JPH03290355A - Al2o3-wc-based high-strength-high-toughness sintered material - Google Patents
Al2o3-wc-based high-strength-high-toughness sintered materialInfo
- Publication number
- JPH03290355A JPH03290355A JP2090181A JP9018190A JPH03290355A JP H03290355 A JPH03290355 A JP H03290355A JP 2090181 A JP2090181 A JP 2090181A JP 9018190 A JP9018190 A JP 9018190A JP H03290355 A JPH03290355 A JP H03290355A
- Authority
- JP
- Japan
- Prior art keywords
- toughness
- strength
- al2o3
- sintered body
- powder
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 239000000463 material Substances 0.000 title abstract description 15
- 239000002245 particle Substances 0.000 abstract description 17
- 238000005245 sintering Methods 0.000 abstract description 11
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 abstract description 6
- 229910052593 corundum Inorganic materials 0.000 abstract description 6
- 229910001845 yogo sapphire Inorganic materials 0.000 abstract description 6
- 230000002706 hydrostatic effect Effects 0.000 abstract 1
- 239000000843 powder Substances 0.000 description 16
- 239000000919 ceramic Substances 0.000 description 14
- 239000002131 composite material Substances 0.000 description 14
- 230000000052 comparative effect Effects 0.000 description 13
- 238000000034 method Methods 0.000 description 11
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 6
- 238000005452 bending Methods 0.000 description 6
- 230000009257 reactivity Effects 0.000 description 6
- 229910033181 TiB2 Inorganic materials 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 238000007731 hot pressing Methods 0.000 description 5
- QYEXBYZXHDUPRC-UHFFFAOYSA-N B#[Ti]#B Chemical compound B#[Ti]#B QYEXBYZXHDUPRC-UHFFFAOYSA-N 0.000 description 4
- 229910007948 ZrB2 Inorganic materials 0.000 description 4
- VWZIXVXBCBBRGP-UHFFFAOYSA-N boron;zirconium Chemical compound B#[Zr]#B VWZIXVXBCBBRGP-UHFFFAOYSA-N 0.000 description 4
- 239000011812 mixed powder Substances 0.000 description 4
- 229910052786 argon Inorganic materials 0.000 description 3
- 239000006185 dispersion Substances 0.000 description 3
- 238000001272 pressureless sintering Methods 0.000 description 3
- 229910009043 WC-Co Inorganic materials 0.000 description 2
- BYFGZMCJNACEKR-UHFFFAOYSA-N aluminium(i) oxide Chemical compound [Al]O[Al] BYFGZMCJNACEKR-UHFFFAOYSA-N 0.000 description 2
- 238000009694 cold isostatic pressing Methods 0.000 description 2
- 238000013329 compounding Methods 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 229910052723 transition metal Inorganic materials 0.000 description 2
- 150000003624 transition metals Chemical class 0.000 description 2
- 238000007088 Archimedes method Methods 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910001018 Cast iron Inorganic materials 0.000 description 1
- -1 Cr and No Chemical class 0.000 description 1
- 229910003862 HfB2 Inorganic materials 0.000 description 1
- 229910000997 High-speed steel Inorganic materials 0.000 description 1
- VCUFZILGIRCDQQ-KRWDZBQOSA-N N-[[(5S)-2-oxo-3-(2-oxo-3H-1,3-benzoxazol-6-yl)-1,3-oxazolidin-5-yl]methyl]-2-[[3-(trifluoromethoxy)phenyl]methylamino]pyrimidine-5-carboxamide Chemical compound O=C1O[C@H](CN1C1=CC2=C(NC(O2)=O)C=C1)CNC(=O)C=1C=NC(=NC=1)NCC1=CC(=CC=C1)OC(F)(F)F VCUFZILGIRCDQQ-KRWDZBQOSA-N 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 229910001315 Tool steel Inorganic materials 0.000 description 1
- 238000002441 X-ray diffraction Methods 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 239000011230 binding agent Substances 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 229910010293 ceramic material Inorganic materials 0.000 description 1
- 239000011195 cermet Substances 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 229910017052 cobalt Inorganic materials 0.000 description 1
- 239000010941 cobalt Substances 0.000 description 1
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 238000011049 filling Methods 0.000 description 1
- 239000010419 fine particle Substances 0.000 description 1
- 238000010304 firing Methods 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 238000001513 hot isostatic pressing Methods 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 238000004898 kneading Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 150000002816 nickel compounds Chemical class 0.000 description 1
- 238000013001 point bending Methods 0.000 description 1
- 229910052594 sapphire Inorganic materials 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 238000009834 vaporization Methods 0.000 description 1
- 230000008016 vaporization Effects 0.000 description 1
Landscapes
- Ceramic Products (AREA)
- Compositions Of Oxide Ceramics (AREA)
Abstract
Description
【発明の詳細な説明】
産業上の利用分野
本発明は高硬度、高強度、高靭性でかつ熱伝導性に優れ
たｕ、ｏ３−ｗｃ系高強度・高靭性焼結体に関するもの
である。DETAILED DESCRIPTION OF THE INVENTION Field of Industrial Application The present invention relates to a u, o3-wc-based high-strength, high-toughness sintered body that has high hardness, high strength, high toughness, and excellent thermal conductivity.
