JPS63252965A - Arsenic nitride zirconia base composite ceramic material - Google Patents
Arsenic nitride zirconia base composite ceramic materialInfo
- Publication number
- JPS63252965A JPS63252965A JP62083924A JP8392487A JPS63252965A JP S63252965 A JPS63252965 A JP S63252965A JP 62083924 A JP62083924 A JP 62083924A JP 8392487 A JP8392487 A JP 8392487A JP S63252965 A JPS63252965 A JP S63252965A
- Authority
- JP
- Japan
- Prior art keywords
- ceramic material
- composite ceramic
- cutting
- base composite
- zirconia base
- 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
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- Compositions Of Oxide Ceramics (AREA)
- Ceramic Products (AREA)
Abstract
(57)【要約】本公報は電子出願前の出願データであるた
め要約のデータは記録されません。(57) [Summary] This bulletin contains application data before electronic filing, so abstract data is not recorded.
Description
【発明の詳細な説明】
（産業上の利用分野）
この発明は機械工作におけるフライス加工用などのセラ
ミックス工具用材料に関し、特に重切削用高靭性を要求
される工具用材料に用いて好適なものである。[Detailed Description of the Invention] (Industrial Application Field) This invention relates to ceramic tool materials for milling in mechanical work, etc., and is particularly suitable for use in tool materials that require high toughness for heavy cutting. It is.
（従来の技術）
窒化硅素（以下に於て５ｉＪａ と記す）系材料は、高
い硬度（ピンカース硬度Ｈｖ１９００前後）を持ってい
るので、現在切削工具用材料として用いられている。(Prior Art) Silicon nitride (hereinafter referred to as 5iJa) based materials have high hardness (Pinkers hardness Hv around 1900) and are currently used as materials for cutting tools.
（発明が解決しようとする問題点）
上記従来のＳｔ、Ｎ、系切削工具材料は、破壊靭性値Ｋ
ｒｃ−６Ｍ Ｐａ＠′Ａ前後であってあまり高くないた
め重切削用工具としては不適当であった。(Problems to be Solved by the Invention) The above-mentioned conventional St, N, cutting tool materials have a fracture toughness value of K
rc-6M Pa@'A, which is not very high, was unsuitable as a heavy cutting tool.
（問題点を解決するための手段及び作用）この発明は上
記問題点に鑑みなされたものであって、５ｉＪ４と２Ｍ
化イツトリウム （以下に於てＹ２Ｏ，と記す）を固溶
した酸化ジルコニウム（以下に於てＺｒＯ，と記す）と
を、ポリカルボン酸系の解膠剤を用いて湿式ボールミリ
ングして均一な分散組織を持つように調整して成るセラ
ミックス複合材料であって、特にＹ、０．を２．０〜５
．０ｍｏ１％固溶した平均粒子径が０．１〜２μｍから
成る微細部分安定化ＺｒＯ□を体積％で３０〜７０％を
Ｓｉ３Ｎ４の母相に均一分散させ、ホットプレスや熱間
静水圧焼結法（以下において＋ｉ ｒ ｐと記す）など
により加圧焼結した複合セラミックス材料は、硬度と破
壊靭性値が特に高いので、従来のセラミックス工具では
不可能であった黒皮部の断続切削に使用可能な工具用材
料である。(Means and effects for solving the problems) This invention was made in view of the above problems, and includes the 5iJ4 and 2M
Zirconium oxide (hereinafter referred to as ZrO) containing yttrium oxide (hereinafter referred to as Y2O) as a solid solution is uniformly dispersed by wet ball milling using a polycarboxylic acid-based deflocculant. A ceramic composite material prepared to have a texture, particularly Y, 0. 2.0-5
．． Finely stabilized ZrO□ with an average particle size of 0.1 to 2 μm in 0mol1% solid solution is uniformly dispersed in a volume percent of 30 to 70% into the Si3N4 matrix, and then hot pressed or hot isostatically sintered. (hereinafter referred to as +ir p), etc., the composite ceramic material pressure-sintered has particularly high hardness and fracture toughness values, so it can be used for interrupted cutting of black scale parts, which is impossible with conventional ceramic tools. It is a material for tools.
