、 この A 1 2〇3セラミックスは強度と靭性に乏しいために、 利 - 用範囲が限られたものになるという欠点があつた。
5 その改善策として、 八 1 2〇3に丁 1 ゃ丁 1 ( C , N) を含有させて炭窒化 - 物粒子を分散強化したいわゆる黒色セラミックスも知られている。 しかしなが • ら、 このような黒色セラミックスは、 例えば鋼ゃ錶鉄の粗切削のような高負荷 - のかかる用途には強度、 靭性は十分とは言えず信頼性に乏しい。
• また、 A 1 2〇3に WCを添加した焼結体は、 強度、 靭性は大幅に改善され、0 かつ高硬度であることから、 耐摩耗部材への適用が試みられている。
• 例えば、 特開平 3— 2 9 0 3 5 5号公報には、 A 1 2〇3に WCを 1 0〜9 0 - 容量％配合した原料粉末を、 常圧焼結、 ホットプレスまたは熱間静水圧成形す - ることにより、 密度が理論値の 9 0 %以上の高硬度かつ高靭性の焼結体を得る • ことができることが開示されている。
5 また、 特開平 5— 2 7 9 1 2 1号公報には、 A 1 203に 5〜9 5重量％の\¥
• Cを添加して 1 4 0 0〜 1 9 5 O t:で焼結し、 W C原料粉中に酸素を 0 . 0 5 - 〜 6重量％存在させ、 W2 C相を出現させた焼結体は、 とくに強度、 靭性に優 • れているいることが開示されている。 - しかしながら、 この A 1 2〇3— WC系セラミックスは、 確かに強度、 靭性に - 優れているものの、 高温での耐酸化性が十分でないため、 鋼ゃ銬鉄の高速切削 • のような過酷な摺動の状況下では十分な耐摩耗性を発揮できない。 このため、 - 切削工具等の高温耐摩耗性が必要とされる部材にはほとんど使用されていな 5 い。
- 発明の開示
- この発明の目的は、 優れた耐酸化性と耐摩耗性を保持したまま、 強度と靭性 - を格段に改善した A 1 203系セラミックスを提供することにある。
0 この発明は、 WCを 5〜7 0容量％と、 T i ( C， N) 固溶体を 5〜7 0容 - 量％を含有し、 残部が A 1 2〇3からなる緻密焼結体であり、 この焼結体は高強 • 度且つ高靭性であって、 高温においても優れた耐摩耗性を示す。
- A 1 203としては、 その結晶ひ相の割合が 9 0容量％以上のものを使用し、 • 且つ、 それぞれの平均結晶粒径は、 5 m以下であるのがよい。
5 A 1 2〇3焼結体中に WC粒子を含有させることによって著しく強度および靭 - 性が向上する。 この特性の向上は、 まず高硬度である WC粒子の分散強化が挙 - げられ、 さらに焼結温度から室温に下がるときに発生する A 1 203粒子と WC - 粒子の熱膨張率の差による残留応力が 2種類の結晶粒子間で作用する強靭化で - ある。 また、 A 1 2〇3への WCの添加は焼結時の粒成長を抑える慟きがあり、0 これにより焼結体の結晶粒の微細化が焼結体を強靭にする。
• しかしながら、 WCの含有量は 5〜 7 0容量％の範囲に規定される。これは、 - W Cの含有量が 5容量％未満の場合には、 WC相が少なくなり焼結体の強度お - よび靭性の向上の割合が小さいためである。 また、 7 0容量％を超えると、 緻 - 密な焼結体を得ることが困難になることに加え、 高温における耐酸化性が低下5 す傾向がある。 しかしな力 ら、 ホットプレスなどで 9 5 %以上の相対密度が得 - られた焼結体を H I P (熱間静水圧加圧焼結） 処理することにより、 7 0容量 - %までの WC添加量でも緻密な焼結体が得られる。 強度、 靭性の向上効果は W - Cの添加量に依存しているが、 自己焼結性に乏しい WCの量が 7 0容量％以上 - では、 焼結性が低下して緻密な焼結体が得られない。
- A 1 2〇3に WCを添加すると、 A 1 2〇3単味の焼結体に比べ、 著しく強度、
. 靭性は向上し、 衝撃に強い焼結体が得られる反面、 A 1 203の持つ優れた耐摩 • 耗性は損なわれ、 とくに高温における耐摩耗性は大幅に劣化するが、 T i ( C ,
5 N)を添加含有させると、粒子分散により強度と耐熱衝撃性の改善をもたらす。 • さらに、 高温における酸化や相手材との反応による摩耗も少なく、 本来、 A I - 203が持つ高い耐摩耗性を維持できる。 とくに、 T i ( C， N) における C : - Nのモル比率は 1 ： 9 ~ 9 ： 1の範囲で効果がある。
. この発明の A 1 2〇3基セラミックス焼結体は、 WCと T i ( C , N) 両者を0 所定量を同時に含有させることによって、 優れた耐摩耗性を有し、 なおかつ高 - い強度、 靭性を兼ね備えたものとなる。