従来の技術
！’ｊ１２０３は高硬度で耐摩耗性に優れ、またセラミ
ックス材料の中では比較的安価なため、広く摺動耐摩耗
部材として使用されている。Conventional technology! 'j1203 has high hardness and excellent wear resistance, and is relatively inexpensive among ceramic materials, so it is widely used as a sliding wear-resistant member.
また、Ｍ、０３系セラミツクスの焼結性向上、粒成長抑
制を目的として、ＫｇＯ、ＣａＯ等の焼結助剤を添加し
た焼結体、あるいは靭性向上を目的としてＺｒ０７を添
加した複合焼結体は、一般に白色セラミックスとして知
られ、切削工具チップ（スローアウェイチップ）をはじ
め、種々の工具材料として用いられている。In addition, sintered bodies containing sintering aids such as KgO and CaO are added to improve the sinterability of M and 03-based ceramics and suppress grain growth, and composite sintered bodies are added with Zr07 to improve toughness. are generally known as white ceramics and are used as cutting tool tips (throw-away tips) and various other tool materials.
また、紋２０３セラミックスの強度、靭性さらに硬さ、
熱伝導率を改善するために、ＴｉＣあるいはＴｉ（Ｃ：
Ｎ）を添加した複合焼結体は、いわゆる黒色セラミック
スとして知られ、鋳鉄、鋼等の切削工具チップ、その他
工具材料等に実用化されている。In addition, the strength, toughness and hardness of Mon 203 ceramics,
To improve thermal conductivity, TiC or Ti(C:
Composite sintered bodies containing N) are known as so-called black ceramics, and have been put to practical use as cutting tool tips for cast iron, steel, etc., and other tool materials.
これらセラミックス工具は、従来の工具鋼、ハイス鋼、
ＷＣ−Ｃｏ系超硬合金、あるいはＴｉＣ（ＴａＣ） −
Ｎ＋／Ｍａ系サーメーすトとは異なり、金属相を含まな
いため、硬さ、耐熱性に優れ、また被削金属との反応性
も乏しいので、例えば切削工具チップでは、高速加工、
高温加工などの条件の厳しい加工に適している。These ceramic tools are made of conventional tool steel, high-speed steel,
WC-Co cemented carbide or TiC (TaC) -
Unlike N+/Ma-based thermates, it does not contain a metallic phase, so it has excellent hardness and heat resistance, and also has poor reactivity with the workpiece metal.
Suitable for processing with severe conditions such as high temperature processing.
このようにセラミ−２クス工具は負荷の大きな条件で使
用されることが多いため、工具寿命向上を目的として材
料の高硬度化、高強度化、高靭化、さらに工具に発生す
る熱を有効に発散させるために熱伝導率のさらなる改善
が望まれている。In this way, ceramic 2x tools are often used under conditions of heavy load, so in order to extend tool life, we have made the material harder, stronger, and tougher, and we have also made effective use of the heat generated by the tool. Further improvement in thermal conductivity is desired in order to dissipate heat.
Ｍ２Ｏ３セラミックスの特性を向上させるため、ＴｉＣ
、Ｔｉ（ＣＭ）を添加した黒色セラミックス以外に１例
えば特開昭５２−３０８１２号公報では、４８重量％以
下のＡｌ１２０３にＴｉＢ２、ＺｒＢ２及びＨｆＢ２よ
り選ばれた耐火性ニー化物を５〜５０重量％、Ｖ 、
Ｗｂ、 Ｔａ。To improve the properties of M2O3 ceramics, TiC
In addition to black ceramics containing Ti (CM), 1 For example, in JP-A-52-30812, 5 to 50 weight % of a refractory nephride selected from TiB2, ZrB2 and HfB2 is added to 48 weight % or less of Al1203. ,V,
Wb, Ta.