また、前記ＳｉＪ＊−ＺｒＯｔ系材料に、平均粒子系が
０．１〜２μｍから成る酸化アルミニウム（以下に於て
ＡｌｘＯｓと記す）を２０〜６０体積％混合し。Further, 20 to 60 volume % of aluminum oxide (hereinafter referred to as AlxOs) having an average particle size of 0.1 to 2 μm is mixed into the SiJ*-ZrOt-based material.
ポリカルボン酸系の解膠剤を用いて湿式ボールミリング
して材料調整した混合粉末を焼結して得られた材料では
、破壊靭性値ＫＩＣはＡｌｔｏｓ無添加の前記５ｉＪｎ
−ＺｒＯ１系材料に比し最高値では少々劣るがビッカー
ス硬度（以下に於てＨｖ と記す）は高（、かつ高価な
５ｔｓＮａ−ＺｒＯｚ（ＹｚＯｓ）を節約できる作用が
ある。In the material obtained by sintering a mixed powder prepared by wet ball milling using a polycarboxylic acid-based deflocculant, the fracture toughness value KIC is the same as the above 5iJn without Altos addition.
Although it is slightly inferior in maximum value to -ZrO1-based materials, it has a high Vickers hardness (hereinafter referred to as Hv) and has the effect of saving expensive 5tsNa-ZrOz (YzOs).
（実施例） 以下にこの発明の詳細な説明する。(Example) This invention will be explained in detail below.
（実施例１） ＹｚＯｘ を３＊ｏ１％固溶したＺｒ
Ｌに。(Example 1) Zr with 3*O1% YzOx dissolved in solid solution
To L.
Ｓｉ３Ｎ４ を５０体積％加えたものをホットプレス焼
結したｍ織の研磨面を走査型電子顕微鏡で観察した写真
を第１図に示す。図かられかるようにＹｔＯｓを固溶し
たＺｒＯ□及び５ｉ３Ｎｎ の両相共、数μｍの微粒子
から成る微細＆ＩＮ織を示していた。また、第２図及び
第３図にＺｒＯ□（ＹｚＯｓ）の添加量を各種変えたと
きのＳｉ３Ｎａ−ＺｒＯｘ（ＹｚＯｉ）複合セラミック
ス材料のピンカース硬度Ｈ１と破壊靭性値ＫＩＣを示す
、（焼結条件は１８００℃×３０分、ホットプレス焼結
である。）両図かられかるように。FIG. 1 shows a photograph of the polished surface of a m-weave prepared by hot-press sintering with 50% by volume of Si3N4 added thereto, observed with a scanning electron microscope. As can be seen from the figure, both the ZrO□ and 5i3Nn phases containing YtOs as a solid solution exhibited a fine &IN weave consisting of fine particles of several μm. In addition, Figures 2 and 3 show the Pinkers hardness H1 and fracture toughness value KIC of Si3Na-ZrOx (YzOi) composite ceramic materials when the amount of ZrO□ (YzOs) added is varied (the sintering conditions are (Hot press sintering at 1800°C for 30 minutes.) As can be seen from both figures.
Ｈｖ及びＫＩＣ共、 Ｓｉ３Ｎｔ−５０体積％Ｚｒ０ｚ
（Ｙｚ（ｈ）付近で最高値を示し、特に優れた破壊靭性
を有していることがわかる。この原因として考えられる
のは次の３点である。すなわち。Both Hv and KIC, Si3Nt-50 volume% Zr0z
(It shows the highest value near Yz(h), and it can be seen that it has particularly excellent fracture toughness.The following three points are considered to be the cause of this.
＋ｔｌ Ｓ ｉ ３ Ｎ ａ とＺｒ０ｚの熱膨張率
の差により材料中に複雑な残留応力が存在する。A complex residual stress exists in the material due to the difference in thermal expansion coefficient between +tl S i 3 N a and Zr0z.
（２） 第４図に示す写真はこの実施例１のものをフ
ン酸によりＺｒ０ｚ相を溶出した組織を顕微鏡で観察し
たものであるが５図かられかるように均一に分散してい
る５ｉＪ４が焼結中に直径１μｍ。(2) The photograph shown in Fig. 4 is a microscopic observation of the structure of Example 1 in which the Zr0z phase was eluted with hydrochloric acid. 1 μm in diameter during sintering.