- 一般に、 アルミナ系セラミックスを焼結する場合には、 M g O , Υ 2〇3， C
• a O , Z r〇2などの焼結促進のための助剤を添加することが多い。 これらの - 助剤を使用すると、 確かに焼結性は改善され、 緻密化が容易となるが、 切削ェ5 具などの厳しい状況で用いる場合には、 焼結助剤である酸化物の単独相あるい • は A 1 2〇3との複合化合物相が発生することになり、 これらの存在が、 強度や • 硬度、 耐摩耗性を低下させることになる。
- この発明の A 1 203基セラミックスは、 焼結助剤を用いないため、 この焼結 - 助剤が原因で生じる諸特性の劣化を招かないことも大きな特徴であり、 このよ 0 うな焼結性のみを改善するような助剤は一切使用せず、 A 1 203、 WCおよび
• T i ( C， N) の完全な 3相のみにより構成される。
- また、 原料粉末中に含まれるフリーカーボンは焼結体中に数^ mから数 + ^ - mの大きさの異物として存在することになり、 曲げ強度の低下、 ひいては、 切 • 削中の欠損の原因となる。 このフリーカーボンの影響を低減するために、 1 .
25 0容量％までの金属 W、 T iなどのカーボンとの化合物を形成し易く、 焼結体 • の特性に悪影響を与えない金属の添加は許容される。 この発明では、 この場合 - に金属 Wまたは T iを添加することによって、 焼結中にこの Cを Wまたは T i • と結合させて W Cまたは T i Cとすることによって残存カーボンを除去するこ - とも信頼性の向上につながる。
- この発明の A 12〇3基セラミックス焼結体は、 所定の組成となるよう配合し
- た粉末を十分混合し、 1600 〜 1900°Cで 0. 5〜 5時間、 不活性ガス • 雰囲気中 50~300 k g f Zcm2の圧力でホットプレスすることによって 5 製造される。
- また、 粉末に若干バインダを添加し、 金型成形や冷間静水圧成形、 またはそ • の両者を用いて成形し、 その後、 1600〜1900 で不活性ガス雰囲気中 - 0. 5~5時間焼結し、 場合によってはさらに 1400で〜 1700°C、 不活 - 性雰囲気、 500〜2000気圧の圧力で熱間静水圧焼結を施し製造してもよ0 レ
• 発明を実施するための最良の形態
- 表 1にテストに供した組成と諸特性の関係を示す。 同表において、 No. 1 • から No. 14はこの発明の組成範囲内にあるものであり、 No. 15から N5 o. 25は組成範囲外、 さらに、 No. 26から No. 29は従来のセラミツ . ク工具の例を示す。
. それぞれの試料は、 平均粒径が 2 /im以下の原料粉末を所定量秤量し、 ボー - ルミルに投入してメタノール溶媒で 20時間混合し、 乾燥造粒した調製粉末を - 力一ボンダイスに入れて 1700°Cの温度でプレス圧力 20〜25MP aに 6 0 0分保持して焼結した。 この焼結体を切断研削加工して 3 X 4X40 mmの曲 - げ試験片と J I S規格 SNGN432の切削チップに加工して、 各種のテスト • に供した。
- 同表において、 耐摩耗テストは、 被削材として、 FCD450の Φ250Χ - 500mmで、 切削速度 20 OmZm i n、 切り込み 1. 5 mm、 送り 0. 2
25 mmZr e vで行い、 逃げ面が 0. 5mmとなる時間を切削可能時間とし、 こ - れによって耐摩耗性を評価した。 表 1.組成と諸特性の関係
組成 （VOに/。） TiGN比率相対密度 硬度 曲げ強度 破壊靱性 耐摩耗テスト 耐欠損テスト チルド錶鋼切削
WC TiCN W Τί MgO Y2O3 AI2O: TiC:TiN % HRA MPa MPam-1 /,切削時間：分 FGD切削 切削可能時間：分
No.1 40 10 0.2 50 5:5 99.7 94.3 1020 3.9 18 〇 42
No.2 30 20 0.1 50 5:5 100.0 93.6 1000 3.9 16 〇 40
No.3 20 30 0.1 50 5:5 100.0 93.7 950 3.6 18 〇 41
No.4 本 10 40 0.2 50 5:5 100.0 93.8 950 3.7 15 〇 38
No.5 発 60 10 0.2 30 5:5 99.8 94.7 970 4.8 13 ◎ 37
No.6 明 10 60 0.2 30 5:5 99.7 94.5 950 4.7 16 〇 33
No.7 40 40 0.2 0.2 20 5:5 99.6 94.5 920 4.2 12 ◎ 35