Ｃｒ、 Ｎｏ等のニー化物を２０重量％以下、■族、Ｖ
族、■族耐天性遷移金属の炭化物又は炭窒化物を３５重
量％、さらに３重量％以下のＮｇＯを添加することを開
示している。20% by weight or less of nickel compounds such as Cr and No, group II, V
It is disclosed that 35% by weight of carbides or carbonitrides of weather-resistant transition metals of groups 1 and 2 and 3% or less of NgO are added.
ＴｉＢ２、ＺｒＢ２、Ｈｆ１ｈ等の耐熱遷移金属のニー
化物は高融点、高硬度という特性を有し、Ｍ２Ｏ３セラ
ミックスの特性改善には有効である。しかしながら強度
及び靭性の点に関しては、未だ改善の余地がある。Nied compounds of heat-resistant transition metals such as TiB2, ZrB2, and Hf1h have the characteristics of high melting point and high hardness, and are effective in improving the characteristics of M2O3 ceramics. However, there is still room for improvement in terms of strength and toughness.
一方、ｌ１ｌＣは、高硬度でありまた被削材との反応性
にも乏しく、工具材として優れた特性を宥しているが、
一方で単体では強度・靭性に劣るという欠点も併せ持っ
ている。そこでＷＣに５〜２０重量％の金属ｃｏを結合
相として加え、サーメット化した、いわゆる超硬合金と
して広く実用化されてきた。On the other hand, l1lC has high hardness and poor reactivity with the workpiece material, and has excellent properties as a tool material.
On the other hand, it also has the disadvantage of being inferior in strength and toughness when used alone. Therefore, 5 to 20% by weight of metallic cobalt is added to WC as a binder phase to form a cermet, which has been widely put into practical use as a so-called cemented carbide.
しかしながら、このようなＷＣ−Ｃｏ系硬合金において
は、ＷＣ単体とくらべて強度・靭性は飛躍的に改善され
るものの、前述した様に結合金属相としてのＧｏを多量
に含むため硬さ、耐熱性、さらには被削材との低反応性
といった特性を著しく劣化させてしまう問題点を有して
いた。However, although the strength and toughness of such WC-Co-based hard alloys are dramatically improved compared to WC alone, as mentioned above, they contain a large amount of Go as a bonding metal phase, so they have poor hardness and heat resistance. However, this technique has the problem of significantly deteriorating properties such as poor reactivity and low reactivity with the workpiece material.
発明が解決しようとする課題
Ｍ ２０ ｓ及びｌｌＩＣは、高硬度でかつ被削材との
反応性にも乏しいという特徴を有しているものの、共に
単体では強度及び靭性が低いという欠点を有していた。Problems to be Solved by the Invention Although M20s and llIC have the characteristics of high hardness and poor reactivity with the work material, both have the drawback of low strength and toughness when used alone. was.
本発明の目的は、Ｍ２Ｏ３とｌ１ｌＣとを複合化するこ
とにより、硬さ、被削材との低反応性という特徴を失う
ことなく強度、靭性を向上させ、ざらにＡｌ２Ｏ３の熱
伝導率を改良することにある。The purpose of the present invention is to improve the strength and toughness without losing the characteristics of hardness and low reactivity with the work material, and to roughly improve the thermal conductivity of Al2O3 by combining M2O3 and l11C. It's about doing.
課題を解決するための手段
本発明は賀Ｃが１０〜９０容量％で残部が実質Ａｌ２Ｏ
３より成る相対密度が９０％以上の高密度かつ高強度・
高靭性なＭ２Ｏ３−ｗｃ系焼結体に関するものである。Means for Solving the Problems The present invention consists of 10 to 90% by volume of carbon and the remainder being substantially Al2O.
High density and high strength with a relative density of 90% or more.
The present invention relates to a highly tough M2O3-wc-based sintered body.
すなわち、本発明はｗＣが１０〜９０容量％で残部が実
質Ｍ２Ｏ３より威る混合粉末を成形・焼結して得られた
密度が理論値の９０％以上であることを特徴とするＡｌ
２Ｏ，−’ｄＣ系高強度・高靭性焼結体に関するもので
ある。That is, the present invention is an Al powder characterized in that the density obtained by molding and sintering a mixed powder with a wC of 10 to 90% by volume and the balance being substantially higher than M2O3 is 90% or more of the theoretical value.
This invention relates to a 2O, -'dC-based high-strength and high-toughness sintered body.
以下に本発明の内容について詳細に説明する。The content of the present invention will be explained in detail below.