長さ１０μ−以上の高アスペクト比（アスペクト比−長
さ／径）の針状結晶粒になっている。They are acicular crystal grains with a length of 10 μm or more and a high aspect ratio (aspect ratio-length/diameter).
（３） 靭性の高いＺｒＯ□（Ｙｇ０３）を添加した
こと。(3) Addition of ZrO□ (Yg03), which has high toughness.
（実施例２）次に５ｉＪ４−ＺｒＪ系材料に八１．０．
を混合し、ポリカルボン酸系解膠剤を用いて湿式ボール
ミリングして材料調整を行なった実施例について説明す
る。この混合粉体を焼結して得られた組織は、前記（実
施例１）の場合と同様。(Example 2) Next, 81.0.
An example will be described in which the material was prepared by mixing and performing wet ball milling using a polycarboxylic acid peptizer. The structure obtained by sintering this mixed powder is the same as that in Example 1 above.
数８１０粒径から成る均一な微細分散組織であった。ま
た、 ＳｉＪ４−ＺｒＯｇ（Ｙｇ（ｈ）−ＡＩｇＯｚの
組成を変化させた場合のビッカース硬度ＨＶ、破壊靭性
値ＫＩＣをそれぞれ第５図、第６図に示す、第３図と第
６図を比較してわかるように、破壊靭性値ＫＩＣは実施
例１に比し実施例２の方が最高値で２ＭＰａｅ＋３４程
度の低下が生じるが、第２図と第５図を比較してわかる
ようにビッカース硬度Ｈ１の方は実施例１に比し実施例
２の方が２００弱の上昇を示す、さらにこのときの実施
例２の組成は３０体積％ＡｌｚＯｚ付近であり、実施例
１に比し高価なＳｉＪ４−ＺｒＯｔ（ＹｇＯｚ）を節約
できる特徴を有するものである。It had a uniform finely dispersed structure consisting of several 810 grains in size. In addition, the Vickers hardness HV and fracture toughness KIC when changing the composition of SiJ4-ZrOg (Yg(h)-AIgOz) are shown in Figures 5 and 6, respectively, and Figures 3 and 6 are compared. As can be seen, the fracture toughness value KIC of Example 2 is lower than that of Example 1 by about 2 MPae + 34 at the highest value, but as can be seen by comparing Figures 2 and 5, the Vickers hardness H1 shows an increase of slightly less than 200 in Example 2 compared to Example 1. Furthermore, the composition of Example 2 at this time is around 30% by volume AlzOz, which is more expensive than in Example 1. It has the feature of saving ZrOt (YgOz).
（発明の効果） この発明は以上詳述したようにして成り。(Effect of the invention) This invention is constructed as described above in detail.
ＳｉＪ＊−ＺｒＯｔ（ＹｉＯ３）系材料は優れた靭性を
有するので、従来のセラミックス工具では不可能であっ
た黒皮部の断続切削に使用が可能である。第７図にこの
発明による５ｉｘＮａ−１ｒＱｚ系セラミツクス材料を
用いた切削工具と、従来技術によるＳｉ、Ｎ４系セラミ
ツクス材料及びＡ１．０３−Ｔｉｅ系セラミックス材料
を用いた切削工具との、刃先欠損までの切削長さの実験
データを示す０図かられかるようにＳｉＪｌ−ＺｒＯｍ
系セラミックス材料による切削工具が最もすぐれている
。Since SiJ*-ZrOt (YiO3)-based materials have excellent toughness, they can be used for interrupted cutting of black scale parts, which was impossible with conventional ceramic tools. FIG. 7 shows the relationship between the cutting tool using the 5ixNa-1rQz ceramic material according to the present invention and the cutting tool using the Si, N4 ceramic material and A1.03-Tie ceramic material according to the prior art, up to cutting edge breakage. As can be seen from Figure 0 showing the experimental data of cutting length, SiJl-ZrOm
Cutting tools made of ceramic materials are the best.