No.8 35 35 30 5:5 99.7 94.4 880 4.1 14 ◎ 37
No.9 30 30 40 5:5 99.8 94.3 850 4.0 15 〇 34
No.10 25 25 50 5:5 99.8 94.0 840 4.1 1 7 〇 35
No.1 1 20 20 60 5:5 99.9 93.9 800 3.7 1 9 〇 40
No.12 1 5 1 5 70 5:5 100.0 93.7 780 3.6 20 〇 38
No.13 30 30 40 2:8 99.8 94.3 860 4.1 15 o 32
No.14 30 30 40 8:2 99.8 94.0 800 3.9 16 〇 35
No.15 30 30 40 0.2:9.8 98.5 93.4 680 3.5 14 〇 10分で欠損
No.16 30 30 40 9.8:0.2 99.2 94.0 710 3.6 1 1 〇
No.1 7 80 10 10 5:5 95.2 93.0 620 3.3 5 X 5分で欠損
No.18 60 0 40 5:5 99.6 94.5 930 4.3 13 〇 22分で摩耗
No.1 9 車 β 40 0 60 5:5 99.7 94.2 900 3.8 1 1 〇 26分で摩耗
No.20 10 80 10 5:5 94.0 92.8 590 3.1 3 X 5分で欠損
No.21 囲 0 60 40 5:5 99.8 93.9 750 3.7 19 Δ 22分で欠損
No.22外 0 40 60 5:5 99.9 93.8 720 3.6 21 △ 1 7分で欠損
No.23 30 20 0.2 50 5:5 100.0 93.9 820 3.8 16 〇 21分で摩耗
No.24 30 20 0.2 50 5:5 100.0 93.8 800 3.8 1 5 〇 24分で摩耗
No.25 40 40 20 5:5 95.1 93.2 610 3.1 4 X 5分で欠損
No.26比 アルミナ（純 ΑΙ203) 99.6 93.5 700 3.1 25 X 2分で欠損
No.27較 黒セラ （ΑΙ203 - 30TiG) 99.9 94.0 800 3.5 21 X 7分で欠損
No.28 □ 窒化珪素（Si3N4) 98.9 93.5 1200 7.0 8
100.0 91.0 230 10.0 12 ◎ 1 5分で摩耗
No.29 超硬コーティング ◎ 1 2分で摩耗 逃げ面摩耗 ◎ : 0.7mm/rev以上
0.5mmまでの ◦： 0.7〜 0.5mm/rev 切削時間 I Δ： 0.5~0.3mm/rev
0.3mm/ rev以 F
• 耐欠損テストは、 工具の欠損に対する抵抗性を調べるためのもので、 4個所 • の切り欠きを入れて衝撃を付加した被削材（Φ 2 5 0 X 5 0 0 mm)を用いて、 - 切削速度 2 0 OmZm i n、 切り込み 1. 5 mmを一定とし、 送りを変化させ • て行ったものである。
5 チルド錶鋼切削テス卜は、 Φ40 0 Χ 5 0 0 mmの被削材を用い、 切削速度 - 7 Om/m i n, 切り込み 1. 5mm、 送り 2mmZr e vで、 耐摩耗テ • ストを行った。 その評価は逃げ面摩耗が 1. Ommとなって切削不可能となる - 時間を切削可能時間とし、 切削可能な時間を従来工具と比較したものである。 • この結果より、 以下のことが明らかになった。
0 切削中に冷却と潤滑を兼ねた冷却水を使用しないいわゆる乾式切削では、 W
• Cは耐酸化性が低いために耐摩耗性は低下する。 耐摩耗性の低下率は WCの添 • 加量に比例しており、 40 v o 1 %以下、 好ましくは 3 0 V o 1 %以下で工具 - としての性能が発揮される。 しかしながら、 冷却水を使用する湿式切削におい . ては、 切削中の刃先温度の上昇がないために WCの酸化が抑制されて摩耗は進5 行せず、 むしろ、 強靭化効果による耐粒子脱落性に起因する耐欠損性や耐チッ
- ビング性の大幅な向上が認められた。
- また、 WCと T i (C, N) をアルミナに添加することで、 WCのもつ靭性 - 強化効果と同時に T i (C， N) のもつ耐摩耗性向上の効果が発揮され、 従来 - 工具ではできなかった難削材の高能率切削での長時間切削が可能となった。
0 WCと T i (C, N) の添加量は、 合計 40容量％以上で効果が出はじめる • が、 顕著な効果は 5 0〜8 0容量％で発揮される。 50容量％以下では、 アル . ミナの比率が高く、 靭性が低下することになり、 また、 80容量％以上では、 - 焼結性が低下し、焼結体中に気孔が存在して硬さ、強度、靭性が低下する結果、 - 工具としての性能が低下することとなる。