本発明のＡｌ１２０．−ｗｃ複合焼結体中においては、
高硬度のＭ２Ｏ３粒子と、同じ〈高硬度のＷＣ粒子とが
互いに分散した構造を威しており、他に低硬度な第３相
を右さないため高硬度という特徴は失われない、また、
複合体中において、いわゆる粒子分散効果等により破壊
源からのクラ−２りの進展は偏向、湾曲し、強度及び靭
性が向上している。Al120 of the present invention. -In the wc composite sintered body,
The high hardness M2O3 particles and the same high hardness WC particles have a mutually dispersed structure, and there is no other low hardness third phase, so the high hardness characteristic is not lost.
In the composite, the progress of cracks from the fracture source is deflected and curved due to the so-called particle dispersion effect, and the strength and toughness are improved.
さらにＭ２Ｏ３中に−Ｃを、また逆にｗＣ中にＭ、０３
を添加することにより、互いに焼結体中で粒成長を抑制
するために複合体中での構成相は微細化し１強度の向上
に寄与している。また、Ａｌ１２０３にくらべＷＣは熱
伝導率が高いためＭ２Ｏ３にｗＣを添加することにより
本発明のＮ１２０３−Ｗｅ焼結体の熱伝導車も向上する
。Furthermore, -C is added to M2O3, and conversely, M, 03 is added to wC.
By adding , the constituent phases in the composite are made finer in order to mutually suppress grain growth in the sintered body, contributing to an improvement in strength. Furthermore, since WC has a higher thermal conductivity than Al1203, adding wC to M2O3 also improves the thermal conductivity of the N1203-We sintered body of the present invention.
本発明の焼結体で貿ＣがｌＯ〜８０容量％であるのはＷ
Ｃが１０容量％未満では複合化量が少ないためＭ２Ｏ３
セラミックスの強度・靭性・熱伝導率の向上は小さく、
また同様に％ｌｌＣが８０容量％を超えると−Ｃに対す
るＭ２Ｏ３の複合化量が小くて粒子分散の効果が小さく
なり、強度ｅ靭性の向上も期待できないからである。In the sintered body of the present invention, the trade C is 1O to 80% by volume.
If C is less than 10% by volume, the amount of compounding is small, so M2O3
Improvements in strength, toughness, and thermal conductivity of ceramics are small;
Similarly, if %llC exceeds 80% by volume, the amount of composite of M2O3 with respect to -C will be small, the effect of particle dispersion will be small, and no improvement in strength or toughness can be expected.
本発明において、焼結方法としては常圧焼結法、ホット
プレス焼結法、熱間静水圧加圧（ＨＩＰ）焼結法等既知
の焼結法のいずれも用いることができる。In the present invention, any known sintering method can be used as the sintering method, such as a pressureless sintering method, a hot press sintering method, a hot isostatic pressing (HIP) sintering method, and the like.
また本発明において、使用するＭ２Ｏ３粉体としては、
通常はα型Ｍ２Ｏ３であるが、その化β型、γ型等の結
晶でも差支えない、さらに非晶質のＡｌ２Ｏ３、あるい
は加熱中にα−Ａｌ２Ｏ３を生成するＭ（ＯＨ）３．
Ａ１００Ｈ等でもよい。In addition, in the present invention, the M2O3 powder used is as follows:
Usually it is α-type M2O3, but crystals such as β-type and γ-type may also be used, as well as amorphous Al2O3 or M(OH)3, which generates α-Al2O3 during heating.
A100H etc. may also be used.
またＭ２Ｏ３粒体の粒径として、通常は焼結性の優れる
１０ｐｍ以下のものが好ましく、ＩＩＬｍ以下（サブミ
クロン）の微細なものはさらに望ましい。Furthermore, the particle size of the M2O3 particles is preferably 10 pm or less, which provides excellent sinterability, and more preferably fine particles of IILm or less (submicron).
Ｍ、０３と複合化するＷＣ粉体も通常は焼結性の優れる
１０ｇ、ｍ以下のものが好ましく、ＩＩＬｍ以下（サブ
ミクロン）の微細なものはさらに望ましい。The WC powder to be composited with M and 03 is preferably 10 g, m or less because of its excellent sinterability, and more preferably fine powder of IILm or less (submicron).
以上のようにＭ ２０３にｌＯ〜８０容量％の範囲で−
Ｃを添加した混合材料を酸形・焼結することによって高
密度で高硬度、高強度、高靭性かつ熱伝導性にも優れた
Ｍ２Ｏ３ＷＣ系複合焼結体が製造可能となる。As mentioned above, M 203 has −
By acid-forming and sintering a C-added mixed material, an M2O3WC-based composite sintered body with high density, high hardness, high strength, high toughness, and excellent thermal conductivity can be manufactured.