また、第８図はこの発明による５ｉ３Ｎ４−ＺｒＯ□−
＾ｌｘ’ｓ系セラミックス材料による切削工具と。Moreover, FIG. 8 shows 5i3N4-ZrO□- according to the present invention.
^Lx's cutting tools made from ceramic materials.
従来技術による＾１，０＝−Ｔｉｅ系セラミックス材料
。^1,0=-Tie ceramic material according to conventional technology.
＾１□０．系セラミックス材料及び超硬合金ＰＴＯ材料
による切削工具の切削速度に対する切削寿命の実験デー
タを示す。図かられかるように５ｉ３Ｎ４−ＺｒＯｔ−
Ａｌ□０．系セラミックス材料による切削工具が最も便
れている。さらにＳｌ、Ｎａ−Ｚｒ０ｚ−Ａｌ□Ｏ１系
セラミックス材料は、！ロウ０．含存星に相当する高価
な５１３Ｎａ−ＺｒＯ□を節約できるので、安価で長寿
命の工具材料が得られるという大きい効果を奏するもの
である。＾１□0． 2 shows experimental data on cutting life versus cutting speed of cutting tools made of PTO-based ceramic materials and cemented carbide PTO materials. As shown in the figure, 5i3N4-ZrOt-
Al□0. Cutting tools made of ceramic materials are the most convenient. Furthermore, Sl, Na-Zr0z-Al□O1-based ceramic materials are! Row 0. Since the expensive 513Na-ZrO□, which corresponds to the contained stars, can be saved, this has the great effect of providing a tool material that is inexpensive and has a long life.
第１図はこの発明の一実施例のものの組織研群面をＳＥ
Ｘ観察した写真、第２図及び第３図はそれぞれ、この発
明によるＳＩ３Ｎｍ−ＺｒＯｘ（ＹｉＯ３）複合セラミ
ックス材料において、 Ｚｒ０ｘ（ＹｘＯｓ）添加量を
各種変えたときのビッカース硬度Ｈｗ及び破壊靭性４Ｉ
！に＋Ｃの実験データを示すグラフであり、第４図は実
施例１のものをフン酸によりＺｒＪ相を溶出した組織の
顕微鏡写真、第５図及び第６図はそれぞれ、この発明に
よる５ｉＪｎ−ＺｒＯｘ（Ｙｚ（ｈ）−Ａ１ｘＯｓ複合
セラミンクス材において。
各成分組成を変えたときのビッカース硬度Ｈｖ及び破壊
靭性値ＫＩＣの実験データを示すグラフ。
第７図はこの発明によるＳＩＪ＊−ＺｒＯ，系セラミッ
クス材料を用いた切削工具と、従来技術によるセラミッ
クス材料を用いた切削工具との、切削長さの比較実験デ
ータを示すグラフ、第８図はこの発明による５ｉＪａ−
ＺｒＯｚ−ＡｌｘＯｔ系セラミックス材料を用いた切削
工具と、従来技術によるセラミックス材料を用いた切削
工具との、切削寿命の比較実験データを示すグラフであ
る。
特許出願人 株式会社小松製作所
代理人 （弁理士）松 澤 統
第１図
第２図
５１３Ｎ４２０ ４０ ６０ ８０ ｚ、ｑ、（ｙ２０
３）イトオ禽・ム
第３図
第４図
ｉＩ ５ 図
第６図
切斉・濤命（ｍｉｎ）
第８図
手続補正書
昭和６２年１１月２Ｇ 日Figure 1 shows an SE view of the structure of one embodiment of this invention.
The X-observed photographs, Figures 2 and 3 respectively show the Vickers hardness Hw and fracture toughness 4I when the amount of ZrOx (YxOs) added was varied in the SI3Nm-ZrOx (YiO3) composite ceramic material according to the present invention.
! FIG. 4 is a micrograph of the structure of Example 1 in which the ZrJ phase was eluted with hydrochloric acid, and FIGS. 5 and 6 are graphs showing the experimental data of 5iJn-ZrOx according to the present invention. (In Yz(h)-A1xOs composite ceramic material. Graph showing experimental data of Vickers hardness Hv and fracture toughness value KIC when each component composition is changed. Figure 7 shows the SIJ*-ZrO, ceramic material according to the present invention. Figure 8 is a graph showing comparative experimental data on cutting length between a cutting tool using 5iJa according to the present invention and a cutting tool using ceramic material according to the prior art.