25 したがって、 添加量として、 WCが 5〜7 0容量％、 T i (C, N) が 5〜
• 7 0容量％であって、 残部は α率が 9 0容量％以上のアルミナ、 及び、 不可避 • 不純物からなる焼結体であれば、 優れた耐摩耗性と靭性を兼ね備えた材料を得 • ることができる。 - この発明による組成では、 WCの効果で結晶粒子間の結合力が強化され、 さ - らに、 T i ( C， N) により耐摩耗性が改善され、 凝着摩耗が低減し、 チルド - 銬鋼切削の例に見られるように、 難削材の高能率切削が可能となった。
- T i ( C， N) の T i C ： T i N比率は、 1 ： 9〜9 ： 1の間で所望の性能 5 が得られたが、 N o . 1 5のように T i Nが多すぎる場合には T i N添加効果 . が現れ、 低硬度で早期欠損が認められた。 また、 N o . 1 6のょぅに丁 1 が - 多すぎる場合には、 T i Cの添加効果が現れ、 やや焼結性が低下して気孔が残 - りやすく、 チルド銬鋼切削で早期摩耗を生じた。
- また、表 1の N o . 2 6から N o . 2 9に見られる従来のセラミック工具は、0 靭性が低く、 チルド銬鋼ゃ鍛鋼などの難削材と呼ばれる金属材料には使用する
- ことができなかった。
- アルミナ系切削工具は、 耐摩耗性では優れているものの、 材料強度が低いた • めに断続切削や難削材のような工具靭性の必要な用途では早期欠損で使用でき - ない。 超硬工具では強度ゃ靭性が高いので耐欠損性は高いが、 切削時の切削熱5 で早期に摩耗する傾向にある。 とくに、 高速切削では顕著に現れる。 S i 3 N 4 - 系工具は金属成分を含まないセラミックスであるため、高速切削が可能となり、 . セラミックスのなかでも高強度 Z高靭性であるために耐欠損は高いが、 被削材 - 中の鉄成分との反応により凝着 Z脱落摩耗が進行して早期に摩耗し、 チルド錶
• 鋼切削のような難削材に適さない。 さらに、 黒セラミック、 超硬コーティング0 等は、 欠損ゃチッビングの他に、 結晶粒子の脱落が摩耗や微少チッビングにな - つて現れた結果、 低寿命であった。
• 産業上の利用可能性
• この発明による A 1 〇 基セラミックス焼結体は靭性と耐摩耗性が必要とさ 5 れる幅広い部材に使用することができ、 例えば、 铸鉄ゃ鋼の高速粗切削のよう
• な高温で高負荷のかかる過酷な状況にも十分耐え得る。

Claims

請求の範囲
1. WCを 5〜70容量％と、 T i (C, N) を 5〜70容量％を含有し、 残部が A 12〇3からなる高強度かつ高靭性のアルミナ基セラミックス焼結体。
2. A l 2〇3、 WCおよび T i (C， N) の完全な 3相のみにより構成さ れる請求項 1に記載のアルミナ基セラミックス焼結体。
3. A 12 O 3の結晶中の α相の割合が 90容量％以上である請求項 1に記 載のアルミナ基セラミックス焼結体。
4. T i (C, N) における Cと Nとのモル比率が、 1 ： 9〜9 ： 1の範 囲である請求項 1または請求項 2に記載のアルミナ基セラミックス焼結体。
5. A 1203、 WCおよび T i (C, N) の平均結晶粒径がそれぞれ 5 μ m以下である請求項 1に記載のアルミナ基セラミックス。
6. 用途が、 切削工具あるいは耐摩耗部材用である請求項 1から請求項 5 の何れかに記載のアルミナ基セラミックス。
7. それぞれの平均粒径が 2 m以下の A 1203、 WC、 T i (C， N) 粉末を、 WC粉末が 5〜70容量％、 T i (C， N) 粉末が 5〜70容量％、 残りが A 12〇3粉末となるよう配合して十分混合した粉末を、 常圧焼結、 ホッ トプレス、 熱間静水圧焼結の何れか、 または、 それらを組み合わせて焼結する アルミナ基セラミックスの製造方法。
PCT/JP1998/004727 1996-10-23 1998-10-19 Agglomere ceramique a base d'alumine et procede de production dudit agglomere WO1999021806A1 (fr)

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CA002275468A CA2275468A1 (en) 1997-10-23 1998-10-19 Alumina-base ceramic sinter and process for producing the same
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