本発明のような複合セラミックスの理論密度を正確に決
定することは容易ではなく、また一般に焼結体の密度と
しては高い方が好ましいが、少なくとも密度が理論値の
９０％以上の焼結体でなければ前述の好ましい特性は損
われ、望ましいものではない。It is not easy to accurately determine the theoretical density of composite ceramics such as the one of the present invention, and generally a higher density is preferable for the sintered body, but it is preferable to use a sintered body whose density is at least 90% of the theoretical value. Otherwise, the aforementioned favorable properties would be impaired and would not be desirable.
作用
本発明における焼結体は、ＷＣが１０〜９０容量％で残
部が実質Ｍ２Ｏ３より成り、焼結体中で高硬度のＷＣ粒
子とＡＱ２０３粒子とが分散した構造を有しているため
、ｌ）高硬度であり、２）粒子分散効果により靭性が向
上し、３）靭性向上に伴って強度も改善され、４）良熱
伝導性のＷＣの添加によりＡｌ２Ｏ３の熱伝導率を改善
する作用を威している。Function The sintered body in the present invention has a structure in which WC is 10 to 90% by volume and the remainder is substantially M2O3, and highly hard WC particles and AQ203 particles are dispersed in the sintered body. ) has high hardness, 2) toughness is improved due to the particle dispersion effect, 3) strength is improved with improved toughness, and 4) the addition of WC, which has good thermal conductivity, has the effect of improving the thermal conductivity of Al2O3. It's intimidating.
以下実施例を挙げて説明する。This will be explained below with reference to examples.
実施例
実施例１〜７
α型Ｍ２Ｏ３粉末（平均粒径０．２ｇｍ、純度９９．９
９％以上）に実施例１〜７に示す容量比で１ｌｌＣ粉末
（平均粒径１．ＯＩＬｍ、純度９９％以上）を添加し、
ボールミルを用いて充分混合した後、１７００℃の温度
で２時間、アルゴン不活性雰囲気中で、 ４００ｋｇｆ
／ｃｍ２の圧力でホットプレス焼結を行った。Examples Examples 1 to 7 α-type M2O3 powder (average particle size 0.2 gm, purity 99.9
9% or more) and 1llC powder (average particle size 1.OILm, purity 99% or more) at the volume ratio shown in Examples 1 to 7.
After thorough mixing using a ball mill, 400 kgf was heated at a temperature of 1700°C for 2 hours in an argon inert atmosphere.
Hot press sintering was performed at a pressure of /cm2.
焼結体はＪＩＳ Ｒ１８０１に準拠し、３ｍｍＸ４ｓｍ
Ｘ３８０鳳の試験片に加工し、アルキメデス法により密
度を測定した後、室温で三点曲げ試験を行った。焼結体
の靭性としては、予き裂導入法（Ｓ Ｅ ＰＨ法）を用
いて、破壊靭性値；Ｋｘｃを測定した。また、硬さの評
価として、ビッカース硬さを荷重１ｋｇｆ 、保持時間
１５秒で測定した。さらに、熱伝導率についてはレーザ
ーフラッシュ法を用いて測定した。The sintered body conforms to JIS R1801 and is 3mm x 4sm.
After processing the sample into a test piece of X380 and measuring its density by the Archimedes method, a three-point bending test was conducted at room temperature. As for the toughness of the sintered body, the fracture toughness value; Kxc was measured using a pre-crack introduction method (SE PH method). Further, as a hardness evaluation, Vickers hardness was measured under a load of 1 kgf and a holding time of 15 seconds. Furthermore, thermal conductivity was measured using a laser flash method.
第１表中、実施例１〜７に各組成について得られた焼結
体の相対密度（理論値に対して百分率で示す）、曲げ強
さ、破壊靭性値、硬さ及び熱伝導率を示す。In Table 1, Examples 1 to 7 show the relative density (expressed as a percentage of the theoretical value), bending strength, fracture toughness, hardness, and thermal conductivity of the sintered bodies obtained for each composition. .
また同第１表中、比較例１〜３には１ｌｌＣを添加しな
いＵ２Ｏ５単体を１３５０．１５００及び１７００℃の
各温度でホットプレスした焼結体について、また比較例
４〜６には逆に般、０３を添加しないＷＣ単体を１５０
０．１７００及び１８００℃でホットプレスした焼結体
について同様にその特性を示している。In addition, in Table 1, Comparative Examples 1 to 3 are for sintered bodies obtained by hot pressing U2O5 alone without addition of 1llC at temperatures of 1350, 1500 and 1700°C, and Comparative Examples 4 to 6 are for general use. , 150 WC alone without adding 03
The properties of sintered bodies hot-pressed at 0.1700°C and 1800°C are similarly shown.