1 is a graph showing comparison experimental data of cutting life between a cutting tool using a ZrOz-AlxOt-based ceramic material and a cutting tool using a conventional ceramic material. Patent Applicant Komatsu Ltd. Representative (Patent Attorney) Osamu Matsuzawa Figure 1 Figure 2 513N420 40 60 80 z, q, (y20
3) Ito Toki・Mu Figure 3 Figure 4 iI 5 Figure 6 Kirisai・Tomei (min) Figure 8 Procedural amendment November 2G, 1988
Claims (2)
、平均粒子径が０．１〜２μｍから成る微細部分安定化
ＺｒＯ＿２を３０〜７０体積％の範囲で、Ｓｉ＿３Ｎ＿
４の母相に均一分散させ、加圧焼結したことを特徴とす
る複合セラミックス材料。(1) Finely stabilized ZrO_2 consisting of 2.0 to 5.0 mol% of Y_2O_3 and having an average particle size of 0.1 to 2 μm is added to Si_3N_ in a range of 30 to 70 volume %.
A composite ceramic material characterized by being uniformly dispersed in the matrix of No. 4 and sintered under pressure.
＿３を２０〜６０体積％の範囲で、有していることを特
徴とする特許請求の範囲第１項記載の複合セラミックス
材料。(2) Al_2O with an average particle diameter of 0.1 to 2 μm
The composite ceramic material according to claim 1, characterized in that it contains _3 in a range of 20 to 60% by volume.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62083924A JPS63252965A (en) | 1987-04-07 | 1987-04-07 | Arsenic nitride zirconia base composite ceramic material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62083924A JPS63252965A (en) | 1987-04-07 | 1987-04-07 | Arsenic nitride zirconia base composite ceramic material |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS63252965A true JPS63252965A (en) | 1988-10-20 |
Family
ID=13816148
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP62083924A Pending JPS63252965A (en) | 1987-04-07 | 1987-04-07 | Arsenic nitride zirconia base composite ceramic material |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS63252965A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5266404A (en) * | 1990-07-19 | 1993-11-30 | Tioxide Group Services Limited | Non-oxide ceramic particles coated with zirconium oxide or hydrous oxide |
| WO2017203738A1 (en) * | 2016-05-27 | 2017-11-30 | 住友電気工業株式会社 | Sintered body and cutting tool containing same |
| WO2018074017A1 (en) * | 2016-10-17 | 2018-04-26 | 住友電気工業株式会社 | Sintered body and cutting tool including same |
-
1987
- 1987-04-07 JP JP62083924A patent/JPS63252965A/en active Pending
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5266404A (en) * | 1990-07-19 | 1993-11-30 | Tioxide Group Services Limited | Non-oxide ceramic particles coated with zirconium oxide or hydrous oxide |
| WO2017203738A1 (en) * | 2016-05-27 | 2017-11-30 | 住友電気工業株式会社 | Sintered body and cutting tool containing same |
| CN107922274A (en) * | 2016-05-27 | 2018-04-17 | 住友电气工业株式会社 | Sintered material and cutting tool comprising said sintered material |
| JPWO2017203738A1 (en) * | 2016-05-27 | 2019-04-18 | 住友電気工業株式会社 | Sintered body and cutting tool containing the same |
| US10532951B2 (en) | 2016-05-27 | 2020-01-14 | Sumitomo Electric Industries, Ltd. | Sintered material and cutting tool including same |
| WO2018074017A1 (en) * | 2016-10-17 | 2018-04-26 | 住友電気工業株式会社 | Sintered body and cutting tool including same |
| JPWO2018074017A1 (en) * | 2016-10-17 | 2019-08-08 | 住友電気工業株式会社 | Sintered body and cutting tool including the same |
| US12070802B2 (en) | 2016-10-17 | 2024-08-27 | Sumitomo Electric Industries, Ltd. | Sintered material and cutting tool including same |
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