さらに比較例７及び８にはそれぞれＭ２Ｏ３にＷＣを５
及び９５容量％添加した混合粉体を１７００℃でホット
プレス焼結した場合についても同様にその特性を示して
いる。尚、比較例３ （Ａｉ２０３単体、１７００℃で
ホットプレス）及び比較例６ （ｗｃ単体、１９００℃
でホットプレス）では焼結体中で粒成長が著しく、テス
トピースの加工が不可能であり、従って各特性の測定は
できなかった。Furthermore, in Comparative Examples 7 and 8, 5 WC was added to M2O3.
The same characteristics are also shown when a mixed powder containing 95% by volume is hot-press sintered at 1700°C. In addition, Comparative Example 3 (Ai203 alone, hot pressed at 1700°C) and Comparative Example 6 (wc alone, 1900°C
(hot pressing), the grain growth in the sintered body was significant, making it impossible to process a test piece, and therefore it was not possible to measure each characteristic.
実施例１〜７及び比較例１〜６より、種々の温度でホッ
トプレスしたＭ２Ｏ３単体、ＷＣ単体にくらべ、その両
者を複合化した本発明のｕ、ｏ３−ｗｅ系複合焼結体は
、曲げ強さ、破壊靭性値等において、特性が著しく改善
されていることが明らかである。From Examples 1 to 7 and Comparative Examples 1 to 6, compared to M2O3 alone and WC alone hot-pressed at various temperatures, the u, o3-we composite sintered body of the present invention, which is a composite of both, is It is clear that the properties are significantly improved in terms of strength, fracture toughness, etc.
また比較例７．８及び実施例１〜７より、Ｍ２Ｏ３に添
加するｗＣの量としてはｌＯ〜８０容量％が特性の改良
の見地から適当であることがわかる。Further, from Comparative Example 7.8 and Examples 1 to 7, it is understood that the amount of wC added to M2O3 is 10 to 80% by volume from the viewpoint of improving properties.
また、Ｘ線回折の結果から実施例１〜７の焼結体からａ
−Ｍ２Ｏ３とＷｅ （ｈｅｘａｇｏｎａｌ相）のピーク
が観察され、焼結体はα−Ａｌ ２０３と賀Ｃ粒の分散
した構造より成ることがわかった。In addition, from the results of X-ray diffraction, it was found that a
-M2O3 and We (hexagonal phase) peaks were observed, and it was found that the sintered body had a structure in which α-Al 203 and KaC grains were dispersed.
実施例８〜ｌＯ
実施例１〜７で用いたと同様の平均粒径０．２井ｍ、純
度９９．８！３％以上のα型Ｍ２Ｏ３粉末に７０容量％
のＷＣ粉末（平均粒径１．Ｏｇｍ、純度９９％以上）を
添加し、ボールミルを用いて充分、粉体を混合後、１６
００〜１９００℃の温度で２時間、アルゴンガス中で４
００ｋｇｆ／ｃｍ’の圧力でホットプレス焼結した。Example 8-IO 70% by volume of α-type M2O3 powder with an average particle size of 0.2 μm and a purity of 99.8!3% or more as used in Examples 1-7
of WC powder (average particle size 1.0gm, purity 99% or more) was added, and the powder was thoroughly mixed using a ball mill.
4 hours in argon gas at a temperature of 00 to 1900 °C for 2 hours.
Hot press sintering was performed at a pressure of 00 kgf/cm'.
得られた焼結体について、実施例１〜７と同様にその相
対密度、曲げ強さ及び破Ｉｓ靭性値について測定し、第
２表中に結果をまとめている。The relative density, bending strength, and fracture Is toughness of the obtained sintered bodies were measured in the same manner as in Examples 1 to 7, and the results are summarized in Table 2.
また比較例９として、実施例８〜１０と全く同じ混合粉
体を１５００℃でホットプレスした場合についても、そ
の特性を第２表に示している。Table 2 also shows the properties of Comparative Example 9, in which the same mixed powder as in Examples 8 to 10 was hot pressed at 1500°C.
また比較例９と実施例３及び８〜１０より、ホットプレ
ス条件が適切で、９０％以上の相対密度を有する焼結体
は、曲げ強さと破壊靭性値において優れた特性を示して
いるのに対し、相対密度が８０％を下回る焼結体では著
しく特性が低下することが明らかである。Furthermore, from Comparative Example 9 and Examples 3 and 8 to 10, a sintered body with appropriate hot pressing conditions and a relative density of 90% or more shows excellent properties in terms of bending strength and fracture toughness. On the other hand, it is clear that a sintered body with a relative density of less than 80% has significantly lower characteristics.
実施例Ｕ
本発明のＭ２Ｏ３−ｗｃ系複合体の優位性を明らかにす
るため、Ａ１２０３−ＴｉＣ、Ｍ２Ｏ３−ＴｉＢ２等の
黒色セラミックスとの特性の比較を行った。Example U In order to clarify the superiority of the M2O3-wc-based composite of the present invention, the properties were compared with black ceramics such as A1203-TiC and M2O3-TiB2.
実施例１〜１０で用いたと同様のα−Ｍ２０３粉末に３
０容量％のＷＣ（実施例１−１０と同じ）粉末を添加し
、さらに比較用として、α−Ａ１２０３に３０容量％の
ＴｉＣ（平均粒径１．２ ｐ−ｍ、純度９９％以上）、
ＴｉＢ２ （平均粒径２〜３１Ｌｍ、純度８８％以上）
、及びＺｒＢ２（平均粒径３ＪＬｍ、純度９８％以上）
粉末を各々添加した。3 to α-M203 powder similar to that used in Examples 1 to 10.
0 volume % WC (same as Example 1-10) powder was added, and for comparison, 30 volume % TiC (average particle size 1.2 p-m, purity 99% or more) was added to α-A1203.
TiB2 (average particle size 2-31Lm, purity 88% or more)
, and ZrB2 (average particle size 3JLm, purity 98% or more)
Each powder was added.
混合粉末をボールミルにより、充分混練した後、１７５
０℃で２時間ホットプレス焼結し、得られた焼結体につ
いて、密度、曲げ強さ及び破壊靭性値を測定した。After thoroughly kneading the mixed powder with a ball mill, 175
Hot press sintering was carried out at 0° C. for 2 hours, and the density, bending strength and fracture toughness values of the obtained sintered body were measured.
第３表に実施例１１と比較例１０−１２として、その結
果を示している。Table 3 shows the results as Example 11 and Comparative Examples 10-12.
実施例１１と比較例１０〜１２より、Ｍ２Ｏ３にＴｉｅ
、ＴｉＢ２あるいはＺｒＢ２を添加するよりも本発明の
ようにＷＣを添加する方がより高強度・高靭性な焼結体
が得られることが明らかである。From Example 11 and Comparative Examples 10 to 12, Tie in M2O3
It is clear that a sintered body with higher strength and toughness can be obtained by adding WC as in the present invention than by adding , TiB2 or ZrB2.
実施例１２〜１３
本発明のＡｌＡｌ１２ｏ３−系焼結体について、常圧焼
結の適応性について検討した。Examples 12 to 13 The adaptability of the AlAl12o3-based sintered body of the present invention to pressureless sintering was investigated.
実施例８〜ｌＯと同様にα型Ｍ２Ｏ３粉末に７０容量％
のＷＣ粉末を添加し、ボールミルを用いて充分混合した
後、５０Ｘ ５ｈａの金型を用いて１００ｋｇｆ／ｃ層
２の圧力で一軸加圧成形した。その後成形体を７０００
ｋｇｆ／ｃｍ２（７）圧力でｃＩＰ（冷間静水圧プレス
）ｒｆｔ。Example 8 - 70% by volume of α-type M2O3 powder as in IO
WC powder was added thereto, thoroughly mixed using a ball mill, and then uniaxially pressed using a 50×5 ha mold at a pressure of 100 kgf/c layer 2. After that, the molded body was 7000
cIP (cold isostatic pressing) rft at kgf/cm2 (7) pressure.
形し、アルゴン気流中、１８００及び１８５０℃の温度
で１時間常圧焼成した。It was molded and baked at normal pressure for 1 hour at temperatures of 1800 and 1850° C. in an argon stream.
この時、サンプル中ＡＱ ２０３相の分解・気化を防止
するため、成形体はＡｎ ２０３粉体（詰め粉）中に埋
めて焼成に供した。At this time, in order to prevent decomposition and vaporization of the AQ 203 phase in the sample, the molded body was buried in An 203 powder (filling powder) and subjected to firing.
得られた焼結体について実施例８〜ｌＯと同様に密度、
曲げ強さ、及び破壊靭性値を測定し、その結果を第４表
中実施例１２、工３に示している。Regarding the obtained sintered body, the density,
The bending strength and fracture toughness values were measured and the results are shown in Example 12 and Work 3 in Table 4.
実施例１２．１３と比較例１〜６より、本発明のＭ２Ｏ
３ＷＣ系複合焼結体は常圧焼結によっても十分緻密化し
、またその特性もホットプレスで作製したＭ２Ｏ３単体
、貿Ｃ単体よりも優れていることが明らかである。From Example 12.13 and Comparative Examples 1 to 6, M2O of the present invention
It is clear that the 3WC-based composite sintered body is sufficiently densified by pressureless sintering, and its properties are superior to M2O3 alone and TradeC alone produced by hot pressing.
また実施例３と実施例１２．１３を比較しても、常圧焼
結したＡｌ２Ｏ３７０容量％ＷＣ複合体は密度、曲げ強
さにおいてはホットプレス法で作製した場合には及ばな
いものの、破壊靭性値においては逆にホットプレス材の
特性を凌いでいることがわかる。Furthermore, even when comparing Example 3 and Examples 12 and 13, the Al2O3 70% by volume WC composite sintered under pressure is not as good as those produced by the hot pressing method in terms of density and bending strength, but the fracture toughness is On the contrary, it can be seen that the properties of the hot-pressed material are superior to those of the hot-pressed material.
茎
実施例８
３
Ｏ
比較例９
第
第
表
表
発明の効果
本発明のように、ＭＬ２０３に’ｄＣを複合化すること
により、高密度で機械的性質に優れるＡｌ１２０３−Ｉ
ｄＣ系複合焼結体が得られる。Stem Example 8 3 O Comparative Example 9 Table 1 Effects of the Invention As in the present invention, by compounding ML203 with 'dC, Al1203-I which has high density and excellent mechanical properties
A dC-based composite sintered body is obtained.
本発明のＭ２Ｏ５−ＷＣ系高密度焼結体は、Ｍ２Ｏ３セ
ラミックスの強度、靭性及び熱伝導率等の特性を著しく
向上させており、Ａ９！２０３基セラミックス工具の寿
命をより一層延ばすことが可能である。The M2O5-WC-based high-density sintered body of the present invention has significantly improved properties such as strength, toughness, and thermal conductivity of M2O3 ceramics, and can further extend the life of A9!203 ceramic tools. be.
Claims (1)
より成る、密度が理論値の９０％以上である高強度・高
靭性なＡｌ＿２Ｏ＿３−ＷＣ系焼結体。WC is 10-90% by volume and the remainder is essentially Al_2O_3
A high-strength and high-toughness Al_2O_3-WC-based sintered body having a density of 90% or more of the theoretical value.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2090181A JPH03290355A (en) | 1990-04-06 | 1990-04-06 | Al2o3-wc-based high-strength-high-toughness sintered material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2090181A JPH03290355A (en) | 1990-04-06 | 1990-04-06 | Al2o3-wc-based high-strength-high-toughness sintered material |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH03290355A true JPH03290355A (en) | 1991-12-20 |
Family
ID=13991320
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2090181A Pending JPH03290355A (en) | 1990-04-06 | 1990-04-06 | Al2o3-wc-based high-strength-high-toughness sintered material |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH03290355A (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5286684A (en) * | 1992-02-14 | 1994-02-15 | Ngk Spark Plug Company, Ltd. | Aluminum oxide-based sintered object and process for producing the same |
| JP2006248803A (en) * | 2005-03-08 | 2006-09-21 | Kyocera Corp | Magnetic head substrate and method for producing the same |
| WO2006115016A1 (en) * | 2005-04-21 | 2006-11-02 | Hitachi Metals, Ltd. | Material of ceramic substrate for thin-film magnetic head |
| JP2010265173A (en) * | 2010-07-08 | 2010-11-25 | Kyocera Corp | Substrate for magnetic head |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS4920207A (en) * | 1972-06-16 | 1974-02-22 |
-
1990
- 1990-04-06 JP JP2090181A patent/JPH03290355A/en active Pending
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS4920207A (en) * | 1972-06-16 | 1974-02-22 |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5286684A (en) * | 1992-02-14 | 1994-02-15 | Ngk Spark Plug Company, Ltd. | Aluminum oxide-based sintered object and process for producing the same |
| JP2006248803A (en) * | 2005-03-08 | 2006-09-21 | Kyocera Corp | Magnetic head substrate and method for producing the same |
| JP4624139B2 (en) * | 2005-03-08 | 2011-02-02 | 京セラ株式会社 | Manufacturing method of magnetic head substrate |
| WO2006115016A1 (en) * | 2005-04-21 | 2006-11-02 | Hitachi Metals, Ltd. | Material of ceramic substrate for thin-film magnetic head |
| JP5354901B2 (en) * | 2005-04-21 | 2013-11-27 | 日立金属株式会社 | Ceramic substrate materials for thin film magnetic heads |
| JP2010265173A (en) * | 2010-07-08 | 2010-11-25 | Kyocera Corp | Substrate for magnetic head |
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